Classifications

• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08G—MACROMOLECULAR COMPOUNDS OBTAINED OTHERWISE THAN BY REACTIONS ONLY INVOLVING UNSATURATED CARBON-TO-CARBON BONDS
  • C08G65/00—Macromolecular compounds obtained by reactions forming an ether link in the main chain of the macromolecule
  • C08G65/02—Macromolecular compounds obtained by reactions forming an ether link in the main chain of the macromolecule from cyclic ethers by opening of the heterocyclic ring
  • C08G65/32—Polymers modified by chemical after-treatment
  • C08G65/329—Polymers modified by chemical after-treatment with organic compounds
  • C08G65/333—Polymers modified by chemical after-treatment with organic compounds containing nitrogen
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08G—MACROMOLECULAR COMPOUNDS OBTAINED OTHERWISE THAN BY REACTIONS ONLY INVOLVING UNSATURATED CARBON-TO-CARBON BONDS
  • C08G73/00—Macromolecular compounds obtained by reactions forming a linkage containing nitrogen with or without oxygen or carbon in the main chain of the macromolecule, not provided for in groups C08G12/00 - C08G71/00
  • C08G73/02—Polyamines
  • C08G73/0206—Polyalkylene(poly)amines
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08G—MACROMOLECULAR COMPOUNDS OBTAINED OTHERWISE THAN BY REACTIONS ONLY INVOLVING UNSATURATED CARBON-TO-CARBON BONDS
  • C08G73/00—Macromolecular compounds obtained by reactions forming a linkage containing nitrogen with or without oxygen or carbon in the main chain of the macromolecule, not provided for in groups C08G12/00 - C08G71/00
  • C08G73/02—Polyamines
  • C08G73/024—Polyamines containing oxygen in the form of ether bonds in the main chain
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
  • C08J5/00—Manufacture of articles or shaped materials containing macromolecular substances
  • C08J5/20—Manufacture of shaped structures of ion-exchange resins
  • C08J5/22—Films, membranes or diaphragms
  • C08J5/2206—Films, membranes or diaphragms based on organic and/or inorganic macromolecular compounds
  • C08J5/2218—Synthetic macromolecular compounds
  • C08J5/2256—Synthetic macromolecular compounds based on macromolecular compounds obtained by reactions other than those involving carbon-to-carbon bonds, e.g. obtained by polycondensation
• • 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
  • H01M10/0565—Polymeric materials, e.g. gel-type or solid-type
• • H—ELECTRICITY
  • H01—ELECTRIC ELEMENTS
  • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
  • H01M8/00—Fuel cells; Manufacture thereof
  • H01M8/10—Fuel cells with solid electrolytes
  • H01M8/1016—Fuel cells with solid electrolytes characterised by the electrolyte material
  • H01M8/1018—Polymeric electrolyte materials
  • H01M8/102—Polymeric electrolyte materials characterised by the chemical structure of the main chain of the ion-conducting polymer
  • H01M8/1027—Polymeric electrolyte materials characterised by the chemical structure of the main chain of the ion-conducting polymer having carbon, oxygen and other atoms, e.g. sulfonated polyethersulfones [S-PES]
• • H—ELECTRICITY
  • H01—ELECTRIC ELEMENTS
  • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
  • H01M8/00—Fuel cells; Manufacture thereof
  • H01M8/10—Fuel cells with solid electrolytes
  • H01M8/1016—Fuel cells with solid electrolytes characterised by the electrolyte material
  • H01M8/1018—Polymeric electrolyte materials
  • H01M8/102—Polymeric electrolyte materials characterised by the chemical structure of the main chain of the ion-conducting polymer
  • H01M8/103—Polymeric electrolyte materials characterised by the chemical structure of the main chain of the ion-conducting polymer having nitrogen, e.g. sulfonated polybenzimidazoles [S-PBI], polybenzimidazoles with phosphoric acid, sulfonated polyamides [S-PA] or sulfonated polyphosphazenes [S-PPh]
• • H—ELECTRICITY
  • H01—ELECTRIC ELEMENTS
  • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
  • H01M8/00—Fuel cells; Manufacture thereof
  • H01M8/10—Fuel cells with solid electrolytes
  • H01M8/1016—Fuel cells with solid electrolytes characterised by the electrolyte material
  • H01M8/1018—Polymeric electrolyte materials
  • H01M8/1069—Polymeric electrolyte materials characterised by the manufacturing processes
  • H01M8/1072—Polymeric electrolyte materials characterised by the manufacturing processes by chemical reactions, e.g. insitu polymerisation or insitu crosslinking
• • 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
• • 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
  • 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
  • Y02E60/30—Hydrogen technology
  • Y02E60/50—Fuel cells
• • 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
  • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
  • Y02P70/00—Climate change mitigation technologies in the production process for final industrial or consumer products
  • Y02P70/50—Manufacturing or production processes characterised by the final manufactured product

Definitions

• the present invention provides a room temperature crosslinkable polymer system comprising an anhydride containing polymer and an oxyalkylene amine and a polymer electrolyte derived therefrom.
• the polymer and electrolyte are useful as ion conducting materials for batteries such as lithium ion battery, solar cells and electrochromic devices.
• Polymer electrolytes have attracted great interest because of their potential in the development of new technologies such as polymer batteries, fuel cells and sensors.
• the lithium ion battery provides high energy density due to the small atomic weight and the large ionization energy of lithium and has become widely used as a power source for many portable electronics such as cellular phones, laptop computers, mini-cameras, etc.
• an electron insulating separator is used to separate the two electrodes and electrolytes are used to facilitate the necessary passage of ions between reduction and oxidation sites.
• Membranes made from polymeric electrolytes can serve as a combination of separator and electrolyte providing greater efficiency in manufacture of the batteries while addressing growing concerns about their safety by eliminating the flammable organic solvents used in many electrolyte systems.
• PEO poly(ethylene oxide)
• This complex has a relatively good ionic conductivity in a solid state.
• the ionic conductivity is insufficient as compared with the ionic conductivity of the non aqueous electrolyte solution and the cation transport number of the complex is extremely low.
• polymer electrolytes composed of linear polyethylene oxide related polymers such as polypropylene oxide, polyethyleneimine, polyurethane and polyester were developed.
• these polymer electrolytes have an ionic conductivity at room temperature of about 10 ⁇ 7 to 10 ⁇ 6 S/cm. It is believed that ion conduction is due mainly to the amorphous portion of a polyether polymer which conducts ions by local movement of polymer chain segments, Armand, Solid State Ionics, Vol. 9/10, p. 745-754, 1983.
• a linear polyether polymer such as PEO tends to crystallize with metallic salt dissolved therein and thus limits ion movement so that actual ion conductivity is much lower than the predicted value.
• the cation transport number of the PEO complex tends to be extremely low due to a strong interaction of cations with polar groups of the matrix polymer relative to that of anions.
• the electrodes used are active to cations.
• an electrolyte with both moveable cations and anions is used, the movement of anions can be interrupted by the cathode resulting in a concentration polarization which may cause fluctuations in voltage or output of the secondary battery.
• an ionic conductor having non-moveable anions is desirable.
• Such material is often referred to as single-ion conductor and generally has a high cation transport number.
• the conducting branched polyvinyl alcohol is not covalently linked to the crosslinked network.
• Solid polymer electrolytes with tackiness were formed by heating (e.g., at 100° C.) to achieve crosslinking.
• U.S. Pat. No. 6,881,820 discloses a series of rod-coil block polyimide copolymers formed by condensation polymerization of a tetracarboxylic acid dianhydride with a polyoxyalkylene diamine and an aromatic polyfunctional amine that can be fabricated into mechanically resilient film with acceptable ionic or protonic conductivity at variety temperatures.
• the copolymers consist of short-rigid polyimide rod segments alternating with polyether coil segments.
• copolymers with graft or comb structures consisting of a rigid polymer backbone with polyether coil graft segments is not disclosed, nor is preparation of crosslinked copolymers using polyfunctional anhydride such as styrene and maleic anhydride copolymer with more than two anhydride functional groups.
• an inorganic solid electrolyte such as lithium sulfide (Li 2 S) and silicon sulfide (SiS 2 )
• an organic binder polymer such as polybutadiene copolymer rubber
• GPE gel polymer electrolytes
• PEO poly(ethylene oxide)
• PVC poly(acrylonitrile)
• PMMA poly(methyl methacrylate)
• PVDF poly(vinylidene fluoride)
• PEO-based electrolytes typically have either high conductivity with poor mechanical properties or good mechanical properties with low conductivity.
• PEO-based electrolytes have a high degree of crystallinity unfavorably affecting its ionic conduction.
• PAN-based electrolytes undergo solvent exudation upon long storage and solvent will ooze to the surface of the polymer membrane decreasing the ionic conductivity dramatically.
• PMMA-based electrolytes have a high ionic conductivity but it is difficult to form a polymer membrane with stable dimensions and good physical properties.
• solid polymer electrolytes there are many potential advantages in the use of solid polymer electrolytes, for example, adjustable physical properties such as flexibility, rigidity, processibility, softness, hardness, porosity, tackiness etc, low toxicity, minimal fire hazard, light weight, high energy density, lower manufacturing costs, improved performance, etc.
• adjustable physical properties such as flexibility, rigidity, processibility, softness, hardness, porosity, tackiness etc, low toxicity, minimal fire hazard, light weight, high energy density, lower manufacturing costs, improved performance, etc.
• room temperature conductivity of conventional solid conductive polymer electrolytes is 1 ⁇ 10 ⁇ 6 s/cm or lower which is insufficient for many applications.
• polyanhydride can react with a mono- and/or poly-oxyalkleneamine at ambient temperature to form a grafted and/or crosslinked oxyalkyleneamide polymer, e.g., an oxyalkylene amic acid containing polymer.
• the polyanhydride can be a homopolymer or copolymer.
• each of the anhydride moieties comprised in the backbone are the same, e.g., maleic anhydride, but more than one type of anhydride moiety may be present.
• polymer is a general term which encompasses homopolymers and copolymers. When the phrase “polymer or copolymer” is used, it is used to reinforce the concept that either homopolymers or copolymers may be encountered in the practice of this invention. Typically, however, the polymers are anhydride copolymers.
• the graft and/or crosslink reaction can be run at room temperature at low concentration to form the crosslinked or grafted amic acid containing polymer as a gel which is readily converted to a solid membrane by, e.g., solution casting followed by solvent evaporation and completion of the crosslinking or grafting reaction.
• the graft and/or crosslink reaction can also be carried out in the presence of electrolyte dissolved in organic solvent (organic electrolyte) to form a gel or solid polymer electrolyte with good ion conductivity.
• organic electrolyte organic solvent
• the reaction of polyanhydride and polyoxyalkyleneamine proceeds in the presence of a lithium salt at room temperature to form solid polymer electrolyte membranes. Clear rubbery insoluble membranes containing high content of oxyalkylene ether with good ion conductivity are obtained.
• the oxyalkyleneamide polymer can also be further treated with heat to transform some or all of the aminic amide moieties into imides for improved mechanical properties.
• the oxyalkylene amic acid groups of the polymer can also be neutralized with a Li base to form a single ion conductive polymer with fixed anionic carboxylate groups and oxyalkylene ether segments for enhanced ion conductivity and improved cation transference number.
• the reaction of polyanhydride and mono-oxy or polyoxyalkyleneamine also proceeds at room temperature in presence of lithium base.
• the added lithium base neutralizes the formed amic acid providing fixed anion groups in the polymer for enhanced cation transportation.
• a method is provided for preparing a polymer electrolyte containing a high content of amorphous oxyalkylene ether and fixed anion group having the advantages of both branched polyoxyalkylene and single ion conductive polymer.
• the grafted or crosslinked polymer readily forms a molded solid membrane and is suitable for use as solid polymer electrolyte in various applications such as batteries, solar cell and electrochromic devices.
• the present invention provides a grafted or crosslinked ion conducting polymer comprising in the backbone of the polymer one or more amic acid or maleimide moieties selected from
• Alkyl is straight or branched chain of the specified number of carbon atoms, for example, methyl, ethyl, iso-propyl, n-propyl, n-butyl, sec-butyl, tert-butyl, n-hexyl, n-octyl, tert-octyl, 2-ethylhexyl, n-nonyl, n-decyl, n-undecyl, n-dodecyl.
• Alkyl carbonyl or alkanoyl is a straight or branched chain of the specified number of carbon atoms which has a carbonyl at the point of attachment.
• Alkylene is a chain, which may be linear or branched, of the specified number of carbon atoms substituted at each terminus, for example, methylene, ethylene, propylene, butylene, pentylene, hexylene, octylene, nonylene, decylene, dodecylene, or one of the preceding substituted by one or more C 1-12 alkyl groups, for example, methylmethylene, dimethylmethylene, ethylmethylene, diethylmethylene, propylmethylene, pentylmethylene, heptylmethylene, nonylmethylene, undecylmethylene, methylethylene, propylethylene, butylethylene, pentylethylene, hexylethylene, decylethylene, 1,1-dimethylethylene, 1,2-dimethylethylene, 1,1-diethylethylene, 1,2-diethylethylene, 1-methyl-1-ethylethylene, 1-methyl-2-propylethylene, methylpropy
• alkylene groups represented by A, A′ and A′′ are independently of each other ethylene or alkyl substituted ethylene such as methylethylene.
• One embodiment of the invention is therefore a grafted or crosslinked ion conducting polymer comprising in the backbone of the polymer one or more amic acid or maleimide moieties selected from
• each R independently of the others is H or C 1-12 alkyl, for example, each R independently of the others is H or methyl, and the other variables are as described above.
• G is H, C 1-12 alkyl or a metal cation selected from Li, Na, K, Mg and Ca, for example, the metal is Li, E is H; each R independently of the others is H or C 1-12 alkyl, for example, each R independently of the others is H or methyl; R′ is H or methyl and R′′ is H or a group
• each E′ is H or one E′ is H and the other is a carbonyl linking group which forms a crosslink as described above, or the two E′ groups together form a maleimide group to form a crosslink as described above.
• the polymer contains in the backbone aminic acid or maleimide moieties selected from
• G is H, C 1-12 alkyl, metal cation or amino cation, for example, G is H or Li; each R is independently C 1-12 alkyl, for example methyl; R′ is H or C 1-12 alkyl, for example methyl; R′′ is H, C 1-12 alkyl, C 1-12 alkylcarbonyl, phenyl, phenyl substituted by 1 or more C 1-12 alkyl, benzyl, phenethyl, benzyl or phenethyl substituted by 1 or more C 1-12 alkyl, or a group
• each E′ is independently H, C 1-12 alkyl, or C 1-12 alkylcarbonyl.
• the polymers of the invention are conveniently prepared by reacting a polymer containing anhydride repeating units in its backbone, for example, a maleic anhydride copolymer, many of which are commercially available, with at least one amine substituted by an alkyleneoxy or polyalkyleneoxy chain or with a diamine wherein the amino groups are linked by an alkyleneoxy or polyalkyleneoxy chain.
• a polymer containing anhydride repeating units in its backbone for example, a maleic anhydride copolymer, many of which are commercially available
• at least one amine substituted by an alkyleneoxy or polyalkyleneoxy chain or with a diamine wherein the amino groups are linked by an alkyleneoxy or polyalkyleneoxy chain Typically, polyalkyleneoxy amines or diamines are used.
• Any number of the anhydride groups of the anhydride containing polymer may be reacted depending on reaction conditions and stoichiometry, for example, 1-99%, for example 10-99%,
• the invention therefore provides a method for the preparation of grafted or crosslinked ion conducting polymers, and the polymers thus prepared, which method comprises reacting a polyanhydride polymer, for example, a maleic anhydride copolymer, with at least one amine of the formula
• alkylene groups represented by A, A′ and A′′ are independently of each other ethylene or alkyl substituted ethylene such as methylethylene as in the formula
• each R independently of the others is H or C 1-12 alkyl, for example, each R independently of the others is H or methyl, and the other variables are as described above.
• an anhydride containing polymer for example, a maleic anhydride copolymer
• each R is independently C 1-12 alkyl, for example methyl
• R′ is H or C 1-12 alkyl, for example methyl
• R′′ is H, C 1-12 alkyl, C 1-12 alkylcarbonyl, phenyl, phenyl substituted by 1 or more C 1-12 alkyl, benzyl, phenethyl, benzyl or phenethyl substituted by 1 or more C 1-12 alkyl, or a group
• each E′ is independently H, C 1-12 alkyl, or C 1-12 alkylcarbonyl.
• Poly-oxyalkylene amine compounds useful in the invention include those prepared by reacting a polyol initiator with propylene oxide and/or ethylene oxide followed by amination of the terminal hydroxyl groups, for example, glycerol tris[poly(propylene glycol), amine terminated] ether and trimethylolpropane (TMP) tris[poly(propylene glycol), amine terminated] ether, and 2,2-bis(hydroxymethyl)-1-butanol tris[poly(propylene glycol), amine terminated] ether.
• TMP trimethylolpropane
• Suitable oxyalkyleneamine compounds include commercial products sold by HUNTSMAN under trade name of JEFFAMINES, for example, JEFFAMINE XTJ 502, XTJ505, XTJ 509, and D2000.
• Polyanhydride polymers and copolymers useful in the present invention are polymers and copolymers which contain as a repeating unit a cyclic anhydride, such as copolymers comprising maleic anhydride as a monomer unit, for example, maleic anhydride polymers and maleic anhydride copolymers with an ethylenically unsaturated monomer such styrene, olefins, and (meth)acrylic acid esters and amides.
• polyanhydrides examples include poly(styrene-alt-maleic anhydride) poly(methyl vinyl ether-alt-maleic anhydride), poly(ethyylene-g-maleic anhydride), poly(isobutylene-alt-maleic anhydride), polyisoprene-g-maleic anhydride, poly(maleic anhydride-alt-1-octadecene), poly(ethylene-co-ethyl acrylate-co-maleic anhydride), polyethylene-graft-maleic anhydride .
• the polyanhydride is a copolymer of maleic anhydride and styrene (PSMAn).
• PSMAn may contain alkyl ester groups corresponding to an ester produced from a reaction of an anhydride group with an alcohol.
• Preferred partially esterified PSMAn is one containing methyl ester groups with less than 50% of total anhydride groups being esterified.
• styrene repeating units into the polyanhydride copolymers facilitates formation of amorphous regions of the polyether segments in the grafted or crosslinked polymer, especially in the presence of high concentration of ion conductive salt.
• the grafted or crosslinked ion conducting polymer of the invention is a poly(styrene-co-PEO maleicamic acid) obtained by reacting PSMAn with an oxyalkyleneamine, preferably a polyfunctional oxyalkyleneamine, such as polyoxyethylene (PEO) diamine.
• the lithium salt of the poly(styrene-co-PEO maleicamic acid) is readily obtained by neutralization with a lithium base such as lithium hydroxide or lithium methoxide, and conversion to poly(styrene-co-PEO maleic imide) can be effected by heating in vacuum.
• polystyrene-co-PEO maleicamic acid polystyrene-co-PEO maleicamic acid
• any of these processes or any combination of these processes may contain a certain amount of aminic acid moieties, acid salts and/or imides based on partial conversion to salt or imide.
• Solid polymer electrolyte membranes can be prepared by performing the grafting or crosslinking reaction in the presence of a lithium salt.
• Gel polymer electrolyte membranes are also prepared by post soaking the preformed poly(styrene-co-PEO maleic) polymers with a liquid electrolyte.
• Solid polymer electrolyte membranes can be prepared by dissolving the oxyalkyleneamide or oxyalkyleneimide product in a suitable solvent and/or a liquid electrolyte solution and casting the polymer solution on substrate.
• Crosslinked polymers are similarly prepared by reacting PSMAn with an oxyalkylene diamine, or an oxyalkylene poly-amine with more than one amine group per molecule.
• insoluble membranes can be formed by carrying out the reaction in a suitable solvent and casting the reacting solution on a substrate or in a container.
• Solid polymer electrolyte membranes or films can be obtained by allowing complete evaporation of solvent at ambient temperature and/or at elevated temperature. Gel polymer electrolyte membranes can be obtained without drying or by partial drying to allow partial solvent evaporation. Solvent or plasticizer content of a gel polymer electrolyte can be easily controlled by preparing the initial reaction solution with desired amount of solvent or by allowing partial evaporation solvent. Solvent mixtures containing volatile and non-volatile solvent (or plasticizer) can be used to prepare gel polymer electrolytes containing desirable amount of solvent or plasticizer content to balance mechanical properties and ion conductivity.
• the present invention therefore provides a simple synthesis and easy process for the preparation of membranes with good conductivity and mechanical properties. Clear rubbery insoluble membranes with high oxyalkylene ether content are obtained which are potentially inexpensive to manufacture.
• the method is versatile and membranes with different mechanical and electrical properties can be made by changing the composition and proportion of the amine/polyanhydride crosslink system.
• the presently provided polymer electrolytes contain a high content of amorphous oxyalkylene ether and fixed anion group and possess the advantages of both branched polyoxyalkylene and single ion conductive polymers.
• the present solid polymer electrolyte membranes without solvent or plasticizer can give high conductivity at room temperature (>10 ⁇ 6 S/cm).
• Polymer electrolyte gel membranes of the present invention can provide high room temperature conductivity comparable to that of liquid electrolytes (>10 ⁇ 4 S/cm).
• the covalently crosslinked solid electrolyte and gel electrolyte membranes also have excellent mechanical properties and solvent resistance.
• the solid polymer electrolyte or gel electrolyte may include electrolyte salts, including the well-known lithium salts, alkali metal salts, etc.
• electrolyte salts including the well-known lithium salts, alkali metal salts, etc.
• salts such as lithium bis trifluoromethanesulfonate, lithium perchlorate, lithium tetrafluoroborate, etc can be used individually or in mixtures.
• the solid polymer electrolyte may include additional known ion conductive polymers along with the ion conductive polymer of the present invention.
• a solid polymer electrolyte constructed as above comprising the present ion conductive polymer can be employed as an electrolyte material in, for example, a battery.
• the battery may be applied to either a primary battery or a secondary battery, either of which are well known in the art.
• one embodiment of the present invention provides a room temperature crosslinkable polymer system, and a polymer derived therefrom, that can be used as a solid polymer electrolyte for ion conducting.
• Another embodiment of the present invention provides a solid polymer electrolyte having good conductivity and high cation transport number at room temperature.
• Other embodiments include a flexible solid electrolyte film or membrane to give good contact with an electrode, a crosslinkable polymer system that can be used as binder for making positive electrode (cathode) and negative electrode (anode) for lithium ion batteries.
• Another embodiment provides a crosslinked polymer in the form of solid gel containing liquid electrolyte that can be used as a gel polymer electrolyte with excellent ion conductivity in, for example, Li ion batteries.
• Another embodiment provides a crosslinked polymer matrix in the form of membranes which are non-soluble but swellable in an organic liquid electrolyte for use as a gel polymer electrolyte with stable dimensions and good physical properties.
• Another embodiment provides a versatile method to make clear rubbery insoluble membranes containing a high content of oxyalkylene ether.
• the membranes can be formed at room temperature and room temperature ion conductivity higher than conventional solid polymer electrolyte can be achieved.
• Li salts however offer advantages in solid polymer electrolyte membranes as related in other portions of the specification.
• Inorganic or organic metal salts can be used, but organic metal salts offer advantages in solubility of solvents commonly employed in the above processes.
• the reaction of an anhydride containing polymer and oxyalkyleneamine can be carried out in solvent without or with an electrolyte or lithium salt.
• suitable solvents for dissolving polyanhydrides and oxyalkyleneamine include, but are not limited to, ethers such as tetrahydrofuran (THF); ketones such as acetone and methyl ethyl ketone; nitriles such as acetonitrile, propionitrile and valeronitrile; N-alkylamides such as N-methylpyrrolidinone; N-alkylimide such as N-methyl succinimide; carbonates such as ethylene carbonate, propylene carbonate and dimethyl carbonate; and mixtures of the solvents.
• ethers such as tetrahydrofuran (THF); ketones such as acetone and methyl ethyl ketone; nitriles such as acetonitrile, propionitrile and valeronitrile; N-alky
• lithium salts include lithium perchlorate, lithium trifluoromethane sulfonate, lithium hexafluorophosphate, lithium hexafluoroarsenate, lithium tetrafluoroborate, lithium bromide, lithium trifloromethanesulfonimide, lithium iodide and mixtures of the lithium salts.
• Ion conductive polymer electrolyte membranes or films in many cases can be conveniently prepared by solution casting, spin coating or any suitable coating method directly from the reaction solution.
• the obtained membranes can be further treated with heat at elevated temperature from 60 to 250° C., preferably, 100 to 180° C. to convert to succinimide containing polymers.
• Soluble oxyalkyleneamides and polyoxyalkyleneimides can be prepared in solution or solid product forms using a mono-functional oxyalkyleneamine.
• Ion conductive polymer electrolyte membranes and films can then be prepared by dissolving the polymer in a liquid electrolyte and solution casting or coating the solution onto the substrate.
• Table 1 lists three commercially available maleic anhydride/styrene copolymers (PSMAn) with different molecular weight (MW), methyl ester content, Tg and ratio of styrene to maleic anhydride (St:MAN ratio).
• Table 2 lists three commercially available JEFFAMINE polyoxyalkyleneamines with similar molecular weight (2000) but different functionality.
• JEFFAMINE XTJ502 (C11) and D2000 (C12) are di-functional amine crosslinkers containing mainly polyoxyethylene (PEO) and polyoxypropylene (PPO) segments respectively;
• XTJ507 (C13) is a mono-functional amine PEO.
• Tetrahydrofuran (THF) solutions of the copolymers and polyoxyalkyleneamines are readily available by simply dissolving the desired amount of copolymer or polyoxyalkyleneamines in an appropriate amount of THF.
• Table 3 lists commercially available lithium salts used to prepare polymer electrolytes with the PEO/PPO containing polymer.
• Lithium Salts FW, Formula g/mole Purities
• G LiTFSI Lithium LiN(CF 3 SO 2 ) 2 287.08 99.95% bis(trifluoromethane- sulfonyl)imide
• solid polymer electrolyte membranes or gel polymer electrolyte membranes are sandwiched between two symmetrical electrodes of the same metal (brass or stainless steel).
• the electric conductivity is determined by AC impedance measurement using a SOLARTRON 1252A frequency response analyzer (FRA) in combination with a SOLARTRON 1287A electrochemical interface (ECI).
• FFA frequency response analyzer
• ECI electrochemical interface
• Complex impedance spectra is obtained with a frequency range from 0.1 to 300 kHz with an AC voltage amplitude of 20 mV.
• Bulk resistance is obtained from a semicircular arc of the complex impedance spectra to calculate the ion conductivity of the analyzed polymer electrolyte film with known area and thickness.
• Solid membranes comprising the crosslinked polymers of the invention are prepared by mixing 2.9 grams of a 12% by weight solution of PSMAn copolymer A7 in tetrahydrofuran (THF) and 7.5 grams of a 40% by weight solution of polyethyleneoxide diamine C11 in THF to form a clear reaction solution of low viscosity and about three minutes after preparation of the reaction solution casting approximately 1.5 grams of the reaction solution into each of two glass Petri dishes and an aluminum weighing dish.
• the cast solutions are allowed to cure and evaporate out solvent at room temperature. After about 15 minutes the cast films were dry to touch and insoluble in THF. Cure, as determined by no further change in appearance, mechanical properties and solvent swelling, is considered complete after standing overnight at room temperature producing clear, rubbery, dry films which are peeled off the casting dishes to yield solid membranes.
• reaction solution which is not cast increases in viscosity and starts to gel in about 150 minutes (pot life) at room temperature.
• a clear solid gel containing crosslinked polyoxyethyleneamide and THF solvent is obtained over night.
• the crosslinked polyoxyethyleneamide in the solid membranes and the gel obtained in this example contain about 90% by weight of ethylene oxide (EO)/propylene oxide (PO) units available for ion complexing and conducting.
• EO ethylene oxide
• PO propylene oxide
• solid membranes comprising crosslinked polymers of differing compositions are prepared by mixing different amounts of a 20% weight solution of PSMAn copolymer A7 in THF and a 40% by weight solution of polyethyleneoxide diamine C11 in THF solution as shown in the table to form a clear solution and casting, after about 5 minutes into each of three separate Petri dishes.
• the cured dry films are obtained after standing overnight at room temperature and their properties are summarized in Table Ex2 along with their compositions.
• Solubility of the polymers is tested by putting a small piece of cured film in different testing solvent: H2O, THF, acetonitrile (CH3CN), chloroform, methanol (MeOH), and isopropanol IPA. Formation of maleicamic acid by reaction of anhydride with primary amine is confirmed by FTIR spectra of the water extracted membrane and non-extracted membrane.
• membranes of crosslinked EO/PO containing copolymers are prepared by mixing solutions of different PSMAn copolymers with solutions of different polyoxyalkyleneamines as shown in Table Ex 3 to produce a mixture containing a 1:1 ratio of amine to anhydride ratio in a solution containing approximately 20% solids.
• Thin free-standing films (membranes) with predetermined thickness are obtained by casting the appropriate amount of this reaction solution in Teflon Petri dishes of 28 cm 2 area.
• Crosslinked polymer electrolyte membranes with fixed anionic carboxylate groups and movable Li + ions are obtained in Examples 3F, 3G and 3H by including appropriate amount of lithium methoxide (LiOMe) to achieve desired degree of neutralization (DN) of the amic acid.
• LiOMe lithium methoxide
• Crosslinked polymer electrolyte membranes of polyethyleneoxide imide are obtained from Example 3C by heating the membrane of Example 3B at 140° C. in a vacuum oven and from Example 3H by heating the membrane of Example F at 140° C. in a vacuum oven.
• the membranes after the heat treatment turn color to brown or yellow and appear to have improved mechanic properties.
• Example 4A provides membranes with 50 wt % of EO/PO ether content with an amine/anhydride ratio of 0.1 from a low MW (1600) PSMAn (A7).
• Example 4B provides membranes with a high EO/PO content 83 wt % and a high amine/anhydride ratio (0.5) from a high MW (350,000) partially methyl esterified PSMAn (A7′).
• Membranes prepared with monofunctional EO/PO amine C13 are transparent but have much poorer mechanical properties than those crosslinked with diamine EO/PO C11 and C12, and require more time to form coherent films with a gel time of about 45 hours even at relatively high polymer concentration. Films with better mechanical properties and solvent resistance are obtained from the high MW (350,000) partially methyl esterified PSMAn (A7′) than from PSMAn (A7.
• crosslinked polymer electrolyte membranes containing Li salt are prepared by mixing 8.4 grams of a 20 wt % solution of PSMAn A7 in tetrahydrofuran (THF), 20.8 grams of a 40 wt % solution of polyethyleneoxide diamine C11 in THF, and 0.5 g of lithium perchlorate (LiClO 4 ) (pre-dissolved in THF to give a 10% solution) to form a clear reaction solution and about two minutes after preparation of the reaction solution casting portions of the reaction solution into glass Petri dishes.
• THF tetrahydrofuran
• LiClO 4 lithium perchlorate
• Reaction solution remaining in the reaction vessel gels in less than 8 hour at room temperature indicating that crosslinking reaction of the polymers can proceed in presence of the Li salt.
• the cast solutions in Petri dishes are allowed to cure and evaporate out solvent at room temperature for seven days to provide transparent and rubbery insoluble membranes of solid polymer electrolyte containing 5 wt % of LiClO 4 .
• Example 6A Following the procedure of Example 6A using different Li salts and concentrations, polymer electrolyte membranes containing 10 wt % of lithium trifluoromethanesulfonate (CF 3 SO 3 Li) (based on total polymer weight) Example 6B, and polymer electrolyte membranes containing 10 wt % of lithium bromide (LiBr) Example 6C, are prepared.
• CF 3 SO 3 Li lithium trifluoromethanesulfonate
• LiBr lithium bromide
• crosslinked polymer electrolyte membranes containing Li salts are prepared from solutions in methylethylketone (MEK) by dissolving 0.5 g of LiClO 4 in MEK and then adding with mixing 10.4 grams of a 40% by weight solution of polyethyleneoxide diamine C11 in MEK followed by addition of 4.2 grams of a 20% by weight solution of PSMAn copolymer A7 in MEK. After 5 minutes of mixing portions of the reaction solution are cast into glass Petri dishes and dried overnight under vacuum to provide solid polymer electrolyte membranes containing no solvent.
• MEK methylethylketone
• Example 7B The procedure of Example 7B is repeated except that 0.45 grams of a 10% lithium methoxide (LiOCH 3 ) solution in methanol is added to the MEK solution of LiBF 4 to provide solid polymer electrolyte membranes with multiple lithium salts.
• LiOCH 3 lithium methoxide
• a polymer electrolyte gel of crosslinked polymer is prepared by dissolving 0.83 g of LiClO 4 in MEK in a beaker and then adding with mixing 10.4 grams of a 40% by weight solution of polyethyleneoxide diamine C11 in MEK followed by addition of 4.2 grams of a 20% by weight solution of PSMAn copolymer A7 in MEK.
• the reaction solution is not cast but allowed to gel in the beaker to provide after about 3 hours a semi-solid elastic gel containing about 30% polymer and about 5% LiClO 4 (16.6% based on polymer weight).
• Example 8A The procedure of Example 8A is repeated except that 1.5 g instead of 0.83 g of LiClO 4 is used to provide a solution that gels in about 65 hours to give a semi-solid elastic gel containing about 20% polymer and about 6% LiClO 4 (30% based on polymer weight).
• solid polymer electrolyte membranes of poly(ethylene oxide) (PEO) containing various amounts of lithium salts are prepared by adding to 37.4 grams of a 6.7 wt % solution of a PEO polymer (MW ⁇ 900,000 g/mole) in acetonitrile either 0.25 g of LiClO 4 pre-dissolved in acetonitrile, 0.5 g of LiClO 4 pre-dissolved in acetonitrile or 0.37 g of CF 3 SO 3 Li pre-dissolved in acetonitrile.
• PEO poly(ethylene oxide)
• the resulting solutions are cast into Petri dishes as above and allowed to stand overnight at room temperature to provide turbid white membranes containing 10% LiClO 4 based on PEO weight, 20% LiClO 4 based on PEO weight and 15% CF 3 SO 3 Li based on PEO weight respectively.
• the solid polymer electrolyte of the present invention as shown in Examples 6-8 provide room temperature conductivity above 10 ⁇ 6 S/cm, more than 10 times higher than that of conventional solid PEO polymer electrolyte.

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