WO2001053198A1 - Preparation of lithium-containing materials - Google Patents

Preparation of lithium-containing materials Download PDF

Info

Publication number
WO2001053198A1
WO2001053198A1 PCT/US2000/035438 US0035438W WO0153198A1 WO 2001053198 A1 WO2001053198 A1 WO 2001053198A1 US 0035438 W US0035438 W US 0035438W WO 0153198 A1 WO0153198 A1 WO 0153198A1
Authority
WO
WIPO (PCT)
Prior art keywords
lithium
metal
compound
starting materials
phosphate
Prior art date
Application number
PCT/US2000/035438
Other languages
French (fr)
Inventor
Jeremy Barker
M. Yazid Saidi
Jeffrey L. Swoyer
Original Assignee
Valence Technology, Inc.
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Family has litigation
First worldwide family litigation filed litigation Critical https://patents.darts-ip.com/?family=23926183&utm_source=google_patent&utm_medium=platform_link&utm_campaign=public_patent_search&patent=WO2001053198(A1) "Global patent litigation dataset” by Darts-ip is licensed under a Creative Commons Attribution 4.0 International License.
Application filed by Valence Technology, Inc. filed Critical Valence Technology, Inc.
Priority to EP00989532A priority Critical patent/EP1252093B1/en
Priority to DK00989532T priority patent/DK1252093T3/en
Priority to DE60013909T priority patent/DE60013909T2/en
Priority to AT00989532T priority patent/ATE276200T1/en
Priority to AU2001226030A priority patent/AU2001226030A1/en
Priority to KR20027009266A priority patent/KR100539341B1/en
Priority to CA002395115A priority patent/CA2395115C/en
Priority to JP2001553213A priority patent/JP3933470B2/en
Publication of WO2001053198A1 publication Critical patent/WO2001053198A1/en
Priority to HK03102844A priority patent/HK1051174A1/en

Links

Classifications

    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/36—Selection of substances as active materials, active masses, active liquids
    • H01M4/58—Selection of substances as active materials, active masses, active liquids of inorganic compounds other than oxides or hydroxides, e.g. sulfides, selenides, tellurides, halogenides or LiCoFy; of polyanionic structures, e.g. phosphates, silicates or borates
    • H01M4/5825—Oxygenated metallic salts or polyanionic structures, e.g. borates, phosphates, silicates, olivines
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01D—COMPOUNDS OF ALKALI METALS, i.e. LITHIUM, SODIUM, POTASSIUM, RUBIDIUM, CAESIUM, OR FRANCIUM
    • C01D15/00—Lithium compounds
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
    • C01B25/00—Phosphorus; Compounds thereof
    • C01B25/16—Oxyacids of phosphorus; Salts thereof
    • C01B25/26—Phosphates
    • C01B25/37—Phosphates of heavy metals
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01B—NON-METALLIC ELEMENTS; COMPOUNDS THEREOF; METALLOIDS OR COMPOUNDS THEREOF NOT COVERED BY SUBCLASS C01C
    • C01B25/00—Phosphorus; Compounds thereof
    • C01B25/16—Oxyacids of phosphorus; Salts thereof
    • C01B25/26—Phosphates
    • C01B25/45—Phosphates containing plural metal, or metal and ammonium
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
    • C01G21/00—Compounds of lead
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
    • C01G31/00—Compounds of vanadium
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
    • C01G39/00—Compounds of molybdenum
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M10/00—Secondary cells; Manufacture thereof
    • H01M10/05—Accumulators with non-aqueous electrolyte
    • H01M10/052—Li-accumulators
    • H01M10/0525—Rocking-chair batteries, i.e. batteries with lithium insertion or intercalation in both electrodes; Lithium-ion batteries
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
    • H01M4/131—Electrodes based on mixed oxides or hydroxides, or on mixtures of oxides or hydroxides, e.g. LiCoOx
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
    • H01M4/136—Electrodes based on inorganic compounds other than oxides or hydroxides, e.g. sulfides, selenides, tellurides, halogenides or LiCoFy
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
    • H01M4/139—Processes of manufacture
    • H01M4/1391—Processes of manufacture of electrodes based on mixed oxides or hydroxides, or on mixtures of oxides or hydroxides, e.g. LiCoOx
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
    • H01M4/139—Processes of manufacture
    • H01M4/1397—Processes of manufacture of electrodes based on inorganic compounds other than oxides or hydroxides, e.g. sulfides, selenides, tellurides, halogenides or LiCoFy
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/36—Selection of substances as active materials, active masses, active liquids
    • H01M4/48—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides
    • H01M4/485—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of mixed oxides or hydroxides for inserting or intercalating light metals, e.g. LiTi2O4 or LiTi2OxFy
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/36—Selection of substances as active materials, active masses, active liquids
    • H01M4/48—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides
    • H01M4/50—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of manganese
    • H01M4/505—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of manganese of mixed oxides or hydroxides containing manganese for inserting or intercalating light metals, e.g. LiMn2O4 or LiMn2OxFy
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/36—Selection of substances as active materials, active masses, active liquids
    • H01M4/48—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides
    • H01M4/52—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of nickel, cobalt or iron
    • H01M4/525—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of nickel, cobalt or iron of mixed oxides or hydroxides containing iron, cobalt or nickel for inserting or intercalating light metals, e.g. LiNiO2, LiCoO2 or LiCoOxFy
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01F—COMPOUNDS OF THE METALS BERYLLIUM, MAGNESIUM, ALUMINIUM, CALCIUM, STRONTIUM, BARIUM, RADIUM, THORIUM, OR OF THE RARE-EARTH METALS
    • C01F5/00—Compounds of magnesium
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
    • C01G31/00—Compounds of vanadium
    • C01G31/006—Compounds containing, besides vanadium, two or more other elements, with the exception of oxygen or hydrogen
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
    • C01G49/00—Compounds of iron
    • C01G49/009—Compounds containing, besides iron, two or more other elements, with the exception of oxygen or hydrogen
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
    • C01P2002/00—Crystal-structural characteristics
    • C01P2002/70—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data
    • C—CHEMISTRY; METALLURGY
    • C01—INORGANIC CHEMISTRY
    • C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
    • C01P2006/00—Physical properties of inorganic compounds
    • C01P2006/40—Electric properties
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M10/00—Secondary cells; Manufacture thereof
    • H01M10/05—Accumulators with non-aqueous electrolyte
    • H01M10/052—Li-accumulators
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M10/00—Secondary cells; Manufacture thereof
    • H01M10/05—Accumulators with non-aqueous electrolyte
    • H01M10/056—Accumulators with non-aqueous electrolyte characterised by the materials used as electrolytes, e.g. mixed inorganic/organic electrolytes
    • H01M10/0564—Accumulators with non-aqueous electrolyte characterised by the materials used as electrolytes, e.g. mixed inorganic/organic electrolytes the electrolyte being constituted of organic materials only
    • H01M10/0566—Liquid materials
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/02—Electrodes composed of, or comprising, active material
    • H01M4/36—Selection of substances as active materials, active masses, active liquids
    • H01M4/58—Selection of substances as active materials, active masses, active liquids of inorganic compounds other than oxides or hydroxides, e.g. sulfides, selenides, tellurides, halogenides or LiCoFy; of polyanionic structures, e.g. phosphates, silicates or borates
    • H01M4/582—Halogenides
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M6/00—Primary cells; Manufacture thereof
    • H01M6/40—Printed batteries, e.g. thin film batteries
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
    • Y02E60/10—Energy storage using batteries
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T156/00—Adhesive bonding and miscellaneous chemical manufacture
    • Y10T156/10—Methods of surface bonding and/or assembly therefor
    • Y10T156/1002—Methods of surface bonding and/or assembly therefor with permanent bending or reshaping or surface deformation of self sustaining lamina
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T29/00—Metal working
    • Y10T29/10—Battery-grid making

Definitions

  • This invention relates, to improved materials usable as electrode active materials and to their preparation.
  • Lithium batteries are prepared from one or more lithium electrochemical cells containing electrochemically active (electroactive) materials. Such cells typically include an anode (negative electrode) , a cathode (positive electrode) , and an electrolyte interposed between spaced apart positive and negative electrodes. Batteries with anodes of metallic lithium and containing metal chalcogenide cathode active material are known.
  • the electrolyte typically comprises a salt of lithium dissolved in one or more solvents, typically nonaqueous (aprotic) organic solvents.
  • electrolytes are solid electrolytes typically called polymeric matrixes that contain an ionic conductive medium, typically a metallic powder or salt, in combination with a polymer that itself may be ionically conductive which is electrically insulating.
  • an ionic conductive medium typically a metallic powder or salt
  • the negative electrode of the cell is defined as the anode.
  • Cells having a metallic lithium anode and metal chalcogenide cathode are charged in an initial condition.
  • lithium ions from the metallic anode pass through the liquid electrolyte to the electrochemical active (electroactive) material of the cathode whereupon they release electrical energy to an external circuit.
  • Preferred positive electrode active materials include LiCo0 2 , LiMn 2 0 4 , and LiNi0 2 .
  • a relatively economical positive electrode is LiMn 2 0 4 , for which methods of synthesis are known.
  • NiNi0 2 nickel oxide all have a common disadvantage in that the charge capacity of a cell comprising such cathodes suffers a significant loss in capacity. That is, the initial capacity available (amp hours/gram) from LiMn 2 0 4 , LiNi0 2 , and LiCo0 2 is less than the theoretical capacity because significantly less than 1 atomic unit of lithium engages in the electrochemical reaction. Such an initial capacity value is significantly diminished during the first cycle operation and such capacity further diminishes on every successive cycle of operation. For LiNi0 2 and LiCo0 2 only about 0.5 atomic units of lithium is reversibly cycled during cell operation. Many attempts have been made to reduce capacity fading, for example, as described in U.S. Patent No.
  • the invention provides novel lithium-mixed metal materials which, upon electrochemical interaction, release lithium ions, and are capable of reversibly cycling lithium ions .
  • the invention provides a rechargeable lithium battery which comprises an electrode formed from the novel lithium-mixed metal materials. Methods for making the novel lithium-mixed metal materials and methods for using such lithium-mixed metal materials in electrochemical cells are also provided.
  • the lithium-mixed metal materials comprise lithium and at least one other metal besides lithium.
  • Preferred materials are lithium-mixed metal phosphates whic contain lithium and two other metals besides lithium.
  • the invention provides a rechargeable lithium battery which comprises an electrolyte; a first electrode having a compatible active material; and a second electrode comprising the novel materials.
  • the novel materials are lithium-mixed metal phosphates ' which preferably used as a positive electrode active material, reversibly cycle lithium ions with the compatible negative electrode active material.
  • the lithium-mixed metal phosphate' is represented by the nominal general formula Li a MI b MII c (P0 4 ) d .
  • Such compounds include Li 1 MI a MII b P0 4 and Li 3 MI a MII b (P0 4 ) 3 ; therefore, in an initial condition 0 ⁇ a ⁇ l or 0 ⁇ a ⁇ 3, respectively.
  • x quantity of lithium is released where 0 ⁇ x ⁇ a.
  • the sum of b plus c is up to about 2.
  • Specific examples are Li 1 MI 1 _ y MII y P0 4 and Li 3 MI 2 _ y MII y (P0 4 ) 3 .
  • MI and Mil are the same. In a preferred aspect, MI and Mil are different from one another. At least one of Ml and Mil is an element capable of an oxidation state higher than that initially present in the lithium-mixed metal phosphate compound. Correspondingly, at least one of MI and Mil has more than one oxidation state in the phosphate compound, and more than one oxidation State above the ground state M°.
  • oxidation state and valence state are used in the art interchangeably.
  • both MI and Mil may have more than one oxidation state and both may be oxidizable from the state initially present in the phosphate compound.
  • Mil is a metal or semi-metal having a +2 oxidation state, and is selected from Groups 2, 12 and 14 of the Periodic Table.
  • Mil is selected from non-transition metals and semi-metals.
  • Mil has only one oxidation state and is nonoxidizable from its oxidation state in the lithium- mixed metal compound.
  • Mil has more than one oxidation state. Examples of semi-metals having more than one oxidation state are selenium and tellurium; other non-transition metals with more than one oxidation state are tin and lead.
  • Mil is selected from Mg (magnesium) , Ca (calcium) , Zn (zinc) , Sr (strontium) , Pb (lead) , Cd (cadmium) , Sn (tin) , Ba (barium), and Be (beryllium), and mixtures thereof.
  • Mil is a metal having a +2 oxidation state and having more than one oxidation state, and is oxidizable from its oxidation state in lithium- mixed metal compound.
  • Ml is selected from Fe (iron) , Co
  • Ml is preferably selected from the first row of transition metals and further includes tin, and Ml preferably initially has a +2 oxidation state.
  • the product LiMI 1 _ y MII y P0 4 is an olivine structure and the product (P0 4 ) 3 is a rhombohedral or monoclinic Nasicon structure.
  • the term "nominal formula" refers to the fact that the relative proportion of atomic species may vary slightly on the order of 2 percent to 5 percent, or more typically, 1 percent to 3 percent.
  • any portion of P (phosphorous) may be substituted by Si (silicon) , S (sulfur) , and/or As (arsenic) ; and any portion of 0 (oxygen) may be substituted by halogen, preferably F (fluorine) .
  • the metal phosphates are alternatively represented by the nominal general formulas such as Li 1 _ x MI 1 _ y MII y P0 4 (0 ⁇ x ⁇ 1), and Li 3 _ x MI 2 _ y MII y (P0 4 ) 3 signifying capability to release and reinsert lithium.
  • the term "general" refers to a family of compounds, with M, x and y representing variations therein.
  • the expressions 2-y and 1-y each signify that the relative amount of MI and Mil may vary.
  • MI may be a mixture of metals meeting the earlier stated criteria for MI.
  • Mil may be a ' mixture of metallic elements meeting the stated criteria for Mil.
  • each such metal- and metallic element has a +2 oxidation state in the initial phosphate compound.
  • the active material of the counter electrode is any material compatible with the lithium-mixed metal phosphate of the invention.
  • metallic lithium, lithium-containing material,- or non-lithium-containing material may be used as the negative electrode active material.
  • the negative electrode is desirably a nonmetallic insertion material.
  • the negative electrode comprises an active material from the group consisting of metal oxide, particularly transition metal oxide, metal chalcogenide, carbon, graphite, and mixtures thereof. It is preferred that the anode active material comprises a carbonaceous material such as graphite.
  • the lithium-mixed metal phosphate of the invention may also be used as a negative electrode material.
  • the present invention provides a method of preparing a compound of the nominal general formula Li a MI b MII c (P0 4 ) d where 0 ⁇ a ⁇ 3; the sum of b plus c is greater than zero and up to about 2;, and 0 ⁇ d ⁇ 3.
  • Preferred compounds include Li 3 MI b MII c (P0 4 ) 3 where b plus c is about 2; and LiMI b MII c P0 4 where b plus c is about 1.
  • the method comprises providing starting materials in particle form.
  • the starting- (precursor) materials include a lithium-containing compound, one or more metal containing compounds, a compound capable of providing the phosphate (P0 4 ) -3 anion, and carbon.
  • the lithium-containing compound is in particle form, and an example is lithium salt.
  • the phosphate-containing anion compound is in particle form, and examples include metal phosphate salt and diammonium hydrogen phosphate (DAHP) and ammonium dihydrogen phosphate (ADHP) .
  • the lithium compound, one or more metal compounds, and phosphate compound are included in a proportion which provides the stated nominal general formula.
  • the starting materials are mixed together with carbon, which is included in an amount sufficient to reduce the metal ion of one or more of the metal-containing starting materials without full, reduction to an elemental metal state. Excess quantities of carbon and one or more other starting materials (i.e., 5 to 10% excess) may be used to enhance product quality.
  • the carbon present during compound formation is thought to be intimately dispersed throughout the precursor and product. This provides many ⁇ advantages, including the enhanced, conductivity of the product.
  • the presence of carbon particles in the starting materials is also thought to provide nucleation sites for the production of the product crystals.
  • the starting materials are intimately mixed and then reacted together where the reaction is initiated by heat and is preferably conducted in a nonoxidizing, inert atmosphere, whereby the lithium, metal from the metal compound (s), and phosphate combine to form the Li a MI b MII c (P0 4 ) d product.
  • the particles are intermingled to form an essentially homogeneous powder mixture of the precursors.
  • the precursor powders are dry-mixed using a ball mill, such as zirconia media. Then the mixed powders are pressed into pellets.
  • the precursor powders are mixed with a binder. The binder is selected so as to not inhibit reaction between particles of the . powders.
  • preferred binders decompose or evaporate at a temperature less than the reaction temperature.
  • examples include mineral oils (i.e., glycerol, or C-18 hydrocarbon mineral .oil) and polymers which decompose (carbonize) to form a carbon residue ⁇ before the reaction starts, or which evaporate before the reaction starts.
  • intermingling is conducted ' by forming a wet mixture using a volatile solvent and then the intermingled particles are pressed together -in pellet form to provide good grain-to-grain contact.
  • the precursor compounds be present in a proportion which provides the stated general formula of the .product
  • the lithium compound may be present in an excess amount .on the order of 5 percent excess lithium compared to a stoichiometric mixture of the precursors.
  • the carbon may be present at up to 100% excess compared to the stoichiometric amount.
  • the method of the invention may also be used to prepare other novel products, and to prepare known products..
  • lithium compounds are available as precursors, such as lithium acetate (LiOOCCH 3 ) , lithium hydroxide, lithium nitrate (LiN0 3 ) , lithium oxalate (Li 2 C 2 0 4 ) , lithium oxide ⁇ (Li 2 0) , lithium phosphate (Li 3 P0 4 ) , lithium dihydrogen phosphate (LiH 2 P0 4 ) , lithium vanadate (LiV0 3 ) , and lithium carbonate (Li 2 C0 3 ), .
  • the lithium carbonate is preferred for the solid state reaction since it has a very high melting point and commonly reacts with the other precursors before melting.
  • Lithium carbonate has a melting point over 600°C and it decomposes in the presence of the other precursors and/or effectively reacts with the other precursors before melting.
  • lithium hydroxide melts at about 400°C. At some reaction temperatures preferred herein of over 450°C the lithium hydroxide will melt before any significant reaction with the other precursors occurs to an effective extent. This melting renders the reaction very difficult to control.
  • anhydrous LiOH is highly hygroscopic and a significant quantity of. water is released during the reaction. Such water needs to be removed from the oven and the resultant product may need to be dried.
  • the solid state reaction made possible by the present invention is much preferred since it is conducted at temperatures at which the lithium-containing compound reacts with the other reactants before melting. Therefore, lithium hydroxide is useable as a precursor in the method of the invention in combination with some precursors, particularly the phosphates.
  • the method of the invention is able to be conducted as an economical carbothermal-based process with a wide variety of precursors and over a relatively broad temperature range.
  • the aforesaid precursor compounds are generally crystals, granules, and powders and are generally referred to as being in particle form.
  • phosphate salts diammoniu hydrogen phosphate (NH 4 ) 2 HP0 4 (DAHP) or ammonium dihydrogen phosphate (NH 4 )H,P0 4 (ADHP) .
  • ADHP and DAHP meet the preferred criteria that the precursors decompose in the presence of one another or react with one another before melting of such precursor.
  • Exemplary metal compounds are Fe 2 0 3 , Fe 3 0 4 ,- V 2 0 5 , V0 2 , LiV0 3 ', NH 4 V0 3 , Mg(OH) 2 , Cao, MgO, Ca(OH) 2 , Mn0 2 , Mn 2 0 3 , Mn 3 (P0 4 ) 2 , CuO, SnO, Sn0 2 , Ti0 2 , Ti 2 0 3 , Cr 2 0 3 , Pb0 2 , PbO, Ba(OH) 2 , BaO, Cd(OH) 2 .
  • starting materials serve as both the source of metal ion and phosphate, such as FeP0 4 , Fe 3 (PQ 4 ) 2 , Zn 3 (P0 4 ) 2 , and Mg 3 (P0 4 ) 2 . Still others contain both lithium ion and phosphate such as Li 3 P0 4 and LiH 2 P0 4 .
  • Other exemplary precursors are H 3 P0 4 (phosphoric acid) ; and P 2 0 5 (PO 10 ) phosphoric oxide; and HP0 3 meta phosphoric acid, which is a decomposition product of P 2 0 5 .
  • the starting materials further include a fluorine compound such as LiF.
  • the starting materials further include silicon oxide (Si0 2 ) .
  • ammonium sulfate in the starting materials is useable to replace phosphorus with sulfur.
  • Vanadium pentoxide of the formula V 2 0 5 is obtainable from any number of suppliers including Kerr McGee, Johnson
  • Vanadium pentoxide has a CAS number of 1314-62-1.
  • Iron oxide Fe 3 0 3 is a common and very inexpensive material available in powder form from the ' same suppliers. The other precursor materials mentioned above are also available from well known suppliers, such as those listed above .
  • the method of the invention may also be used to react starting materials in the presence of carbon to form a variety of other novel products, such as gamma- LiV 2 0 5 and also to produce known products.
  • the carbon functions to reduce metal ion of a starting metal compound to provide a product containing such reduced metal ion.
  • the method is particularly useful to also add lithium to the resultant product, which thus contains the metallic element ions, namely, the lithium ion and the other metal ion, thereby forming a mixed metal product.
  • An example is the reaction of vanadium pentoxide (V 2 0 5 ) with lithium carbonate in the presence of carbon to form gamma-LiV 2 0 5 .
  • V 2 0 5 vanadium pentoxide
  • V +S V +5 is reduced to V +4 V +5 in the final product.
  • a single phase gamma-LiV 2 0 5 product is not known to .have been directly and independently formed before.
  • the reaction it is desirable to conduct the reaction at a temperature where the lithium compound reacts before melting.
  • the temperature should be about 400°C or greater, and desirably 450°C or greater, and preferably 500°C or greater, and generally will proceed at a faster rate at higher temperatures.
  • the various reactions involve production of CO or C0 2 as an effluent gas.
  • the equilibrium at higher temperature favors CO formation.
  • Some of the reactions are more desirably conducted at temperatures greater than 600°C; most desirably greater than 650°C; preferably 700°C or greater; more preferably 750°C or greater. Suitable ranges for many reactions are about 700 to 950°C, or about 700 to 800°C.
  • the higher temperature reactions produce CO effluent and the stoichiometry requires more carbon be used than the case where C0 2 effluent is produced at lower temperature. This is because the reducing effect of the C to C0 2 reaction is greater than the C. to CO reaction.
  • the C to C0 2 reaction involves an increase in carbon oxidation state of +4 (from 0 to ' 4) and the C to CO reaction involves an increase in carbon oxidation state of +2 (from ground state zero to 2) .
  • higher temperature generally refers to a range of about 650°C to about 1000°C and lower temperature refers to up to about 650°C. Temperatures higher than 1200°C are not thought to be needed.
  • the method of the invention utilizes the reducing capabilities of carbon in a unique and controlled manner to produce desired products having structure and lithium content suitable for electrode active materials.
  • the method of the invention makes it possible to produce products containing lithium, metal and oxygen in an economical and convenient process.
  • the ability to lithiate precursors, and change the oxidation " state of a metal without causing abstraction of oxygen from a precursor is heretofore unexpected.
  • These advantages are at least in part achieved by the reductant, carbon, having an oxide whose free energy of formation becomes more negative as temperature increases. Such oxide of carbon is more stable at high temperature than at low temperature. This feature is used to produce products having one or more metal ions in a reduced oxidation state relative to the precursor metal ion ⁇ oxidation state.
  • the method utilizes an effective- combination of quantity ,of carbon, time and temperature to produce new products and to produce known products in a hew way.
  • temperature at about 700°C both the carbon to carbon monoxide and the carbon to carbon dioxide reactions are occurring.
  • C to C0 2 reaction is 5 the dominant reaction.
  • C to CO reaction is dominant. Since the reducing effect of the C to C0 2 reaction is greater, the result is that less carbon is needed per atomic unit of metal to be reduced. In the case of carbon to carbon monoxide, each atomic
  • the starting materials it is preferred to heat the starting materials at a ramp rate of a fraction of a degree to 10°C per minute and preferably about 2°C per minute.
  • starting materials are held at the reaction temperature for several hours.
  • the heating is preferably conducted .under non-oxidizing or inert gas such as argon or vacuum.
  • a reducing atmosphere is not required, although it may be used if desired.
  • the cooling occurs at a rate similar to the earlier ramp rate, and preferably 2°C/minute cooling.
  • Such cooling rate has been found to be adequate to achieve the desired structure of the final product. It is also possible to quench the products at a cooling rate on the order of about 100°C/minute. In some instances, ⁇ such rapid cooling (quench) may be preferred.
  • the present invention resolves the capacity problem posed by widely used cathode active material. It has been found that the capacity and capacity retention of cells having the preferred active material of the invention are " improved over conventional materials.
  • Optimized cells containing lithium-mixed metal phosphates, of the invention potentially have performance improved over commonly used lithium metal oxide compounds. • • Advantageously, the new method of making the novel lithium-mixed metal phosphate compounds of the invention is relatively economical and readily adaptable to commercial production.
  • Objects, features, and advantages of the invention include an electrochemical cell or battery based on lithium-mixed metal phosphates. Another object is to provide an electrode active material which combines the advantages of good discharge capacity and capacity retention. It is also an object of the present invention to provide electrodes which can be manufactured economically. Another object is to provide a method for forming electrode active- material which lends itself to commercial scale production for preparation of large quantities.
  • Figure 2 is a voltage/capacity plot of LiFeP0 4 - containing cathode cycled with a lithium metal anode using constant current cycling at ⁇ 0.2 milliamps per square centimeter in a range of 2.5 to 4.0 volts at a temperature of about 23°C.
  • the cathode contained 19.0mg of the LiFeP0 4 active material, prepared by the method of the invention.
  • the electrolyte comprised ethylene carbonate (EC) and dimethyl carbonate (DMC) in a weight ratio of 2:1 and included a 1 molar concentration of LiPF 5 salt.
  • EC ethylene carbonate
  • DMC dimethyl carbonate
  • the lithium-metal-phosphate containing electrode and the lithium metal counter electrode are maintained spaced apart by a glass fiber separator which is interpenetrated by the solvent and the salt.
  • Figure 3 shows multiple constant current cycling of LiFeP0 4 active material cycled with a lithium metal anode using the electrolyte as described in connection with Figure 2 and cycled, charge and discharge at ⁇ 0.2 milliamps per square centimeter, 2.5 to 4.0 . volts at two different temperature conditions, 23°C and 60°C.
  • Figure 3 shows the excellent rechargeability of the lithium iron phosphate/lithium metal cell, and also shows the excellent cycling and specific capacity (mAh/g) of the active material.
  • Figure 5 is a voltage/capacity plot of LiFe 0 . 9 Mg 0 . 1 PO 4 -containing cathode cycled with a lithium metal anode using constant current cycling at ⁇ 0.2 milliamps per square centimeter in a range of 2.5 to 4 . 0 volts. Other conditions are as described earlier with respect to Figure 2.
  • the cathode contained 18.9mg of the iFe o . 9 Mg o .iPO 4 active material prepared by the method of- the invention.
  • Fi ure 6 shows multiple constant current cycling of LiFe o . 9 Mg o .iPO 4 cycled with a lithium metal anode using the electrolyte as described in connection ' with Figure 2 and cycled, charge and discharge at ⁇ 0.2 milliamps per square centimeter, 2.5 to 4.0 volts at two different temperature, conditions, 23°C and 60.°C.
  • Figure 6 shows the excellent rechargeability of the lithium- metal-phosphate/lithium metal cell, and also shows the excellent cycling and capacity of the cell.
  • Figure 7 is a voltage/capacity plot of LiFe 0 . 8 Mg 0 .
  • the cathode contained 16mg of' the LiFe 0 .. 8 Mg 0 . 2 PO 4 active material prepared by the method of the invention.
  • Figure 9 is a voltage/capacity plot of LiFe 0 . 8 Ca 0 . 2 P0 4 -containing cathode cycled with a lithium metal anode using constant current cycling at ⁇ 0.2 milliamps per square centimeter in a range of 2.5 to 4 ; 0 volts at 23°. Other conditions are as described earlier with respect to Figure 2.
  • the cathode contained 18.5mg of the LiFe 0 . 8 Ca 0 . 2 PO 4 active material prepared by the method of the invention.
  • Figure 10 is a voltage/capacity plot of LiFe 0 . 8 Zn 0 . 2 PO 4 -containing 'cathode cycled with a lithium metal anode using constant current cycling at ⁇ 0.2 milliamps per square centimeter in a- range of 2.5 to 4.0 ' volts at 23°C. Other conditions are as described earlier with respect to Figure 2.
  • the cathode contained 18.9mg of the LiFe 0 . 8 Zn 0 . 2 PO 4 active material prepared by the method of the invention.
  • Figure 12 is a voltage/capacity plot of gamma-
  • LiV- 2 0 5 -containing cathode cycled with a lithium metal anode using constant current cycling at ⁇ 0.2 milliamps per square centimeter in a range of 2.5 to 3.8 volts at 23°C. Other conditions are as described earlier with respect to Figure 2.
  • the cathode contained 21mg of the gamma-LiV 2 0 5 active material prepared by the method of the invention.
  • Figure 13 is a two-part graph based on multiple constant current cycling of gamma-LiV 2 0 5 cycled with a lithium metal anode using. the electrolyte as described in connection with Figure.2 and cycled, charge and discharge at ⁇ 0.2 milliamps per square centimeter, 2.5 to 3.8 volts.
  • Figure 13 shows the excellent rechargeability of the lithium-metal- oxide/lithium metal cell.
  • Figure 13 shows the excellent cycling and capacity of the cell.
  • Figure 14 shows the results of an x-ray diffraction analysis of the Li 3 V 2 (P0 4 ) 3 prepared according to the invention.
  • Figure 15 shows the results of an x-ray diffraction analysis of Li 3 V 2 (P0 4 ) 3 prepared according to 5 a method described in U.S. Patent No. 5,871,866.
  • the cathode material is 13.8mg of Li 3 V 2 (P0 4 ) 3 .
  • the cell includes a lithium metal counter
  • 1 . 5 electrode in an electrolyte comprising ethylene carbonate (EC) and dimethyl carbonate (DMC) in a weight ratio of 2:1 and including a 1 molar concentration of-LiPF 6 salt.
  • EC ethylene carbonate
  • DMC dimethyl carbonate
  • the conditions are. ⁇ 10 mV steps ' , between about 3.0 and 4.2 volts, and the critical limiting current density is less than or equal to 0.1 mA/cm 2 .
  • Figure 17 is an EVS differential capacity versus voltage plot for the cell as described in connection with Figure 16.
  • Figure 18 shows multiple constant current cycling of LiFe 0 . 8 Mg 0 . 2 PO 4 cycled with a lithium metal 30 anode using the electrolyte as described in connection with Figure 2 and cycled, charge and discharge at + 0.2 milliamps per square centimeter, 2.5 to 4.0 volts at two different temperature conditions, 23°C and 60°C.
  • Figure 18 shows the excellent rechargeability of the lithium- metal-phosphate/lithium metal cell, and also shows the excellent cycling and capacity of the cell.
  • Figure 19 is a graph of potential over time for the first four complete cycles of the LiMg o .iFe o . 9 PO 4 /MCMB graphite cell of the invention.
  • Figure 20 is a two-part graph based on multiple constant current cycling of LiFe 0 . 9 Mg 0 . ⁇ PO 4 cycled ith an MCMB graphite anode using the electrolyte as described in connection with Figure 2 and cycled, charge and discharge at + 0.2 milliamps per square centimeter, 2.5 to 3.6 volts, 23°C and based on a C/10 (10 hour) rate.
  • Figure 20 shows the excellent rechargeability of the lithium-metal-phosphate/graphite cell.
  • Figure 20 shows the excellent cycling and capacity of the cell.
  • Figure 21 is a graph of potential over time for the first three complete cycles of the gamma-LiV 2 0 5 /MCMB graphite cell of the invention.
  • Figure 22 is' a diagrammatic representation of a typical laminated lithium- ⁇ ion battery cell structure.
  • FIG. 23 is a diagrammatic representation of a typical multi-cell battery cell structure. Detailed Description of the Preferred Embodiments
  • the present invention provides lithium-mixed metal-phosphates, which are usable as electrode active materials, for lithium (Li + ) ion removal and insertion. Upon extraction of the lithium ions from the lithium- mixed-metal-phosphates, significant capacity is achieved,.
  • electrochemical energy is provided when combined with a suitable counter electrode by extraction of a quantity x of lithium from lithium- mixed-metal-phosphates Li a _ x MI b MII c (P0 4 ) d .
  • metal MI is oxidized.
  • metal Mil is also oxidized. Therefore, at least one of MI and Mil is oxidizable from its initial condition in the phosphate compound as Li is removed. .
  • LiFei_ y Sn y P0 4 has two oxidizable elements, Fe and Sn; in contrast, LiFe ⁇ _ y Mg y P0 4 has one oxidizable metal, the metal Fe . '
  • the invention provides a lithium ion battery which comprises an electrolyte; a negative electrode having an insertion active material; and a positive electrode comprising a lithium-mixed- metal-phosphate active material characterized by an ability to release lithium ions for insertion into the negative electrode active material.
  • the lithium-mixed- metal-phosphate is desirably represented by the. nominal general formula Li a MI b MII c (P0 4 ) d .
  • the metals MI and Mil may be the same, it is preferred that the metals MI and Mil are different.
  • MI is a metal selected from the group: Fe, Co, Ni, Mn, Cu, V, Sn, Ti, Cr and mixtures thereof, and MI is most desirably a transition metal or mixture thereof selected from said group. Most preferably, MI has a +2 valence or oxidation state.
  • Mil is selected from Mg, Ca, Zn, Sr, Pb, Cd, Sn, Ba, Be, and mixtures thereof. Most preferably, Mil has a +2 valence or- oxidation state.
  • the lithium-mixed-metal-phosphate is preferably a compound represented by the nominal general formula Li a _ x MI b MII c (P0 4 ) d , signifying the preferred composition and its capability to release x lithium. Accordingly, during cycling, charge and discharge, the value of x varies as x greater than or equal to 0 and less than or equal to a. - The present invention resolves a capacity problem posed by conventional cathode active materials.
  • the basic process comprises conducting a reaction between a lithium compound, preferably lithium carbonate (Li 2 C0 3 ) , metal compound(s), for example, vanadium pentoxide (V 2 0 5 ) , iron, oxide (Fe 2 0 3 ) , and/or manganese hydroxide, and a phosphoric acid derivative, preferably the phosphoric acid ammonium salt, diammonium hydrogen phosphate, (NH 4 ) 2 H (P0 4 ) .
  • a lithium compound preferably lithium carbonate (Li 2 C0 3 )
  • metal compound(s) for example, vanadium pentoxide (V 2 0 5 ) , iron, oxide (Fe 2 0 3 ) , and/or manganese hydroxide
  • a phosphoric acid derivative preferably the phosphoric acid ammonium salt, diammonium hydrogen phosphate, (NH 4 ) 2 H (P0 4 ) .
  • NH 4 ) 2 H (P0 4 )
  • Lithium-containing compounds include Li 2 0 (lithium oxide) , LiH 2 P0 4 (lithium hydrogen phosphate) , Li 2 C 2 0 4 (lithium oxalate) , LiOH (lithium hydroxide),
  • LiOH.H 2 0 lithium hydroxide monohydride
  • LiHC0 3 lithium hydrogen carbonate
  • the metal compounds (s) are reduced in the presence of the reducing agent, carbon.
  • the same considerations apply to other lithium-metal- and phosphate-containing precursors.
  • the thermodynamic considerations such as ease of reduction, of the selected precursors, the reaction kinetics, and the melting point of the salts will cause adjustment in the general procedure, such as, amount of carbon reducing agent/ and the temperature of reaction.
  • FIGS 1 through 21 show characterization data and capacity in actual use for the cathode materials (positive electrodes) of the invention. Some tests were conducted in a cell comprising a lithium metal counter electrode . (negative electrode) and other tests were conducted in cells having a carbonaceous counter electrode. All of the cells had an EC:DMC-LiPF 6 electrolyte.
  • test cells are often fabricated using lithium metal electrodes.
  • an insertion positive electrode as per the invention and a graphitic carbon negative electrode.
  • a typical laminated battery cell structure 10 is depicted in Figure 22. It comprises a negative electrode side 12, a positive electrode side 14, and an electrolyte/separator 16 there between. Negative electrode side, 12 includes current collector 18, and positive electrode side 14 includes current collector 22.
  • An electrolyte/separator film 16 membrane is preferably a plasticized copolymer. This electrolyte/separator preferably comprises a polymeric separator and a suitable electrolyte for ion transport.
  • the electrolyte/separator is positioned upon the electrode element and is- covered with -a positive electrode membrane '24 comprising a composition of a finely divided lithium insertion compound in a polymeric binder matrix.
  • An aluminum collector foil o grid 22 completes the assembly.
  • Protective bagging material 40 covers the cell and prevents infiltration of air and moisture.
  • a multi-cell battery configuration as per Figure 23 is prepared with copper current collector 51, negative electrode 53, electrolyte/separator 55, positive electrode 57, and aluminum current collector 59. Tabs 52 and 58 of the current collector elements form respective terminals for the battery structure.
  • the terms "cell” and “battery” refer to an individual cell comprising anode/electrolyte/cathode and also refer to a multi-cell arrangement in a stack.
  • the relative weight proportions of the components of the positive electrode are generally: 50- 90% by weight active material; 5-30% carbon black as the electric conductive diluent; and 3-20% binder chosen to . hold all particulate materials in contact with one another without degrading ionic conductivity. Stated ranges ' are not critical, and the amount of active material in an electrode may range from 25-95 weight percent.
  • the negative electrode comprises about 50-95% by weight of a preferred graphite, with the balance constituted by the binder.
  • a typical electrolyte separator film comprises approximately two parts polymer for every one part of a preferred fumed silica.
  • the conductive solvent comprises any number of suitable solvents and salts. Desirable solvents and salts are described in U.S. Patent Nos. 5,643,695 and 5,418,091. One example is a mixture of EC:DMC:LiPF 6 in a weight ratio of about 60:30:10.
  • Solvents are selected to be used individually or in mixtures, and include dimethyl carbonate (DMC) , diethylcarbonate (DEC) , dipropylcarbonate (DPC) , ethylmethylc ' arbonate (EMC) , ethylene carbonate (EC) , propylene carbonate (PC), butylene carbonate, lactones, esters, . glymes, sulfoxides, sulfolanes, etc.
  • the preferred solvents are EC/DMC, EC/DEC, EC/DPC and EC/EMC.
  • the salt content ranges from 5% to 65% by weight, ⁇ preferably from 8% to 35% by weight.
  • any number of methods are used to form films from the casting solution using conventional meter bar or doctor blade apparatus. It is usually sufficient to air-dry the films at moderate temperature to yield self-supporting films of copolymer composition.
  • Lamination of assembled cell structures is accomplished -by conventional means by pressing between metal plates at a temperature of about 120-160°C. Subsequent, to lamination, the battery cell material may be stored either with the retained plasticizer or as a dry sheet after extraction of the plasticizer with a selective low-boiling point solvent.
  • the plasticizer extraction solvent is not critical, and methanol or ether are often used.
  • Separator membrane element 16 is generally polymeric and prepared from a composition comprising a copolymer.
  • a preferred composition is the 75 to 92% vinylidene fluoride with 8 to- 25% hexafluoropropylene copolymer (available commercially from Atochem North America as Kynar FLEX) and ah organic solvent plasticizer.
  • Such a copolymer composition is also .preferred' for the preparation of the electrode membrane elements, since subsequent laminate interface compatibility is ensured.
  • the plasticizing "solvent may be one of the various organic compounds commonly used as solvents for electrolyte salts, e.g., propylene carbonate or ethylene carbonate, as well as mixtures of these ⁇ compounds.
  • Higher-boiling plasticizer compounds such as dibutyl phthalate, dimethyl phthalate, diethyl phthalate, and tris butoxyethyl phosphate are particularly suitable.
  • Inorganic filler adjuncts such as fumed alumina or silanized fumed silica, may be used to enhance the physical strength and melt viscosity of a separator membrane and, 'in some compositions, to increase the subsequent level of electrolyte solution absorption.
  • a current collector layer of aluminum foil or grid is overlaid with a positive electrode film, ' or membrane, separately prepared as a coated layer of a dispersion of insertion electrode composition.
  • This is typically an insertion compound such as LiMn 2 0 4 (LMO) , LiCo0 2 , or LiNi0 2 , powder in a copolymer matrix solution, which is dried to form the positive electrode.
  • An electrolyte/separator membrane is formed as a dried coating of a composition comprising a solution containing VdF:HFP copolymer and a plasticizer solvent is then ' overlaid on the positive electrode film.
  • a negative electrode membrane formed as a dried coating of a powdered carbon or other negative electrode material dispersion in a VdF:HFP copolymer matrix solution is similarly overlaid on the separator membrane layer.
  • a copper, current collector foil ' or grid is laid upon the negative electrode layer to complete the cell assembly.
  • the VdF:HFP copolymer composition is used as a binder in all of the major cell components, positive electrode film, negative electrode film, and electrolyte/separator membrane.
  • the assembled components are then heated under pressure to achieve heat-fusion bonding between the plasticized copolymer matrix electrode - and electrolyte components, and to the collector grids, to thereby form an effective laminate of cell elements. This produces an essentially unitary and flexible battery cell structure.
  • the electrochemical cell operated as per the invention may be prepared in a variety of ways.
  • the negative electrode may be metallic lithium.
  • the negative electrode is an insertion active material, such as, metal oxides and graphite. .
  • the components of the electrode are the metal oxide, electrically conductive carbon, and binder, in proportions similar to that described above for the positive electrode.
  • the negative electrode active material is graphite particles.
  • test cells are often fabricated using lithium metal electrodes. When forming cells for use as batteries, it is preferred to use an insertion metal oxide positive electrode and a graphitic carbon negative electrode.
  • LiFeP0 4 formed from Fe 2 0 3
  • LiFeo. 9 Mgo.iPO 4 LiFe 1 _ y Mg y P0 4 formed from FeP0 4
  • LiFeo.gMgo.iP04 LiFe 1 _ y Mg y P0 4 formed from Fe 2 0 3
  • LiFe 0 . 9 Mg 0 .iPO 4 LiFei_ y Mg y P0 4 formed from LiH 2 P0 4
  • This reaction is able to be conducted at a temperature in a range of about 400°C to about 650°C in argon as ⁇ shown, and also under other inert atmospheres such as nitrogen or vacuum.
  • This reaction at this temperature range is primarily C - C0 2 .
  • the reaction C - CO primarily occurs at a temperature over about 650°C (HT, high temperature)
  • the reaction C - C0 2 primarily occurs at- a temperature of under about 650°C (LT, low temperature) .
  • the reference to about 650 °C is approximate and the ' designation "primarily" refers to the predominant reaction thermodynamically favored although the alternate reaction may occur to some extent .
  • This reaction is able to be conducted at a temperature in a range of about ' 700°C to about 950°C in argon as shown, and also under other inert atmospheres such as nitrogen or vacuum. A reaction temperature greater than about 670°C ensures C ⁇ CO reaction is primarily carried out.
  • the final product LiFeP0 4 prepared from Fe 2 0 3 metal compound per Reaction 1(b), appeared brown/black in color.
  • This olivine material product included carbon that remained after reaction.
  • Its CuK ⁇ x-ray diffraction pattern contained all of the peaks expected for this material as shown in Figure 1.
  • the pattern evident in Figure 1 is consistent with the single phase olivine phosphate, LiFeP0 4 . This is evidenced by the position of the peaks in terms of the scattering angle 2 ⁇ (theta) , x axis.
  • the x-ray pattern showed no peaks due to the presence of precursor oxides indicating that the solid state reaction is essentially entirely completed.
  • the x-ray pattern demonstrates that the product of the invention was indeed the nominal formula LiFeP0 4 .
  • nominal formula refers to the fact that the relative proportion of atomic species may vary slightly on the order of 2 percent to 5 percent, or more typically, 1 percent to 3 percent, and that some portion of P may be substituted by Si, S or As; and some portion of may be substituted by halogen, preferably F.
  • the LiFeP0 4 prepared as described immediately above, was tested in an electrochemical cell.
  • the positive electrode was prepared as described above, using 19.0mg of active material.
  • the positive electrode contained, on a weight % basis, 65% active material, 10% carbon black, and 5% EPDM.
  • the negative electrode was metallic lithium.
  • the electrolyte was a 2:1 weight ratio mixture of ethylene carbonate and dimethyl carbonate - within which was dissolved 1 molar LiPF 6 .
  • the cells were cycled between about 2.5 and about 4.0 volts with performance as shown in Figures 2 and 3.
  • Figure 2 shows the results of the first constant current cycling at 0.2 milliamps per square" centimeter between about 2.5 and 4.0 volts based upon about 19 milligrams of the LiFeP0 4 active material in the cathode (positive electrode) .
  • the positive electrode active material is LiFeP0 4 .
  • the lithium is extracted from the LiFeP0 4 during charging of the cell.
  • about 0.72' unit of lithium had been removed per formula unit. Consequently, the positive electrode active material corresponds to Lii_ x FeP0 4 where x appears to be equal to about 0.72, when the cathode material is at 4.0 volts versus Li/Li + .
  • the extraction represents approximately 123 milliamp hours per gram corresponding to about 2.3 milliamp hours based on 19 milligrams active material.
  • the cell is discharged whereupon a quantity of lithium is re-inserted into the LiFeP0 4 .
  • the re-insertion corresponds to approximately 121 miiliamp hours per gram proportional to the insertion of essentially all of the lithium.
  • the bottom of the curve corresponds to approximately 2.5 volts.
  • the total cumulative capacity demonstrated during the entire extraction-insertion cycle is 244mAh/g.
  • Figure 3 presents data obtained by multiple constant current cycling at 0.2 milliamp hours per square centimeter of the LiFeP0 4 versus lithium metal counter electrode between 2.5 and 4.0 volts. Data is shown for two temperatures, 23°C and 60°C. Figure 3 shows the excellent rechargeability of the LiFeP0 4 cell, and also shows good cycling and capacity of the cell. The performance shown after about 190 to 200 cycles is good and shows that electrode formulation is very desirable.
  • the x-ray pattern demonstrates that the product of the invention was indeed the nominal formula LiFe 0 . 9 Mg 0 . ⁇ PO 4 .
  • nominal formula refers to the fact that the relative proportion of atomic species may vary slightly on the order of 2 percent to 5 percent, or more -typically, 1 percent to 3 percent, and that some substitution of P and 0 may be made while maintaining the basic olivine structure.
  • the ' LiFe 0 . 9 Mg 0 .iPO 4 prepared as described immediately above, was tested in an electrochemical cell.
  • The. positive electrode was prepared as described above, using 18.9mg of active materials.
  • the positive electrode, negative electrode and electrolyte were prepared as described earlier and in connection with Figure 1.
  • the cell was between about 2.5 and about 4.0 volts with performance as shown in Figures 4, 5 and 6.
  • Figure 5 shows the results of the first constant current cycling at 0.2 milliamps per square centimeter between about 2.5 and 4.0 volts based upon about 18.9 milligrams of the LiFe 0 . 9 Mg 0 . ⁇ PO 4 active material in the cathode (positive electrode) .
  • the positive electrode active material is LiFe 0 . 9 Mg 0 . ⁇ PO 4 .
  • the lithium is extracted from the ' LiFe 0 . 9 Mg o . ⁇ P0 4 during charging of the cell. When fully charged, about 0.87 units of lithium have been removed per formula unit. Consequently, the positive electrode active material corresponds to Li ⁇ _ x Fe 0 .
  • the total cumulative specific capacity over the entire cycle is 296 mAhr/g.
  • This material has a much better cycle profile than the LiFeP0 4 .
  • Figure 5 LiFe 0 . 9 Mg 0 . ⁇ PO 4
  • Figure 2 shows a very shallow slope leading to the peak at about 123 mAh/g.
  • the Fe-phosphate ( Figure 2) provides 123 mAh/g compared to its theoretical capacity of 170 mAh/g. This ratio of 123/170, " 72% is relatively poor compared to the Fe/Mg-phosphate .
  • the Fe/Mg- phosphate ( Figure 5) provides 150 mAh/g compared to a theoretical capacity of 160, a ratio of 150/160 or 94%.
  • Figure 6 presents data obtained by multiple constant current cycling at 0.2 milliamp hours per square centimeter of the LiFe 0 . 9 Mg 0 . ⁇ PO 4 versus lithium metal counter electrode between 2.5 and 4.0 volts.
  • Figure 6 shows the excellent rechargeability of the
  • Li/LiFe 0 . 9 Mg 0 . ⁇ PO 4 cell shows good cycling and capacity of the cell.
  • the performance shown after about 150 to 160 cycles is very good and shows that electrode formulation LiFe 0 . 9 Mg 0 . ⁇ PO 4 performed significantly better than the LiFeP0 4 .
  • Figure 3 (LiFeP0 4 ) to Figure 6 (LiFe 0 . 9 Mg 0 .iPO 4 ) it can be seen that the Fe/Mg-phosphate maintains its capacity .over prolonged cycling, whereas the Fe-phosphate capacity fades significantly.
  • Figure 7 shows the results of the first constant current cycling at 0.2 milliamps per square centimeter between about 2.5 and 4.0 volts based upon about 16 milligrams of the LiFe 0 . 8 Mg 0 . 2 PO 4 active material in the cathode (positive electrode) .
  • the positive electrode active material is LiFe 0 . 8 Mg 0 . 2 PO 4 .
  • the lithium is extracted from the LiFe 0 . 8 Mg 02 PO 4 during charging of the cell. When fully charged, about 0.79 units of lithium have been removed per formula unit. Consequently, the positive electrode active material corresponds to LiFe 0 . 8 g 0 .
  • Figure 9 shows the results of the first constant current cycling at 0.2 milliamps per square centimeter between about 2.5 and 4.0 volts based upon about 18.5 milligrams of the LiFe 0 . 8 Ca 0 . 2 PO 4 active material in the cathode (positive electrode) .
  • the positive electrode active material is LiFe 0 . 8 Ca 0 . 2 PO 4 .
  • the lithium is extracted from the LiFe 0 . 8 Ca 0 . 2 PO 4 during charging' of the cell. When fully charged, about 0.71 units of lithium have been removed per formula unit.
  • the positive electrode active material corresponds to LiFe 0 . 8 Ca 0 . 2 PO 4 where x appears to be equal to about 0.71, when the cathode material is at 4.0 volts versus Li/Li + .
  • the extraction represents approximately 123 milliamp hours per gram corresponding to about 2.3 milliamp hours based on 18.5 milligrams active material.
  • the cell is discharged whereupon a quantity,- of lithium is re-inserted into the LiFe 0 . 8 Ca 0 . 2 PO 4 .
  • the reinsertion corresponds to approximately 110 milliamp hours per gram proportional to the insertion of nearly all of the lithium.
  • the bottom of the curve corresponds to approximately 2.5 volts.
  • the total specific cumulative capacity over the entire cycle is 233 mAhr/g.
  • Figure 10 shows the results of the first constant current cycling at 0.2 milliamps per square centimeter between about 2.5 and 4.0 volts based upon about 18.9 milligrams of the LiFe 0 . 8 Zn 0 . 2 PO 4 olivine active material in the cathode (positive electrode) .
  • the positive electrode active material is LiFe 0 . 8 Zn 0 . 2 PO 4 , prepared from Fe 2 0 3 and Zn 3 (P0 4 ) 2 by Reaction 4.
  • the lithium is extracted from the LiFe 0 . 8 Zn 0 . 2 PO 4 during charging of the cell. When fully charged, about 0.74 units of lithium have been removed per formula unit.
  • the positive electrode active material corresponds to Lii_ x Fe0. ⁇ Zn0.2PO4 where x appears to be equal to about 0.74, when the cathode material is at 4.0 volts versus Li/Li + .
  • the extraction represents approximately 124 milliamp hours per gram corresponding to about 2.3 milliamp hours based on 18.9 milligrams active material.
  • the cell is discharged whereupon a quantity of lithium is re— inserted into the LiFe 0 . 8 Zn 0 . 2 PO 4 .
  • the re-insertion corresponds to approximately 108 milliamp hours per gram proportional to the insertion of nearly all of the lithium.
  • the bottom of the curve corresponds to approximately 2.5 volts.
  • LiV 2 0 5 prepared by Reaction 5, appeared black in color. Its CuK ⁇ x-ray diffraction pattern contained all of the peaks expected for this material as shown in Figure 11. The pattern evident in Figure 11 is consistent with a single oxide compound gamma-LiV 2 0 5 . This is evidenced by the. position of the peaks in terms of the scattering angle 2 ⁇ (theta) , x axis. The x-ray pattern showed no peaks due to the presence of precursor oxides indicating that the solid state reaction is essentially entirely completed.
  • the x-ray pattern demonstrates that the product o -the invention was indeed the nominal formula gamma- LiV 2 0 5 .
  • nominal formula refers to the fact that the relative proportion of atomic species may vary slightly on the order of 2 percent to 5 percent, or more typically, 1 percent to 3 percent.
  • the cel.l was prepared as described above and cycled with performance as shown in Figures 12 and 13.
  • Figure 12 shows the . results of the first - constant current cycling at 0.2 milliamps per square
  • the positive electrode active material is LiV 2 0 5 .
  • the lithium is extracted from the LiV 2 0 5 during charging of the cell.
  • about 0.93 unit of lithium had been removed per formula unit. Consequently, the positive electrode active material corresponds to Lii_ x V 2 0 5 where x appears to be equal to about 0.93, when the cathode material is at 3.8 volts versus Li/Li + .
  • the extraction represents approximately 132 milliamp hours per gram corresponding to about 2.0 milliamp hours based on 15.0 milligrams- active material.
  • the cell is discharged whereupon a quantity of lithium is re-inserted into the LiV 2 0 5 .
  • the re-insertion corresponds to approximately 130 milliamp hours per gram proportional to the insertion of essentially all of the lithium.
  • the bottom of ' the curve corresponds to approximately 2.8 volts.
  • Figure 13 presents data obtained by multiple constant current cycling at 0.4 milliamp hours per square centimeter (C/2 rate) of the LiV 2 0 5 versus lithium metal counter electrode between 3.0 and 3.75 volts. Data for two temperature conditions are shown, 23°C and 60°C.
  • Figure 13 is a two part graph with Figure 13A showing the excellent rechargeability of the LiV 2 0 5 .
  • Figure 13B shows good cycling and capacity of the cell. The performance shown up to about 300 cycles is good.
  • the final product Li 3 V 2 (P0 4 ) 3 prepared by Reaction 6, appeared green/black in color. Its CuK ⁇ x-ray diffraction pattern contained all of the peaks expected for this material. as shown in Figure 14.
  • the pattern' evident in Figure 14 is consistent with a single phosphate compound Li 3 V 2 (P0 4 ) 3 of the monoclinic, Nasicon phase. This is evidenced by the • position of the peaks in terms of the scattering angle 2 ⁇ (theta) , x axis.
  • the x-ray pattern showed no peaks due to the presence of precursor oxides indicating that the solid state reaction is essentially entirely completed.
  • Li 3 V 2 (P0 4 ) 3 Li 3 V 2 (P0 4 ) 3 .
  • nominal formula refers to the fact that the relative proportion, of atomic species may vary slightly oh the order of 2 percent to 5 percent, or more typically, 1 percent to 3 percent; and that substitution of P and 0 may occur.
  • the cell was prepared as described above, using 13. ⁇ mg of active material.
  • the cell was prepared -as described above and cycled between about 3.0 and about 4.2 volts using the
  • Figure 16 shows specific capacity versus electrode potential against Li.
  • Figure 17 shows differential capacity versus electrode potential against Li.
  • a comparative method was used to form Li 3 V 2 (P0 4 ) 3 .
  • Such method was reaction without carbon and under H 2 -reducing gas as described in U.S. Patent No. 5,871,866.
  • Its CuK ⁇ x-ray diffraction pattern contained all of the peaks expected for this material as shown in Figure 15.
  • the pattern evident in Figure 15 is consistent with a- monoclinic Nasicon single phase phosphate compound Li 3 V 2 (P0 4 ) 3 . This is evidenced by the position of the peaks in terms of the scattering angle 2 ⁇ (theta) , x axis.
  • Figure 16 shows a voltage profile of the test cell, based on the Li 3 V 2 (P0 4 ) 3 positive electrode active material made by the process of the invention and as characterized in Figure 14. It was cycled against a lithium metal counter electrode. The data shown in Figure 16 is based on the Electrochemical Voltage Spectroscopy (EVS) technique. Electrochemical and kinetic data were recorded using the Electrochemical
  • Figure 16 the capacity in, and the capacity out are essentially the same, resulting in essentially no capacity loss;
  • Figure 17 is an EVS differential capacity plot based on Figure 16.
  • the relatively symmetrical nature of peaks indicates good electrical " reversibility, there are small peak separations (charge/discharge) , and good correspondence between peaks above and below the zero axis.
  • Figure 18 presents data obtained by multiple constant current cycling, at 0.2 milliamp hours per square centimeter of the LiFe 0 . 8 Mg 0 . 2 PO 4 versus lithium metal counter electrode between 2.5 and 4.0 volts.
  • Figure 18 shows the excellent rechargeability of the Li/LiFe Q . 8 Mg o . 2 P0 4 cell, and also shows good cycling and capacity of the cell.
  • the performance shown after about 110 to 120 cycles at 23°C is very good and shows that electrode formulation LiFe 0 . 8 Mg Q . 2 PO 4 performed significantly better than the LiFeP0 4 .
  • the cell cycling test at 60°C was started after the 23°C test and was ongoing. Comparing Figure 3 (LiFePO to Figure 18 (LiFe Q . 8 Mg 0 . 2 PO 4 ) , it can be seen that the Fe/Mg-phosphate maintains its capacity over prolonged cycling, whereas the Fe-phosphate capacity fades significantly.
  • the ⁇ active materials of the invention were also cycled , against insertion anodes in non-metallic, lithium ion, rocking chair cells.
  • the lithium mixed metal phosphate and the lithium metal oxide were used to formulate a cathode electrode.
  • the electrode was fabricated by solvent casting a slurry of the treated, enriched lithium manganese oxide, conductive carbon, binder, plasticizer and solvent.
  • the conductive carbon used was Super P (MMM Carbon).
  • Kynar Flex 2801® was used as the binder and electronic grade acetone was used as a solvent.
  • the preferred plasticizer was dibutyl phthalate (DPB) .
  • the slurry was cast .onto glass and a free-standing electrode was formed as the solvent was evaporated.
  • the cathode had 23.1mg LiFe 0 . 9 Mg o . ⁇ p °4 active material.
  • the proportions are as follows on a percent weight basis: 80% active material; 8% Super P carbon; and 12% Kynar binder.
  • a graphite counter electrode was prepared for use with the aforesaid cathode.
  • the graphite counter electrode served as the anode in the electrochemical cell.
  • the anode had 10.8 mg of the MCMB graphite active 5 material.
  • the graphite electrode was fabricated by solvent casting a slurry of MCMB2528 graphite, binder, and casting solvent.
  • MCMB2528 is a mesocarbon microbead material supplied by Alumina Trading, which is the U.S. distributor for the supplier, Osaka Gas Company of Japan.
  • This material has a density of about 2.24 grams per cubic centimeter; a particle size maximum for at least 95% by weight of the particles of 37 microns; median size of about 22.5 microns and an interlayer distance of about 0.336.
  • the binder was a
  • a rocking chair battery was prepared comprising the anode, the cathode, and an electrolyte.
  • the ratio of the active cathode mass to the active anode mass was about 2.14:1.
  • the two electrode layers were arranged 30. with an electrolyte layer in between, and the layers were laminated together using heat and pressure as per the Bell Comm. Res. patents incorporated herein by reference earlier.
  • the cell is activated with EC/DMC solvent in a weight ratio of 2 : 1 in ' a solution containing 1 M LiPF 5 salt.
  • Figures 19 and 20 show data for the first four complete cycles of the lithium ion cell having the LiFe o . 9 Mg o .iPO 4 cathode and the MCMB2528 anode.
  • the cell comprised 23.1mg active LiFe 0 . 9 Mg 0 .iPO 4 and 10-. ⁇ g active MCMB2528 for a cathode to anode mass ratio of 2.14.
  • the cell was charged and discharged at 23°C at an approximate C/10 (10 hour) rate between voltage limits of 2.50 V and 3.60 V.
  • the voltage profile plot ( Figure 19) shows the variation in cell voltage versus time for the LiFe 0 . 9 Mg 0 . ⁇ PO 4 /MCMB2528 lithium ion cell.
  • Figure 21 shows data for the first three complete cycles of the lithium ion cell having the ga ma- LiV 2 0 5 cathode and the MCMB2528 anode.
  • the cell prepared was a rocking chair, lithium ion cell as described above.
  • the cell comprised 29.1mg gamma-LiV 2 0 5 cathode active material and 12.2mg MCMB252 ⁇ anode active material, for a cathode to anode mass ratio of 2.39.
  • the liquid electrolyte used was EC/DMC (2:1) and 1M LiPF 5 .
  • the cell was charged and discharged at 23°C at an approximate C/10 (10 hour) rate between voltage limits of 2.50 V and 3.65 V.
  • the voltage profile plot ( Figure 21) shows the variation in cell voltage versus time for the LiV 2 0 5 /MCMB2528 lithium ion cell.
  • the symmetrical nature of the charge-discharge is clearly evident.
  • the small degree of voltage hysteresis between the charge and discharge processes is evidence for the low overvoltage in the system, which is very good.
  • the invention provides new compounds Li a MI b MII c (P0 4 ) d and gamma-LiN 2 0 5 by new methods which are adaptable to commercial scale production.
  • the Li ⁇ MI ⁇ _ y MII y P0 4 compounds are isostructural olivine compounds as demonstrated by XRD analysis.
  • Substituted compounds, such as LiFei_ y Mg y P0 4 show better performance than LiFeP0 4 unsubstituted compounds when used as electrode active materials .
  • the method of the invention utilizes the reducing capabilities of carbon along with selected precursors and reaction conditions to produce high quality products suitable as electrode active materials or as ion conductors.
  • the reduction capability of carbon over a broad temperature range is selectively applied along with thermodynamic and kinetic considerations to provide an energy-efficient, economical and convenient process to produce compounds of a desired composition and structure. This is in contrast to known methods .
  • alpha-V 2 0 5 is conventionally lithiated electrochemically against metallic lithium.
  • alpha-V 2 0 5 is not suitable as a source. of lithium for a cell.
  • alpha-V 2 0 5 is not used in an ion cell.
  • alpha-V 2 0 5 is lithiated by carbothermal reduction using a simple lithium-containing compound and the reducing capabiLity of carbon to form a gamma-LiV 2 0 5 .
  • the single phase compound, gamma-LiV 2 0 5 is not known to have been directly and independently prepared before. There is not known to be a direct synthesis route.
  • LiFeP0 4 is the reducing agent, and simple, inexpensive and even naturally occurring precursors are useable.
  • LiFeP0 4 it is possible to produce LiFeP0 4 from Fe 2 0 3 , a simple common oxide. (See Reaction lb).
  • the production of, LiFeP0 4 provides a good example of the thermodynamic and kinetic features of the method. Iron phosphate is reduced by carbon .and lithiated over a broad temperature range. At about 600°C, the C to C0 2 reaction predominates and takes about a week to complete.
  • the C to CO reaction predominates and takes about ⁇ hours to complete.
  • the C to C0 2 reaction requires less carbon reductant but takes longer due to the low temperature kinetics.
  • the C to CO reaction requires about twice as much carbon, but due to the high temperature reaction kinetics, it proceeds relatively fast.
  • the Fe in the precursor Fe 2 0 3 has oxidation state +3 and is reduced to oxidation (valence) state. +2 in the product LiFeP0 4 .-
  • the C to CO reaction requires that atomic unit of carbon be used for each atomic unit of Fe reduced by one valence state.
  • the CO to ,C0 2 reaction requires that 1/4 atomic unit of carbon be used for each atomic unit of Fe reduced by one valence state .
  • the active materials of the invention are also characterized by being stable in an as-prepared condition, in ' the presence of air and particularly humid air. This is a striking advantage, because it facilitates preparation of and assembly of battery cathodes and cells, without the requirement for controlled atmosphere. This feature is particularly important, as those skilled in the art will recognize that air stability, that is, lack of degradation on exposure to air, is very important for commercial processing. Air-stability is known in the art to more specifically indicate that a material does not hydrolyze in presence of moist air. Generally, air-stable materials are also characterized by Li being extracted therefrom above about 3.0 volts versus lithium. The higher the extraction potential, the more tightly bound the lithium ions are to the host lattice.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Inorganic Chemistry (AREA)
  • Organic Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Engineering & Computer Science (AREA)
  • Electrochemistry (AREA)
  • General Chemical & Material Sciences (AREA)
  • Materials Engineering (AREA)
  • Manufacturing & Machinery (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Battery Electrode And Active Subsutance (AREA)
  • Secondary Cells (AREA)
  • Inorganic Compounds Of Heavy Metals (AREA)
  • Glass Compositions (AREA)
  • Pharmaceuticals Containing Other Organic And Inorganic Compounds (AREA)

Abstract

The invention provides novel lithium-mixed metal materials which, upon electrochemical interaction, release lithium ions, and are capable of reversibly cycling lithium ions. The invention provides a rechargeable lithium battery which comprises an electrode formed from the novel lithium-mixed metal materials. Methods for making the novel lithium-mixed metal materials and methods for using such lithium-mixed metal materials in electrochemical cells are also provided. The lithium-mixed metal materials comprise lithium and at least one other metal besides lithium. Preferred materials are lithium-mixed metal phosphates which contain lithium and two other metals besides lithium.

Description

PREPARATION OF LITHIUM-CONTAINING MATERIALS
Field of the Invention
This invention relates, to improved materials usable as electrode active materials and to their preparation.
Background of the Invention
Lithium batteries are prepared from one or more lithium electrochemical cells containing electrochemically active (electroactive) materials. Such cells typically include an anode (negative electrode) , a cathode (positive electrode) , and an electrolyte interposed between spaced apart positive and negative electrodes. Batteries with anodes of metallic lithium and containing metal chalcogenide cathode active material are known. The electrolyte typically comprises a salt of lithium dissolved in one or more solvents, typically nonaqueous (aprotic) organic solvents. Other electrolytes are solid electrolytes typically called polymeric matrixes that contain an ionic conductive medium, typically a metallic powder or salt, in combination with a polymer that itself may be ionically conductive which is electrically insulating. By convention, during discharge of the cell, the negative electrode of the cell is defined as the anode. Cells having a metallic lithium anode and metal chalcogenide cathode are charged in an initial condition. During discharge, lithium ions from the metallic anode pass through the liquid electrolyte to the electrochemical active (electroactive) material of the cathode whereupon they release electrical energy to an external circuit.
It has recently been suggested to replace the lithium metal anode with an insertion anode, such as a 5 lithium metal chalcogenide or lithium metal oxide. Carbon anodes, such as coke and graphite, are also insertion materials. Such negative electrodes are used with lithium- containing insertion cathodes, in order to form an electroactive couple in a cell. Such cells, in
10. an initial condition, are not charged. In order to be used to deliver electrochemical energy, such cells must be charged in order to transfer lithium to the anode from the lithium- containing cathode. During discharge,the lithium is transferred from the anode back to the
15 cathod-e. During a subsequent recharge, the lithium is transferred back to the anode where it re-inserts. Upon subsequent charge and discharge, the lithium ions (Li+) are transported between the electrodes. Such rechargeable batteries, having no free metallic species
20 are called rechargeable ion batteries or rocking- chair batteries. See U.S. Patent Nos. 5,418,090; 4,464,447; 4,194,062; and 5,130,211'.
Preferred positive electrode active materials include LiCo02, LiMn204, and LiNi02. The cobalt compounds
25 are relatively expensive and the nickel compounds are difficult to synthesize. A relatively economical positive electrode is LiMn204, for which methods of synthesis are known. The lithium cobalt oxide (LiCo02) , the lithium manganese oxide (LiMn204) , and the lithium
30 nickel oxide (LiNi02) all have a common disadvantage in that the charge capacity of a cell comprising such cathodes suffers a significant loss in capacity. That is, the initial capacity available (amp hours/gram) from LiMn204, LiNi02, and LiCo02 is less than the theoretical capacity because significantly less than 1 atomic unit of lithium engages in the electrochemical reaction. Such an initial capacity value is significantly diminished during the first cycle operation and such capacity further diminishes on every successive cycle of operation. For LiNi02 and LiCo02 only about 0.5 atomic units of lithium is reversibly cycled during cell operation. Many attempts have been made to reduce capacity fading, for example, as described in U.S. Patent No. 4,828,834 by Nagaura et al. However, the presently known and commonly used, alkali transition metal oxide compounds suffer from relatively low capacity. Therefore, there remains the difficulty of obtaining a lithium-containing electrode material having acceptable capacity without disadvantage of significant capacity loss when used in a cell.
Summary of the Invention
The invention provides novel lithium-mixed metal materials which, upon electrochemical interaction, release lithium ions, and are capable of reversibly cycling lithium ions . The invention provides a rechargeable lithium battery which comprises an electrode formed from the novel lithium-mixed metal materials. Methods for making the novel lithium-mixed metal materials and methods for using such lithium-mixed metal materials in electrochemical cells are also provided.
The lithium-mixed metal materials comprise lithium and at least one other metal besides lithium. Preferred materials are lithium-mixed metal phosphates whic contain lithium and two other metals besides lithium. Accordingly, • the invention provides a rechargeable lithium battery which comprises an electrolyte; a first electrode having a compatible active material; and a second electrode comprising the novel materials. In one aspect, the novel materials are lithium-mixed metal phosphates' which preferably used as a positive electrode active material, reversibly cycle lithium ions with the compatible negative electrode active material. Desirably, the lithium-mixed metal phosphate' is represented by the nominal general formula LiaMIbMIIc (P04)d. Such compounds include Li1MIaMIIbP04 and Li3MIaMIIb (P04) 3; therefore, in an initial condition 0 ≤ a ≤ l or 0 ≤ a ≤ 3, respectively. During cycling, x quantity of lithium is released where 0 ≤ x < a. In the general formula, the sum of b plus c is up to about 2. Specific examples are Li1MI1_yMIIyP04 and Li3MI2_yMIIy (P04) 3.
In one aspect, MI and Mil are the same. In a preferred aspect, MI and Mil are different from one another. At least one of Ml and Mil is an element capable of an oxidation state higher than that initially present in the lithium-mixed metal phosphate compound. Correspondingly, at least one of MI and Mil has more than one oxidation state in the phosphate compound, and more than one oxidation State above the ground state M°. The term oxidation state and valence state are used in the art interchangeably.
In another aspect, both MI and Mil may have more than one oxidation state and both may be oxidizable from the state initially present in the phosphate compound. Desirably, Mil is a metal or semi-metal having a +2 oxidation state, and is selected from Groups 2, 12 and 14 of the Periodic Table. Desirably, Mil is selected from non-transition metals and semi-metals. In one embodiment, Mil has only one oxidation state and is nonoxidizable from its oxidation state in the lithium- mixed metal compound. In another embodiment, Mil has more than one oxidation state. Examples of semi-metals having more than one oxidation state are selenium and tellurium; other non-transition metals with more than one oxidation state are tin and lead. Preferably, Mil is selected from Mg (magnesium) , Ca (calcium) , Zn (zinc) , Sr (strontium) , Pb (lead) , Cd (cadmium) , Sn (tin) , Ba (barium), and Be (beryllium), and mixtures thereof. ' In another preferred aspect, Mil is a metal having a +2 oxidation state and having more than one oxidation state, and is oxidizable from its oxidation state in lithium- mixed metal compound.
Desirably, Ml is selected from Fe (iron) , Co
(cobalt), Ni (nickel), Mn (manganese), Cu (copper), V (vanadium) , Sn (tin) , Ti (titanium) , Cr (chromium) , and mixtures thereof. As can be seen, Ml is preferably selected from the first row of transition metals and further includes tin, and Ml preferably initially has a +2 oxidation state.
In a preferred aspect, the product LiMI1_yMIIyP04 is an olivine structure and the product
Figure imgf000008_0001
(P04) 3 is a rhombohedral or monoclinic Nasicon structure. In another aspect, the term "nominal formula" refers to the fact that the relative proportion of atomic species may vary slightly on the order of 2 percent to 5 percent, or more typically, 1 percent to 3 percent. In still another aspect, any portion of P (phosphorous) may be substituted by Si (silicon) , S (sulfur) , and/or As (arsenic) ; and any portion of 0 (oxygen) may be substituted by halogen, preferably F (fluorine) . These aspects are also disclosed in U.S. Patent Application Serial Numbers 09/105,748 filed June 26, 1998, and 09/274,371 filed March 23, 1999; and in U.S. Patent No. 5,871,866 issued February 16, 1999, which is incorporated by reference in its entirety; each of the listed applications and patents are co-owned by the assignee of the present invention.
The metal phosphates are alternatively represented by the nominal general formulas such as Li1_xMI1_yMIIyP04 (0 < x ≤ 1), and Li3_xMI2_yMIIy (P04) 3 signifying capability to release and reinsert lithium.
The term "general" refers to a family of compounds, with M, x and y representing variations therein. The expressions 2-y and 1-y each signify that the relative amount of MI and Mil may vary. In addition, as stated above, MI may be a mixture of metals meeting the earlier stated criteria for MI. In addition, Mil may be a' mixture of metallic elements meeting the stated criteria for Mil. Preferably, where Mil is a mixture, it is a mixture of 2 metallic elements; and where MI is a mixture, it is a mixture of 2 metals. Preferably, each such metal- and metallic element has a +2 oxidation state in the initial phosphate compound.
The active material of the counter electrode is any material compatible with the lithium-mixed metal phosphate of the invention. Where the lithium-mixed metal phosphate is used as a positive electrode active material, metallic lithium, lithium-containing material,- or non-lithium-containing material may be used as the negative electrode active material. The negative electrode is desirably a nonmetallic insertion material. Desirably, the negative electrode comprises an active material from the group consisting of metal oxide, particularly transition metal oxide, metal chalcogenide, carbon, graphite, and mixtures thereof. It is preferred that the anode active material comprises a carbonaceous material such as graphite. The lithium-mixed metal phosphate of the invention may also be used as a negative electrode material.
In another embodiment, the present invention provides a method of preparing a compound of the nominal general formula LiaMIbMIIc (P04)d where 0 < a ≤ 3; the sum of b plus c is greater than zero and up to about 2;, and 0 < d ≤ 3. Preferred compounds include Li3MIbMIIc (P04) 3 where b plus c is about 2; and LiMIbMIIcP04 where b plus c is about 1. The method comprises providing starting materials in particle form. The starting- (precursor) materials include a lithium-containing compound, one or more metal containing compounds, a compound capable of providing the phosphate (P04)-3 anion, and carbon. Preferably, the lithium-containing compound is in particle form, and an example is lithium salt. Preferably, the phosphate-containing anion compound is in particle form, and examples include metal phosphate salt and diammonium hydrogen phosphate (DAHP) and ammonium dihydrogen phosphate (ADHP) . The lithium compound, one or more metal compounds, and phosphate compound are included in a proportion which provides the stated nominal general formula. The starting materials are mixed together with carbon, which is included in an amount sufficient to reduce the metal ion of one or more of the metal-containing starting materials without full, reduction to an elemental metal state. Excess quantities of carbon and one or more other starting materials (i.e., 5 to 10% excess) may be used to enhance product quality. A small amount of carbon, remaining after the reaction, functions as a conductive constituent in the ultimate electrode formulation. This is an advantage since such remaining carbon is very intimately mixed with- the product active material. Accordingly, large quantities of excess carbon, on the order of 100% excess carbon are useable in the process. The carbon present during compound formation is thought to be intimately dispersed throughout the precursor and product. This provides many ■ advantages, including the enhanced, conductivity of the product. The presence of carbon particles in the starting materials is also thought to provide nucleation sites for the production of the product crystals.
The starting materials are intimately mixed and then reacted together where the reaction is initiated by heat and is preferably conducted in a nonoxidizing, inert atmosphere, whereby the lithium, metal from the metal compound (s), and phosphate combine to form the LiaMIbMIIc(P04)d product. Before reacting the compounds, the particles are intermingled to form an essentially homogeneous powder mixture of the precursors.- In one aspect, the precursor powders are dry-mixed using a ball mill, such as zirconia media. Then the mixed powders are pressed into pellets. In another aspect, the precursor powders are mixed with a binder. The binder is selected so as to not inhibit reaction between particles of the . powders. Therefore, preferred binders decompose or evaporate at a temperature less than the reaction temperature.' Examples include mineral oils (i.e., glycerol, or C-18 hydrocarbon mineral .oil) and polymers which decompose (carbonize) to form a carbon residue ■before the reaction starts, or which evaporate before the reaction starts. In still another aspect, intermingling is conducted' by forming a wet mixture using a volatile solvent and then the intermingled particles are pressed together -in pellet form to provide good grain-to-grain contact.
Although it is -desired that the precursor compounds be present in a proportion which provides the stated general formula of the .product, the lithium compound may be present in an excess amount .on the order of 5 percent excess lithium compared to a stoichiometric mixture of the precursors. And the carbon may be present at up to 100% excess compared to the stoichiometric amount. The method of the invention may also be used to prepare other novel products, and to prepare known products.. A number of lithium compounds are available as precursors, such as lithium acetate (LiOOCCH3) , lithium hydroxide, lithium nitrate (LiN03) , lithium oxalate (Li2C204) , lithium oxide ■(Li20) , lithium phosphate (Li3P04) , lithium dihydrogen phosphate (LiH2P04) , lithium vanadate (LiV03) , and lithium carbonate (Li2C03), . The lithium carbonate is preferred for the solid state reaction since it has a very high melting point and commonly reacts with the other precursors before melting. Lithium carbonate has a melting point over 600°C and it decomposes in the presence of the other precursors and/or effectively reacts with the other precursors before melting. In contrast, lithium hydroxide melts at about 400°C. At some reaction temperatures preferred herein of over 450°C the lithium hydroxide will melt before any significant reaction with the other precursors occurs to an effective extent. This melting renders the reaction very difficult to control. In addition, anhydrous LiOH is highly hygroscopic and a significant quantity of. water is released during the reaction. Such water needs to be removed from the oven and the resultant product may need to be dried. In one preferred aspect, the solid state reaction made possible by the present invention is much preferred since it is conducted at temperatures at which the lithium-containing compound reacts with the other reactants before melting. Therefore, lithium hydroxide is useable as a precursor in the method of the invention in combination with some precursors, particularly the phosphates. The method of the invention is able to be conducted as an economical carbothermal-based process with a wide variety of precursors and over a relatively broad temperature range.
The aforesaid precursor compounds (starting materials) are generally crystals, granules, and powders and are generally referred to as being in particle form. Although- many types of phosphate salts are known, it is preferred to use diammoniu hydrogen phosphate (NH4)2HP04 (DAHP) or ammonium dihydrogen phosphate (NH4)H,P04 (ADHP) . Both ADHP and DAHP meet the preferred criteria that the precursors decompose in the presence of one another or react with one another before melting of such precursor. Exemplary metal compounds are Fe203, Fe304,- V205, V02, LiV03', NH4V03, Mg(OH)2, Cao, MgO, Ca(OH)2, Mn02, Mn203, Mn3(P04)2, CuO, SnO, Sn02, Ti02, Ti203, Cr203, Pb02, PbO, Ba(OH)2, BaO, Cd(OH)2. In addition, some starting materials serve as both the source of metal ion and phosphate, such as FeP04, Fe3(PQ4)2, Zn3(P04)2, and Mg3(P04)2. Still others contain both lithium ion and phosphate such as Li3P04 and LiH2P04. Other exemplary precursors are H3P04 (phosphoric acid) ; and P205 (PO10) phosphoric oxide; and HP03 meta phosphoric acid, which is a decomposition product of P205. If it is desired to replace any of the oxygen with a halogen, such as fluorine, the starting materials further include a fluorine compound such as LiF. If it is desired to replace any of the phosphorous with silicon, then the starting materials further include silicon oxide (Si02) . Similarly, ammonium sulfate in the starting materials is useable to replace phosphorus with sulfur.
The starting materials are available from a number of sources. The following are typical. Vanadium pentoxide of the formula V205 is obtainable from any number of suppliers including Kerr McGee, Johnson
Matthey, or Alpha Products of Daver.s, Massachusetts. Vanadium pentoxide has a CAS number of 1314-62-1. Iron oxide Fe303 is a common and very inexpensive material available in powder form from the' same suppliers. The other precursor materials mentioned above are also available from well known suppliers, such as those listed above . The method of the invention may also be used to react starting materials in the presence of carbon to form a variety of other novel products, such as gamma- LiV205 and also to produce known products. Here, the carbon functions to reduce metal ion of a starting metal compound to provide a product containing such reduced metal ion. The method is particularly useful to also add lithium to the resultant product, which thus contains the metallic element ions, namely, the lithium ion and the other metal ion, thereby forming a mixed metal product. An example is the reaction of vanadium pentoxide (V205) with lithium carbonate in the presence of carbon to form gamma-LiV205. Here the starting metal ion V+SV+5 is reduced to V+4V+5 in the final product. A single phase gamma-LiV205 product .is not known to .have been directly and independently formed before.
As described earlier, it is desirable to conduct the reaction at a temperature where the lithium compound reacts before melting. The temperature should be about 400°C or greater, and desirably 450°C or greater, and preferably 500°C or greater, and generally will proceed at a faster rate at higher temperatures. The various reactions involve production of CO or C02 as an effluent gas. The equilibrium at higher temperature favors CO formation. Some of the reactions are more desirably conducted at temperatures greater than 600°C; most desirably greater than 650°C; preferably 700°C or greater; more preferably 750°C or greater. Suitable ranges for many reactions are about 700 to 950°C, or about 700 to 800°C.
Generally, the higher temperature reactions produce CO effluent and the stoichiometry requires more carbon be used than the case where C02 effluent is produced at lower temperature. This is because the reducing effect of the C to C02 reaction is greater than the C. to CO reaction. The C to C02 reaction involves an increase in carbon oxidation state of +4 (from 0 to' 4) and the C to CO reaction involves an increase in carbon oxidation state of +2 (from ground state zero to 2) . Here, higher temperature generally refers to a range of about 650°C to about 1000°C and lower temperature refers to up to about 650°C. Temperatures higher than 1200°C are not thought to be needed.
In one aspect, the method of the invention utilizes the reducing capabilities of carbon in a unique and controlled manner to produce desired products having structure and lithium content suitable for electrode active materials. The method of the invention makes it possible to produce products containing lithium, metal and oxygen in an economical and convenient process. The ability to lithiate precursors, and change the oxidation" state of a metal without causing abstraction of oxygen from a precursor is heretofore unexpected. These advantages are at least in part achieved by the reductant, carbon, having an oxide whose free energy of formation becomes more negative as temperature increases. Such oxide of carbon is more stable at high temperature than at low temperature. This feature is used to produce products having one or more metal ions in a reduced oxidation state relative to the precursor metal ion ■oxidation state. The method utilizes an effective- combination of quantity ,of carbon, time and temperature to produce new products and to produce known products in a hew way. Referring back to the discussion of temperature, at about 700°C both the carbon to carbon monoxide and the carbon to carbon dioxide reactions are occurring. At closer to 600°C the C to C02 reaction is 5 the dominant reaction. At closer to 80Q°C the C to CO reaction is dominant. Since the reducing effect of the C to C02 reaction is greater, the result is that less carbon is needed per atomic unit of metal to be reduced. In the case of carbon to carbon monoxide, each atomic
10 unit of carbon -is oxidized from ground state -zero to plus 2. Thus, for each atomic unit of metal ion (M) which is being reduced by one oxidation state, one half atomic . unit of carbon is required. In the case of the carbon to carbon dioxide reaction, one quarter atomic unit of
15 carbon is stoichio etrically required for each atomic unit of metal ion (M) which is reduced by one oxidation state, because carbon goes from ground state zero to a plus 4 oxidation state. These same relationships apply for each such metal ion being reduced and for each unit
•20 reduction in oxidation state desired.
It is preferred to heat the starting materials at a ramp rate of a fraction of a degree to 10°C per minute and preferably about 2°C per minute. Once the desired reaction temperature is attained, the reactants
25 (starting materials) are held at the reaction temperature for several hours. The heating is preferably conducted .under non-oxidizing or inert gas such as argon or vacuum. Advantageously, a reducing atmosphere is not required, although it may be used if desired. After reaction, the
30 products are preferably cooled from the elevated temperature to ambient (room) temperature (i.e., 10°C to 40°C) . Desirably, the cooling occurs at a rate similar to the earlier ramp rate, and preferably 2°C/minute cooling. Such cooling rate has been found to be adequate to achieve the desired structure of the final product. It is also possible to quench the products at a cooling rate on the order of about 100°C/minute. In some instances, ■ such rapid cooling (quench) may be preferred.
The present invention resolves the capacity problem posed by widely used cathode active material. It has been found that the capacity and capacity retention of cells having the preferred active material of the invention are " improved over conventional materials.
Optimized cells containing lithium-mixed metal phosphates, of the invention potentially have performance improved over commonly used lithium metal oxide compounds. •• Advantageously, the new method of making the novel lithium-mixed metal phosphate compounds of the invention is relatively economical and readily adaptable to commercial production.
Objects, features, and advantages of the invention include an electrochemical cell or battery based on lithium-mixed metal phosphates. Another object is to provide an electrode active material which combines the advantages of good discharge capacity and capacity retention. It is also an object of the present invention to provide electrodes which can be manufactured economically. Another object is to provide a method for forming electrode active- material which lends itself to commercial scale production for preparation of large quantities. These and other objects, features, and advantages will become apparent from the following description of the preferred embodiments, claims,' and accompanying drawings .
Brief Description of the Drawings
Figure 1 shows the results, of. an x-ray diffraction analysis, of the LiFeP04 prepared according to the invention using CuK radiation, λ = 1.5405A. Bars refer to simulated pattern from refined cell parameters, ' Space Group, SG = Pnma (62). The values are a = 10.2883A (0.0020), b = 5.9759A (0.0037), c = 4.6717A (0.0012) 0.0072, cell volume = 287.2264A3 (0.0685). Density, p = 3.605 g/cc, zero = 0.452 (0.003). Peak at full width half maximum, PFWHM = 0.21. Crystallite size from XRD data = 704A.
Figure 2 is a voltage/capacity plot of LiFeP04- containing cathode cycled with a lithium metal anode using constant current cycling at ± 0.2 milliamps per square centimeter in a range of 2.5 to 4.0 volts at a temperature of about 23°C. The cathode contained 19.0mg of the LiFeP04 active material, prepared by the method of the invention. The electrolyte comprised ethylene carbonate (EC) and dimethyl carbonate (DMC) in a weight ratio of 2:1 and included a 1 molar concentration of LiPF5 salt. The lithium-metal-phosphate containing electrode and the lithium metal counter electrode are maintained spaced apart by a glass fiber separator which is interpenetrated by the solvent and the salt.
Figure 3 shows multiple constant current cycling of LiFeP04 active material cycled with a lithium metal anode using the electrolyte as described in connection with Figure 2 and cycled, charge and discharge at ± 0.2 milliamps per square centimeter, 2.5 to 4.0 .volts at two different temperature conditions, 23°C and 60°C. Figure 3 shows the excellent rechargeability of the lithium iron phosphate/lithium metal cell, and also shows the excellent cycling and specific capacity (mAh/g) of the active material.
Figure 4 shows the results of an x-ray diffraction analysis, of the LiFeo.9Mgo.iPO4 prepared according to the invention, using CuKα radiation, λ = 1.5405A. Bars refer to simulated pattern from refined cell parameters SG = Pnma (62) . ' The values are a = 10.'2688A (0.0069), b = 5.9709A (0.0072), c = 4.6762A , (0.0054), cell volume = 286.7208A (0.04294), p = 3.617 g/cc, zero = 0.702 (0.003), PFWHM =.0.01, and crystallite = 950A.
Figure 5 is a voltage/capacity plot of LiFe0.9Mg0.1PO4-containing cathode cycled with a lithium metal anode using constant current cycling at ± 0.2 milliamps per square centimeter in a range of 2.5 to 4 . 0 volts. Other conditions are as described earlier with respect to Figure 2. ' The cathode contained 18.9mg of the iFeo.9Mgo.iPO4 active material prepared by the method of- the invention.
Fi ure 6 shows multiple constant current cycling of LiFeo.9Mgo.iPO4 cycled with a lithium metal anode using the electrolyte as described in connection ' with Figure 2 and cycled, charge and discharge at ± 0.2 milliamps per square centimeter, 2.5 to 4.0 volts at two different temperature, conditions, 23°C and 60.°C. Figure 6 shows the excellent rechargeability of the lithium- metal-phosphate/lithium metal cell, and also shows the excellent cycling and capacity of the cell. Figure 7 is a voltage/capacity plot of LiFe0.8Mg0.2PO4-containing cathode cycled with a lithium metal anode using constant current cycling at ± 0.2 milliamps per square centimeter" in a range of 2.5 to 4.0 volts at 23°C. Other conditions are as described earlier with respect to Figure 2. The cathode contained 16mg of' the LiFe0..8Mg0.2PO4 active material prepared by the method of the invention.
Figure 8 shows the results of an x-ray diffraction analysis, of the LiFe0.9Ca0.ιPO4 prepared according to the invention, using CuKα radiation, λ = 1.5405A. Bars refer to simulated pattern from refined cell parameters SG = Pnma (62) . The values are a = ' 10.3240A (0.0045), b = 6.0042A (0.0031), c = 4.6887A (0.-0020), cell volume = 29-0.637θA (0.1807), zero = 0.702' (0.003), p = 3.62 g/cc, PF HM = 0.18, and crystallite = 680A.
Figure 9 is a voltage/capacity plot of LiFe0.8Ca0.2P04-containing cathode cycled with a lithium metal anode using constant current cycling at ± 0.2 milliamps per square centimeter in a range of 2.5 to 4 ; 0 volts at 23°. Other conditions are as described earlier with respect to Figure 2. The cathode contained 18.5mg of the LiFe0.8Ca0.2PO4 active material prepared by the method of the invention.
Figure 10 is a voltage/capacity plot of LiFe0.8Zn0.2PO4-containing 'cathode cycled with a lithium metal anode using constant current cycling at ± 0.2 milliamps per square centimeter in a- range of 2.5 to 4.0' volts at 23°C. Other conditions are as described earlier with respect to Figure 2. The cathode contained 18.9mg of the LiFe0.8Zn0.2PO4 active material prepared by the method of the invention.
Figure 11 shows the results of an x-ray diffraction analysis of the gamma-LixV205 (x = 1, gamma LiV205) prepared according to the invention using CuK radiation λ = 1.5405A. The values are a = 9.687A (1), b = 3.603A (2), and c = 10.677Ar (3); phase type is gamma- LixV205 (x = 1) ; symmetry is orthorhombic; and space group is Pnma.
Figure 12 is a voltage/capacity plot of gamma-
LiV-205-containing cathode cycled with a lithium metal anode using constant current cycling at ± 0.2 milliamps per square centimeter in a range of 2.5 to 3.8 volts at 23°C. Other conditions are as described earlier with respect to Figure 2. The cathode contained 21mg of the gamma-LiV205 active material prepared by the method of the invention.
Figure 13 is a two-part graph based on multiple constant current cycling of gamma-LiV205 cycled with a lithium metal anode using. the electrolyte as described in connection with Figure.2 and cycled, charge and discharge at ± 0.2 milliamps per square centimeter, 2.5 to 3.8 volts. In the two-part graph, Figure 13 shows the excellent rechargeability of the lithium-metal- oxide/lithium metal cell. Figure 13 shows the excellent cycling and capacity of the cell.
Figure 14 shows the results of an x-ray diffraction analysis of the Li3V2(P04)3 prepared according to the invention. The analysis is based on CuKα radiation, λ = 1.5405A. The values are a = 12.184A (2), b = 8.679A (2), c = 8.627A (3), and β = 90.457° (4).
Figure 15 shows the results of an x-ray diffraction analysis of Li3V2(P04)3 prepared according to 5 a method described in U.S. Patent No. 5,871,866. The analysis is based on CuKα radiation, λ = 1.5405A. The values are a = 12.155A (2), b = 8.71lA (2), c = 8.645A (3); the angle beta is 90.175 (6); symmetry is Monoclinic; and space group is P2ι/n.
10 Figure 16 is an EVS (Electrochemical Voltage
Spectroscopy) voltage/capacity profile for a cell with ■ cathode material formed by the carbothermal reduction method of the invention. The cathode material is 13.8mg of Li3V2(P04)3. The cell includes a lithium metal counter
1.5 electrode in an electrolyte comprising ethylene carbonate (EC) and dimethyl carbonate (DMC) in a weight ratio of 2:1 and including a 1 molar concentration of-LiPF6 salt. The lithium-metal-phosphate containing electrode arid the lithium metal counter electrode are maintained spaced
20 apart by a fiberglass separator which is interpenetrated by the' solvent and the salt. The conditions are.± 10 mV steps', between about 3.0 and 4.2 volts, and the critical limiting current density is less than or equal to 0.1 mA/cm2.
25 Figure 17 is an EVS differential capacity versus voltage plot for the cell as described in connection with Figure 16.
Figure 18 shows multiple constant current cycling of LiFe0.8Mg0.2PO4 cycled with a lithium metal 30 anode using the electrolyte as described in connection with Figure 2 and cycled, charge and discharge at + 0.2 milliamps per square centimeter, 2.5 to 4.0 volts at two different temperature conditions, 23°C and 60°C. Figure 18 shows the excellent rechargeability of the lithium- metal-phosphate/lithium metal cell, and also shows the excellent cycling and capacity of the cell.
Figure 19 is a graph of potential over time for the first four complete cycles of the LiMgo.iFeo.9PO4/MCMB graphite cell of the invention.
Figure 20 is a two-part graph based on multiple constant current cycling of LiFe0.9Mg0.ιPO4 cycled ith an MCMB graphite anode using the electrolyte as described in connection with Figure 2 and cycled, charge and discharge at + 0.2 milliamps per square centimeter, 2.5 to 3.6 volts, 23°C and based on a C/10 (10 hour) rate. In the two-part graph, Figure 20 shows the excellent rechargeability of the lithium-metal-phosphate/graphite cell. Figure 20 shows the excellent cycling and capacity of the cell.
Figure 21 is a graph of potential over time for the first three complete cycles of the gamma-LiV205/MCMB graphite cell of the invention.
Figure 22 is' a diagrammatic representation of a typical laminated lithium-^ion battery cell structure.
Figure 23 is a diagrammatic representation of a typical multi-cell battery cell structure. Detailed Description of the Preferred Embodiments
The present invention provides lithium-mixed metal-phosphates, which are usable as electrode active materials, for lithium (Li+ ) ion removal and insertion. Upon extraction of the lithium ions from the lithium- mixed-metal-phosphates, significant capacity is achieved,. In one aspect of the invention, electrochemical energy is provided when combined with a suitable counter electrode by extraction of a quantity x of lithium from lithium- mixed-metal-phosphates Lia_xMIbMIIc(P04) d. When a quantity x of lithium is removed- per formula unit of the lithium- mixed-metal phosphate, metal MI is oxidized. In another aspect, metal Mil is also oxidized. Therefore, at least one of MI and Mil is oxidizable from its initial condition in the phosphate compound as Li is removed..
Consider the following which illustrate the- mixed metal compounds of the invention: LiFei_ySnyP04, has two oxidizable elements, Fe and Sn; in contrast, LiFeι_yMgyP04 has one oxidizable metal, the metal Fe . '
In another aspect, the invention provides a lithium ion battery which comprises an electrolyte; a negative electrode having an insertion active material; and a positive electrode comprising a lithium-mixed- metal-phosphate active material characterized by an ability to release lithium ions for insertion into the negative electrode active material. The lithium-mixed- metal-phosphate is desirably represented by the. nominal general formula LiaMIbMIIc (P04) d. Although the metals MI and Mil may be the same, it is preferred that the metals MI and Mil are different. Desirably, in the phosphate compound MI is a metal selected from the group: Fe, Co, Ni, Mn, Cu, V, Sn, Ti, Cr and mixtures thereof, and MI is most desirably a transition metal or mixture thereof selected from said group. Most preferably, MI has a +2 valence or oxidation state.
In another aspect, Mil is selected from Mg, Ca, Zn, Sr, Pb, Cd, Sn, Ba, Be, and mixtures thereof. Most preferably, Mil has a +2 valence or- oxidation state. The lithium-mixed-metal-phosphate is preferably a compound represented by the nominal general formula Lia_xMIbMIIc(P04) d, signifying the preferred composition and its capability to release x lithium. Accordingly, during cycling, charge and discharge, the value of x varies as x greater than or equal to 0 and less than or equal to a. - The present invention resolves a capacity problem posed by conventional cathode active materials. Such problems with conventional active materials are described by Tarascon in U.S. Patent No. 5,425,932, using LiMn204 as an example. Similar problems are observed with LiCo02, LiNi02, and many, if not all, lithium metal chalcogenide materials . The present invention demonstrates that significant capacity of the cathode active material is utilizable and maintained.
A preferred novel procedure for forming the lithium-mixed-metal-phosphate. LiaMIbMIIc (P04) d compound active material will now be described. In addition, the preferred novel procedure is- also applicable to formation of other lithium metal compounds, and will be described as such. The basic procedure will be described with reference to exemplary starting materials but is not • limited thereby. The basic process comprises conducting a reaction between a lithium compound, preferably lithium carbonate (Li2C03) , metal compound(s), for example, vanadium pentoxide (V205) , iron, oxide (Fe203) , and/or manganese hydroxide, and a phosphoric acid derivative, preferably the phosphoric acid ammonium salt, diammonium hydrogen phosphate, (NH4) 2H (P04) . Each of the precursor starting materials are available from a number of chemical outfits including Aldrich Chemical Company and Fluka. Using the method described herein, LiFeP04 and LiFe0.9Mgo.ιP04, Li3V2(P04)3 were prepared with approximately a stoichiometric amount of Li2C03, the respective metal compound, and (NH4)2HP04. Carbon powder was included with ■ these precursor materials. The precursor materials were initially intimately mixed and dry ground for about 30 minutes . The intimately mixed compounds were then pressed into pellets. Reaction was conducted by heating in an- oven at a preferred ramped heating rate to an elevated temperature, and held at such elevated temperature for several hours to complete formation of the reaction product. The entire reaction was conducted in a non-oxidizing atmosphere, under flowing pure argon gas. The flow rate will depend upon the size of the oven and the quantity needed to maintain the atmosphere. The oven was permitted to cool down at the end of the reaction period, where cooling occurred at a desired rate under .argon. Exemplary and preferred ramp rates, elevated reaction temperatures and reaction times are described herein. In one aspect, a ramp rate of
2°/minute to an elevated temperature in "a range of 750°C -to 800°C was suitable along with a dwell (reaction time) of 8 hours. ' Refer to Reactions.1, 2, 3 and 4 herein. In another variation per Reaction 5, a reaction temperature of 600°C was used along with a dwell time of about one hour. In still another variation, as per Reaction 6, a • two-stage heating was conducted, first to a temperature ' of 300°C and then to a temperature of 850°. The general aspects of the above synthesis route are applicable to a variety of starting materials. Lithium-containing compounds include Li20 (lithium oxide) , LiH2P04 (lithium hydrogen phosphate) , Li2C204 (lithium oxalate) , LiOH (lithium hydroxide),
LiOH.H20 (lithium hydroxide monohydride) , and LiHC03 (lithium hydrogen carbonate). The metal compounds (s) are reduced in the presence of the reducing agent, carbon. The same considerations apply to other lithium-metal- and phosphate-containing precursors. The thermodynamic considerations such as ease of reduction, of the selected precursors, the reaction kinetics, and the melting point of the salts will cause adjustment in the general procedure, such as, amount of carbon reducing agent/ and the temperature of reaction.
Figures 1 through 21 which will be described more particularly below show characterization data and capacity in actual use for the cathode materials (positive electrodes) of the invention. Some tests were conducted in a cell comprising a lithium metal counter electrode . (negative electrode) and other tests were conducted in cells having a carbonaceous counter electrode. All of the cells had an EC:DMC-LiPF6 electrolyte.
Typical cell configurations will now be described with reference to Figures 22 and 23; and such battery or cell utilizes the novel active material of the invention. Note that the preferred cell arrangement described here is illustrative and the invention is not limited thereby. Experiments are often performed, based on full and half cell arrangements, as per the following description. For test purposes, test cells are often fabricated using lithium metal electrodes. When forming cells for use as batteries, it is preferred to use an insertion positive electrode as per the invention and a graphitic carbon negative electrode.
A typical laminated battery cell structure 10 is depicted in Figure 22. It comprises a negative electrode side 12, a positive electrode side 14, and an electrolyte/separator 16 there between. Negative electrode side, 12 includes current collector 18, and positive electrode side 14 includes current collector 22. A copper collector foil 18, preferably. in the form of an-' open mesh grid, upon which is laid a negative electrode membrane 20 comprising an insertion material such 'as carbon or graphite or low-voltage lithium insertion compound, dispersed in a polymeric binder matrix. An electrolyte/separator film 16 membrane is preferably a plasticized copolymer. This electrolyte/separator preferably comprises a polymeric separator and a suitable electrolyte for ion transport. The electrolyte/separator is positioned upon the electrode element and is- covered with -a positive electrode membrane '24 comprising a composition of a finely divided lithium insertion compound in a polymeric binder matrix. An aluminum collector foil o grid 22 completes the assembly. Protective bagging material 40 covers the cell and prevents infiltration of air and moisture.
In another embodiment, a multi-cell battery configuration as per Figure 23 is prepared with copper current collector 51, negative electrode 53, electrolyte/separator 55, positive electrode 57, and aluminum current collector 59. Tabs 52 and 58 of the current collector elements form respective terminals for the battery structure. As used herein, the terms "cell" and "battery" refer to an individual cell comprising anode/electrolyte/cathode and also refer to a multi-cell arrangement in a stack.
The relative weight proportions of the components of the positive electrode are generally: 50- 90% by weight active material; 5-30% carbon black as the electric conductive diluent; and 3-20% binder chosen to . hold all particulate materials in contact with one another without degrading ionic conductivity. Stated ranges' are not critical, and the amount of active material in an electrode may range from 25-95 weight percent. The negative electrode comprises about 50-95% by weight of a preferred graphite, with the balance constituted by the binder. A typical electrolyte separator film comprises approximately two parts polymer for every one part of a preferred fumed silica. The conductive solvent comprises any number of suitable solvents and salts. Desirable solvents and salts are described in U.S. Patent Nos. 5,643,695 and 5,418,091. One example is a mixture of EC:DMC:LiPF6 in a weight ratio of about 60:30:10.
Solvents are selected to be used individually or in mixtures, and include dimethyl carbonate (DMC) , diethylcarbonate (DEC) , dipropylcarbonate (DPC) , ethylmethylc'arbonate (EMC) , ethylene carbonate (EC) , propylene carbonate (PC), butylene carbonate, lactones, esters, . glymes, sulfoxides, sulfolanes, etc. The preferred solvents are EC/DMC, EC/DEC, EC/DPC and EC/EMC. The salt content ranges from 5% to 65% by weight, ■■ preferably from 8% to 35% by weight. Those skilled in the art will understand that any number of methods are used to form films from the casting solution using conventional meter bar or doctor blade apparatus. It is usually sufficient to air-dry the films at moderate temperature to yield self-supporting films of copolymer composition. Lamination of assembled cell structures is accomplished -by conventional means by pressing between metal plates at a temperature of about 120-160°C. Subsequent, to lamination, the battery cell material may be stored either with the retained plasticizer or as a dry sheet after extraction of the plasticizer with a selective low-boiling point solvent. The plasticizer extraction solvent is not critical, and methanol or ether are often used.
Separator membrane element 16 is generally polymeric and prepared from a composition comprising a copolymer. A preferred composition is the 75 to 92% vinylidene fluoride with 8 to- 25% hexafluoropropylene copolymer (available commercially from Atochem North America as Kynar FLEX) and ah organic solvent plasticizer. Such a copolymer composition is also .preferred' for the preparation of the electrode membrane elements, since subsequent laminate interface compatibility is ensured. The plasticizing "solvent may be one of the various organic compounds commonly used as solvents for electrolyte salts, e.g., propylene carbonate or ethylene carbonate, as well as mixtures of these ■ compounds. Higher-boiling plasticizer compounds such as dibutyl phthalate, dimethyl phthalate, diethyl phthalate, and tris butoxyethyl phosphate are particularly suitable. Inorganic filler adjuncts, such as fumed alumina or silanized fumed silica, may be used to enhance the physical strength and melt viscosity of a separator membrane and, 'in some compositions, to increase the subsequent level of electrolyte solution absorption.
In the construction of a lithium-ion battery, a current collector layer of aluminum foil or grid is overlaid with a positive electrode film,' or membrane, separately prepared as a coated layer of a dispersion of insertion electrode composition. This is typically an insertion compound such as LiMn204 (LMO) , LiCo02, or LiNi02, powder in a copolymer matrix solution, which is dried to form the positive electrode. An electrolyte/separator membrane is formed as a dried coating of a composition comprising a solution containing VdF:HFP copolymer and a plasticizer solvent is then ' overlaid on the positive electrode film. A negative electrode membrane formed as a dried coating of a powdered carbon or other negative electrode material dispersion in a VdF:HFP copolymer matrix solution is similarly overlaid on the separator membrane layer. A copper, current collector foil' or grid is laid upon the negative electrode layer to complete the cell assembly.
Therefore, the VdF:HFP copolymer composition is used as a binder in all of the major cell components, positive electrode film, negative electrode film, and electrolyte/separator membrane. The assembled components are then heated under pressure to achieve heat-fusion bonding between the plasticized copolymer matrix electrode - and electrolyte components, and to the collector grids, to thereby form an effective laminate of cell elements. This produces an essentially unitary and flexible battery cell structure.
Examples of forming cells containing metallic lithium anode, insertion electrodes, solid electrolytes and liquid electrolytes can be found in U.S. Patent Nos. 4,668,595; 4,830,939; 4,935,317; 4,990,413; 4,792,504; 5,037,712; 5,262,253; 5,300,373; 5,435,054; 5,463,179; 5,399,447; 5,482,795 and 5,411,820; each of which is. incorporated herein by reference in its entirety. Note that the older generation of cells contained organic polymeric and inorganic electrolyte matrix materials., with the polymeric being most preferred. The polyethylene oxide of 5,411,820 is an example. More modern examples are the VdF:HFP polymeric matrix.
Examples of casting, lamination and formation of cells using VdF:HFP are as described in U.S. Patent Nos. 5,418,091; 5,460,904; 5,456,000; and 5,540,741;' assigned to Bell Communications Research, each of which is incorporated herein by reference in its entirety.
As described earlier, the electrochemical cell operated as per the invention, may be prepared in a variety of ways. In one embodiment, the negative electrode may be metallic lithium. In more desirable embodiments, the negative electrode is an insertion active material, such as, metal oxides and graphite. . When a metal oxide active material is used,' the components of the electrode are the metal oxide, electrically conductive carbon, and binder, in proportions similar to that described above for the positive electrode. In a preferred embodiment, the negative electrode active material is graphite particles. For test purposes, test cells are often fabricated using lithium metal electrodes. When forming cells for use as batteries, it is preferred to use an insertion metal oxide positive electrode and a graphitic carbon negative electrode. Various methods for fabricating electrochemical cells and batteries and for forming electrode components are described herein . The invention is not, however, limite.d by any particular fabrication method.
Formation of Active Materials
EXAMPLE I
Reaction 1 (a) . LiFeP04 formed from FeP04
. FeP04 + 0.5 Li2C03 + 0.5 C - LiFeP04 + 0.5 C02 + 0.5 CO
(a) Pre-mix reactants in .the following .proportions using ball mill. Thus,
1 mol FeP04 150 . 82g
0 . 5 mol Li2C03 36. 95g
0 .5 mol carbon 6 . Og
(but use 100% excess carbon - 12.0.0g)
(b) Pelletize powder mixture
(c) Heat pellet to 750°C at a rate of 2°/minute in flowing inert atmosphere (e.g. argon) . Dwell for 8 hours at 750°C, under argon.
(d) Cool to room temperature at 2°/minute under argon.
(e) Powderize pellet.
Note that at 750°C this is predominantly a^CO reaction. This reaction is able to be conducted at a temperature in a range of about
700°C to about 950°C in argon as shown, and also under other inert atmospheres such as nitrogen or vacuum. EXAMPLE II
Reaction 1(b) . LiFeP04 formed from Fe203
0.5 Fe203 + 0.5 Li2C03 + (NH4)2HP04 + 0.5 C → LiFeP04 + 0.5 C02 + 2 NH3 + 3/2 H20 + 0.5 CO
(a) Premix powders in the following proportions
0.5 mol Fe203 79.85g
0.5 mol Li2C03 36.95g
1 mol (NH4)2HP04 132.06g
0.5' mol carbon 6.00g
(use 100% excess carbon → 12.00g)
(b) Pelletize powder mixture
(c) Heat pellet to 750°C at a rate of 2°/minute in flowing inert atmosphere (e.g. argon) . Dwell for 8 hours at 75.0°C under argon.
(d) Cool to room temperature at 2°/minute under argon.
(e) ' Powderize
EXAMPLE III
Reaction 1(c). LiFeP04 - from Fe3(P04)2
Two steps: Part I. Carbothermal preparation of Fe3(P04)2
3/2 Fe203 + 2(NH4)2HP04 + 3/2 C - Fe3(P04)2 +
3/2 CO + 4NH3 + 5/2 H20
(a) Premix reactants in the following proportions 3/2 mol Fe203 239.54g
2 mol (NH4)2HP04 264.12g
3/2 mol carbon 18.00g
(use 100% excess carbon - 36.00g)
(b) Pelletize powder mixture
(c) Heat pellet to 800°C at a rate of 2°/minute in flowing inert atmosphere (e.g. argon) . Dwell for 8 hours at 750°C under argon.
(d) Cool to room temperature at 2°C/minute under argon .
(e) Powderize pellet.
Part II. Preparation of LiFeP04 from the Fe3(P04)2of Part I .
Li3P04 + Fe3(P04)2-3 LiFeP04
(a) Premix reactants in the following proportions 1 mol Li3P04 115.79g
1 mol Fe3(P04)2 357.48g
(b) Pelletize powder mixture (c) Heat pellet to 750°C at a rate of 2°/minute in flowing inert atmosphere (e.g. argon) . Dwell for 8 hours at 750°C under argon.
(d) Cool to room. temperature at 2°C/minute under 5 argon.
-(e) Powderize pellet.
EXAMPLE IV
Reaction 2 (a) . LiFeo.9Mgo.iPO4 (LiFe1_yMgyP04) formed from FeP04
10 0.5 Li2C03 + 0.9 FeP04 + 0.1 Mg(0H)2 + 0.1 (NH4) 2HP04 +
0.45C -* LiFe0.9Mg0.ιPO4 + 0.5CO2 + 0.45CO + 0.2NH3 + 0.25 H20
(a) Pre-mix reactants in the following proportions
0.50 mol Li2C03 = 36.95g
15 0.90 mol FeP04 = 135.74g
0.10 mol Mg(0H)2 = • 5.83g *
0.10 mol (NH4)2HP04 -= 1.32g
0.45 mol carbon = 5.40g
(use 100% excess carbon - 10.80g)
'20 (b) Pelletize powder mixture
(c) Heat to 750°C at a rate of 2°/minute in argon. Hold for 8 hours dwell at 750°C in argon
(d) Cool at a rate of 2°/minute (e) Powderize pellet.
EXAMPLE V
Reaction 2(b) . LiFeo.gMgo.iP04 (LiFe1_yMgyP04) formed from Fe203
0.50 Li2C03 + 0.45 Fe203 + 0.10 Mg (0H)2 + (NH4)2HP04 + 0.45C - LiFe0.9 g0.iPO4 + 0.5 COz + 0.45 CO + 2 NH3 + 1.6 H20
.(a) Pre-mix reactants in following ratio
0.50 mol Li2C03 . = 36.95g
0.45. mol Fe203 = 71.86g
0.10 mol Mg(0H)2 = 5.83g
1.00 mol (NH4)2HP04 - 132.06g 0.45 mol carbon = 5.40g
(use 100% excess carbon -+ 10.80g)
(b) . Pelletize powder mixture
(c) Heat to 750°C at a rate of 2°/minute in argon. Hold for 8 hours dwell at 750°C in argon
(d) Cool at a rate of 2°/minute
(e) Powderize pellet. EXAMPLE VI
Reaction 2(c) . LiFe0.9Mg0.iPO4 (LiFei_yMgyP04) formed from LiH2P04
1.0 LiH2P04 + 0.45 Fe203 + 0.10 Mg(OH)2 + 0.45C -
LiFe0.9Mg0.ιPO4 + 0.45 CO + 1.1 H20
(a) Pre-mix reactants in the following proportions
1.00 mol LiH2P04 = 103.93g
0.45 mol Fe203 = 71.86g 0.10 mol Mg(OH)2 , . 5.83g
0.45 mol carbon = 5.40g
(use 100% excess carbon - 10.80g)
(b) Pelletize powder mixture
(c) Heat to 750°C at a rate of 2°/minute in argon.
Hold for 8 hours dwell at 750°C in argon
(d) Cool at a rate of 2°/minute
(e) Powderize pellet.
EXAMPLE VII
Reaction 3. Formation of LiFe0.9Ca0.iPO4
(LiFei_yCayP04) from Fe203
0.50 Li2C03 + 0.45 Fe203 + 0.1 Ca(OH)2 + (NH4)2HP04 + 0-.45C - LiFeo.9Cao.iP04 + 0.5 C02 + 0.45 CO + 2 NH3 + 1.6 H20 (a) Pre-mix reactants in the following proportions
0.50 mol Li2C03 = 36.95g
0.45 mol Fe203 = 71.86g
0.10 mol Ca(OH)2 = 7.41g 1.00 mol (NH4)2HP04 = 132.06g
0.45 mol carbon = 5.40g
(100% excess carbon → 10.80g)
(b) Pelletize powder mixture
(c) Heat to 750°C at a rate of 2°/minute in argon.
Hold for 8 hours dwell at 750 °C in argon
(d) Cool at a rate of 2° /minute
(e) Powderize pellet.
EXAMPLE VIII
Reaction 4. Formation of LiFe0.9Zn0 1PO4
(LiFe1.yZnyP04) from Fe203.
0.50 Li2C03 + 0.45 Fe203 + 0.033 Zn3 (P04)2 +
0.933 (NH4)2HP04 + 0.45 C - LiFeQ.9Zno.iPO4 + 0.50 C02 +
0.45 CO + 1.866 NH3 + .1.2 H20
Pre-mix reactants in the following proportions
0.50 mol Li2C03 = 3β.95g
0.45 mol Fe203 = 71.86g
0.033 mol Zn3(P04)2 = 12.74g
0.933 mol (NH4)2HP04 = 123.21g 0.45 mol carbon = 5.40g
(100% excess carbon - 10.80g)
(b) Pelletize powder mixture
(c) Heat to 750°C at a rate of 2°/minute in argon. Hold for 8 hours dwell at 750°C in argon
(d) Cool at a rate of 2°/minute
(e) Powderize pellet.
EXAMPLE IX
Reaction 5. Formation of gamma-LiV205 (γ)
V205 + 0.5 Li2C03 + 0.25 C →' LiV205 + 3/4 C02
(a) Pre-mix alpha V205, Li2C03 and Shiwinigan Black (carbon) using ball mix with suitable media. Use a 25% weight excess of carbon over the reaction amounts above. For example, according to reaction above:
Need: 1 mol V205 181.88g
.- 0,5 mol Li2C03 ' 36.95g
0.25 mol carbon 3.00g
(but' use 25% excess carbon → 3.75g) (b) Pelletize powder mixture
(c) Heat pellet to 600°C in flowing argon (or other inert atmosphere) at a heat rate of approximately 2°/minute. Hold at 600°C for- about 60 minutes.
(d) Allow to cool to room temperature in argon at cooling rate of about 2°/minute.
(e) Powderize pellet using, mortar and pestle
This reaction is able to be conducted at a temperature in a range of about 400°C to about 650°C in argon as^shown, and also under other inert atmospheres such as nitrogen or vacuum. This reaction at this temperature range is primarily C - C02. Note that the reaction C - CO primarily occurs at a temperature over about 650°C (HT, high temperature) ; and the reaction C - C02 primarily occurs at- a temperature of under about 650°C (LT, low temperature) . The reference to about 650 °C is approximate and the ' designation "primarily" refers to the predominant reaction thermodynamically favored although the alternate reaction may occur to some extent .
EXAMPLE X
Reaction 6 . Formation of Li3 3VV 22
Figure imgf000043_0001
l 3
V205 + 3 /2 Li2C03 + 3 (NH4 ) 2HP04 + C - Li3V2 ( P04 ) 3 + 2 CO + 3 /2 C02 + 6 NH3 + 9 /2 H20 ■ (a ) Pre-mix reactants above using ball mill with suitable media ." Use a 25% weight exces s of carbon . Thus ,
1 mol V205 181 . 88g 3/2 mol Li2C03 110 . 84g
3 mol (NH4) 2HP04 396. 18g
1 mol carbon 12 . 01g
(but use 25% excess carbon - 15.01g)
(b) Pelletize powder mixture
(c) Heat pellet at 2°/minute to 300°C to remove C02
(from Li2C03) and to remove NH3, H20. Heat in' an inert atmosphere (e.g. argon). Cool to room temperature.
(d) Powderize and repelletize
(e) Heat pellet in inert atmosphere at a rate of
2°C/minute to δ50°C. Dwell' for δ hours at δ50°C
(f) Cool to room temperature at a rate of 2°/minute in argon.
(e) Powderize
This reaction is able to be conducted at a temperature in a range of about '700°C to about 950°C in argon as shown, and also under other inert atmospheres such as nitrogen or vacuum. A reaction temperature greater than about 670°C ensures C → CO reaction is primarily carried out. Characterization of Active Materials and Formation and Testing of Cells
Referring to Figure 1, the final product LiFeP04, prepared from Fe203 metal compound per Reaction 1(b), appeared brown/black in color. This olivine material product included carbon that remained after reaction. Its CuKα x-ray diffraction pattern contained all of the peaks expected for this material as shown in Figure 1. The pattern evident in Figure 1 is consistent with the single phase olivine phosphate, LiFeP04. This is evidenced by the position of the peaks in terms of the scattering angle 2 θ (theta) , x axis. The x-ray pattern showed no peaks due to the presence of precursor oxides indicating that the solid state reaction is essentially entirely completed. Here the space group SG = pnma (62) and the lattice parameters from XRD refinement are consistent with the olivine structure. The values are a = 10.2δδ3A (0.0020), b = 5.9759 (0.0037), c = 4.6717A (0.0012) 0.0072, cell volume = 2δ7.2264A3 (0.0685). Density, p = 3.605 g/cc, zero = 0.452 (0.003). Peak at full width half maximum, PFWHM = 0.21. Crystallite size from XRD data = 704A.
The x-ray pattern demonstrates that the product of the invention was indeed the nominal formula LiFeP04. The term "nominal formula" refers to the fact that the relative proportion of atomic species may vary slightly on the order of 2 percent to 5 percent, or more typically, 1 percent to 3 percent, and that some portion of P may be substituted by Si, S or As; and some portion of may be substituted by halogen, preferably F. The LiFeP04, prepared as described immediately above, was tested in an electrochemical cell. The positive electrode was prepared as described above, using 19.0mg of active material. The positive electrode contained, on a weight % basis, 65% active material, 10% carbon black, and 5% EPDM. The negative electrode was metallic lithium. The electrolyte was a 2:1 weight ratio mixture of ethylene carbonate and dimethyl carbonate - within which was dissolved 1 molar LiPF6. The cells were cycled between about 2.5 and about 4.0 volts with performance as shown in Figures 2 and 3.
Figure 2 shows the results of the first constant current cycling at 0.2 milliamps per square" centimeter between about 2.5 and 4.0 volts based upon about 19 milligrams of the LiFeP04 active material in the cathode (positive electrode) . In an as prepared, as assembled, initial condition, the positive electrode active material is LiFeP04. The lithium is extracted from the LiFeP04 during charging of the cell. When fully charged, about 0.72' unit of lithium had been removed per formula unit. Consequently, the positive electrode active material corresponds to Lii_xFeP04 where x appears to be equal to about 0.72, when the cathode material is at 4.0 volts versus Li/Li+. The extraction represents approximately 123 milliamp hours per gram corresponding to about 2.3 milliamp hours based on 19 milligrams active material. Next, the cell is discharged whereupon a quantity of lithium is re-inserted into the LiFeP04. The re-insertion corresponds to approximately 121 miiliamp hours per gram proportional to the insertion of essentially all of the lithium. The bottom of the curve corresponds to approximately 2.5 volts. The total cumulative capacity demonstrated during the entire extraction-insertion cycle is 244mAh/g.
Figure 3 presents data obtained by multiple constant current cycling at 0.2 milliamp hours per square centimeter of the LiFeP04 versus lithium metal counter electrode between 2.5 and 4.0 volts. Data is shown for two temperatures, 23°C and 60°C. Figure 3 shows the excellent rechargeability of the LiFeP04 cell, and also shows good cycling and capacity of the cell. The performance shown after about 190 to 200 cycles is good and shows that electrode formulation is very desirable.
Referring to Figure 4, there is shown data for the final product LiFe0.9Mg0.iPO4, prepared from the metal compounds Fe203 and Mg(OH), → Mg(OH)2, per Reaction 2(b) . Its CuKα x-ray diffraction pattern contained all of the peaks expected for this material as shown in Figure' 4. The pattern evident in Figure 4 is consistent with the single phase olivine phosphate compound, LiFe0.9Mg0.ιPO4. This is evidenced by the position of "the peaks in terms of the scattering angle 2 θ (theta) , x. axis. The x-ray pattern showed no peaks due to the presence of precursor oxides indicating that the solid state reaction is essentially entirely completed. Here the space group SG = Pnma (62) and the lattice parameters from XRD refinement are consistent with the olivine structure. The values are a = 10.26δ8λ (0.0069), b =.5.9709A (0.0072), c = 4.6762A (0.0054), cell volume = 286.7208A (0.04294), p = 3'.617 g/cc, zero = 0.702 (0.003), PFWHM = 0.01, and crystallite = 95θΛ.
The x-ray pattern demonstrates that the product of the invention was indeed the nominal formula LiFe0.9Mg0.ιPO4. The term "nominal formula" refers to the fact that the relative proportion of atomic species may vary slightly on the order of 2 percent to 5 percent, or more -typically, 1 percent to 3 percent, and that some substitution of P and 0 may be made while maintaining the basic olivine structure.
The 'LiFe0.9Mg0.iPO4, prepared as described immediately above, was tested in an electrochemical cell. The. positive electrode was prepared as described above, using 18.9mg of active materials. The positive electrode, negative electrode and electrolyte were prepared as described earlier and in connection with Figure 1. The cell was between about 2.5 and about 4.0 volts with performance as shown in Figures 4, 5 and 6.
Figure 5 shows the results of the first constant current cycling at 0.2 milliamps per square centimeter between about 2.5 and 4.0 volts based upon about 18.9 milligrams of the LiFe0.9Mg0.ιPO4 active material in the cathode (positive electrode) . In an as- prepared, as assembled, initial condition, the positive electrode active material is LiFe0.9Mg0.ιPO4. The lithium is extracted from the 'LiFe0.9Mgo.ιP04 during charging of the cell. When fully charged, about 0.87 units of lithium have been removed per formula unit. Consequently, the positive electrode active material corresponds to Liι_xFe0.9Mg0.iPθ4 where x appears to be equal to about 0.87, when th cathode material is at 4.0 volts versus Li/Li+. The extraction represents approximately 150 milliamp hours per .gram corresponding to about 2.8 milliamp hours based on 18.9 milligrams active material. Next, the cell is discharged whereupon a quantity of lithium is re-inserted into the LiFe0.9Mgo.ιP04 ' . The re- insertion corresponds to approximately 146 milliamp hours per gram proportional to the insertion of essentially all of the lithium. The bottom of the curve corresponds to approximately 2.5. volts. The total cumulative specific capacity over the entire cycle is 296 mAhr/g. This material has a much better cycle profile than the LiFeP04. Figure 5 (LiFe0.9Mg0.ιPO4) shows a very well defined and sharp peak at about 150 mAh/g. In contrast, Figure 2 (LiFeP04) shows a very shallow slope leading to the peak at about 123 mAh/g. The Fe-phosphate (Figure 2) provides 123 mAh/g compared to its theoretical capacity of 170 mAh/g. This ratio of 123/170, "72% is relatively poor compared to the Fe/Mg-phosphate . The Fe/Mg- phosphate (Figure 5) provides 150 mAh/g compared to a theoretical capacity of 160, a ratio of 150/160 or 94%.
Figure 6 presents data obtained by multiple constant current cycling at 0.2 milliamp hours per square centimeter of the LiFe0.9Mg0.ιPO4 versus lithium metal counter electrode between 2.5 and 4.0 volts. Figure 6 shows the excellent rechargeability of the
Li/LiFe0.9Mg0.ιPO4 cell, and also shows good cycling and capacity of the cell. The performance shown after about 150 to 160 cycles is very good and shows that electrode formulation LiFe0.9Mg0.ιPO4 performed significantly better than the LiFeP04. Comparing Figure 3 (LiFeP04) to Figure 6 (LiFe0.9Mg0.iPO4) it can be seen that the Fe/Mg-phosphate maintains its capacity .over prolonged cycling, whereas the Fe-phosphate capacity fades significantly.
Figure 7 shows the results of the first constant current cycling at 0.2 milliamps per square centimeter between about 2.5 and 4.0 volts based upon about 16 milligrams of the LiFe0.8Mg0.2PO4 active material in the cathode (positive electrode) . In an as prepared, as. assembled, initial condition, the positive electrode active material is LiFe0.8Mg0.2PO4. The lithium is extracted from the LiFe0.8Mg02PO4 during charging of the cell. When fully charged, about 0.79 units of lithium have been removed per formula unit. Consequently, the positive electrode active material corresponds to LiFe0.8 g0.2PO4 where x appears to be equal to about 0.79, when the cathode material is at 4.0 volts versus Li/Li+. The extraction approximately 140 milliamp hours per gram corresponding to about 2.2 milliamp hours based on 16 milligrams active material. Next, the cell is discharged whereupon a quantity of lithium is re-inserted into the LiFe0.8Mg0.2PO4. The re-insertion corresponds to approximately 122 milliamp hours per gram proportional to the insertion of essentially all of the lithium. The • bottom of the curve corresponds to approximately 2.5 volts. The total cumulative specific capacity over the entire cycle is 262 mAhr/g.
Referring to Figure 8, there is shown data for the final product LiFe0.9Ca0.ιPO4, prepared from Fe203 and Ca(OH)2 by Reaction 3. Its CuKα x-ray diffraction pattern contained all of the peaks expected for this material as shown in Figure 8. The pattern evident in Figure 8 is consistent with the single phase olivine phosphate compound, LiFe0.9Ca0.iPO4. This is evidenced by the position of the peaks in terms of the scattering angle 2 θ (theta) , x axis. The x-ray pattern showed no peaks due to the presence of precursor oxides indicating that the solid state reaction is essentially entirely completed. Here the space group SG = Pnma (62) and the lattice parameters from XRD refinement are consistent with olivine. The values are a = 10.324θΛ (0.0045), b = 6.0042A (0.0031), c = 4.6887A (0.0020), cell volume = 290.6370A (0.1807), zero = 0.702 (0.003), p = 3.62 g/cc, PFWHM = 0.18, and crystallite = 680A. The x-ray pattern demonstrates that the product of the invention was indeed the nominal formula LiFe0.9Ca0.ιPO4.
Figure 9 shows the results of the first constant current cycling at 0.2 milliamps per square centimeter between about 2.5 and 4.0 volts based upon about 18.5 milligrams of the LiFe0.8Ca0.2PO4 active material in the cathode (positive electrode) . In an as prepared, as assembled, initial condition, the positive electrode active material is LiFe0.8Ca0.2PO4. The lithium is extracted from the LiFe0.8Ca0.2PO4 during charging' of the cell. When fully charged, about 0.71 units of lithium have been removed per formula unit.
Consequently, the positive electrode active material corresponds to LiFe0.8Ca0.2PO4 where x appears to be equal to about 0.71, when the cathode material is at 4.0 volts versus Li/Li+. The extraction represents approximately 123 milliamp hours per gram corresponding to about 2.3 milliamp hours based on 18.5 milligrams active material. Next, the cell is discharged whereupon a quantity,- of lithium is re-inserted into the LiFe0.8Ca0.2PO4. The reinsertion corresponds to approximately 110 milliamp hours per gram proportional to the insertion of nearly all of the lithium. The bottom of the curve corresponds to approximately 2.5 volts. The total specific cumulative capacity over the entire cycle is 233 mAhr/g.
Figure 10 shows the results of the first constant current cycling at 0.2 milliamps per square centimeter between about 2.5 and 4.0 volts based upon about 18.9 milligrams of the LiFe0.8Zn0.2PO4 olivine active material in the cathode (positive electrode) . In an as prepared, as assembled, initial condition, the positive electrode active material is LiFe0.8Zn0.2PO4, prepared from Fe203 and Zn3(P04)2 by Reaction 4. The lithium is extracted from the LiFe0.8Zn0.2PO4 during charging of the cell. When fully charged, about 0.74 units of lithium have been removed per formula unit. Consequently, the positive electrode active material corresponds to Lii_ xFe0. δZn0.2PO4 where x appears to be equal to about 0.74, when the cathode material is at 4.0 volts versus Li/Li+. The extraction represents approximately 124 milliamp hours per gram corresponding to about 2.3 milliamp hours based on 18.9 milligrams active material. Next, the cell is discharged whereupon a quantity of lithium is re— inserted into the LiFe0.8Zn0.2PO4. The re-insertion corresponds to approximately 108 milliamp hours per gram proportional to the insertion of nearly all of the lithium. The bottom of the curve corresponds to approximately 2.5 volts.
Referring to Figure 11, the- final product
LiV205, prepared by Reaction 5, appeared black in color. Its CuKα x-ray diffraction pattern contained all of the peaks expected for this material as shown in Figure 11. The pattern evident in Figure 11 is consistent with a single oxide compound gamma-LiV205. This is evidenced by the. position of the peaks in terms of the scattering angle 2 θ (theta) , x axis. The x-ray pattern showed no peaks due to the presence of precursor oxides indicating that the solid state reaction is essentially entirely completed.
The x-ray pattern demonstrates that the product o -the invention was indeed the nominal formula gamma- LiV205. The term "nominal formula" refers to the fact that the relative proportion of atomic species may vary slightly on the order of 2 percent to 5 percent, or more typically, 1 percent to 3 percent.
The LiV205 prepared as described immediately above, was tested in an electrochemical cell. The cel.l was prepared as described above and cycled with performance as shown in Figures 12 and 13.
Figure 12 shows the. results of the first - constant current cycling at 0.2 milliamps per square
) centimeter between about 2.8 and 3.8 volts based upon about 15.0 milligrams of the LiV205 active material in the cathode (positive electrode) . In an as prepared, as assembled, initial condition, the positive electrode active material is LiV205. The lithium is extracted from the LiV205 during charging of the cell. When fully charged, about 0.93 unit of lithium had been removed per formula unit. Consequently, the positive electrode active material corresponds to Lii_xV205 where x appears to be equal to about 0.93, when the cathode material is at 3.8 volts versus Li/Li+. The extraction represents approximately 132 milliamp hours per gram corresponding to about 2.0 milliamp hours based on 15.0 milligrams- active material. Next, the cell is discharged whereupon a quantity of lithium is re-inserted into the LiV205. The re-insertion corresponds to approximately 130 milliamp hours per gram proportional to the insertion of essentially all of the lithium. The bottom of ' the curve, corresponds to approximately 2.8 volts.
Figure 13 presents data obtained by multiple constant current cycling at 0.4 milliamp hours per square centimeter (C/2 rate) of the LiV205 versus lithium metal counter electrode between 3.0 and 3.75 volts. Data for two temperature conditions are shown, 23°C and 60°C. Figure 13 is a two part graph with Figure 13A showing the excellent rechargeability of the LiV205. Figure 13B shows good cycling and capacity of the cell. The performance shown up to about 300 cycles is good.
Referring to Figure 14, the final product Li3V2 (P04) 3, prepared by Reaction 6, appeared green/black in color. Its CuKα x-ray diffraction pattern contained all of the peaks expected for this material. as shown in Figure 14. The pattern' evident in Figure 14 is consistent with a single phosphate compound Li3V2(P04)3 of the monoclinic, Nasicon phase. This is evidenced by the • position of the peaks in terms of the scattering angle 2 θ (theta) , x axis. The x-ray pattern showed no peaks due to the presence of precursor oxides indicating that the solid state reaction is essentially entirely completed.
The x-ray pattern demonstrates that the product of the invention was indeed the nominal formula
Li3V2 (P04) 3. The term "nominal formula" refers to the fact that the relative proportion, of atomic species may vary slightly oh the order of 2 percent to 5 percent, or more typically, 1 percent to 3 percent; and that substitution of P and 0 may occur.
The Li3V2 (P04) 3 prepared as described immediately above, was tested in an electrochemical cell. The cell was prepared as described above, using 13.δmg of active material. The cell was prepared -as described above and cycled between about 3.0 and about 4.2 volts using the
EVS technique with .performance as shown in Figures 16 and 17. Figure 16 shows specific capacity versus electrode potential against Li. Figure 17 shows differential capacity versus electrode potential against Li.
A comparative method was used to form Li3V2(P04)3. Such method was reaction without carbon and under H2-reducing gas as described in U.S. Patent No. 5,871,866. The final product, prepared as per U.S. Patent No. 5,871,δ66, appeared green in color. Its CuKα x-ray diffraction pattern contained all of the peaks expected for this material as shown in Figure 15. The pattern evident in Figure 15 is consistent with a- monoclinic Nasicon single phase phosphate compound Li3V2(P04)3. This is evidenced by the position of the peaks in terms of the scattering angle 2 θ (theta) , x axis. The x-ray pattern showed no peaks- due to the presence of precursor oxides indicating that the solid state reaction is essentially entirely completed. Chemical analysis for lithium and vanadium by atomic absorption spectroscopy showed, on a percent by weight basis, 5.17 percent lithium and 26 percent vanadium. This is close to the expected result of 5.11 percent lithium and 25 percent vanadium.
The chemical analysis' and x-ray patterns of Figures 14 and.15 demonstrate that the product of Figure 14 was the same as that of Figure 15. The product of Figure 14 was prepared without the undesirable H2 atmosphere and was prepared by the novel carbothermal solid state synthesis of the invention.
Figure 16 shows a voltage profile of the test cell, based on the Li3V2(P04)3 positive electrode active material made by the process of the invention and as characterized in Figure 14. It was cycled against a lithium metal counter electrode. The data shown in Figure 16 is based on the Electrochemical Voltage Spectroscopy (EVS) technique. Electrochemical and kinetic data were recorded using the Electrochemical
Voltage Spectroscopy (EVS) technique. Such technique is -known in the art as described by J. Barker in Synth, Met 2δ, D217 (1989); Synth. Met. 32, 43 (1989); J. Power Sources, 52, 185 (1994); and Electrochemica Acta, Vol. 40, No. 11, at 1603 (1995) . Figure 16 clearly shows and highlights the reversibility of the product. The positive electrode contained about 13.8 milligrams of the Li3V2(P04)3 active material. The positive electrode showed a performance of about 133 milliamp hours per gram on the first discharge. In Figure 16, the capacity in, and the capacity out are essentially the same, resulting in essentially no capacity loss; Figure 17 is an EVS differential capacity plot based on Figure 16. As can be seen from Figure 17, the relatively symmetrical nature of peaks indicates good electrical " reversibility, there are small peak separations (charge/discharge) , and good correspondence between peaks above and below the zero axis. There are essentially no peaks that can be related to irreversible reactions, since all peaks above the axis (cell charge) have corresponding peaks below the axis
(cell discharge) ,. and there is essentially no separation between the peaks above and below the axis . This shows that the carbothermal method of the invention produces high quality electrode material.
Figure 18 presents data obtained by multiple constant current cycling, at 0.2 milliamp hours per square centimeter of the LiFe0.8Mg0.2PO4 versus lithium metal counter electrode between 2.5 and 4.0 volts. Figure 18 shows the excellent rechargeability of the Li/LiFeQ.8Mgo.2P04 cell, and also shows good cycling and capacity of the cell. The performance shown after about 110 to 120 cycles at 23°C is very good and shows that electrode formulation LiFe0.8MgQ.2PO4 performed significantly better than the LiFeP04. The cell cycling test at 60°C was started after the 23°C test and was ongoing. Comparing Figure 3 (LiFePO to Figure 18 (LiFeQ.8Mg0.2PO4) , it can be seen that the Fe/Mg-phosphate maintains its capacity over prolonged cycling, whereas the Fe-phosphate capacity fades significantly.
In addition to the above cell tests, the^ active materials of the invention were also cycled, against insertion anodes in non-metallic, lithium ion, rocking chair cells.
The lithium mixed metal phosphate and the lithium metal oxide were used to formulate a cathode electrode. The electrode was fabricated by solvent casting a slurry of the treated, enriched lithium manganese oxide, conductive carbon, binder, plasticizer and solvent. The conductive carbon used was Super P (MMM Carbon). Kynar Flex 2801® was used as the binder and electronic grade acetone was used as a solvent. The preferred plasticizer was dibutyl phthalate (DPB) . The slurry was cast .onto glass and a free-standing electrode was formed as the solvent was evaporated. In this example, the cathode had 23.1mg LiFe0.9Mgo.ιp°4 active material. Thus, the proportions are as follows on a percent weight basis: 80% active material; 8% Super P carbon; and 12% Kynar binder. A graphite counter electrode was prepared for use with the aforesaid cathode. The graphite counter electrode served as the anode in the electrochemical cell. The anode had 10.8 mg of the MCMB graphite active 5 material. The graphite electrode was fabricated by solvent casting a slurry of MCMB2528 graphite, binder, and casting solvent. MCMB2528 is a mesocarbon microbead material supplied by Alumina Trading, which is the U.S. distributor for the supplier, Osaka Gas Company of Japan. 0 This material has a density of about 2.24 grams per cubic centimeter; a particle size maximum for at least 95% by weight of the particles of 37 microns; median size of about 22.5 microns and an interlayer distance of about 0.336. As in the case of the cathode, the binder was a
15 copolymer of polyvinylidene difluoride (PVdF) and hexafluoropropylene (HFP) in a wt . ratio of PVdF to HFP of 88:12. This binder is sold under the designation of Kynar Flex 2801®, showing it's a registered trademark. Kynar Flex is available from Atochem Corporation. An 0 electronic grade solvent was used. The slurry was cast onto glass and a free standing electrode was formed as the casting solvent evaporated. The electrode composition was approximately as follows on a dry weight basis: 85% graphite; 12%. binder; and 3% conductive
25 carbon.
A rocking chair battery was prepared comprising the anode, the cathode, and an electrolyte. The ratio of the active cathode mass to the active anode mass was about 2.14:1. The two electrode layers were arranged 30. with an electrolyte layer in between, and the layers were laminated together using heat and pressure as per the Bell Comm. Res. patents incorporated herein by reference earlier. In a preferred method, the cell is activated with EC/DMC solvent in a weight ratio of 2 : 1 in' a solution containing 1 M LiPF5 salt.
Figures 19 and 20 show data for the first four complete cycles of the lithium ion cell having the LiFeo.9Mgo.iPO4 cathode and the MCMB2528 anode. The cell comprised 23.1mg active LiFe0.9Mg0.iPO4 and 10-. δ g active MCMB2528 for a cathode to anode mass ratio of 2.14. The cell was charged and discharged at 23°C at an approximate C/10 (10 hour) rate between voltage limits of 2.50 V and 3.60 V. The voltage profile plot (Figure 19) shows the variation in cell voltage versus time for the LiFe0.9Mg0.ιPO4/MCMB2528 lithium ion cell. The symmetrical nature of the charge-discharge is clearly evident. -The small degree of voltage hysteresis between the charge and discharge processes is evidence for the low overvoltage in the system, which is very good. Figure 20 shows the variation of LiFeQ.9Mgo.iPO4 specific capacity with cycle number.' Clearly, over the cycles shown, the material demonstrates good cycling stability.
Figure 21 shows data for the first three complete cycles of the lithium ion cell having the ga ma- LiV205 cathode and the MCMB2528 anode. The cell prepared was a rocking chair, lithium ion cell as described above. The cell comprised 29.1mg gamma-LiV205 cathode active material and 12.2mg MCMB252δ anode active material, for a cathode to anode mass ratio of 2.39. As stated earlier, the liquid electrolyte used was EC/DMC (2:1) and 1M LiPF5. The cell was charged and discharged at 23°C at an approximate C/10 (10 hour) rate between voltage limits of 2.50 V and 3.65 V. The voltage profile plot (Figure 21) shows the variation in cell voltage versus time for the LiV205/MCMB2528 lithium ion cell. The symmetrical nature of the charge-discharge is clearly evident. The small degree of voltage hysteresis between the charge and discharge processes is evidence for the low overvoltage in the system, which is very good.
In summary, the invention provides new compounds LiaMIbMIIc (P04) d and gamma-LiN205 by new methods which are adaptable to commercial scale production. The LiιMIι_yMIIyP04 compounds are isostructural olivine compounds as demonstrated by XRD analysis. Substituted compounds, such as LiFei_yMgyP04 show better performance than LiFeP04 unsubstituted compounds when used as electrode active materials . The method of the invention utilizes the reducing capabilities of carbon along with selected precursors and reaction conditions to produce high quality products suitable as electrode active materials or as ion conductors. The reduction capability of carbon over a broad temperature range is selectively applied along with thermodynamic and kinetic considerations to provide an energy-efficient, economical and convenient process to produce compounds of a desired composition and structure. This is in contrast to known methods .
Principles of carbothermal reduction have been applied to produce pure metal from metal oxides by removal of oxygen. See, for example, U.S. Patent Nos. 2,580,δ7δ, 2,570,232, 4,177,060, and 5, 603, 974. Principles of carbothermal and thermal reduction have also been used to form carbides. See, for example, U.S. Patent Nos. 3,865,745 and 5,384,291; and non-oxide ceramics (see U.S. Patent No. 5,607,297). Such methods are not known to have been applied to form lithiated products or to form products without oxygen abstraction from the precursor. The methods described with respect to the present invention provide high quality products which are prepared from precursors which are lithiated during the reaction without oxygen abstraction. This is a surprising result. The new methods of the invention also provide new compounds not known to have been made before.
For example, alpha-V205 is conventionally lithiated electrochemically against metallic lithium. Thus, alpha-V205 is not suitable as a source. of lithium for a cell. As a result, alpha-V205 is not used in an ion cell. In the present invention, alpha-V205 is lithiated by carbothermal reduction using a simple lithium-containing compound and the reducing capabiLity of carbon to form a gamma-LiV205. The single phase compound, gamma-LiV205 is not known to have been directly and independently prepared before. There is not known to be a direct synthesis route. Attempts to form it as a single phase resulted in a mixed phase product containing one or more beta phases and having the formula LixV205 with 0 < x ≤ 0.49. This is far different from the present single phase gamma-LixV205 with x equal to one, or very close to one. The flexibility of the process of the present invention is such that it can be conducted over a wide temperature range. The higher the temperature, the more quickly the reaction proceeds. For example, at
650°C, conversion of alpha-V205 to gamma-LiV205 occurs in about one hour, and at 500° it takes about 8 hours. Here, .about one quarter (1/4) atomic unit of carbon is used to reduce one atomic unit of vanadium, that is, v+5V+5 to V+5V+4. The predominate reaction is C to C02 where for each atomic unit of carbon at ground state zero, a plus 4 oxidation state results. Correspondingly, for each 1/4 atomic unit of carbon, one atomic unit of vanadium is reduced from V+5 to V+ . (See Reaction 5) . The new product, gamma-LiV205 is air-stable and suitable as an electrode material for an ion cell or rocking chair battery.
The convenience and energy efficiency of the present process can also be contrasted to known methods for forming products under reducing atmosphere such as H2 which is difficult to control, and from complex and expensive precursors. In the present invention, carbon is the reducing agent, and simple, inexpensive and even naturally occurring precursors are useable. For example, it is possible to produce LiFeP04 from Fe203, a simple common oxide. (See Reaction lb). The production of, LiFeP04 provides a good example of the thermodynamic and kinetic features of the method. Iron phosphate is reduced by carbon .and lithiated over a broad temperature range. At about 600°C, the C to C02 reaction predominates and takes about a week to complete. At about 750°C, the C to CO reaction predominates and takes about δ hours to complete. The C to C02 reaction requires less carbon reductant but takes longer due to the low temperature kinetics. The C to CO reaction requires about twice as much carbon, but due to the high temperature reaction kinetics, it proceeds relatively fast. In both cases, the Fe in the precursor Fe203 has oxidation state +3 and is reduced to oxidation (valence) state. +2 in the product LiFeP04.- The C to CO reaction requires that atomic unit of carbon be used for each atomic unit of Fe reduced by one valence state. The CO to ,C02 reaction requires that 1/4 atomic unit of carbon be used for each atomic unit of Fe reduced by one valence state . The active materials of the invention are also characterized by being stable in an as-prepared condition, in' the presence of air and particularly humid air. This is a striking advantage, because it facilitates preparation of and assembly of battery cathodes and cells, without the requirement for controlled atmosphere. This feature is particularly important, as those skilled in the art will recognize that air stability, that is, lack of degradation on exposure to air, is very important for commercial processing. Air-stability is known in the art to more specifically indicate that a material does not hydrolyze in presence of moist air. Generally, air-stable materials are also characterized by Li being extracted therefrom above about 3.0 volts versus lithium. The higher the extraction potential, the more tightly bound the lithium ions are to the host lattice. This tightly bound property generally confers air stability on the material. The air-stability of the materials of the ' invention is consistent with the stability demonstrated by cycling at- the conditions stated herein. This"- is in contrast to materials which insert Li at lower voltages, below about 3.0 volts versus lithium, and which are not air-stable,' and which hydrolyze in moist air.
While this invention has been described in terms of certain embodiments thereof, it is not intended that it be limited to the above description, but rather -only to the extent set forth in the following claims.
The embodiments of the invention in which an exclusive property or privilege is claimed are defined in the following claims.

Claims

What Is Claimed Is:
1. A method of making a lithium mixed metal compound by reaction of starting materials which comprises: mixing starting materials in particle form, said starting materials comprising a metal compound, a lithium compound having a melting point greater than 450°C, and carbon, where said carbon is present in an amount sufficient to reduce the oxidation state of at least one metal ion of said starting materials without full reduction to an elemental state; and heating said starting materials in a non-oxidizing atmosphere at a temperature sufficient to form a reaction product comprising lithium and said reduced metal ion.
2. The method of claim 1 wherein said lithium compound is selected from the group consisting of lithium carbonate, lithium phosphate, lithium' oxide, lithium vanadate, and mixtures thereof.
3. The method of claim 1 wherein said metal compound is a compound of a metal selected from the group consisting of Fe, Co, Ni, Mn, Cu, V, Sn, Ti, Cr, and mixtures thereof.
4. The method of claim 3 wherein said metal compound is selected from the group consisting of Fe203, V205, FeP04, V02, Fe304, LiV03, NH4V03, and mixtures .thereof.
5. The method of claim 1 wherein said starting materials include a second metal compound having a second metal ion which is not reduced and which forms a part of said reaction product.
6. The method of claim 1 wherein said starting materials include a second metal compound which is a compound of a metal selected from the group consisting of Mg, Ca, Zn, Sr, Pb, Cd, Sn, Ba, Be, and mixtures thereof.
7. The method of claim 6 wherein said second metal compound is selected from the group consisting of magnesium hydroxide and calcium hydroxide.
δ . The method of claim 1 wherein said starting materials include a phosphate compound and said reaction product is a lithium metal phosphate.
9. The method of claim δ wherein said phosphate compound is selected from the group consisting of diammonium hydrogen phosphate, ammonium dihydrogen phosphate, lithium dihydrogen phosphate, and mixtures thereof.
10. The method of claim 1 wherein said metal compound is a metal oxide or a metal phosphate.
11. The method of claim 1 wherein said metal compound is V205, and said lithium compound is lit-hium carbonate .
12. The method of claim 1 wherein said mixing and heating are conducted in a first stage by mixing starting materials consisting of iron oxide, diammonium hydrogen phosphate and carbon and heating said first . stage mixed starting materials at a temperature sufficient to produce iron phosphate; and in a second stage by mixing starting materials consisting of said iron phosphate and lithium phosphate and heating said second stage mixed starting materials at a temperature sufficient to form lithium iron phosphate represented by the nominal formula LiFeP04.
13. A method of making a lithium mixed metal compound by reaction of starting materials which comprises: mixing starting materials in particle form, said starting materials comprising a metal compound; a lithium compound; carbon present in an amount sufficient to reduce the oxidation state of at least' one metal ion of said starting materials without full reduction to an elemental state; and a compound containing a polyanion capable of forming a crystal lattice; and heating said starting materials in a non- oxidizing atmosphere at a temperature sufficient to form a single phase reaction product comprising lithium, said reduced metal ion, and said polyanion.
14. The method of claim 13 wherein said lithium compound is lithium carbonate, said metal compound is a metal oxide, and said polyanion-containing compound is a phosphate compound.
15. The method of claim 13 wherein said starting materials consist of: iron oxide; a hydroxide selected from the group consisting of magnesium hydroxide and calcium hydroxide; lithium carbonate; a phosphate selected from the group consisting of diammonium hydrogen phosphate and ammonium dihydrogen phosphate; and carbon.
16. The method of claim 13 wherein said starting materials consist of: lithium carbonate; iron phosphate; diammonium hydrogen phosphate; a hydroxide selected from the group consisting of magnesium hydroxide and calcium hydroxide; and carbon.
17. The method of claim 13 wherein said starting materials comprise: two of said metal compounds, the first being an oxide of a transition metal selected from Groups 4 to 11 inclusive of the Periodic Table having a +2 valence state, and the second being a compound of a metal selected from Groups 2, 12, and 14 of the Periodic Table having a +2 valence state; said lithium compound selected from the group consisting of lithium carbonate and lithium dihydrogen phosphate; and said polyanion containing compound selected from the group consisting of diammonium hydrogen phosphate, ammonium dihydrogen phosphate, lithium dihydrogen phosphate, and mixtures thereof.
18. The method of claim 13 wherein said starting materials consist of lithium carbonate, iron oxide and a phosphate of a metal selected from the group consisting of Mg, Ca, Zn, Sr, Pb, Cd, Sn, Ba, Be, and mixtures thereof.
19. A method of making a single phase compound which comprises: mixing starting materials in particle form, said starting materials comprising a metal compound, a lithium compound selected from the group consisting of lithium acetate (LiOOCCH3) , lithium nitrate
(LiN03) , lithium oxalate (Li2C204) , lithium oxide (Li20) , lithium phosphate (Li3P04) , lithium dihydrogen phosphate (LiH2P04) , lithium vanadate (LiV03) , and lithium carbonate (Li2C02) , and carbon present in an amount sufficient to reduce the oxidation state of at least one metal ion of said starting materials without full reduction to an elemental state; and heating said starting materials in a non-oxidizing atmosphere at a temperature sufficient to form a single phase reaction product .
20. The method of claim 19 wherein said metal compound is a compound of a metal selected from the group consisting of Fe, Co, Ni , Mn, Cu, V, Sn, Ti, Cr, and mixtures thereof .
21. The method of claim 20 wherein said metal compound is selected from the group consisting of Fe203, V205, FeP04, V02, Fe304, LiV03, NH4V03, and mixtures thereof .
22. The method of claim 19 wherein said starting materials include a second metal compound having a second metal ion which is not reduced and which forms a part of said reaction product.
23. The method of claim 19 wherein said starting materials include a second metal compound which is a compound of a metal selected from the group consisting of Mg, Ca, Zn, Sr, Pb, Cd, Sn, Ba, Be, and mixtures thereof.
24. The method of claim 23 wherein said second metal compound is selected from the group consisting of magnesium hydroxide and calcium hydroxide.
25. The method of claim 19 wherein said starting materials include a phosphate compound selected from the group consisting of diammonium hydrogen phosphate, ammonium dihydrogen phosphate, and mixtures thereof .
26. The method of claim 19 wherein said metal compound is a metal oxide or a metal phosphate.
27. The method of claim 19 wherein said metal compound is V20s, and said lithium compound is lithium carbonate .
28. The method of claim 19 wherein said mixing and heating are conducted in a first stage by mixing starting materials consisting of iron oxide, diammonium hydrogen phosphate and carbon and heating said first stage mixed starting materials at a temperature sufficient to produce iron phosphate; and in a second stage by mixing starting materials consisting of said iron phosphate and lithium phosphate and heating said second stage mixed starting materials at a temperature sufficient to form lithium iron phosphate represented by the nominal formula LiFeP04.
29. The method of claim 19 wherein said heating is conducted at a ramp rate of up to about 10 °C per minute to an elevated temperature of between about 400°C and about 1200°C, and then maintaining said elevated temperature until said reaction product is formed.
30. The method of claim 29 wherein said elevated temperature is maintained for between several minutes to several hours .
PCT/US2000/035438 2000-01-18 2000-12-22 Preparation of lithium-containing materials WO2001053198A1 (en)

Priority Applications (9)

Application Number Priority Date Filing Date Title
EP00989532A EP1252093B1 (en) 2000-01-18 2000-12-22 Preparation of lithium-containing materials
DK00989532T DK1252093T3 (en) 2000-01-18 2000-12-22 Manufacture of lithium-containing materials
DE60013909T DE60013909T2 (en) 2000-01-18 2000-12-22 PREPARATION OF LITHIUM-CONTAINING MATERIALS
AT00989532T ATE276200T1 (en) 2000-01-18 2000-12-22 MANUFACTURING MATERIALS CONTAINING LITHIUM
AU2001226030A AU2001226030A1 (en) 2000-01-18 2000-12-22 Preparation of lithium-containing materials
KR20027009266A KR100539341B1 (en) 2000-01-18 2000-12-22 Preparation of lithium-containing materials
CA002395115A CA2395115C (en) 2000-01-18 2000-12-22 Preparation of lithium-containing materials
JP2001553213A JP3933470B2 (en) 2000-01-18 2000-12-22 Method for producing lithium metal-containing substance, product, composition and battery
HK03102844A HK1051174A1 (en) 2000-01-18 2003-04-22 Preparation of lithium-containing materials.

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
US09/484,919 2000-01-18
US09/484,919 US6528033B1 (en) 2000-01-18 2000-01-18 Method of making lithium-containing materials

Publications (1)

Publication Number Publication Date
WO2001053198A1 true WO2001053198A1 (en) 2001-07-26

Family

ID=23926183

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/US2000/035438 WO2001053198A1 (en) 2000-01-18 2000-12-22 Preparation of lithium-containing materials

Country Status (14)

Country Link
US (10) US6528033B1 (en)
EP (2) EP1252093B1 (en)
JP (2) JP3933470B2 (en)
KR (1) KR100539341B1 (en)
CN (1) CN1248958C (en)
AT (2) ATE276200T1 (en)
AU (1) AU2001226030A1 (en)
CA (3) CA2466366C (en)
DE (2) DE60013909T2 (en)
DK (1) DK1252093T3 (en)
ES (1) ES2225292T3 (en)
HK (1) HK1051174A1 (en)
IN (1) IN2002CH01089A (en)
WO (1) WO2001053198A1 (en)

Cited By (54)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1184920A2 (en) 2000-08-30 2002-03-06 Sony Corporation Cathode active material, method for preparation thereof, non-aqueous electrolyte cell and method for preparation thereof
EP1193784A2 (en) 2000-09-29 2002-04-03 Sony Corporation Method for the preparation of cathode active material and method for the preparation of a non-aqueous electrolyte cell
EP1193783A2 (en) * 2000-09-29 2002-04-03 Sony Corporation Method for the preparation of cathode active material and method for the preparation of a non-aqueous electrolyte cell
EP1193785A2 (en) 2000-09-29 2002-04-03 Sony Corporation Method for the preparation of cathode active material and method for the preparation of a non-aqueous electrolyte cell
EP1193787A2 (en) 2000-09-29 2002-04-03 Sony Corporation Method for the preparation of cathode active material and method for the preparation of a non-aqueous electrolyte cell
WO2002027824A1 (en) * 2000-09-26 2002-04-04 HYDRO-QUéBEC Synthesis method for carbon material based on lixm1-ym'(xo4)n
WO2002044084A2 (en) * 2000-11-28 2002-06-06 Valence Technology, Inc. Methods of making lithium metal compounds useful as cathode active materials
JP2003045430A (en) * 2001-07-31 2003-02-14 Mitsui Eng & Shipbuild Co Ltd Manufacturing method of positive electrode material for secondary battery and secondary battery
WO2003056646A1 (en) * 2001-12-21 2003-07-10 Massachusetts Institute Of Technology Conductive lithium storage electrode
WO2003101909A1 (en) * 2002-05-30 2003-12-11 HYDRO-QUéBEC Method for preparing ceramic powders in the presence of a carbon source, powders obtained and use thereof
US6777132B2 (en) 2000-04-27 2004-08-17 Valence Technology, Inc. Alkali/transition metal halo—and hydroxy-phosphates and related electrode active materials
JP2004525059A (en) * 2001-04-10 2004-08-19 ツェントゥルム フューア ゾンネンエネルギー−ウント ヴァッサーシュトッフ−フォルシュング バーデン−ヴァルテムベルク ゲマインニュッツィヒ シュティフトゥング Binary, ternary and quaternary lithium phosphates, their preparation and use
US6797431B2 (en) 2000-09-29 2004-09-28 Sony Corporation Method for the preparation of cathode active material and method for the preparation of non-aqueous electrolyte
US6815122B2 (en) 2002-03-06 2004-11-09 Valence Technology, Inc. Alkali transition metal phosphates and related electrode active materials
US6855462B2 (en) 2000-04-27 2005-02-15 Valence Technology, Inc. Lithium metal fluorophosphate materials and preparation thereof
EP1506135A1 (en) * 2002-05-17 2005-02-16 Valence Technology, Inc. Synthesis of metal compounds useful as cathode active materials
US6964827B2 (en) 2000-04-27 2005-11-15 Valence Technology, Inc. Alkali/transition metal halo- and hydroxy-phosphates and related electrode active materials
WO2005114769A2 (en) 2004-05-20 2005-12-01 Valence Technology, Inc. Synthesis of cathode active materials
JP2006511038A (en) * 2002-12-19 2006-03-30 ヴァレンス　テクノロジー　インコーポレーテッド Electrode active material and method for producing the same
WO2008048995A2 (en) 2006-10-17 2008-04-24 Valence Technology, Inc. Method and apparatus for monitoring and controlling an electrochemical cell
US7524584B2 (en) 2000-04-27 2009-04-28 Valence Technology, Inc. Electrode active material for a secondary electrochemical cell
WO2009076153A1 (en) 2007-12-11 2009-06-18 Valence Technology, Inc. Process for producing electrode active material for lithium ion cell
WO2011030786A1 (en) 2009-09-09 2011-03-17 戸田工業株式会社 Ferric phosphate hydrate particle powder and process for production thereof, olivine-type lithium iron phosphate particle powder and process for production thereof, and non-aqueous electrolyte secondary battery
US8057769B2 (en) 2000-04-27 2011-11-15 Valence Technology, Inc. Method for making phosphate-based electrode active materials
US8318352B2 (en) 2002-04-03 2012-11-27 Valence Technology, Inc. Batteries comprising alkali-transition metal phosphates and preferred electrolytes
CN102881865A (en) * 2012-09-14 2013-01-16 北京鼎能开源电池科技股份有限公司 Method for manufacturing positive plate of battery
DE112004001997B4 (en) * 2003-10-21 2013-11-21 Valence Technology, Inc. METHOD FOR PRODUCING LITHIUM PHOSPHATE ELECTRODE ACTIVE MATERIALS AND ELECTRODE ACTIVE MATERIALS MADE THEREFOR
US8840869B2 (en) 2002-10-25 2014-09-23 Foamix Ltd. Body cavity foams
CN104080733A (en) * 2011-12-23 2014-10-01 朗盛德国有限责任公司 LiPF6 solution
US8865139B1 (en) 2009-10-02 2014-10-21 Foamix Pharmaceuticals Ltd. Topical tetracycline compositions
WO2014184533A1 (en) * 2013-05-14 2014-11-20 Faradion Limited Metal-containing compounds
US8900554B2 (en) 2002-10-25 2014-12-02 Foamix Pharmaceuticals Ltd. Foamable composition and uses thereof
US8900553B2 (en) 2007-12-07 2014-12-02 Foamix Pharmaceuticals Ltd. Oil and liquid silicone foamable carriers and formulations
US9050253B2 (en) 2003-08-04 2015-06-09 Foamix Pharmaceuticals Ltd. Oleaginous pharmaceutical and cosmetic foam
US9072667B2 (en) 2009-07-29 2015-07-07 Foamix Pharmaceuticals Ltd. Non surface active agent non polymeric agent hydro-alcoholic foamable compositions, breakable foams and their uses
US9101662B2 (en) 2003-08-04 2015-08-11 Foamix Pharmaceuticals Ltd. Compositions with modulating agents
US9167813B2 (en) 2009-07-29 2015-10-27 Foamix Pharmaceuticals Ltd. Non surfactant hydro-alcoholic foamable compositions, breakable foams and their uses
US9211259B2 (en) 2002-11-29 2015-12-15 Foamix Pharmaceuticals Ltd. Antibiotic kit and composition and uses thereof
US9265725B2 (en) 2002-10-25 2016-02-23 Foamix Pharmaceuticals Ltd. Dicarboxylic acid foamable vehicle and pharmaceutical compositions thereof
US9320705B2 (en) 2002-10-25 2016-04-26 Foamix Pharmaceuticals Ltd. Sensation modifying topical composition foam
US9439857B2 (en) 2007-11-30 2016-09-13 Foamix Pharmaceuticals Ltd. Foam containing benzoyl peroxide
US9492412B2 (en) 2002-10-25 2016-11-15 Foamix Pharmaceuticals Ltd. Penetrating pharmaceutical foam
US9539208B2 (en) 2002-10-25 2017-01-10 Foamix Pharmaceuticals Ltd. Foam prepared from nanoemulsions and uses
US9577244B2 (en) 2010-01-28 2017-02-21 Johnson Matthey Plc Substituted lithium-manganese metal phosphate
US9622947B2 (en) 2002-10-25 2017-04-18 Foamix Pharmaceuticals Ltd. Foamable composition combining a polar solvent and a hydrophobic carrier
US9636405B2 (en) 2003-08-04 2017-05-02 Foamix Pharmaceuticals Ltd. Foamable vehicle and pharmaceutical compositions thereof
US9662298B2 (en) 2007-08-07 2017-05-30 Foamix Pharmaceuticals Ltd. Wax foamable vehicle and pharmaceutical compositions thereof
US9668972B2 (en) 2002-10-25 2017-06-06 Foamix Pharmaceuticals Ltd. Nonsteroidal immunomodulating kit and composition and uses thereof
US9682021B2 (en) 2006-11-14 2017-06-20 Foamix Pharmaceuticals Ltd. Substantially non-aqueous foamable petrolatum based pharmaceutical and cosmetic compositions and their uses
US9780372B2 (en) 2015-09-30 2017-10-03 Sumitomo Osaka Cement Co., Ltd. Electrode material for lithium-ion rechargeable battery
US9849142B2 (en) 2009-10-02 2017-12-26 Foamix Pharmaceuticals Ltd. Methods for accelerated return of skin integrity and for the treatment of impetigo
US9884017B2 (en) 2009-04-28 2018-02-06 Foamix Pharmaceuticals Ltd. Foamable vehicles and pharmaceutical compositions comprising aprotic polar solvents and uses thereof
US10398641B2 (en) 2016-09-08 2019-09-03 Foamix Pharmaceuticals Ltd. Compositions and methods for treating rosacea and acne
US11532806B2 (en) 2014-04-01 2022-12-20 The Research Foundation For The State University Of New York Electrode materials that include an active composition of the formula MgzMxOy for group II cation-based batteries

Families Citing this family (243)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6514640B1 (en) 1996-04-23 2003-02-04 Board Of Regents, The University Of Texas System Cathode materials for secondary (rechargeable) lithium batteries
WO2000060680A1 (en) * 1999-04-06 2000-10-12 Sony Corporation Active material of positive plate, nonaqueous electrolyte secondary cell, method for producing active material of positive material
US6528033B1 (en) * 2000-01-18 2003-03-04 Valence Technology, Inc. Method of making lithium-containing materials
US7001690B2 (en) * 2000-01-18 2006-02-21 Valence Technology, Inc. Lithium-based active materials and preparation thereof
JP4769995B2 (en) * 2000-03-06 2011-09-07 ソニー株式会社 Method for producing positive electrode active material and method for producing non-aqueous electrolyte battery
US8367036B2 (en) * 2000-04-27 2013-02-05 Valence Technology, Inc. Alkali/transition metal halo-and hydroxy-phosphates and related electrode active materials
JP4716072B2 (en) * 2001-07-02 2011-07-06 株式会社豊田中央研究所 Lithium vanadium composite oxide for negative electrode active material of water based lithium secondary battery, method for producing the same, and lithium secondary battery using the same
US7189475B2 (en) * 2000-07-27 2007-03-13 Kabushiki Kaisha Toyota Chuo Kenkyusho Lithium secondary battery
JP4491947B2 (en) * 2000-10-04 2010-06-30 ソニー株式会社 Method for producing positive electrode active material and method for producing non-aqueous electrolyte battery
JP3982165B2 (en) * 2000-10-05 2007-09-26 ソニー株式会社 Solid electrolyte battery
JP4126862B2 (en) * 2000-10-05 2008-07-30 ソニー株式会社 Non-aqueous electrolyte battery and solid electrolyte battery
TW513822B (en) * 2000-10-06 2002-12-11 Sony Corp Method for producing cathode active material and method for producing non-aqueous electrolyte cell
JP4491949B2 (en) * 2000-10-06 2010-06-30 ソニー株式会社 Method for producing positive electrode active material and method for producing non-aqueous electrolyte battery
JP3997702B2 (en) * 2000-10-06 2007-10-24 ソニー株式会社 Nonaqueous electrolyte secondary battery
JP3988374B2 (en) * 2000-10-06 2007-10-10 ソニー株式会社 Non-aqueous electrolyte secondary battery
JP4491950B2 (en) * 2000-10-06 2010-06-30 ソニー株式会社 Method for producing positive electrode active material and method for producing non-aqueous electrolyte battery
JP4848582B2 (en) * 2000-10-06 2011-12-28 ソニー株式会社 Method for producing positive electrode active material
KR100929452B1 (en) * 2000-10-20 2009-12-02 매사츄세츠 인스티튜트 오브 테크놀러지 Bipolar device
US7387851B2 (en) 2001-07-27 2008-06-17 A123 Systems, Inc. Self-organizing battery structure with electrode particles that exert a repelling force on the opposite electrode
US7662265B2 (en) * 2000-10-20 2010-02-16 Massachusetts Institute Of Technology Electrophoretic assembly of electrochemical devices
CA2324431A1 (en) 2000-10-25 2002-04-25 Hydro-Quebec New process for obtaining natural graphite particles in spherical shape: modelling and application
JP4643903B2 (en) * 2001-04-06 2011-03-02 ヴァレンス テクノロジー インコーポレーテッド Sodium ion battery
US7025907B2 (en) * 2001-05-15 2006-04-11 Kabushiki Kaisha Toyota Chuo Kenkyusho Carbon-containing lithium-iron composite phosphorus oxide for lithium secondary battery positive electrode active material and process for producing the same
KR101178643B1 (en) * 2001-07-27 2012-09-07 에이일이삼 시스템즈 인코포레이티드 Battery structures, self-organizing structures and related methods
JP4297429B2 (en) * 2001-07-31 2009-07-15 三井造船株式会社 Method for producing secondary battery positive electrode material and secondary battery
US6706445B2 (en) * 2001-10-02 2004-03-16 Valence Technology, Inc. Synthesis of lithiated transition metal titanates for lithium cells
US6908710B2 (en) * 2001-10-09 2005-06-21 Valence Technology, Inc. Lithiated molybdenum oxide active materials
US6818271B2 (en) * 2002-02-12 2004-11-16 Spear Usa, Llc Adhesive coated thin film label
JP4207434B2 (en) * 2002-02-14 2009-01-14 ソニー株式会社 Positive electrode active material and method for producing non-aqueous electrolyte battery
US20090220838A9 (en) * 2002-04-04 2009-09-03 Jeremy Barker Secondary electrochemical cell
US20110052986A1 (en) * 2002-04-04 2011-03-03 Jeremy Barker Sodium Ion Batteries
US6913855B2 (en) * 2002-07-22 2005-07-05 Valence Technology, Inc. Method of synthesizing electrochemically active materials from a slurry of precursors
AU2003259271A1 (en) * 2002-07-26 2004-02-16 A123 Systems, Inc. Bipolar articles and related methods
US7087348B2 (en) * 2002-07-26 2006-08-08 A123 Systems, Inc. Coated electrode particles for composite electrodes and electrochemical cells
DE10242694A1 (en) * 2002-09-13 2004-03-25 MAX-PLANCK-Gesellschaft zur Förderung der Wissenschaften e.V. Compositions used as electrode in lithium battery contain transition metal halide or ruthenium and/or molybdenum oxide, binder and optionally conductive additive or amorphous composition of metal clusters and lithium oxide or fluoride
AU2003297537A1 (en) * 2002-12-23 2004-07-22 A 123 Systems, Inc. High energy and power density electrochemical cells
WO2004066469A2 (en) * 2003-01-22 2004-08-05 Valence Technology, Inc. Electrolyte for use in phosphate based lithium ion/polymer cells
US20040202935A1 (en) * 2003-04-08 2004-10-14 Jeremy Barker Cathode active material with increased alkali/metal content and method of making same
US7318982B2 (en) * 2003-06-23 2008-01-15 A123 Systems, Inc. Polymer composition for encapsulation of electrode particles
CN1591936A (en) * 2003-09-05 2005-03-09 日本电池株式会社 Lithium contained substrate and method for mfg non-aqueous electrolyte electrochemical accomulation apparatus containing the same
CA2539723A1 (en) 2003-09-22 2005-04-07 Valence Technology, Inc. Electrical systems, power supply apparatuses, and power supply operations methods
JP4522682B2 (en) * 2003-10-09 2010-08-11 住友大阪セメント株式会社 Method for producing electrode material powder, electrode material powder and electrode, and lithium battery
DE10353266B4 (en) * 2003-11-14 2013-02-21 Süd-Chemie Ip Gmbh & Co. Kg Lithium iron phosphate, process for its preparation and its use as electrode material
CA2550496C (en) * 2003-12-23 2013-02-19 Universite De Montreal Process for preparing an at least partially lithiated transition metal oxyanion-based lithium-ion reversible electrode material and electrode material obtained therefrom
US10297827B2 (en) 2004-01-06 2019-05-21 Sion Power Corporation Electrochemical cell, components thereof, and methods of making and using same
US7358012B2 (en) 2004-01-06 2008-04-15 Sion Power Corporation Electrolytes for lithium sulfur cells
US8828610B2 (en) 2004-01-06 2014-09-09 Sion Power Corporation Electrolytes for lithium sulfur cells
US7008726B2 (en) * 2004-01-22 2006-03-07 Valence Technology, Inc. Secondary battery electrode active materials and methods for making the same
US20050163699A1 (en) * 2004-01-23 2005-07-28 Jeremy Barker Fluorosulfate-based electrode active materials and method of making the same
US8617745B2 (en) * 2004-02-06 2013-12-31 A123 Systems Llc Lithium secondary cell with high charge and discharge rate capability and low impedance growth
US7719227B2 (en) * 2004-02-13 2010-05-18 Valence Technology, Inc. Electrical energy supply methods and electrical energy power supplies
US7060238B2 (en) * 2004-03-04 2006-06-13 Valence Technology, Inc. Synthesis of metal phosphates
CN100336247C (en) * 2004-03-30 2007-09-05 中国科学院物理研究所 Method for preparing phosphate positive-pole material of lithium-ion cell
US7824800B1 (en) 2004-04-08 2010-11-02 Electrochemical Systems, Inc. Lithium-ion cell with a wide operating temperature range
US7582380B1 (en) 2004-04-08 2009-09-01 Electrochemical Systems, Inc. Lithium-ion cell with a wide operating temperature range
US7960057B2 (en) * 2004-05-17 2011-06-14 Toyota Motor Engineering & Manufacturing North America, Inc. Battery with molten salt electrolyte and phosphorus-containing cathode
US20050260498A1 (en) * 2004-05-20 2005-11-24 Saidi M Y Secondary electrochemical cell
US7629080B1 (en) 2004-07-23 2009-12-08 The United States Of America As Represented By The Secretary Of The Army Electrode materials for electrochemical cells
TWI290781B (en) * 2004-09-02 2007-12-01 Lg Chemical Ltd Electrode active material with multi-element based oxide layers and preparation method thereof
FR2876998B1 (en) * 2004-10-22 2007-01-19 Batscap Sa PROCESS FOR PREPARING GAMMA-LIV205
US7282301B2 (en) 2004-11-02 2007-10-16 T/J Technologies, Inc. Method for making a composite electrode material
US20060091362A1 (en) * 2004-11-02 2006-05-04 Wixom Michael R Composite electrochemical material
JP2006155941A (en) * 2004-11-25 2006-06-15 Kyushu Univ Method of manufacture for electrode active material
JP2006206428A (en) * 2004-12-27 2006-08-10 Mitsui Mining & Smelting Co Ltd Niobium oxide and method for producing the same
US20060139144A1 (en) * 2004-12-28 2006-06-29 Labarge William J Temperature sensor, ceramic device, and method of making the same
US7842420B2 (en) 2005-02-03 2010-11-30 A123 Systems, Inc. Electrode material with enhanced ionic transport properties
US7205067B2 (en) * 2005-02-08 2007-04-17 Valence Technology, Inc. Method and apparatus for dissipation of heat generated by a secondary electrochemical cell
US20070160519A1 (en) * 2005-03-28 2007-07-12 Jeremy Barker Method Of Making Active Materials For Use In Secondary Electrochemical Cells
US7887954B2 (en) * 2005-05-10 2011-02-15 Advanced Lithium Electrochemistry Co., Ltd. Electrochemical composition and associated technology
US20080138710A1 (en) * 2005-05-10 2008-06-12 Ben-Jie Liaw Electrochemical Composition and Associated Technology
TWI254031B (en) * 2005-05-10 2006-05-01 Aquire Energy Co Ltd Manufacturing method of LixMyPO4 compound with olivine structure
US7892676B2 (en) * 2006-05-11 2011-02-22 Advanced Lithium Electrochemistry Co., Ltd. Cathode material for manufacturing a rechargeable battery
US7700236B2 (en) * 2005-09-09 2010-04-20 Aquire Energy Co., Ltd. Cathode material for manufacturing a rechargeable battery
US7799457B2 (en) * 2005-05-10 2010-09-21 Advanced Lithium Electrochemistry Co., Ltd Ion storage compound of cathode material and method for preparing the same
US7824581B2 (en) * 2007-06-18 2010-11-02 Advanced Lithium Electrochemistry Co., Ltd. Cocrystalline metallic compounds and electrochemical redox active material employing the same
US7939201B2 (en) * 2005-08-08 2011-05-10 A123 Systems, Inc. Nanoscale ion storage materials including co-existing phases or solid solutions
US8158090B2 (en) * 2005-08-08 2012-04-17 A123 Systems, Inc. Amorphous and partially amorphous nanoscale ion storage materials
US8323832B2 (en) * 2005-08-08 2012-12-04 A123 Systems, Inc. Nanoscale ion storage materials
US7524529B2 (en) * 2005-09-09 2009-04-28 Aquire Energy Co., Ltd. Method for making a lithium mixed metal compound having an olivine structure
ATE385999T1 (en) * 2005-10-03 2008-03-15 Aquire Energy Co Ltd METHOD FOR PRODUCING LITHIUM-METAL MIXED COMPOUNDS
EP2560229B1 (en) 2005-10-20 2019-06-05 Mitsubishi Chemical Corporation Lithium secondary batteries and nonaqueous electrolyte for use in the same
JP4929182B2 (en) * 2005-11-04 2012-05-09 ステラケミファ株式会社 Electricity storage element
CN100395907C (en) * 2005-12-22 2008-06-18 上海交通大学 Method for preparing lithium ion battery anode material lithium ion phosphate
FR2895572B1 (en) * 2005-12-23 2008-02-15 Commissariat Energie Atomique MATERIAL BASED ON CARBON AND SILICON NANOTUBES FOR USE IN NEGATIVE ELECTRODES FOR LITHIUM ACCUMULATOR
US8501352B2 (en) * 2006-02-03 2013-08-06 The United States Of America, As Represented By The Secretary Of The Navy Lithium-metal-oxide composite electrodes
JP5113081B2 (en) * 2006-02-14 2013-01-09 ダウ グローバル テクノロジーズ エルエルシー Lithium manganese phosphate cathode material for lithium secondary battery
US20070190422A1 (en) * 2006-02-15 2007-08-16 Fmc Corporation Carbon nanotube lithium metal powder battery
CN101432241B (en) 2006-02-28 2013-08-21 普里梅精密材料有限公司 Lithium-based compound nanoparticle compositions and methods of forming the same
WO2007100133A1 (en) * 2006-03-02 2007-09-07 Cataler Corporation Carbon material for lithium battery, and lithium battery
US7494744B2 (en) * 2006-03-08 2009-02-24 Changs-Ascending Enterprise Co. Cathode material for Li-ion battery applications
US7723958B2 (en) * 2006-03-31 2010-05-25 Valence Technology, Inc. Battery charge indication methods, battery charge monitoring devices, rechargeable batteries, and articles of manufacture
US8158071B2 (en) * 2006-04-29 2012-04-17 Chun-Chieh Chang Method and devices for producing air sensitive electrode materials for lithium ion battery applications
AU2007248756A1 (en) 2006-05-02 2007-11-15 Carol Lenk Method of light dispersion and preferential scattering of certain wavelengths of light for light-emitting diodes and bulbs constructed therefrom
US20070259265A1 (en) * 2006-05-02 2007-11-08 Saidi M Yazid Secondary electrochemical cell having a novel electrode active material
MX2008013869A (en) 2006-05-02 2009-02-16 Superbulbs Inc Heat removal design for led bulbs.
KR20090008317A (en) 2006-05-02 2009-01-21 슈퍼불브스, 인크. Plastic led bulb
US20070298317A1 (en) * 2006-05-09 2007-12-27 Ralph Brodd Secondary electrochemical cell with increased current collecting efficiency
US20090183650A1 (en) * 2006-06-12 2009-07-23 The Regents Of The University Of California Optimization of carbon coatings
TWI319920B (en) * 2006-07-06 2010-01-21 The preparation and application of the lifepo4/li3v2(po4)3 composite cathode materials for lithium ion batteries
US7988879B2 (en) * 2006-08-21 2011-08-02 Lg Chem, Ltd. Method for preparing lithium metal phosphate
US20090061314A1 (en) * 2007-08-30 2009-03-05 Ming Dong Method of Processing Active Materials For Use In Secondary Electrochemical Cells
KR20090058559A (en) * 2006-09-13 2009-06-09 발렌스 테크놀로지, 인코포레이티드 Method of processing active materials for use in secondary electrochemical cells
US7718319B2 (en) 2006-09-25 2010-05-18 Board Of Regents, The University Of Texas System Cation-substituted spinel oxide and oxyfluoride cathodes for lithium ion batteries
CN100411978C (en) * 2006-11-21 2008-08-20 华南理工大学 High tap density lithium ion battery positive material vanadium lithium phosphate preparation method
US7824802B2 (en) * 2007-01-17 2010-11-02 The United States Of America As Represented By The Secretary Of The Army Method of preparing a composite cathode active material for rechargeable electrochemical cell
KR20090120461A (en) * 2007-02-07 2009-11-24 발렌스 테크놀로지, 인코포레이티드 Oxynitride-based electrode active materials for secondary electrochemical cells
KR100834054B1 (en) 2007-05-11 2008-06-02 한양대학교 산학협력단 Olivine type positive active material for lithium battery, method for preparing the same, and lithium battery comprising the same
US8021496B2 (en) * 2007-05-16 2011-09-20 Fmc Corporation Stabilized lithium metal powder for Li-ion application, composition and process
CN101070148B (en) * 2007-05-22 2010-05-19 无锡市凯天星电光材料有限公司 Method for preparing lithium iron phosphate as lithium ion cell positive-pole material
US20090202903A1 (en) 2007-05-25 2009-08-13 Massachusetts Institute Of Technology Batteries and electrodes for use thereof
US20080303004A1 (en) * 2007-06-08 2008-12-11 Conocophillips Company Method for producing lithium transition metal polyanion powders for batteries
US20080305256A1 (en) * 2007-06-08 2008-12-11 Conocophillips Company Method for producing lithium vanadium polyanion powders for batteries
US8168329B2 (en) * 2007-06-18 2012-05-01 Advanced Lithium Electrochemistry Co., Ltd. Electrochemical composition and associated technology
WO2009003093A1 (en) * 2007-06-26 2008-12-31 Tiax, Llc Metal phosphate compounds and batteries containing the same
EP2015382A1 (en) * 2007-07-13 2009-01-14 High Power Lithium S.A. Carbon coated lithium manganese phosphate cathode material
US8047288B2 (en) 2007-07-18 2011-11-01 Oxane Materials, Inc. Proppants with carbide and/or nitride phases
US20090035661A1 (en) * 2007-08-01 2009-02-05 Jeffrey Swoyer Synthesis of cathode active materials
KR100972054B1 (en) * 2007-09-12 2010-07-23 한국전기연구원 Manufacturing Method of Active Material
US20120070746A1 (en) * 2007-09-21 2012-03-22 Sion Power Corporation Low electrolyte electrochemical cells
CN101399343B (en) 2007-09-25 2011-06-15 比亚迪股份有限公司 Preparing method of anode active material lithium iron phosphate for lithium ionic secondary cell
CN101809801B (en) * 2007-09-28 2014-03-26 A123系统公司 Batteries having inorganic/organic porous films
KR101519686B1 (en) 2007-10-01 2015-05-12 바스프 에스이 Process for the preparation of crystalline lithium-, vanadium- and phosphate-comprising materials
CA2701144A1 (en) * 2007-10-01 2009-04-09 Hartmut Hibst Process for the preparation of porous lithium-, vanadium and phosphate-comprising materials
US8439528B2 (en) 2007-10-03 2013-05-14 Switch Bulb Company, Inc. Glass LED light bulbs
EP2215403A4 (en) 2007-10-24 2012-08-29 Switch Bulb Co Inc Diffuser for led light sources
CN101420048A (en) * 2007-10-26 2009-04-29 比亚迪股份有限公司 Preparation of lithium ionic secondary cell
US20090117020A1 (en) * 2007-11-05 2009-05-07 Board Of Regents, The University Of Texas System Rapid microwave-solvothermal synthesis and surface modification of nanostructured phospho-olivine cathodes for lithium ion batteries
CN101453019B (en) * 2007-12-07 2011-01-26 比亚迪股份有限公司 Positive pole active substance containing lithium iron phosphate, preparation, positive pole and battery thereof
CN101471432B (en) * 2007-12-27 2012-11-21 比亚迪股份有限公司 Diaphragm and preparation method thereof as well as lithium ion battery
KR101601992B1 (en) 2008-01-08 2016-03-09 시온 파워 코퍼레이션 Porous electrodes and associated methods
TWI466370B (en) 2008-01-17 2014-12-21 A123 Systems Inc Mixed metal olivine electrode materials for lithium ion batteries
CN101494305B (en) 2008-01-25 2011-05-18 比亚迪股份有限公司 Lithium ion battery electrolyte and battery and battery set containing the same
JP2009193745A (en) * 2008-02-13 2009-08-27 Sony Corp Method for manufacturing positive electrode active material
US8088305B2 (en) 2008-02-22 2012-01-03 Byd Company Limited Lithium iron phosphate cathode material
US8062559B2 (en) 2008-02-29 2011-11-22 Byd Company Limited Composite compound with mixed crystalline structure
US8052897B2 (en) 2008-02-29 2011-11-08 Byd Company Limited Composite compound with mixed crystalline structure
US8057711B2 (en) 2008-02-29 2011-11-15 Byd Company Limited Composite compound with mixed crystalline structure
US20090220858A1 (en) * 2008-02-29 2009-09-03 Byd Company Limited Composite Compound With Mixed Crystalline Structure
US8062560B2 (en) 2008-02-29 2011-11-22 Byd Company Limited Composite compound with mixed crystalline structure
EP2597702B1 (en) * 2008-03-05 2016-04-27 EaglePicher Technologies, LLC Lithium-sulfur battery and cathode therefore
US20090233178A1 (en) * 2008-03-13 2009-09-17 Saidi M Yazid Lithium-ion batteries
US8148015B2 (en) 2008-03-21 2012-04-03 Byd Company Limited Cathode materials for lithium batteries
EP2277828B1 (en) 2008-03-31 2018-08-08 Toda Kogyo Corp. Lithium iron phosphate powder manufacturing method, olivine structured lithium iron phosphate powder, cathode sheet using said lithium iron phosphate powder, and non-aqueous solvent secondary battery
KR101494434B1 (en) 2008-04-02 2015-02-24 삼성전자주식회사 A lithium-transition metal complex compounds having hierarchical structure, a method for preparing the same and a lithium battery comprising an electrode comprising the same
TW200951066A (en) * 2008-04-17 2009-12-16 Basf Se Process for the preparation of crystalline lithium-, iron-and phosphate-comprising materials
TW201010944A (en) 2008-04-17 2010-03-16 Basf Se Process for the preparation of crystalline lithium-, iron-and phosphate-comprising materials
TW201002623A (en) * 2008-05-30 2010-01-16 Basf Se Process for preparing lithium vanadium oxides and their use as cathode material
CN101597089A (en) 2008-06-06 2009-12-09 比亚迪股份有限公司 The preparation method of a kind of transition metal hydroxide and oxide compound thereof and positive electrode material
CN101640288B (en) 2008-07-30 2012-03-07 比亚迪股份有限公司 Lithium-ion battery electrolyte and lithium-ion battery containing same
TWI440597B (en) 2008-08-26 2014-06-11 Basf Se Synthesis of lifepo4 under hydrothermal conditions
US8821763B2 (en) * 2008-09-30 2014-09-02 Tdk Corporation Active material and method of manufacturing active material
JP5396798B2 (en) 2008-09-30 2014-01-22 Ｔｄｋ株式会社 Active material, positive electrode and lithium ion secondary battery using the same
JP5376894B2 (en) 2008-10-20 2013-12-25 古河電池株式会社 Multi-component phosphoric acid lithium compound particles having an olivine structure, a method for producing the same, and a lithium secondary battery using the same as a positive electrode material
EP2360117B1 (en) * 2008-10-22 2015-05-06 LG Chem, Ltd. Lithium iron phosphate having an olivine structure, and preparation method thereof
CN102300806B (en) 2008-12-08 2013-11-06 赫斯提亚Tec有限公司 Multicomponent nanoparticle materials and process and apparatus therefor
TWI474970B (en) 2008-12-29 2015-03-01 Basf Se Synthesis of lithium-metal-phosphates under hydrothermal conditions
WO2010081150A1 (en) * 2009-01-12 2010-07-15 A123 Systems, Inc. Laminated battery cell and methods for creating the same
US8022009B2 (en) 2009-01-16 2011-09-20 Intematix Corporation Process for synthesizing LixFeMZO4/ carbon and LixMZO4/ carbon composite materials
TW201029918A (en) * 2009-02-12 2010-08-16 Enerage Inc Method for synthesizing lithium phosphate compound having olivine crystal structure
US20100233545A1 (en) * 2009-03-16 2010-09-16 Tdk Corporation Active material, method of manufacturing active material, electrode, and lithium-ion secondary battery
US9023523B2 (en) 2009-03-17 2015-05-05 Basf Se Synthesis of lithium-iron-phosphates under hydrothermal conditions
CN101519198A (en) * 2009-04-16 2009-09-02 丁建民 Method for preparing cathode material of lithium iron phosphate
US20100266474A1 (en) * 2009-04-16 2010-10-21 Titus Faulkner Method of Making Active Materials for Use in Secondary Electrochemical Cells
US8372540B2 (en) * 2009-04-16 2013-02-12 Valence Technology, Inc. Electrode active material for secondary electrochemical cell
DE102009020832A1 (en) * 2009-05-11 2010-11-25 Süd-Chemie AG Composite material containing a mixed lithium metal oxide
JP2010272272A (en) * 2009-05-20 2010-12-02 Hitachi Ltd Positive electrode for lithium secondary battery, and lithium secondary battery
CA2835382C (en) 2009-05-22 2017-08-22 Sharp Kabushiki Kaisha Cathode active material containing lithium and having transition metal oxide, cathode containing lithium and having transition metal oxide, and nonaqueous secondary battery containing lithium and having transition metal oxide
US9209461B2 (en) 2009-06-24 2015-12-08 Basf Se Process for the preparation of LiFePO4-carbon composites
US20110110838A1 (en) * 2009-07-10 2011-05-12 Intematix Corporation METHOD OF SOLID-LIQUID MIXING GEL PROCESS FOR LiFePO4 SYNTHESIS
EP2471132B1 (en) 2009-08-25 2016-10-12 A123 Systems LLC Mixed metal olivine electrode materials for lithium ion batteries having improved specific capacity and energy density
US20110052995A1 (en) * 2009-08-28 2011-03-03 Tdk Corporation Active material, electrode containing the same, lithium secondary battery provided therewith and method for manufacture of the active material
IN2012DN02063A (en) 2009-08-28 2015-08-21 Sion Power Corp
EP4112543A1 (en) * 2009-09-18 2023-01-04 A123 Systems, LLC Ferric phosphate and methods of preparation thereof
US9660267B2 (en) 2009-09-18 2017-05-23 A123 Systems, LLC High power electrode materials
US8734539B2 (en) * 2009-09-29 2014-05-27 Tdk Corporation Method of manufacturing active material containing vanadium and method of manufacturing lithium-ion secondary battery containing such active material
CN102575142B (en) * 2009-09-30 2014-07-02 旭硝子株式会社 Near-infrared-absorbing particles, process for producing same, dispersion, and article thereof
WO2011065337A1 (en) * 2009-11-24 2011-06-03 旭硝子株式会社 Process for production of phosphoric acid compound, and process for production of secondary battery
US20110135810A1 (en) * 2009-12-03 2011-06-09 Marina Yakovleva Finely deposited lithium metal powder
DE102010006083B4 (en) * 2010-01-28 2014-12-11 Süd-Chemie Ip Gmbh & Co. Kg Substituted lithium manganese metal phosphate
DE102010006082A1 (en) 2010-01-28 2011-08-18 Süd-Chemie AG, 80333 Guide additive-free electrode for a secondary lithium ion battery
WO2011103554A1 (en) * 2010-02-22 2011-08-25 Massachusetts Institute Of Technology Carbophoshates and related compounds
WO2011118350A1 (en) * 2010-03-26 2011-09-29 Semiconductor Energy Laboratory Co., Ltd. Power storage device
JP5858395B2 (en) 2010-03-31 2016-02-10 日本ケミコン株式会社 Method for producing composite of metal compound nanoparticles and carbon
CN103069624B (en) 2010-07-01 2016-06-22 夏普株式会社 Positive electrode active materials, positive pole and non-aqueous secondary batteries
JP5271975B2 (en) * 2010-07-01 2013-08-21 シャープ株式会社 Positive electrode active material, positive electrode and non-aqueous electrolyte secondary battery
US9373844B2 (en) 2010-07-01 2016-06-21 Sharp Kabushiki Kaisha Positive electrode active substance containing lithium-containing metal oxide
CN102315444B (en) * 2010-07-08 2016-01-20 中国科学院宁波材料技术与工程研究所 A kind of preparation method of nano-modified polyanionic cathode active material
AR082147A1 (en) * 2010-07-09 2012-11-14 Res Inst Ind Science & Tech METHOD FOR THE ECONOMIC EXTRACTION OF LITHIUM FROM A SOLUTION CONTAINING LITHIUM
JP5132727B2 (en) 2010-07-12 2013-01-30 シャープ株式会社 Positive electrode active material, positive electrode and non-aqueous electrolyte secondary battery
DE102010032206A1 (en) * 2010-07-26 2012-04-05 Süd-Chemie AG Gas phase coated lithium transition metal phosphate and process for its preparation
JP5635697B2 (en) * 2010-08-12 2014-12-03 リサーチ インスティチュート オブ インダストリアル サイエンス アンド テクノロジー Method for producing olivine-based positive electrode material for lithium secondary battery
CN103270624A (en) 2010-08-24 2013-08-28 巴斯夫欧洲公司 Electrolyte materials for use in electrochemical cells
RU2444815C1 (en) * 2010-08-27 2012-03-10 Учреждение Российской академии наук Институт химии твердого тела и механохимии Сибирского отделения РАН (ИХТТМ СО РАН) METHOD TO PRODUCE HIGHLY DISPERSED CATHODE MATERIALS LixFeyMzPO4/C WITH OLIVINE STRUCTURE
CN103098267B (en) * 2010-09-01 2016-06-15 株式会社Lg化学 Cathode active material for secondary battery
CN103140966B (en) * 2010-09-27 2016-01-20 日本化学工业株式会社 The manufacture method of phosphoric acid vanadium lithium carbon complex
CN103155066B (en) * 2010-10-04 2017-02-08 电子部品研究院 Cathode active material for a lithium ion capacitor, and method for producing the cathode active material
US20120138867A1 (en) * 2010-11-11 2012-06-07 Phostech Lithium Inc. Carbon-deposited alkali metal oxyanion electrode material and process for preparing same
CN102468480A (en) * 2010-11-19 2012-05-23 北京有色金属研究总院 Preparation method of high-rate capacity lithium iron phosphate material
US9160001B2 (en) 2010-12-23 2015-10-13 Wildcat Discovery Technologies, Inc. Lithium-ion battery materials with improved properties
CN102074690B (en) * 2010-12-24 2013-01-30 复旦大学 Method for synthesizing battery anode material LiFePO4 by using controllable carbon clad FePO4
CN102097618B (en) * 2011-01-12 2013-04-17 合肥国轩高科动力能源有限公司 Carbon-coated positive electrode material LiFexM1yM2zPO4Preparation method of (1)
CN102097619A (en) * 2011-01-12 2011-06-15 合肥国轩高科动力能源有限公司 Method for preparing high-performance lithium iron phosphate cathode material by using composite reducing agent
CN102107862B (en) * 2011-01-20 2013-03-27 铜陵金泰电池材料有限公司 Method for preparing lithium iron phosphate by using wood fibers as carbon source
JP5451671B2 (en) 2011-03-23 2014-03-26 シャープ株式会社 Positive electrode active material, positive electrode and non-aqueous secondary battery
US9065093B2 (en) 2011-04-07 2015-06-23 Massachusetts Institute Of Technology Controlled porosity in electrodes
JP5553057B2 (en) * 2011-05-09 2014-07-16 ソニー株式会社 Cathode active material and non-aqueous electrolyte battery
US8735002B2 (en) 2011-09-07 2014-05-27 Sion Power Corporation Lithium sulfur electrochemical cell including insoluble nitrogen-containing compound
CN102244263B (en) * 2011-06-15 2013-09-04 中南大学 Lithium ion battery phosphatic composite cathode material and preparation method thereof
CN102290576B (en) * 2011-07-23 2013-08-21 江西省福斯特新能源有限公司 Multi-doped lithium phosphate anode material, preparation method and lithium ion power cell thereof
CN102306791B (en) 2011-08-18 2014-08-06 合肥国轩高科动力能源股份公司 Method for preparing carbon-cladding non-stoichiometric lithium iron phosphorous oxide material
US8591069B2 (en) 2011-09-21 2013-11-26 Switch Bulb Company, Inc. LED light bulb with controlled color distribution using quantum dots
US20140242457A1 (en) * 2011-09-26 2014-08-28 Cornell University Aluminum ion battery including metal sulfide or monocrystalline vanadium oxide cathode and ionic liquid based electrolyte
JP5871543B2 (en) * 2011-09-29 2016-03-01 富士重工業株式会社 Modified vanadium phosphate lithium carbon composite, method for producing the same, lithium secondary battery positive electrode active material, and lithium secondary battery
CN102427132A (en) * 2011-12-02 2012-04-25 苏州冠硕新能源有限公司 Positive electrode material and preparation method thereof
US9059466B2 (en) 2012-03-22 2015-06-16 Chun-Chieh Chang Direct synthesis of lithium ion battery electrode materials using graphene treated raw materials as the reactant
US9090476B2 (en) 2012-03-22 2015-07-28 Chun-Chieh Chang Direct deposition of graphene on substrate material
CN102642820A (en) * 2012-03-29 2012-08-22 天津巴莫科技股份有限公司 Preparation method of high-density spherical lithium iron phosphate
KR101328585B1 (en) * 2012-04-06 2013-11-12 한국과학기술연구원 Fabricating method of cathode for lithium ion secondary battery by recycling cathode active material and a lithium ion secondary battery fabricated thereby
TW201405920A (en) 2012-05-29 2014-02-01 Clariant Canada Inc Process for preparing crystalline electrode materials and materials obtained therefrom
CN102891300B (en) * 2012-09-24 2016-12-21 上海锦众信息科技有限公司 A kind of preparation method of lithium battery mesoporous carbon composite material
US9577289B2 (en) 2012-12-17 2017-02-21 Sion Power Corporation Lithium-ion electrochemical cell, components thereof, and methods of making and using same
KR101991149B1 (en) 2012-12-19 2019-06-19 시온 파워 코퍼레이션 Electrode structure and method for making same
US10522822B2 (en) 2013-02-01 2019-12-31 Emd Acquisition Llc Lithium manganese oxide compositions
KR101938462B1 (en) 2013-07-09 2019-01-14 다우 글로벌 테크놀로지스 엘엘씨 Mixed positive active material comprising lithium metal oxide and lithium metal phosphate
KR101580842B1 (en) * 2014-01-07 2015-12-29 동국대학교 산학협력단 Surface Treatment Method of Lithium Manganese Oxide and Lithium Manganese Oxide manufactured using the same
WO2015166030A1 (en) 2014-05-01 2015-11-05 Basf Se Electrode fabrication methods and associated articles
US10675819B2 (en) 2014-10-03 2020-06-09 Massachusetts Institute Of Technology Magnetic field alignment of emulsions to produce porous articles
WO2016054530A1 (en) 2014-10-03 2016-04-07 Massachusetts Institute Of Technology Pore orientation using magnetic fields
CN107004856B (en) 2014-12-18 2021-06-04 陶氏环球技术有限责任公司 Lithium ion battery with improved thermal stability
US9653731B2 (en) * 2014-12-23 2017-05-16 Sharp Kabushiki Kaisha Layered oxide materials for batteries
US9660263B2 (en) 2014-12-23 2017-05-23 Sharp Kabushiki Kaisha Layered oxide materials for batteries
JP6500578B2 (en) 2015-04-27 2019-04-17 株式会社デンソー Electrode active material for non-aqueous electrolyte secondary battery, method for producing the same, and non-aqueous electrolyte secondary battery
US20170141245A1 (en) * 2015-11-12 2017-05-18 E I Du Pont De Nemours And Company Conductive paste composition and semiconductor devices made therewith
US10903484B2 (en) 2016-10-26 2021-01-26 The Regents Of The University Of Michigan Metal infiltrated electrodes for solid state batteries
US11909046B2 (en) 2017-03-07 2024-02-20 The Research Foundation For The State University Of New York Synthetic methods for crystallite size control of bimetallic polyanionic battery compositions
TWI821195B (en) 2017-07-19 2023-11-11 加拿大商納諾萬麥帝瑞爾公司 Improved synthesis of olivine lithium metal phosphate cathode materials
US11251430B2 (en) 2018-03-05 2022-02-15 The Research Foundation For The State University Of New York ϵ-VOPO4 cathode for lithium ion batteries
EP3802460A4 (en) * 2018-05-30 2022-10-12 Hydro-Québec Ceramics, methods for the production thereof and uses of same
US10787368B2 (en) * 2018-06-06 2020-09-29 Basf Corporation Process for producing lithiated transition metal oxides
CA3121418A1 (en) 2018-12-03 2020-06-11 Hewlett-Packard Development Company, L.P. Logic circuitry
US11404720B2 (en) * 2019-01-29 2022-08-02 Nippon Chemical Industrial Co., Ltd. Method for producing lithium titanium phosphate
CN114447323B (en) * 2022-02-14 2024-06-04 山东威固新能源科技有限公司 Lithium metal material with surface having phosphate layer, and preparation method and application thereof
WO2023203383A1 (en) 2022-04-19 2023-10-26 Lithium Werks Technology Bv Methods for preparation of electroactive lithium mixed metal materials for high energy density batteries

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1998012761A1 (en) * 1996-09-23 1998-03-26 Valence Technology, Inc. Lithium-containing, lithium-intercalating phosphates and their use as the positive or negative electrode material in a lithium secondary battery
US5910382A (en) * 1996-04-23 1999-06-08 Board Of Regents, University Of Texas Systems Cathode materials for secondary (rechargeable) lithium batteries
WO2000001024A1 (en) * 1998-06-26 2000-01-06 Valence Technology, Inc. Lithium-containing silicon/phosphates, method of preparation, and uses thereof

Family Cites Families (132)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US2508878A (en) 1945-03-24 1950-05-23 Dow Chemical Co Process for the production of carbothermal magnesium furnace charge
US2570232A (en) 1945-06-26 1951-10-09 North Carolina Magnesium Dev C Continuous process for recovery of magnesium
US2580878A (en) 1949-07-22 1952-01-01 Lawrence D Bartlett Twine dispenser
US3865745A (en) 1971-01-15 1975-02-11 Grace W R & Co Process for the preparation of metal carbide and metal oxide microspheres
US3736184A (en) 1972-03-29 1973-05-29 Mallory & Co Inc P R Metal phosphate and metal arsenate organic electrolyte cells
US4087274A (en) * 1975-07-04 1978-05-02 Boliden Aktiebolag Method of producing a partially reduced product from finely-divided metal sulphides
US4009092A (en) 1976-02-27 1977-02-22 E. I. Du Pont De Nemours And Company Substituted lithium phosphates and solid electrolytes therefrom
US4049891A (en) 1976-06-21 1977-09-20 Massachusetts Institute Of Technology Compositions for fast alkali-metal-ion transport
GB1565065A (en) 1976-08-23 1980-04-16 Tetronics Res & Dev Co Ltd Carbothermal production of aluminium
FR2457018A1 (en) 1979-02-16 1980-12-12 Accumulateurs Fixes POSITIVE ACTIVE MATERIAL FOR NON-AQUEOUS ELECTROCHEMICAL ELECTROCHEMICAL GENERATOR AND METHOD FOR PREPARING THE SAME
JPS5626477A (en) 1980-02-22 1981-03-14 Sanyo Electric Co Ltd Variable-capacity diode manufacturing process
JPS56162477A (en) 1980-05-20 1981-12-14 Nippon Telegr & Teleph Corp <Ntt> Battery
US4434216A (en) 1980-10-24 1984-02-28 Rayovac Corporation Solid state electrolyte
US4512905A (en) 1982-05-18 1985-04-23 The Texas A&M University System Method of making sodium zirconium silico-phosphates
US4477541A (en) 1982-12-22 1984-10-16 The United States Of America As Represented By The United States Department Of Energy Solid electrolyte structure
US4707422A (en) 1983-06-27 1987-11-17 Voltaix, Inc. Composite coating for electrochemical electrode and method
FR2563382B1 (en) 1984-04-24 1986-05-30 Elf Aquitaine NEW ELECTROCHEMICAL GENERATOR WITH COMPOSITE ELECTRODE
FR2576712B1 (en) 1985-01-30 1988-07-08 Accumulateurs Fixes NON-AQUEOUS ELECTROCHEMICAL ELECTROCHEMICAL GENERATOR
DE3680249D1 (en) * 1985-05-10 1991-08-22 Asahi Chemical Ind SECONDARY BATTERY.
JPS61263069A (en) 1985-05-17 1986-11-21 Matsushita Electric Ind Co Ltd Battery
JPS62176054A (en) 1986-01-30 1987-08-01 Nippon Telegr & Teleph Corp <Ntt> Lithium battery
GB2196785B (en) 1986-10-29 1990-05-23 Sony Corp Organic electrolyte secondary cell
US4803137A (en) 1987-05-19 1989-02-07 Bridgestone Corporation Non-aqueous electrolyte secondary cell
US4792504A (en) * 1987-09-18 1988-12-20 Mhb Joint Venture Liquid containing polymer networks as solid electrolytes
US4830939B1 (en) 1987-10-30 1996-10-08 Mhb Joint Venture Radiation cured solid electrolytes and electrochemical devices employing the same
US5037712A (en) 1987-10-30 1991-08-06 Ultracell, Inc. Preparation of radiation cured solid electrolytes and electrochemical devices employing the same
US4985317A (en) 1988-11-30 1991-01-15 Japan Synthetic Rubber Co., Ltd. Lithium ion-conductive solid electrolyte containing lithium titanium phosphate
US4990413A (en) * 1989-01-18 1991-02-05 Mhb Joint Venture Composite solid electrolytes and electrochemical devices employing the same
US4925752A (en) * 1989-03-03 1990-05-15 Fauteux Denis G Solid state electrochemical cell having porous cathode current collector
US5011501A (en) * 1989-04-26 1991-04-30 Shackle Dale R Process for making a solid state cell
US4935317A (en) 1989-06-21 1990-06-19 Mhb Joint Venture Method for producing solid state electrochemical laminar cell utilizing cathode rolling step
FR2655777A1 (en) 1989-12-11 1991-06-14 Accumulateurs Fixes RECHARGEABLE ELECTROCHEMICAL GENERATOR COMPRISING A VANADIUM OXIDE-BASED CATHODE.
US5262548A (en) 1990-05-21 1993-11-16 Scientific Design Company, Inc. Phosphorous/vanadium oxidation catalyst
DE4024409A1 (en) 1990-08-01 1992-02-06 Geismar Guenter Green, turquoise and blue metal phosphate pigment - contains alkali metal and zinc, copper and/or cobalt, used for pigmenting (in)organic medium
GB2251119B (en) 1990-12-20 1995-06-07 Technology Finance Corp Electrochemical cell
US5173215A (en) 1991-02-21 1992-12-22 Atraverda Limited Conductive titanium suboxide particulates
DE69204996T2 (en) 1991-03-22 1996-02-08 The Dow Chemical Co., Midland, Mich. METHOD FOR CARBOTHERMAL PRODUCTION OF NON-OXIDE CERAMIC POWDER IN A HIKING BED.
US5232794A (en) 1991-10-17 1993-08-03 The United States Of America As Represented By The United States Department Of Energy Ionic conductors for solid oxide fuel cells
JP3177304B2 (en) 1992-02-18 2001-06-18 三洋電機株式会社 Solid electrolyte and lithium battery using the same
EP0571858B1 (en) 1992-05-18 1996-08-14 Mitsubishi Cable Industries, Ltd. Lithium secondary battery
CA2096386A1 (en) 1992-05-18 1993-11-19 Masahiro Kamauchi Lithium secondary battery
JPH05325961A (en) 1992-05-18 1993-12-10 Mitsubishi Cable Ind Ltd Lithium battery
JPH05326477A (en) 1992-05-26 1993-12-10 Ulvac Japan Ltd Method for removal of halogen from semiconductor substrate surface
US5620810A (en) 1992-07-22 1997-04-15 Valence Technology, Inc. Solid, solvent-containing electrolytes and electrolytic cells produced therefrom
US5262253A (en) * 1992-07-22 1993-11-16 Valence Technology, Inc. Solid electrolytes derived by polymerization of vinyl sulfonate polyalkylene oxides
US5508130A (en) 1992-07-22 1996-04-16 Golovin; Milton N. Solid electrolytes containing LiN(SO2 CF3)2 and a triglyme-carbonate solvent, and electrochemical cells produced therefrom
ZA936168B (en) 1992-08-28 1994-03-22 Technology Finance Corp Electrochemical cell
US5300373A (en) * 1992-09-11 1994-04-05 Valence Technology, Inc. Electrochemical cell stack and method of making an electrochemical cell stack
US5326653A (en) * 1992-10-29 1994-07-05 Valence Technology, Inc. Battery unit with reinforced current collector tabs and method of making a battery unit having strengthened current collector tabs
JP3612330B2 (en) 1992-11-16 2005-01-19 ミネラル ディベラップメント インターナショナル アクティーゼルスカブ Method for producing metal magnesium, magnesium oxide or refractory material
RU2038395C1 (en) 1992-12-17 1995-06-27 Дальневосточный государственный технический университет Method for rendering chromium-containing wastes of electroplating harmless
US5296436A (en) 1993-01-08 1994-03-22 Scientific Design Company, Inc. Phosphorous/vanadium oxidation catalyst
US5871868A (en) * 1993-02-26 1999-02-16 General Dynamics Information Systems, Inc. Apparatus and method for machining conductive structures on substrates
US5460904A (en) 1993-08-23 1995-10-24 Bell Communications Research, Inc. Electrolyte activatable lithium-ion rechargeable battery cell
US5418091A (en) 1993-03-05 1995-05-23 Bell Communications Research, Inc. Polymeric electrolytic cell separator membrane
US5540741A (en) 1993-03-05 1996-07-30 Bell Communications Research, Inc. Lithium secondary battery extraction method
WO1994021560A1 (en) † 1993-03-17 1994-09-29 Ultralife Batteries (Uk) Limited Lithiated manganese oxide
US5512214A (en) 1993-03-30 1996-04-30 Koksbang; Rene Lithium battery electrode compositions
JPH08111218A (en) * 1994-10-07 1996-04-30 Honda Motor Co Ltd Positive electrode material for lithium secondary battery and manufacture of the positive electrode material
US5411820A (en) * 1993-06-08 1995-05-02 Valence Technology, Inc. Solid, glyme-containing electrolytes including ion salt derivatives and electrolytic cells produced therefrom
US5384291A (en) 1993-06-25 1995-01-24 The Dow Chemical Company Carbothermal synthesis precursors
US5541020A (en) 1993-07-22 1996-07-30 Golovin; Milton N. Compositions and methods for improving the cumulative capacity of solid, secondary electrolytic cells
JP2966261B2 (en) 1993-11-02 1999-10-25 三菱電線工業株式会社 Positive electrode material for lithium battery and method for producing the same
US5435054A (en) 1993-11-15 1995-07-25 Valence Technology, Inc. Method for producing electrochemical cell
US5399447A (en) 1993-12-06 1995-03-21 Valence Technology, Inc. Acidity reduction of adhesion promoter layer and electrolytic cells produced therefrom
US5463179A (en) 1993-12-06 1995-10-31 Chaloner-Gill; Benjamin Solid electrolyte obtained by the polymerization of diacrylate monomer having a rigid alkane segment
US5482795A (en) * 1994-05-25 1996-01-09 Chaloner-Gill; Benjamin Solid electrolyte utilizing a polymeric matrix obtained by the polymerization of a substituted allylic chloroformate
CN2200998Y (en) * 1994-08-15 1995-06-21 陈振勤 Multifunctional shoulder-protecting warm-keeping pillow
US5496663A (en) 1994-08-19 1996-03-05 Tracor Applied Sciences, Inc. Lithium ion battery with lithium vanadium pentoxide positive electrode
US5514490A (en) 1994-08-30 1996-05-07 Industrial Technology Research Institute Secondary lithium battery using a new layered anode material
JPH08131228A (en) † 1994-11-04 1996-05-28 Hori Lock Kogyo Kk Key holding device of key case
JPH08171938A (en) 1994-12-15 1996-07-02 Mitsubishi Cable Ind Ltd Li secondary battery and its positive electrode
US5830993A (en) * 1995-04-10 1998-11-03 Kansas State University Research Foundation Synthetic antimicrobial peptide
JP3606289B2 (en) * 1995-04-26 2005-01-05 日本電池株式会社 Cathode active material for lithium battery and method for producing the same
US5736957A (en) * 1995-06-30 1998-04-07 The Johns Hopkins University Delay compensated doppler radar altimeter
US5630993A (en) * 1995-07-05 1997-05-20 Bell Communications Research, Inc. Low temperature synthesis of layered lithiated transition metal oxides
US5712059A (en) 1995-09-26 1998-01-27 Valence Technology, Inc. Carbonaceous electrode and compatible electrolyte solvent
US5643695A (en) 1995-09-26 1997-07-01 Valence Technology, Inc. Carbonaceous electrode and compatible electrolyte
US5660948A (en) * 1995-09-26 1997-08-26 Valence Technology, Inc. Lithium ion electrochemical cell
JP3484003B2 (en) 1995-11-07 2004-01-06 日本電信電話株式会社 Non-aqueous electrolyte secondary battery
JP3523397B2 (en) 1995-11-07 2004-04-26 日本電信電話株式会社 Non-aqueous electrolyte secondary battery
JP3024537B2 (en) 1995-12-20 2000-03-21 株式会社村田製作所 Multilayer ceramic capacitors
JP3319258B2 (en) 1995-12-21 2002-08-26 ソニー株式会社 Method for producing positive electrode active material for lithium secondary battery and method for producing lithium secondary battery
US5700298A (en) 1996-03-15 1997-12-23 Valence Technology, Inc. Carbon anode for lithium ion electrochemical cell
JP2833585B2 (en) * 1996-05-17 1998-12-09 日本電気株式会社 Semiconductor nonvolatile storage device
JPH09314724A (en) 1996-05-23 1997-12-09 Toray Ind Inc Structure and manufacture thereof
US6103419A (en) 1996-09-06 2000-08-15 Valence Technology, Inc. Solid secondary lithium cell based on lithiated zirconium, titanium or hafnium oxide cathode material
US5851504A (en) * 1996-09-23 1998-12-22 Valence Technology, Inc. Carbon based electrodes
US5824285A (en) * 1996-10-23 1998-10-20 Valence Technology, Inc. Method of making lithium manganese oxide compounds
US5869207A (en) 1996-12-09 1999-02-09 Valence Technology, Inc. Stabilized electrochemical cell
US5871886A (en) * 1996-12-12 1999-02-16 Taiwan Semiconductor Manufacturing Company, Ltd. Sandwiched middle antireflection coating (SMARC) process
US5993998A (en) 1996-12-20 1999-11-30 Japan Storage Battery Co., Ltd. Positive active material for lithium battery, lithium battery having the same and method for producing the same
US5932375A (en) * 1997-02-18 1999-08-03 Aluminum Company Of America Form charging aluminum-lithium battery cells
US5830602A (en) 1997-02-20 1998-11-03 Valence Technology, Inc. Carbonaceous active material and method of making same
CA2200998A1 (en) 1997-03-25 1998-09-25 Hydro-Quebec New lithium insertion electrode materials based on tetraoxyanions derivatives with olivine structure
US6085015A (en) 1997-03-25 2000-07-04 Hydro-Quebec Lithium insertion electrode materials based on orthosilicate derivatives
US5942204A (en) * 1997-03-31 1999-08-24 Omg Americas, Inc. Method to produce a transition metal carbide from a partially reduced transition metal compound
JPH10312792A (en) * 1997-05-12 1998-11-24 Toyota Central Res & Dev Lab Inc Positive electrode for lithium secondary battery and manufacture thereof
JPH1125893A (en) 1997-06-30 1999-01-29 Shimadzu Corp X-ray tube
JPH1125983A (en) 1997-07-04 1999-01-29 Japan Storage Battery Co Ltd Active material for lithium battery
JP3144674B2 (en) † 1997-09-29 2001-03-12 町夫 清崎 Pilot hole drilling machine
JP3965657B2 (en) 1997-10-03 2007-08-29 株式会社ジーエス・ユアサコーポレーション Active material for lithium battery and positive electrode for lithium battery using the same
JPH11195417A (en) † 1998-01-05 1999-07-21 Mitsubishi Materials Corp Manufacture of high-purity tetragonal lithium manganate powders suitable to be used as positive electrode active material of lithium-ion secondary battery
US6020087A (en) 1998-01-30 2000-02-01 Valence Technology, Inc. Polymer electrolytes containing lithiated fillers
US6306215B1 (en) 1998-03-10 2001-10-23 Valence Technology, Inc. Apparatus for coating current collectors
JP2978874B2 (en) † 1998-03-25 1999-11-15 アンリツ株式会社 Electronic equipment housing
US6153333A (en) 1999-03-23 2000-11-28 Valence Technology, Inc. Lithium-containing phosphate active materials
JP4521542B2 (en) * 1999-03-30 2010-08-11 ルネサスエレクトロニクス株式会社 Semiconductor device and semiconductor substrate
WO2000060680A1 (en) 1999-04-06 2000-10-12 Sony Corporation Active material of positive plate, nonaqueous electrolyte secondary cell, method for producing active material of positive material
CN1300449A (en) † 1999-04-06 2001-06-20 索尼株式会社 Method for manufacturing active material of positive plate and method for manufacturing nanoqueous electrolyte secondary cell
JP4949543B2 (en) 1999-04-06 2012-06-13 ソニー株式会社 Method for synthesizing LiFePO4 and method for producing nonaqueous electrolyte battery
CA2270771A1 (en) 1999-04-30 2000-10-30 Hydro-Quebec New electrode materials with high surface conductivity
JP2001052733A (en) 1999-08-05 2001-02-23 Matsushita Electric Ind Co Ltd Entirely solid lithium secondary battery
JP3504195B2 (en) 1999-09-16 2004-03-08 日本電信電話株式会社 Lithium secondary battery positive electrode active material and lithium secondary battery
JP2001110414A (en) 1999-10-04 2001-04-20 Nippon Telegr & Teleph Corp <Ntt> Material for activating positive electrode of lithium secondary battery and the lithium secondary battery
JP2001110455A (en) 1999-10-12 2001-04-20 Sony Corp Nonaqueous electrolyte battery
US7001690B2 (en) * 2000-01-18 2006-02-21 Valence Technology, Inc. Lithium-based active materials and preparation thereof
US6528033B1 (en) * 2000-01-18 2003-03-04 Valence Technology, Inc. Method of making lithium-containing materials
US6387568B1 (en) * 2000-04-27 2002-05-14 Valence Technology, Inc. Lithium metal fluorophosphate materials and preparation thereof
JP3475911B2 (en) * 2000-05-25 2003-12-10 宇部興産株式会社 Non-aqueous electrolyte and lithium secondary battery using the same
EP1180810A2 (en) * 2000-08-18 2002-02-20 Nissan Motor Co., Ltd. Positive electrode active material for rechargeable lithium-ion battery
CA2320661A1 (en) * 2000-09-26 2002-03-26 Hydro-Quebec New process for synthesizing limpo4 materials with olivine structure
JP4491946B2 (en) * 2000-09-29 2010-06-30 ソニー株式会社 Method for producing positive electrode active material and method for producing non-aqueous electrolyte battery
JP3687515B2 (en) * 2000-10-06 2005-08-24 日本電気株式会社 battery
JP3997702B2 (en) * 2000-10-06 2007-10-24 ソニー株式会社 Nonaqueous electrolyte secondary battery
US6645452B1 (en) * 2000-11-28 2003-11-11 Valence Technology, Inc. Methods of making lithium metal cathode active materials
JP4643903B2 (en) * 2001-04-06 2011-03-02 ヴァレンス テクノロジー インコーポレーテッド Sodium ion battery
US7025907B2 (en) * 2001-05-15 2006-04-11 Kabushiki Kaisha Toyota Chuo Kenkyusho Carbon-containing lithium-iron composite phosphorus oxide for lithium secondary battery positive electrode active material and process for producing the same
JP2003203628A (en) * 2001-12-28 2003-07-18 Sanyo Electric Co Ltd Nonaqueous electrolyte battery and its manufacturing method
US7482097B2 (en) * 2002-04-03 2009-01-27 Valence Technology, Inc. Alkali-transition metal phosphates having a +3 valence non-transition element and related electrode active materials
US7422823B2 (en) * 2002-04-03 2008-09-09 Valence Technology, Inc. Alkali-iron-cobalt phosphates and related electrode active materials
US6913855B2 (en) * 2002-07-22 2005-07-05 Valence Technology, Inc. Method of synthesizing electrochemically active materials from a slurry of precursors

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5910382A (en) * 1996-04-23 1999-06-08 Board Of Regents, University Of Texas Systems Cathode materials for secondary (rechargeable) lithium batteries
WO1998012761A1 (en) * 1996-09-23 1998-03-26 Valence Technology, Inc. Lithium-containing, lithium-intercalating phosphates and their use as the positive or negative electrode material in a lithium secondary battery
WO2000001024A1 (en) * 1998-06-26 2000-01-06 Valence Technology, Inc. Lithium-containing silicon/phosphates, method of preparation, and uses thereof

Cited By (151)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6777132B2 (en) 2000-04-27 2004-08-17 Valence Technology, Inc. Alkali/transition metal halo—and hydroxy-phosphates and related electrode active materials
US8057769B2 (en) 2000-04-27 2011-11-15 Valence Technology, Inc. Method for making phosphate-based electrode active materials
US7524584B2 (en) 2000-04-27 2009-04-28 Valence Technology, Inc. Electrode active material for a secondary electrochemical cell
US7270915B2 (en) 2000-04-27 2007-09-18 Valence Technology, Inc. Alkali/transition metal HALO-and hydroxy-phosphates and related electrode active materials
US7261977B2 (en) 2000-04-27 2007-08-28 Valence Technology, Inc. Lithium metal fluorophosphate and preparation thereof
US7214448B2 (en) 2000-04-27 2007-05-08 Valence Technology, Inc. Alkali/transition metal halo-and hydroxy-phosphates and related electrode active materials
US6964827B2 (en) 2000-04-27 2005-11-15 Valence Technology, Inc. Alkali/transition metal halo- and hydroxy-phosphates and related electrode active materials
US6855462B2 (en) 2000-04-27 2005-02-15 Valence Technology, Inc. Lithium metal fluorophosphate materials and preparation thereof
EP1184920A2 (en) 2000-08-30 2002-03-06 Sony Corporation Cathode active material, method for preparation thereof, non-aqueous electrolyte cell and method for preparation thereof
EP1184920A3 (en) * 2000-08-30 2004-03-03 Sony Corporation Cathode active material, method for preparation thereof, non-aqueous electrolyte cell and method for preparation thereof
US7285260B2 (en) 2000-09-26 2007-10-23 Hydro Quebec Synthesis method for carbon material based on LixM1-yM'(XO4)n
US7457018B2 (en) 2000-09-26 2008-11-25 Hydro-Quebec Synthesis method for carbon material based on LiMPO4
US7601318B2 (en) 2000-09-26 2009-10-13 Hydro-Quebec Method for synthesis of carbon-coated redox materials with controlled size
WO2002027824A1 (en) * 2000-09-26 2002-04-04 HYDRO-QUéBEC Synthesis method for carbon material based on lixm1-ym'(xo4)n
EP2362467A1 (en) 2000-09-26 2011-08-31 Hydro Quebec Synthesis process of redox materials coated with carbon having a controlled size
EP2442387A1 (en) 2000-09-26 2012-04-18 Hydro-Québec Synthesis method for carbon material based on LIxM1-yM'(XO4)N
US6797431B2 (en) 2000-09-29 2004-09-28 Sony Corporation Method for the preparation of cathode active material and method for the preparation of non-aqueous electrolyte
EP2256846A1 (en) * 2000-09-29 2010-12-01 Sony Corporation Method for the preparation of cathode active material and method for the preparation of a non-aqueous electrolyte cell
EP1193784A3 (en) * 2000-09-29 2004-03-10 Sony Corporation Method for the preparation of cathode active material and method for the preparation of a non-aqueous electrolyte cell
EP1193785A3 (en) * 2000-09-29 2004-03-03 Sony Corporation Method for the preparation of cathode active material and method for the preparation of a non-aqueous electrolyte cell
US6811924B2 (en) 2000-09-29 2004-11-02 Sony Corporation Method for the preparation of cathode active material and method for the preparation of non-aqueous electrolyte
EP1193787A3 (en) * 2000-09-29 2004-03-03 Sony Corporation Method for the preparation of cathode active material and method for the preparation of a non-aqueous electrolyte cell
EP1193785A2 (en) 2000-09-29 2002-04-03 Sony Corporation Method for the preparation of cathode active material and method for the preparation of a non-aqueous electrolyte cell
KR100777932B1 (en) * 2000-09-29 2007-11-20 소니 가부시끼 가이샤 Method for the preparation of cathode active material and method for the preparation of non-aqueous electrolyte cell
EP1193783A3 (en) * 2000-09-29 2003-05-14 Sony Corporation Method for the preparation of cathode active material and method for the preparation of a non-aqueous electrolyte cell
EP2256845A1 (en) * 2000-09-29 2010-12-01 Sony Corporation Method for the preparation of cathode active material and method for the preparation of a non-aqueous electrolyte cell
EP1193787A2 (en) 2000-09-29 2002-04-03 Sony Corporation Method for the preparation of cathode active material and method for the preparation of a non-aqueous electrolyte cell
EP1193783A2 (en) * 2000-09-29 2002-04-03 Sony Corporation Method for the preparation of cathode active material and method for the preparation of a non-aqueous electrolyte cell
EP1193784A2 (en) 2000-09-29 2002-04-03 Sony Corporation Method for the preparation of cathode active material and method for the preparation of a non-aqueous electrolyte cell
US7101521B2 (en) 2000-09-29 2006-09-05 Sony Corporation Method for the preparation of cathode active material and method for the preparation of non-aqueous electrolyte
EP1574477A3 (en) * 2000-11-28 2005-11-09 Valence Technology, Inc. Methods of making lithium metal compounds useful as cathode active materials
KR100851484B1 (en) * 2000-11-28 2008-08-08 발렌스 테크놀로지, 인코포레이티드 Method of making lithium metal phosphate compounds useful as cathode active materials
JP2009018989A (en) * 2000-11-28 2009-01-29 Valence Technology Inc Method for preparing lithium metal compound useful as cathode active material
WO2002044084A2 (en) * 2000-11-28 2002-06-06 Valence Technology, Inc. Methods of making lithium metal compounds useful as cathode active materials
US6960331B2 (en) 2000-11-28 2005-11-01 Valence Technology, Inc. Methods of making lithium metal cathode active materials
WO2002044084A3 (en) * 2000-11-28 2002-08-15 Valence Technology Inc Methods of making lithium metal compounds useful as cathode active materials
EP2277829A3 (en) * 2000-11-28 2011-12-07 Valence Technology, Inc. Methods of making lithium metal compounds useful as cathode active materials
US6645452B1 (en) 2000-11-28 2003-11-11 Valence Technology, Inc. Methods of making lithium metal cathode active materials
KR100851486B1 (en) * 2000-11-28 2008-08-08 발렌스 테크놀로지, 인코포레이티드 Method of making metal phosphate compounds useful as cathode active materials
KR100851487B1 (en) * 2000-11-28 2008-08-08 발렌스 테크놀로지, 인코포레이티드 Method of making lithium transition metal oxide compounds useful as cathode active materials
KR100851485B1 (en) * 2000-11-28 2008-08-08 발렌스 테크놀로지, 인코포레이티드 Method of making lithium metal fluorophosphate compounds useful as cathode active materials
JP4932130B2 (en) * 2001-04-10 2012-05-16 ツェントゥルム フューア ゾンネンエネルギー−ウント ヴァッサーシュトッフ−フォルシュング バーデン−ヴァルテムベルク ゲマインニュッツィヒ シュティフトゥング Binary, ternary and quaternary lithium phosphates, methods for their production and use
JP2004525059A (en) * 2001-04-10 2004-08-19 ツェントゥルム フューア ゾンネンエネルギー−ウント ヴァッサーシュトッフ−フォルシュング バーデン−ヴァルテムベルク ゲマインニュッツィヒ シュティフトゥング Binary, ternary and quaternary lithium phosphates, their preparation and use
US8168150B2 (en) 2001-04-10 2012-05-01 Zentrum Fur Sonnenenergie-Und Wasserstoff-Forschung Baden-Wurttenberg, Gemeinnutzige Stiftung Binary, ternary and quaternary lithium phosphates, method for the production thereof and use of the same
JP2003045430A (en) * 2001-07-31 2003-02-14 Mitsui Eng & Shipbuild Co Ltd Manufacturing method of positive electrode material for secondary battery and secondary battery
EP2242134A1 (en) 2001-10-26 2010-10-20 Valence Technology, Inc. Alkali/transition metal halo - and hydroxy-phosphates and related electrode active materials
JP2005514304A (en) * 2001-12-21 2005-05-19 マサチューセッツ・インスティチュート・オブ・テクノロジー Conductive lithium storage electrode
EP2278643A1 (en) * 2001-12-21 2011-01-26 Massachusetts Institute of Technology (MIT) Conductive Lithium Storage Electrode
CN100414746C (en) * 2001-12-21 2008-08-27 麻省理工学院 Conductive lithium storage electrode
WO2003056646A1 (en) * 2001-12-21 2003-07-10 Massachusetts Institute Of Technology Conductive lithium storage electrode
JP4712302B2 (en) * 2001-12-21 2011-06-29 マサチューセッツ インスティテュート オブ テクノロジー Conductive lithium storage electrode
US8148013B2 (en) 2001-12-21 2012-04-03 Massachusetts Institute Of Technology Conductive lithium storage electrode
AU2011204875B2 (en) * 2001-12-21 2013-12-05 Massachusetts Institute Of Technology Conductive lithium storage electrode
US8852807B2 (en) 2001-12-21 2014-10-07 Massachusetts Institute Of Technology Conductive lithium storage electrode
US6815122B2 (en) 2002-03-06 2004-11-09 Valence Technology, Inc. Alkali transition metal phosphates and related electrode active materials
EP2436647A3 (en) * 2002-03-06 2012-07-04 Valence Technology, Inc. Alkali/transition metal phosphates and related electrode active materials
US7767332B2 (en) 2002-03-06 2010-08-03 Valence Technology, Inc. Alkali/transition metal phosphates and related electrode active materials
EP2436647A2 (en) 2002-03-06 2012-04-04 Valence Technology, Inc. Alkali/transition metal phosphates and related electrode active materials
US8318352B2 (en) 2002-04-03 2012-11-27 Valence Technology, Inc. Batteries comprising alkali-transition metal phosphates and preferred electrolytes
EP1506135A1 (en) * 2002-05-17 2005-02-16 Valence Technology, Inc. Synthesis of metal compounds useful as cathode active materials
EP2583939A2 (en) 2002-05-17 2013-04-24 Valence Technology (Nevada), Inc. Synthesis of metal compounds useful as cathode active materials
KR100968678B1 (en) * 2002-05-17 2010-07-06 발렌스 테크놀로지, 인코포레이티드 Synthesis of metal compounds useful as cathode active materials
EP1506135A4 (en) * 2002-05-17 2010-05-05 Valence Technology Inc Synthesis of metal compounds useful as cathode active materials
EP2583939A3 (en) * 2002-05-17 2015-03-11 Valence Technology (Nevada), Inc. Synthesis of metal compounds useful as cathode active materials
JP2010047471A (en) * 2002-05-17 2010-03-04 Valence Technology Inc Method for synthesizing metal compound useful as cathode active material
US8425976B2 (en) 2002-05-30 2013-04-23 Hydro-Quebec Method for preparing ceramic powders in the presence of a carbon source, powders obtained and use thereof
US20130247863A1 (en) * 2002-05-30 2013-09-26 Hydro-Quebec Process for preparing ceramic powders in the presence of a source of carbon, powders thus obtained and their use
US9394205B2 (en) 2002-05-30 2016-07-19 Hydro-Quebec Process for preparing ceramic powders in the presence of a source of carbon, powders thus obtained and their use
US20100173160A1 (en) * 2002-05-30 2010-07-08 Hydro-Quebec Method for preparing ceramic powders in the presence of a carbon source, powders obtained and use thereof
WO2003101909A1 (en) * 2002-05-30 2003-12-11 HYDRO-QUéBEC Method for preparing ceramic powders in the presence of a carbon source, powders obtained and use thereof
US20140309100A1 (en) * 2002-05-30 2014-10-16 Hydro-Quebec Process for preparing ceramic powders in the presence of a source of carbon, powders thus obtained and their use
JP2005528315A (en) * 2002-05-30 2005-09-22 イドロ−ケベック Process for producing ceramic powder in the presence of a carbon source and the resulting powder and its use
US8765261B2 (en) 2002-05-30 2014-07-01 Hydro-Quebec Process for preparing ceramic powders in the presence of a source of carbon, powders thus obtained and their use
US9492412B2 (en) 2002-10-25 2016-11-15 Foamix Pharmaceuticals Ltd. Penetrating pharmaceutical foam
US9622947B2 (en) 2002-10-25 2017-04-18 Foamix Pharmaceuticals Ltd. Foamable composition combining a polar solvent and a hydrophobic carrier
US9265725B2 (en) 2002-10-25 2016-02-23 Foamix Pharmaceuticals Ltd. Dicarboxylic acid foamable vehicle and pharmaceutical compositions thereof
US10821077B2 (en) 2002-10-25 2020-11-03 Foamix Pharmaceuticals Ltd. Dicarboxylic acid foamable vehicle and pharmaceutical compositions thereof
US9668972B2 (en) 2002-10-25 2017-06-06 Foamix Pharmaceuticals Ltd. Nonsteroidal immunomodulating kit and composition and uses thereof
US8900554B2 (en) 2002-10-25 2014-12-02 Foamix Pharmaceuticals Ltd. Foamable composition and uses thereof
US11033491B2 (en) 2002-10-25 2021-06-15 Vyne Therapeutics Inc. Dicarboxylic acid foamable vehicle and pharmaceutical compositions thereof
US9320705B2 (en) 2002-10-25 2016-04-26 Foamix Pharmaceuticals Ltd. Sensation modifying topical composition foam
US9713643B2 (en) 2002-10-25 2017-07-25 Foamix Pharmaceuticals Ltd. Foamable carriers
US8840869B2 (en) 2002-10-25 2014-09-23 Foamix Ltd. Body cavity foams
US9539208B2 (en) 2002-10-25 2017-01-10 Foamix Pharmaceuticals Ltd. Foam prepared from nanoemulsions and uses
US10322085B2 (en) 2002-10-25 2019-06-18 Foamix Pharmaceuticals Ltd. Dicarboxylic acid foamable vehicle and pharmaceutical compositions thereof
US10117812B2 (en) 2002-10-25 2018-11-06 Foamix Pharmaceuticals Ltd. Foamable composition combining a polar solvent and a hydrophobic carrier
US9211259B2 (en) 2002-11-29 2015-12-15 Foamix Pharmaceuticals Ltd. Antibiotic kit and composition and uses thereof
US7718317B2 (en) 2002-12-19 2010-05-18 Valence Technology, Inc. Electrode active material and method of making the same
JP2006511038A (en) * 2002-12-19 2006-03-30 ヴァレンス　テクノロジー　インコーポレーテッド Electrode active material and method for producing the same
US9636405B2 (en) 2003-08-04 2017-05-02 Foamix Pharmaceuticals Ltd. Foamable vehicle and pharmaceutical compositions thereof
US9101662B2 (en) 2003-08-04 2015-08-11 Foamix Pharmaceuticals Ltd. Compositions with modulating agents
US9050253B2 (en) 2003-08-04 2015-06-09 Foamix Pharmaceuticals Ltd. Oleaginous pharmaceutical and cosmetic foam
DE112004001997B4 (en) * 2003-10-21 2013-11-21 Valence Technology, Inc. METHOD FOR PRODUCING LITHIUM PHOSPHATE ELECTRODE ACTIVE MATERIALS AND ELECTRODE ACTIVE MATERIALS MADE THEREFOR
WO2005114769A2 (en) 2004-05-20 2005-12-01 Valence Technology, Inc. Synthesis of cathode active materials
EP1751810A4 (en) * 2004-05-20 2012-05-09 Valence Technology Inc Synthesis of cathode active materials
EP1751810A2 (en) * 2004-05-20 2007-02-14 Valence Technology, Inc. Synthesis of cathode active materials
WO2008048995A2 (en) 2006-10-17 2008-04-24 Valence Technology, Inc. Method and apparatus for monitoring and controlling an electrochemical cell
US9682021B2 (en) 2006-11-14 2017-06-20 Foamix Pharmaceuticals Ltd. Substantially non-aqueous foamable petrolatum based pharmaceutical and cosmetic compositions and their uses
US10369102B2 (en) 2007-08-07 2019-08-06 Foamix Pharmaceuticals Ltd. Wax foamable vehicle and pharmaceutical compositions thereof
US9662298B2 (en) 2007-08-07 2017-05-30 Foamix Pharmaceuticals Ltd. Wax foamable vehicle and pharmaceutical compositions thereof
US11103454B2 (en) 2007-08-07 2021-08-31 Vyne Therapeutics Inc. Wax foamable vehicle and pharmaceutical compositions thereof
US9439857B2 (en) 2007-11-30 2016-09-13 Foamix Pharmaceuticals Ltd. Foam containing benzoyl peroxide
US8900553B2 (en) 2007-12-07 2014-12-02 Foamix Pharmaceuticals Ltd. Oil and liquid silicone foamable carriers and formulations
US11433025B2 (en) 2007-12-07 2022-09-06 Vyne Therapeutics Inc. Oil foamable carriers and formulations
US9549898B2 (en) 2007-12-07 2017-01-24 Foamix Pharmaceuticals Ltd. Oil and liquid silicone foamable carriers and formulations
US9795564B2 (en) 2007-12-07 2017-10-24 Foamix Pharmaceuticals Ltd. Oil-based foamable carriers and formulations
US9161916B2 (en) 2007-12-07 2015-10-20 Foamix Pharmaceuticals Ltd. Carriers, formulations, methods for formulating unstable active agents for external application and uses thereof
EP2220707A1 (en) * 2007-12-11 2010-08-25 Valence Technology, INC. Process for producing electrode active material for lithium ion cell
WO2009076153A1 (en) 2007-12-11 2009-06-18 Valence Technology, Inc. Process for producing electrode active material for lithium ion cell
EP2220707A4 (en) * 2007-12-11 2013-06-19 Valence Technology Inc Process for producing electrode active material for lithium ion cell
US10213384B2 (en) 2009-04-28 2019-02-26 Foamix Pharmaceuticals Ltd. Foamable vehicles and pharmaceutical compositions comprising aprotic polar solvents and uses thereof
US10588858B2 (en) 2009-04-28 2020-03-17 Foamix Pharmaceuticals Ltd. Foamable vehicles and pharmaceutical compositions comprising aprotic polar solvents and uses thereof
US9884017B2 (en) 2009-04-28 2018-02-06 Foamix Pharmaceuticals Ltd. Foamable vehicles and pharmaceutical compositions comprising aprotic polar solvents and uses thereof
US10363216B2 (en) 2009-04-28 2019-07-30 Foamix Pharmaceuticals Ltd. Foamable vehicles and pharmaceutical compositions comprising aprotic polar solvents and uses thereof
US9572775B2 (en) 2009-07-29 2017-02-21 Foamix Pharmaceuticals Ltd. Non surfactant hydro-alcoholic foamable compositions, breakable foams and their uses
US10350166B2 (en) 2009-07-29 2019-07-16 Foamix Pharmaceuticals Ltd. Non surface active agent non polymeric agent hydro-alcoholic foamable compositions, breakable foams and their uses
US11219631B2 (en) 2009-07-29 2022-01-11 Vyne Pharmaceuticals Inc. Foamable compositions, breakable foams and their uses
US9072667B2 (en) 2009-07-29 2015-07-07 Foamix Pharmaceuticals Ltd. Non surface active agent non polymeric agent hydro-alcoholic foamable compositions, breakable foams and their uses
US10092588B2 (en) 2009-07-29 2018-10-09 Foamix Pharmaceuticals Ltd. Foamable compositions, breakable foams and their uses
US9167813B2 (en) 2009-07-29 2015-10-27 Foamix Pharmaceuticals Ltd. Non surfactant hydro-alcoholic foamable compositions, breakable foams and their uses
KR20120079058A (en) 2009-09-09 2012-07-11 도다 고교 가부시끼가이샤 Ferric phosphate hydrate particle powder and process for production thereof, olivine-type lithium iron phosphate particle powder and process for production thereof, and non-aqueous electrolyte secondary battery
WO2011030786A1 (en) 2009-09-09 2011-03-17 戸田工業株式会社 Ferric phosphate hydrate particle powder and process for production thereof, olivine-type lithium iron phosphate particle powder and process for production thereof, and non-aqueous electrolyte secondary battery
US8871184B2 (en) 2009-10-02 2014-10-28 Foamix Ltd. Topical tetracycline compositions
US8992896B2 (en) 2009-10-02 2015-03-31 Foamix Pharmaceuticals Ltd. Topical tetracycline compositions
US10137200B2 (en) 2009-10-02 2018-11-27 Foamix Pharmaceuticals Ltd. Surfactant-free water-free foamable compositions, breakable foams and gels and their uses
US10213512B2 (en) 2009-10-02 2019-02-26 Foamix Pharmaceuticals Ltd. Topical tetracycline compositions
US10029013B2 (en) 2009-10-02 2018-07-24 Foamix Pharmaceuticals Ltd. Surfactant-free, water-free formable composition and breakable foams and their uses
US10238746B2 (en) 2009-10-02 2019-03-26 Foamix Pharmaceuticals Ltd Surfactant-free water-free foamable compositions, breakable foams and gels and their uses
US10265404B2 (en) 2009-10-02 2019-04-23 Foamix Pharmaceuticals Ltd. Compositions, gels and foams with rheology modulators and uses thereof
US10322186B2 (en) 2009-10-02 2019-06-18 Foamix Pharmaceuticals Ltd. Topical tetracycline compositions
US9849142B2 (en) 2009-10-02 2017-12-26 Foamix Pharmaceuticals Ltd. Methods for accelerated return of skin integrity and for the treatment of impetigo
US8865139B1 (en) 2009-10-02 2014-10-21 Foamix Pharmaceuticals Ltd. Topical tetracycline compositions
US9675700B2 (en) 2009-10-02 2017-06-13 Foamix Pharmaceuticals Ltd. Topical tetracycline compositions
US10967063B2 (en) 2009-10-02 2021-04-06 Vyne Therapeutics Inc. Surfactant-free, water-free formable composition and breakable foams and their uses
US10946101B2 (en) 2009-10-02 2021-03-16 Vyne Therapeutics Inc. Surfactant-free water-free foamable compositions, breakable foams and gels and their uses
US10463742B2 (en) 2009-10-02 2019-11-05 Foamix Pharmaceuticals Ltd. Topical tetracycline compositions
US10517882B2 (en) 2009-10-02 2019-12-31 Foamix Pharmaceuticals Ltd. Method for healing of an infected acne lesion without scarring
US10086080B2 (en) 2009-10-02 2018-10-02 Foamix Pharmaceuticals Ltd. Topical tetracycline compositions
US10610599B2 (en) 2009-10-02 2020-04-07 Foamix Pharmaceuticals Ltd. Topical tetracycline compositions
US8945516B2 (en) 2009-10-02 2015-02-03 Foamix Pharmaceuticals Ltd. Surfactant-free water-free foamable compositions, breakable foams and gels and their uses
US10821187B2 (en) 2009-10-02 2020-11-03 Foamix Pharmaceuticals Ltd. Compositions, gels and foams with rheology modulators and uses thereof
US10835613B2 (en) 2009-10-02 2020-11-17 Foamix Pharmaceuticals Ltd. Compositions, gels and foams with rheology modulators and uses thereof
US9577244B2 (en) 2010-01-28 2017-02-21 Johnson Matthey Plc Substituted lithium-manganese metal phosphate
CN104080733A (en) * 2011-12-23 2014-10-01 朗盛德国有限责任公司 LiPF6 solution
CN102881865A (en) * 2012-09-14 2013-01-16 北京鼎能开源电池科技股份有限公司 Method for manufacturing positive plate of battery
WO2014184533A1 (en) * 2013-05-14 2014-11-20 Faradion Limited Metal-containing compounds
US11532806B2 (en) 2014-04-01 2022-12-20 The Research Foundation For The State University Of New York Electrode materials that include an active composition of the formula MgzMxOy for group II cation-based batteries
US9780372B2 (en) 2015-09-30 2017-10-03 Sumitomo Osaka Cement Co., Ltd. Electrode material for lithium-ion rechargeable battery
US10849847B2 (en) 2016-09-08 2020-12-01 Foamix Pharamaceuticals Ltd. Compositions and methods for treating rosacea and acne
US10398641B2 (en) 2016-09-08 2019-09-03 Foamix Pharmaceuticals Ltd. Compositions and methods for treating rosacea and acne
US11324691B2 (en) 2016-09-08 2022-05-10 Journey Medical Corporation Compositions and methods for treating rosacea and acne

Also Published As

Publication number Publication date
ES2225292T3 (en) 2005-03-16
EP1391424A2 (en) 2004-02-25
CA2395115A1 (en) 2001-07-26
US20050255026A1 (en) 2005-11-17
KR20020090210A (en) 2002-11-30
EP1391424B1 (en) 2009-02-18
DE60013909D1 (en) 2004-10-21
CA2395115C (en) 2004-07-20
US20050255383A1 (en) 2005-11-17
EP1252093A1 (en) 2002-10-30
US20040214084A1 (en) 2004-10-28
DE60013909T2 (en) 2005-09-29
CA2568211C (en) 2009-11-17
ATE423080T1 (en) 2009-03-15
US6528033B1 (en) 2003-03-04
US20020086214A1 (en) 2002-07-04
US6702961B2 (en) 2004-03-09
IN2002CH01089A (en) 2007-04-06
US20040185344A1 (en) 2004-09-23
EP1391424A3 (en) 2005-12-28
US20030215715A1 (en) 2003-11-20
US7060206B2 (en) 2006-06-13
CA2466366C (en) 2007-03-27
JP4387401B2 (en) 2009-12-16
US6716372B2 (en) 2004-04-06
JP3933470B2 (en) 2007-06-20
US7276218B2 (en) 2007-10-02
DK1252093T3 (en) 2005-01-10
US6730281B2 (en) 2004-05-04
CN1248958C (en) 2006-04-05
US7550098B2 (en) 2009-06-23
US20030215714A1 (en) 2003-11-20
CA2568211A1 (en) 2001-07-26
ATE276200T1 (en) 2004-10-15
US20070001153A1 (en) 2007-01-04
JP2007115709A (en) 2007-05-10
CN1424980A (en) 2003-06-18
EP1391424B2 (en) 2012-11-07
EP1252093B1 (en) 2004-09-15
AU2001226030A1 (en) 2001-07-31
JP2003520405A (en) 2003-07-02
US8163430B2 (en) 2012-04-24
HK1051174A1 (en) 2003-07-25
CA2466366A1 (en) 2001-07-26
KR100539341B1 (en) 2005-12-28
DE60041605D1 (en) 2009-04-02
US20080020277A1 (en) 2008-01-24

Similar Documents

Publication Publication Date Title
EP1252093B1 (en) Preparation of lithium-containing materials
EP1252671B1 (en) Lithium-based electrochemically active materials and preparation thereof
US6136472A (en) Lithium-containing silicon/phosphates, method of preparation, and uses thereof including as electrodes for a battery
EP1173897B1 (en) Lithium-containing phosphate active materials
CA2460875C (en) Lithium-based electrochemically active materials and preparation thereof
CA2596239C (en) Lithium-based electrochemically active materials and preparation thereof

Legal Events

Date Code Title Description
AK Designated states

Kind code of ref document: A1

Designated state(s): AE AG AL AM AT AU AZ BA BB BG BR BY BZ CA CH CN CR CU CZ DE DK DM DZ EE ES FI GB GD GE GH GM HR HU ID IL IN IS JP KE KG KP KR KZ LC LK LR LS LT LU LV MA MD MG MK MN MW MX MZ NO NZ PL PT RO RU SD SE SG SI SK SL TJ TM TR TT TZ UA UG US UZ VN YU ZA ZW

AL Designated countries for regional patents

Kind code of ref document: A1

Designated state(s): GH GM KE LS MW MZ SD SL SZ TZ UG ZW AM AZ BY KG KZ MD RU TJ TM AT BE CH CY DE DK ES FI FR GB GR IE IT LU MC NL PT SE TR BF BJ CF CG CI CM GA GN GW ML MR NE SN TD TG

121 Ep: the epo has been informed by wipo that ep was designated in this application
DFPE Request for preliminary examination filed prior to expiration of 19th month from priority date (pct application filed before 20040101)
WWE Wipo information: entry into national phase

Ref document number: 2395115

Country of ref document: CA

WWE Wipo information: entry into national phase

Ref document number: 2000989532

Country of ref document: EP

WWE Wipo information: entry into national phase

Ref document number: IN/PCT/2002/1089/CHE

Country of ref document: IN

ENP Entry into the national phase

Ref document number: 2001 553213

Country of ref document: JP

Kind code of ref document: A

WWE Wipo information: entry into national phase

Ref document number: 008184992

Country of ref document: CN

Ref document number: 1020027009266

Country of ref document: KR

WWP Wipo information: published in national office

Ref document number: 2000989532

Country of ref document: EP

WWP Wipo information: published in national office

Ref document number: 1020027009266

Country of ref document: KR

REG Reference to national code

Ref country code: DE

Ref legal event code: 8642

WWG Wipo information: grant in national office

Ref document number: 2000989532

Country of ref document: EP

WWG Wipo information: grant in national office

Ref document number: 1020027009266

Country of ref document: KR