WO2013146168A1 - 電極材料 - Google Patents
電極材料 Download PDFInfo
- Publication number
- WO2013146168A1 WO2013146168A1 PCT/JP2013/056297 JP2013056297W WO2013146168A1 WO 2013146168 A1 WO2013146168 A1 WO 2013146168A1 JP 2013056297 W JP2013056297 W JP 2013056297W WO 2013146168 A1 WO2013146168 A1 WO 2013146168A1
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- WIPO (PCT)
- Prior art keywords
- electrode
- carbonaceous film
- electrode active
- active material
- mass
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- 239000007772 electrode material Substances 0.000 title claims abstract description 220
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- 229910052799 carbon Inorganic materials 0.000 claims description 64
- 150000002894 organic compounds Chemical class 0.000 claims description 31
- 239000011230 binding agent Substances 0.000 claims description 16
- 229910052744 lithium Inorganic materials 0.000 claims description 16
- 239000012298 atmosphere Substances 0.000 claims description 15
- WHXSMMKQMYFTQS-UHFFFAOYSA-N Lithium Chemical compound [Li] WHXSMMKQMYFTQS-UHFFFAOYSA-N 0.000 claims description 14
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- 239000002243 precursor Substances 0.000 claims description 12
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- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 7
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- 229910052782 aluminium Inorganic materials 0.000 claims description 7
- 229910052759 nickel Inorganic materials 0.000 claims description 7
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- 230000001590 oxidative effect Effects 0.000 claims description 6
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- 229910052719 titanium Inorganic materials 0.000 claims description 6
- 229910052725 zinc Inorganic materials 0.000 claims description 6
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 5
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- 229910052733 gallium Inorganic materials 0.000 claims description 4
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- 229910052738 indium Inorganic materials 0.000 claims description 4
- 229910052706 scandium Inorganic materials 0.000 claims description 4
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- QHGJSLXSVXVKHZ-UHFFFAOYSA-N dilithium;dioxido(dioxo)manganese Chemical compound [Li+].[Li+].[O-][Mn]([O-])(=O)=O QHGJSLXSVXVKHZ-UHFFFAOYSA-N 0.000 claims description 3
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- LUEWUZLMQUOBSB-FSKGGBMCSA-N (2s,3s,4s,5s,6r)-2-[(2r,3s,4r,5r,6s)-6-[(2r,3s,4r,5s,6s)-4,5-dihydroxy-2-(hydroxymethyl)-6-[(2r,4r,5s,6r)-4,5,6-trihydroxy-2-(hydroxymethyl)oxan-3-yl]oxyoxan-3-yl]oxy-4,5-dihydroxy-2-(hydroxymethyl)oxan-3-yl]oxy-6-(hydroxymethyl)oxane-3,4,5-triol Chemical compound O[C@H]1[C@@H](O)[C@H](O)[C@@H](CO)O[C@H]1O[C@@H]1[C@@H](CO)O[C@@H](O[C@@H]2[C@H](O[C@@H](OC3[C@H](O[C@@H](O)[C@@H](O)[C@H]3O)CO)[C@@H](O)[C@H]2O)CO)[C@H](O)[C@H]1O LUEWUZLMQUOBSB-FSKGGBMCSA-N 0.000 claims description 2
- OWEGMIWEEQEYGQ-UHFFFAOYSA-N 100676-05-9 Natural products OC1C(O)C(O)C(CO)OC1OCC1C(O)C(O)C(O)C(OC2C(OC(O)C(O)C2O)CO)O1 OWEGMIWEEQEYGQ-UHFFFAOYSA-N 0.000 claims description 2
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- WQZGKKKJIJFFOK-QTVWNMPRSA-N D-mannopyranose Chemical compound OC[C@H]1OC(O)[C@@H](O)[C@@H](O)[C@@H]1O WQZGKKKJIJFFOK-QTVWNMPRSA-N 0.000 claims description 2
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- GUBGYTABKSRVRQ-PICCSMPSSA-N Maltose Natural products O[C@@H]1[C@@H](O)[C@H](O)[C@@H](CO)O[C@@H]1O[C@@H]1[C@@H](CO)OC(O)[C@H](O)[C@H]1O GUBGYTABKSRVRQ-PICCSMPSSA-N 0.000 claims description 2
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- CZMRCDWAGMRECN-UGDNZRGBSA-N Sucrose Chemical compound O[C@H]1[C@H](O)[C@@H](CO)O[C@@]1(CO)O[C@@H]1[C@H](O)[C@@H](O)[C@H](O)[C@@H](CO)O1 CZMRCDWAGMRECN-UGDNZRGBSA-N 0.000 claims description 2
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- 150000004781 alginic acids Chemical class 0.000 claims description 2
- WQZGKKKJIJFFOK-PHYPRBDBSA-N alpha-D-galactose Chemical compound OC[C@H]1O[C@H](O)[C@H](O)[C@@H](O)[C@H]1O WQZGKKKJIJFFOK-PHYPRBDBSA-N 0.000 claims description 2
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- DLGJWSVWTWEWBJ-HGGSSLSASA-N chondroitin Chemical compound CC(O)=N[C@@H]1[C@H](O)O[C@H](CO)[C@H](O)[C@@H]1OC1[C@H](O)[C@H](O)C=C(C(O)=O)O1 DLGJWSVWTWEWBJ-HGGSSLSASA-N 0.000 claims description 2
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- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 1
- DKPFZGUDAPQIHT-UHFFFAOYSA-N Butyl acetate Natural products CCCCOC(C)=O DKPFZGUDAPQIHT-UHFFFAOYSA-N 0.000 description 1
- OIFBSDVPJOWBCH-UHFFFAOYSA-N Diethyl carbonate Chemical compound CCOC(=O)OCC OIFBSDVPJOWBCH-UHFFFAOYSA-N 0.000 description 1
- KMTRUDSVKNLOMY-UHFFFAOYSA-N Ethylene carbonate Chemical compound O=C1OCCO1 KMTRUDSVKNLOMY-UHFFFAOYSA-N 0.000 description 1
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 229910021577 Iron(II) chloride Inorganic materials 0.000 description 1
- 229910000733 Li alloy Inorganic materials 0.000 description 1
- 229910010707 LiFePO 4 Inorganic materials 0.000 description 1
- 229910013870 LiPF 6 Inorganic materials 0.000 description 1
- 239000011149 active material Substances 0.000 description 1
- 150000001298 alcohols Chemical class 0.000 description 1
- 150000001336 alkenes Chemical class 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 150000001408 amides Chemical class 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 125000003118 aryl group Chemical group 0.000 description 1
- 230000004888 barrier function Effects 0.000 description 1
- 239000011324 bead Substances 0.000 description 1
- OJIJEKBXJYRIBZ-UHFFFAOYSA-N cadmium nickel Chemical compound [Ni].[Cd] OJIJEKBXJYRIBZ-UHFFFAOYSA-N 0.000 description 1
- 239000006229 carbon black Substances 0.000 description 1
- 238000003763 carbonization Methods 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011651 chromium Substances 0.000 description 1
- 238000003776 cleavage reaction Methods 0.000 description 1
- CKFRRHLHAJZIIN-UHFFFAOYSA-N cobalt lithium Chemical compound [Li].[Co] CKFRRHLHAJZIIN-UHFFFAOYSA-N 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000004807 desolvation Methods 0.000 description 1
- MNNHAPBLZZVQHP-UHFFFAOYSA-N diammonium hydrogen phosphate Chemical compound [NH4+].[NH4+].OP([O-])([O-])=O MNNHAPBLZZVQHP-UHFFFAOYSA-N 0.000 description 1
- 229910000388 diammonium phosphate Inorganic materials 0.000 description 1
- 235000019838 diammonium phosphate Nutrition 0.000 description 1
- XXJWXESWEXIICW-UHFFFAOYSA-N diethylene glycol monoethyl ether Chemical compound CCOCCOCCO XXJWXESWEXIICW-UHFFFAOYSA-N 0.000 description 1
- 229940075557 diethylene glycol monoethyl ether Drugs 0.000 description 1
- NBIIXXVUZAFLBC-UHFFFAOYSA-M dihydrogenphosphate Chemical compound OP(O)([O-])=O NBIIXXVUZAFLBC-UHFFFAOYSA-M 0.000 description 1
- 239000002270 dispersing agent Substances 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 150000002148 esters Chemical class 0.000 description 1
- 150000002170 ethers Chemical class 0.000 description 1
- 229940116333 ethyl lactate Drugs 0.000 description 1
- 229920001973 fluoroelastomer Polymers 0.000 description 1
- 150000002334 glycols Chemical class 0.000 description 1
- FUZZWVXGSFPDMH-UHFFFAOYSA-M hexanoate Chemical compound CCCCCC([O-])=O FUZZWVXGSFPDMH-UHFFFAOYSA-M 0.000 description 1
- 150000002431 hydrogen Chemical class 0.000 description 1
- 238000001027 hydrothermal synthesis Methods 0.000 description 1
- 238000003780 insertion Methods 0.000 description 1
- 230000037431 insertion Effects 0.000 description 1
- 150000002505 iron Chemical class 0.000 description 1
- NMCUIPGRVMDVDB-UHFFFAOYSA-L iron dichloride Chemical compound Cl[Fe]Cl NMCUIPGRVMDVDB-UHFFFAOYSA-L 0.000 description 1
- 159000000014 iron salts Chemical class 0.000 description 1
- LNOZJRCUHSPCDZ-UHFFFAOYSA-L iron(ii) acetate Chemical compound [Fe+2].CC([O-])=O.CC([O-])=O LNOZJRCUHSPCDZ-UHFFFAOYSA-L 0.000 description 1
- 229960001375 lactose Drugs 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 239000001989 lithium alloy Substances 0.000 description 1
- KWGKDLIKAYFUFQ-UHFFFAOYSA-M lithium chloride Chemical compound [Li+].[Cl-] KWGKDLIKAYFUFQ-UHFFFAOYSA-M 0.000 description 1
- GELKBWJHTRAYNV-UHFFFAOYSA-K lithium iron phosphate Chemical compound [Li+].[Fe+2].[O-]P([O-])([O-])=O GELKBWJHTRAYNV-UHFFFAOYSA-K 0.000 description 1
- 229910002102 lithium manganese oxide Inorganic materials 0.000 description 1
- RSNHXDVSISOZOB-UHFFFAOYSA-N lithium nickel Chemical compound [Li].[Ni] RSNHXDVSISOZOB-UHFFFAOYSA-N 0.000 description 1
- VLXXBCXTUVRROQ-UHFFFAOYSA-N lithium;oxido-oxo-(oxomanganiooxy)manganese Chemical compound [Li+].[O-][Mn](=O)O[Mn]=O VLXXBCXTUVRROQ-UHFFFAOYSA-N 0.000 description 1
- 229910052987 metal hydride Inorganic materials 0.000 description 1
- 239000013081 microcrystal Substances 0.000 description 1
- YPEWWOUWRRQBAX-UHFFFAOYSA-N n,n-dimethyl-3-oxobutanamide Chemical compound CN(C)C(=O)CC(C)=O YPEWWOUWRRQBAX-UHFFFAOYSA-N 0.000 description 1
- JRZJOMJEPLMPRA-UHFFFAOYSA-N olefin Natural products CCCCCCCC=C JRZJOMJEPLMPRA-UHFFFAOYSA-N 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229960000292 pectin Drugs 0.000 description 1
- 150000003016 phosphoric acids Chemical class 0.000 description 1
- 238000012643 polycondensation polymerization Methods 0.000 description 1
- LLHKCFNBLRBOGN-UHFFFAOYSA-N propylene glycol methyl ether acetate Chemical compound COCC(C)OC(C)=O LLHKCFNBLRBOGN-UHFFFAOYSA-N 0.000 description 1
- 150000002910 rare earth metals Chemical class 0.000 description 1
- 230000007017 scission Effects 0.000 description 1
- 238000010532 solid phase synthesis reaction Methods 0.000 description 1
- 238000007614 solvation Methods 0.000 description 1
- 241000894007 species Species 0.000 description 1
- 229910052596 spinel Inorganic materials 0.000 description 1
- 239000011029 spinel Substances 0.000 description 1
- 229960004793 sucrose Drugs 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 239000010409 thin film Substances 0.000 description 1
- 239000012808 vapor phase Substances 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
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
- H01M4/362—Composites
- H01M4/366—Composites as layered products
-
- 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
- H01M4/36—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
- H01M4/583—Carbonaceous material, e.g. graphite-intercalation compounds or CFx
- H01M4/587—Carbonaceous material, e.g. graphite-intercalation compounds or CFx for inserting or intercalating light metals
-
- 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
- H01M4/62—Selection of inactive substances as ingredients for active masses, e.g. binders, fillers
- H01M4/621—Binders
- H01M4/622—Binders being polymers
-
- 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
- H01M4/62—Selection of inactive substances as ingredients for active masses, e.g. binders, fillers
- H01M4/624—Electric conductive fillers
- H01M4/625—Carbon or graphite
-
- 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
- H01M2004/026—Electrodes composed of, or comprising, active material characterised by the polarity
- H01M2004/028—Positive electrodes
-
- 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
-
- 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
-
- 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
Definitions
- the present invention relates to an electrode material.
- This application claims priority on March 30, 2012 based on Japanese Patent Application No. 2012-078860 filed in Japan, the contents of which are incorporated herein by reference.
- non-aqueous electrolyte secondary batteries such as lithium ion batteries have been proposed and put into practical use as batteries that are expected to be reduced in size, weight, and capacity.
- This lithium ion battery is composed of a positive electrode and a negative electrode having a property capable of reversibly inserting and removing lithium ions, and a non-aqueous electrolyte.
- a negative electrode material of a lithium ion battery a Li-containing metal oxide having a property capable of reversibly inserting and removing lithium ions, such as a carbon-based material or lithium titanate (Li 4 Ti 5 O 12 ), as a negative electrode active material are commonly used.
- a positive electrode material of a lithium ion battery as a positive electrode active material, a lithium-containing metal oxide, such as lithium iron phosphate (LiFePO 4 ), which has a property capable of reversibly inserting and removing lithium ions, a binder, and the like. Including electrode material mixtures are used. And the positive electrode of a lithium ion battery is formed by apply
- Such a lithium ion battery is lighter and smaller than a conventional secondary battery such as a lead battery, a nickel cadmium battery, and a nickel metal hydride battery, and has high energy. Therefore, it is used not only as a small power source used in portable electronic devices such as portable telephones and notebook personal computers, but also as a stationary emergency large power source.
- lithium ion batteries have also been studied as high-output power sources for plug-in hybrid vehicles, hybrid vehicles, and electric tools. Batteries used as these high-output power sources are required to have high-speed charge / discharge characteristics.
- an electrode material including an electrode active material for example, an electrode material including a lithium phosphate compound having a property capable of reversibly removing and inserting lithium ions has a problem that electron conductivity is low.
- the particle surface of the electrode active material was covered with an organic compound as a carbon source, and then the organic compound was carbonized to form a carbonaceous film on the surface of the electrode active material. That is, an electrode material in which carbon of this carbonaceous film is interposed as an electron conductive substance has been proposed (Patent Document 1).
- a carbonaceous film is formed on the surface of the electrode active material to provide electronic conductivity. It is desirable to increase it.
- this carbonaceous film becomes a barrier when lithium ions diffuse. That is, the thicker the carbonaceous film is, and the higher the crystallinity of the carbonaceous film is, the more lithium ion conductivity is impaired. As a result, the internal resistance of the battery is increased due to the carbonaceous film, and the voltage is remarkably decreased particularly when high-speed charging / discharging is performed.
- the present inventors have so far aggregated the electrode active material particles having a carbonaceous film formed on the surface for the purpose of reducing the unevenness of the carbonaceous film thickness of the electrode active material to obtain an average particle diameter.
- lithium phosphate compounds to high power sources has been limited to date.
- further improvements have been made so far, for example, addition of fibrous conductive carbon or layered oxide or spinel type positive electrode with excellent high-speed charge / discharge characteristics. It was necessary to mix materials. However, even when these are added, there still remains a problem that the conductivity of lithium ions is impaired.
- the present invention has been made to solve the above problems.
- an electrode active material having a carbonaceous film formed on the surface is used as an electrode material, not only electronic conductivity but also lithium ions can be controlled by controlling the density, crystallinity and film thickness of the carbonaceous film.
- An object of the present invention is to provide an electrode material capable of improving conductivity.
- the present inventors have determined that the volume density of the aggregate obtained by aggregating the electrode active material particles having a carbonaceous film formed on the surface is solid.
- the volume density is 50% by volume or more and 80% by volume or less, and the coverage of the carbonaceous film on the surface of the electrode active material particles is 80% or more, and the average film thickness of the carbonaceous film is 1.0 nm or more.
- the thickness is 7.0 nm or less, the lithium phosphate compound has improved electron conductivity without impairing lithium ion conductivity, and thus satisfies high-speed charge / discharge characteristics and lithium ion conductivity. As a result, the present invention has been completed.
- the electrode material of the present invention comprises an aggregate in which electrode active material particles having a carbonaceous film formed on the surface are aggregated,
- the volume density of the aggregate is 50% by volume or more and 80% by volume or less with respect to the volume density when the aggregate is solid.
- the coverage of the carbonaceous film on the surface of the electrode active material particles is 80% or more, and the average film thickness of the carbonaceous film is 1.0 nm or more and 7.0 nm or less.
- the mass of carbon in the carbonaceous film is 0.6% by mass or more and 2.0% by mass or less with respect to the mass of the electrode active material particles, and the electrode active in which the carbonaceous film is formed on the surface.
- the specific surface area of the substance particles is preferably 5 m 2 / g or more and 20 m 2 / g or less.
- the mass of the carbon component in the carbonaceous film is 50% by mass or more based on the total mass of the carbonaceous film, and the density required from the carbon component of the carbonaceous film is 0.3 g / cm 3 or more. And it is preferable that it is 1.5 g / cm 3 or less.
- the electrode active material particles lithium cobaltate, lithium nickelate, lithium manganate, lithium titanate and Li x A y D z PO 4 (where, A is Co, Mn, Ni, Fe, Cu, from the group of Cr
- D is selected from the group of Mg, Ca, S, Sr, Ba, Ti, Zn, B, Al, Ga, In, Si, Ge, Sc, Y, rare earth elements
- the main component is one type selected from the group of 1 type or 2 types or more, 0 ⁇ x ⁇ 2, 0 ⁇ y ⁇ 1.5, 0 ⁇ z ⁇ 1.5).
- the electrode material of the present invention is an aggregate obtained by aggregating electrode active material particles having a carbonaceous film formed on the surface, and the volume density when the aggregate is solid is 100% by volume.
- the volume density of the aggregate is 50% by volume or more and 80% by volume or less
- the coverage of the carbonaceous film on the surface of the electrode active material particles is 80% or more
- the average film thickness of the carbonaceous film is It was set to 1.0 nm or more and 7.0 nm or less. Due to this feature, the unevenness of the amount of the carbonaceous film formed on the surface of the electrode active material particles can be reduced, and the electron conductivity can be improved without impairing the lithium ion conductivity. Therefore, when this electrode active material is used for a lithium ion battery positive electrode, the internal resistance of the battery can be kept low, and as a result, high-speed charging / discharging can be performed without the risk of a significant voltage drop.
- the electrode material of the present invention can be applied to a high-output power source that requires high-speed charging / discharging.
- the volume density of the aggregate formed by aggregating the electrode active material particles having the carbonaceous film formed on the surface is 50% by volume or more and 80% by volume or less of the volume density when the aggregate is solid.
- the unevenness of the amount of the carbonaceous film formed on the surface of the electrode active material particles can be reduced, and hence the unevenness of the electronic conductivity of the electrode active material can be reduced.
- the reaction relating to the desorption / insertion of lithium ions can be performed uniformly on the entire surface of the electrode active material, Therefore, the internal resistance of the electrode can be reduced.
- the present invention relates to an electrode material.
- the present invention relates to an electrode material suitably used for a positive electrode material for a battery and further a positive electrode material for a lithium ion battery.
- the form for implementing the electrode material of this invention is demonstrated below. This embodiment is specifically described for better understanding of the gist of the invention, and does not limit the present invention unless otherwise specified. The number, amount, type, and ratio may be omitted or changed without departing from the scope of the invention, as long as there is no particular problem.
- the electrode material of this embodiment consists of an aggregate obtained by aggregating electrode active material particles having a carbonaceous film formed on the surface. That is, the electrode material includes one or more aggregates.
- the volume density of the aggregate is 50 volume% or more and 80 volume% or less of the volume density when the aggregate is solid, and the coverage of the carbonaceous film on the surface of the electrode active material particles is 80%.
- the average film thickness of the carbonaceous film is 1.0 nm or more and 7.0 nm or less.
- the carbonaceous film is a film formed by thermal decomposition of an organic compound, is located on the electrode active material, and is a film connecting the electrode active materials.
- the aggregate formed by aggregating the electrode active material particles having the carbonaceous film formed on the surface means that the electrode active material particles having the carbonaceous film formed on the surface are aggregated in a point contact state. It means to do. That is, the contact portion between the electrode active material particles has a neck shape with a small cross-sectional area, which means that the electrode active material particles are agglomerated in a state of being firmly connected. As described above, the contact portion between the electrode active material particles has a cervical shape with a small cross-sectional area, so that a channel-like (network-like) gap is three-dimensionally expanded inside the aggregate.
- the neck shape means that the cross section is narrower than the head (particle body).
- the volume density of the aggregate can be measured using a mercury porosimeter.
- the volume density of the aggregate is calculated from the mass of the entire electrode material constituted by the aggregate, the volume of the electrode active material particles, and the volume of the gaps of the particles constituting the aggregate excluding the gaps between the aggregates. Is the value to be In other words, the particle gap inside the aggregate obtained by excluding the volume of the electrode active material particles and the volume of the gap between the aggregates from the sum of the volumes as aggregates of the aggregates, and the aggregates It is the density of the aggregate computed from the mass of the whole electrode material comprised by this.
- the volume density of the aggregate As the volume density of the aggregate, the volume density (100 mass) when the volume density when the aggregate is solid is assumed to be 100 mass%, that is, when there is no void in the aggregate. %) Is preferably 50% by volume or more and 80% by volume or less, more preferably 55% by volume or more and 75% by volume or less, and still more preferably 60% by volume or more and 75% by volume or less.
- the solid aggregate means an aggregate having no voids, and the density of the solid aggregate is equal to the theoretical density of the electrode active material.
- the volume density of the aggregate to 50% by volume or more and 80% by volume or less, it is possible to adopt a compact that has a certain amount of pores (voids).
- This makes it possible to increase the strength of the entire aggregate while having voids.
- an electrode slurry is prepared by mixing an electrode active material with a binder, a conductive additive, and a solvent, the aggregate is less likely to collapse. .
- the increase in the viscosity of the electrode slurry is suppressed and the fluidity is maintained, so that the coating property is improved and the filling property of the electrode active material in the coating film of the electrode slurry is also improved. be able to.
- the volume density of the aggregate is outside the above range, for example, less than 50% by volume of the volume density when the aggregate is solid, there are too many void portions, and the fineness inside the aggregate of the electrode active material is small.
- the concentration of the aromatic carbon compound vapor in the pores may become too low.
- the aromatic carbon compound is an intermediate substance that is generated when the organic compound is carbonized.
- the aromatic carbon compound is generated by thermal decomposition of the organic compound, and then the aromatic carbon compound is heated. By condensation polymerization, a carbonaceous film is formed. If the vapor concentration becomes too low, the carbonaceous film at the center of the aggregate becomes thin and the internal resistance of the electrode active material becomes high.
- the volume density of the aggregate exceeds 80% by volume of the volume density when the aggregate is solid, the void portion becomes too small, that is, the density inside the aggregate becomes too high, and the aggregate density becomes too high. There is a possibility that the channel-like (network-like) pores inside the aggregate will be small. As a result, the tar-like substance generated during carbonization of the organic compound may be trapped inside the aggregate, which is not preferable.
- the electrode active material constituting the electrode active material particles can be arbitrarily selected.
- Lithium cobaltate, lithium nickelate, lithium manganate, lithium titanate and Li x A y D z PO 4 (where, A is one or selected Co, Mn, Ni, Fe, Cu, from the group of Cr Species or more, D is Mg, Ca, S, Sr, Ba, Ti, Zn, B, Al, Ga, In, Si, Ge, Sc, Y, one or more selected from the group of rare earth elements,
- the main component is preferably one selected from the group of 0 ⁇ x ⁇ 2, 0 ⁇ y ⁇ 1.5, 0 ⁇ z ⁇ 1.5.
- A is selected from Co, Mn, Ni, and Fe
- D is selected from Mg, Ca, Sr, Ba, Ti, Zn, and Al.
- the rare earth elements are 15 elements of La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu which are lanthanum series.
- the electrode active material particle of the present invention When the electrode active material particle of the present invention is used as an electrode material of a lithium ion battery, a reaction related to lithium ion desorption is uniformly performed on the entire surface of the electrode active material particle. For this reason, it is preferable that 80% or more, more preferably 85% or more, and still more preferably 90% or more of the surface of the electrode active material particles is covered with a carbonaceous film.
- the coverage of a carbonaceous film can be measured using a transmission electron microscope (TEM) and an energy dispersive X-ray spectrometer (EDX). Specifically, the carbonaceous film formed on the electrode active material particles was observed for 100 electrode active material particles using a transmission electron microscope (TEM) and an energy dispersive X-ray spectrometer (EDX).
- the ratio of the part which the carbonaceous film has covered among the surfaces of electrode active material particles is calculated, and it is set as a coverage.
- the coverage of the carbonaceous film is less than 80%, the coating effect of the carbonaceous film is insufficient, and when the lithium ion desorption reaction is performed on the surface of the electrode active material, the carbonaceous film is not formed. In this case, the reaction resistance related to lithium ion desorption is increased, and the voltage drop at the end of discharge may become remarkable.
- the upper limit of the coverage with the carbonaceous film on the surface of the electrode active material particles can be arbitrarily selected.
- the upper limit can be set to 100%, that is, the upper limit of the range can be set to 100% or less. If necessary, it can be selected from 98% or less, 96% or less, 93% or less, 90% or less, and the like.
- the mass of carbon in the carbonaceous film of the present invention can be selected as necessary. It is preferable that it is 0.6 mass% or more and 2.0 mass% or less with respect to the mass (100 mass%) of said electrode active material particle, More preferably, it is 0.8 mass% or more and 1.9 mass. % Or less, and more preferably 1.1% by mass or more and 1.7% by mass or less.
- the mass fraction of the carbon component of the carbonaceous coating is obtained by weighing the obtained electrode material, then immersing it in an acidic aqueous solution, separating only the carbonaceous coating that is the residue after dissolution, and then analyzing the carbon analyzer. Can be obtained by measuring the carbon fraction of the carbonaceous coating film.
- the reason why the mass of the carbon in the carbonaceous film is limited to the above range is that if the amount of carbon is less than 0.6% by mass, the discharge capacity at the high-speed charge / discharge rate is low when a battery is formed, and is sufficient. This is because it may be difficult to achieve a satisfactory charge / discharge rate performance.
- the carbon content exceeds 2.0 mass% the lithium ion migration resistance increases due to steric hindrance when lithium ions diffuse in the carbonaceous film, resulting in an increase in the internal resistance of the battery, resulting in high-speed charging. This is because the voltage drop at the discharge rate may become significant.
- the average film thickness of the carbonaceous film of the present invention is preferably 1.0 nm or more and 7.0 nm or less, more preferably 2.0 nm or more and 6.0 nm or less, and further preferably 3.0 nm or more and 5.0 nm or less.
- the film thickness can be calculated based on the transmission electron microscope (TEM) image obtained by observing the carbonaceous film on the surface of the electrode material using a transmission electron microscope (TEM).
- the reason why the average film thickness of the carbonaceous film is limited to the above range is that if the average film thickness is less than 1.0 nm, the charge transfer resistance in the carbonaceous film increases, and as a result, the inside of the battery This is because the resistance increases and the voltage drop at the high-speed charge / discharge rate may become significant.
- the average film thickness of the carbonaceous film exceeds 7.0 nm, the lithium ion migration resistance increases due to steric hindrance when lithium ions diffuse in the carbonaceous film, resulting in an increase in the internal resistance of the battery. This is because the voltage drop at the high-speed charge / discharge rate may become significant.
- the “internal resistance” is mainly a sum of charge transfer resistance and lithium ion transfer resistance.
- the charge transfer resistance is proportional to the film thickness of the carbonaceous film, the density of the carbonaceous film, and the crystallinity
- the lithium ion transfer resistance is inversely proportional to the film thickness of the carbonaceous film, the density of the carbonaceous film, and the crystallinity.
- a current pause method or the like is used as an evaluation method of the internal resistance.
- the internal resistance is the wiring resistance, contact resistance, charge transfer resistance, lithium ion transfer resistance, lithium reaction resistance at the positive and negative electrodes, interelectrode resistance determined by the distance between the positive and negative electrodes, lithium ion solvation, desolvation It is measured as the sum of the resistance related to the sum and the SEI (Solid Electrolyte Interface) movement resistance of lithium ions.
- the mass of the carbon component in the carbonaceous film of the electrode material of the present invention is preferably 50% by mass or more, more preferably 60% by mass or more of the total mass of the carbonaceous film.
- an upper limit can be selected arbitrarily, it is good also considering the upper limit of a range as 100 mass%, for example, 100 mass%, for example. Other examples include 95% by mass or less, 90% by mass or less, 85% by mass or less, or 80% by mass or less.
- the reason why the mass of the carbon component in the carbonaceous film is limited to the above range is that when the mass of the carbon component in the obtained carbonaceous film is less than 50% by mass, the charge transfer of the carbonaceous film is performed.
- the carbonaceous film of the electrode material is produced by thermal decomposition of an organic compound that is a precursor of carbon. Therefore, this carbonaceous film inevitably contains elements such as hydrogen and oxygen in addition to carbon. Therefore, for example, when firing in a temperature range of 500 ° C. or less, the mass of the carbon component in the obtained carbonaceous film may be less than 50% by mass. In that case, the charge transfer resistance of the carbonaceous film increases, and as a result, the internal resistance of the battery increases, and the voltage drop at the high-speed charge / discharge rate may become significant.
- the density obtained from the carbon component of the carbonaceous film of the present invention is preferably 0.3 g / cm 3 or more and 1.5 g / cm 3 or less, more preferably 0.35 g / cm 3 or more and 1.3 g / cm. It is cm 3 or less, more preferably 0.4 g / cm 3 or more and 1.0 g / cm 3 or less.
- the density can be measured using a separated carbonaceous film and a dry density meter.
- the reason why the density obtained from the carbon component of the carbonaceous film is limited to the above range is that the electronic conductivity of the carbonaceous film may be insufficient when the density is less than 0.3 g / cm 3. Because.
- the specific surface area of the electrode active material particles having the carbonaceous film formed on the surface is preferably 5 m 2 / g or more and 20 m 2 / g or less, more preferably 7 m 2 / g or more and 16 m 2 / g or less. And more preferably 9 m 2 / g or more and 13 m 2 / g or less.
- the specific surface area can be obtained by measuring the electrode material using a specific surface area meter.
- the reason why the specific surface area of the electrode active material particles having the carbonaceous film formed on the surface is limited to the above range is that if the specific surface area is less than 5 m 2 / g, the amount of carbon in the carbonaceous film is 2 This is because the average film thickness of the carbonaceous film may exceed 7 nm when the content is 0.0 mass% or more. On the other hand, if the specific surface area exceeds 20 m 2 / g, the average film thickness of the carbonaceous film may be less than 1.0 nm when the amount of carbon in the carbonaceous film is less than 0.6%. That is, if it is out of the above range, an appropriate carbon amount may not be maintained.
- Electrode material A preferred method for producing the electrode material of the present invention will be described below.
- a slurry in which the above components including an electrode active material or a precursor thereof, an organic compound, and water are mixed is prepared.
- the electrode active material or the precursor thereof is in the particle size distribution with respect to the particle diameter (D90) when the cumulative volume percentage is 90% and the particle diameter (D10) when the cumulative volume percentage is 10%.
- the ratio (D90 / D10) is preferably 5 or more and 30 or less. More preferably, it is 10-25. When the value is within the above range, it is advantageous in that desirable control of the volume density of the aggregate can be achieved.
- this slurry is dried. Next, the obtained dried product is fired in a non-oxidizing atmosphere of 500 ° C. or higher and 1000 ° C. or lower.
- the particle size and particle size distribution of the electrode active material or its precursor can be measured with a particle size distribution meter or the like.
- the electrode active material can be arbitrarily selected. Similar to the example described in the above description of the electrode material, lithium cobalt acid, lithium nickel acid, lithium manganese oxide, lithium titanate, and Li x A y D z PO 4 (where, A is Co, Mn, Ni, Fe , Cu, Cr, one or more selected from the group, D is Mg, Ca, S, Sr, Ba, Ti, Zn, B, Al, Ga, In, Si, Ge, Sc, Y, rare earth 1 type or 2 types or more selected from the group of elements, 1 type selected from the group of 0 ⁇ x ⁇ 2, 0 ⁇ y ⁇ 1.5, 0 ⁇ z ⁇ 1.5) is included as a main component It is preferable.
- A is selected from Co, Mn, Ni, and Fe
- D is selected from Mg, Ca, Sr, Ba, Ti, Zn, and Al.
- the rare earth elements are 15 elements of La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, and Lu which are lanthanum series.
- Li x A y D z PO compounds represented by 4 as (Li x A y D z PO 4 powder) is a solid phase method, liquid phase method, and the like vapor phase method, were prepared by conventional methods Compounds can be used.
- the compound (Li x A y D z PO 4 powder) can be arbitrarily selected. For example, a slurry mixture obtained by mixing a Li source, a divalent iron salt, a phosphoric acid compound, and water is hydrothermally synthesized using a pressure-resistant sealed container, and the resulting precipitate is washed with water to obtain a cake.
- a compound (Li x A y D z PO 4 powder) obtained by producing a cake-like precursor material and firing this cake-like precursor material can be suitably used.
- a lithium source selected from the group consisting of lithium acetate (LiCH 3 COO) and lithium chloride (LiCl) or lithium hydroxide (LiOH), and iron (II) chloride (FeCl 2 ), divalent iron salts such as iron (II) acetate (Fe (CH 3 COO) 2 ) and iron (II) sulfate (FeSO 4 ), phosphoric acid (H 3 PO 4 ), dihydrogen phosphate
- a slurry-like mixture obtained by mixing phosphoric acid compounds such as ammonium (NH 4 H 2 PO 4 ) and diammonium hydrogen phosphate ((NH 4 ) 2 HPO 4 ) and water was obtained, and the above To obtain a compound (Li x A y D z PO 4 powder) (0 ⁇ x ⁇ 2, 0
- the Li x A y D z PO 4 powder may be crystalline particles or amorphous particles, or mixed crystal particles in which crystalline particles and amorphous particles coexist.
- the reason that the Li x A y D z PO 4 powder may be amorphous particles is that the amorphous Li x A y D z PO 4 powder is 500 ° C. or more and 1000 ° C. or less. This is because crystallization occurs when heat-treated in a non-oxidizing atmosphere.
- the size of the electrode active material of the present invention is not particularly limited, but the average primary particle size is preferably 0.01 ⁇ m or more and 20 ⁇ m or less, more preferably 0.01 ⁇ m or more and 12 ⁇ m or less, More preferably, it is 0.02 ⁇ m or more and 5 ⁇ m or less.
- the particle diameter is a volume average particle diameter.
- the reason why the average particle diameter of the primary particles of the electrode active material is limited to the above range is that the surface of the primary particles is sufficiently thin film carbon if the average particle diameter of the primary particles is less than 0.01 ⁇ m. This is not preferable because it is difficult to coat the film, the discharge capacity at the high-speed charge / discharge rate is lowered, and it may be difficult to realize sufficient charge / discharge rate performance.
- the average particle size of the primary particles exceeds 20 ⁇ m, the internal resistance of the primary particles increases, and therefore the discharge capacity at a high-speed charge / discharge rate may be insufficient, which is not preferable. .
- the shape of the electrode active material of the present invention is not particularly limited. However, since it is easy to produce an electrode material composed of spherical, particularly spherical secondary particles, the shape of the electrode active material is also preferably spherical, particularly true spherical.
- the shape of the electrode active material can be determined by using a scanning electron microscope (SEM). That is, it can be determined by taking a picture, for example.
- SEM scanning electron microscope
- the reason why the shape of the electrode active material is preferably spherical is that the amount of solvent when preparing the positive electrode paste by mixing the electrode active material, the binder resin (binder), and the solvent. This is because the positive electrode paste can be easily applied to the current collector.
- the shape of the electrode active material is spherical, the surface area of the electrode active material is minimized, and the amount of binder resin (binder) added to the electrode material mixture can be minimized and obtained. This is preferable because the internal resistance of the positive electrode can be reduced. Furthermore, since the electrode active material is easily packed most closely, the filling amount of the positive electrode material per unit volume is increased, so that the electrode density can be increased. As a result, the capacity of the lithium ion battery can be increased, which is preferable.
- the organic compound used for forming the carbonaceous film can be arbitrarily selected.
- the compounding ratio of the electrode active material and the organic compound is such that when the total amount of the organic compound is converted into the carbon amount, the carbon amount of the organic compound is 0.6 parts by mass or more and 2.0 parts per 100 parts by mass of the electrode active material.
- the amount is preferably not more than parts by mass, more preferably not less than 0.8 parts by mass and not more than 1.8 parts by mass, and more preferably not less than 1.1 parts by mass and not more than 1.7 parts by mass.
- the compounding ratio in terms of carbon amount of the organic compound is less than 0.6 parts by mass, when the battery is formed, the discharge capacity at the high-speed charge / discharge rate is low, and it is difficult to realize sufficient charge / discharge rate performance. There is a possibility.
- the compounding ratio in terms of carbon amount of the organic compound exceeds 2.0 parts by mass
- the average film thickness of the carbonaceous film exceeds 7 nm
- lithium ions diffuse due to steric hindrance when lithium ions diffuse in the carbonaceous film.
- the movement resistance tends to be high.
- the internal resistance of the battery increases, and there is a possibility that the voltage drop at the high-speed charge / discharge rate cannot be ignored.
- Electrode active materials and organic compounds are dissolved or dispersed in water to prepare a uniform slurry. In the dissolution or dispersion, it is better to add a dispersant as necessary.
- the method for dissolving or dispersing the electrode active material and the organic compound in water is not particularly limited as long as the electrode active material is dispersed and the organic compound is dissolved or dispersed.
- a medium stirring type dispersion device that stirs medium particles at high speed, such as a planetary ball mill, a vibration ball mill, a bead mill, a paint shaker, and an attritor.
- the electrode active material in the dissolution or dispersion, it is preferable to disperse the electrode active material as primary particles in water, and then stir to add and dissolve the organic compound. In this way, the surface of the primary particles of the electrode active material is coated with the organic compound, and as a result, the carbon derived from the organic compound can be uniformly interposed between the primary particles of the electrode active material. .
- the dispersion conditions of the slurry so that the ratio of electrode active material or its precursor (D90 / D10) is 5 or more and 30 or less.
- the volume density of the obtained aggregate is 100% by volume when the volume of the aggregate is solid. It can adjust so that it may become 50 volume% or more and 80 volume% or less. Accordingly, the concentration of the aromatic carbon compound vaporized substance in the aggregate can be increased, and as a result, a carbonaceous film having a small thickness unevenness can be formed on the surface of the electrode active material in the aggregate. it can.
- the vaporized substance of the aromatic carbon compound inside the aggregate is a compound having an aromatic ring composed of an olefin generated by cleavage of a C—C single bond by heating of an organic compound in an inert atmosphere. It is a vaporized substance and is a gaseous substance that is generated during firing at 400 to 500 ° C. due to the organic compound.
- the concentration of the electrode active material and the organic compound in the slurry is in the range of 5 m 2 / g to 20 m 2 / g, preferably in the range of 7 m 2 / g to 17 m 2 / g. More preferably, it can be controlled to an arbitrary value in the range of 9 m 2 / g or more and 13 m 2 / g or less.
- the concentration of the electrode active material and the organic compound in the slurry can be arbitrarily selected.
- the slurry solid content is preferably 20 to 70% by mass or 30 to 60% by mass.
- the stirring time can also be arbitrarily selected, but preferred examples include 20 to 7000 minutes and 30 to 4000 minutes.
- the obtained slurry is sprayed in a high-temperature atmosphere, for example, in the air of 70 ° C. or higher and 250 ° C. or lower and dried.
- the temperature range of the high temperature atmosphere may be arbitrarily selected. For example, ranges of 90 ° C. or higher and 220 ° C. or lower, 100 ° C. or higher and 200 ° C. or lower, or 80 ° C. or higher and 190 ° C. or lower can be preferably selected as necessary. .
- this dried product is fired in a non-oxidizing atmosphere. For example, at a temperature in the range of 500 ° C. to 1000 ° C., preferably 550 ° C. to 950 ° C., more preferably 600 ° C.
- the firing temperature can be arbitrarily selected and is preferably in the range of 700 to 1000 ° C.
- the firing time can also be arbitrarily selected. For example, 0.5 hours to 15 hours or 0.5 hours to 3 hours can be preferably used.
- the non-oxidizing atmosphere is preferably an inert atmosphere such as nitrogen (N 2 ) or argon (Ar).
- an inert atmosphere such as nitrogen (N 2 ) or argon (Ar).
- a reducing atmosphere containing a reducing gas such as hydrogen (H 2 ) in an inert atmosphere of about several volume%.
- a combustion-supporting gas or a combustible gas such as oxygen (O 2 ) may be introduced into the inert atmosphere.
- the reason for setting the firing temperature of the dried product to 500 ° C. or more and 1000 ° C. or less is that when the firing temperature is less than 500 ° C., the decomposition and reaction of the organic compound contained in the dried product does not proceed sufficiently. It tends to be inadequate. As a result, a high-resistance organic compound decomposition product may be generated in the obtained aggregate, which is not preferable.
- the firing temperature exceeds 1000 ° C. Li in the electrode active material evaporates, and not only composition deviation occurs in the electrode active material, but also grain growth of the electrode active material tends to be promoted. As a result, the discharge capacity at a high-speed charge / discharge rate is lowered, and it may be difficult to realize sufficient charge / discharge rate performance, which is not preferable.
- the firing process it is possible to control the particle size distribution of the obtained aggregates by appropriately adjusting the conditions for firing the dried product, for example, the heating rate, the maximum holding temperature, and the holding time. is there.
- the surface of the primary particles of the electrode active material is coated with carbon generated by thermal decomposition of the organic compound in the dried product. Therefore, an aggregate composed of secondary particles in which carbon is interposed between the primary particles of the electrode active material is obtained. That is, the secondary particles include a plurality of primary particles bonded by carbonaceous matter.
- This aggregate serves as an electrode material in the present embodiment.
- the electrode material includes a plurality of aggregates.
- the size of the agglomerates can be arbitrarily selected, but the average particle size is preferably 0.05 ⁇ m to 100 ⁇ m, more preferably 0.1 ⁇ m to 50 ⁇ m, and further preferably 1.0 ⁇ m to 20 ⁇ m.
- the size can be obtained by photo determination taken with a scanning electron microscope.
- the electrode of this embodiment is an electrode containing the electrode material of this embodiment.
- An example of producing the electrode of this embodiment will be described below.
- the electrode material, the binder that is a binder resin, and a solvent are mixed to prepare an electrode-forming paint or electrode-forming paste.
- a conductive aid such as carbon black may be added as necessary.
- Said binder, ie, binder resin can be selected arbitrarily.
- PTFE polytetrafluoroethylene
- PVdF polyvinylidene fluoride
- fluororubber fluororubber and the like are preferably used.
- the mixing ratio of the electrode material and the binder resin is not particularly limited.
- the binder resin can be mixed at a ratio of 1 part by mass to 30 parts by mass, preferably 3 parts by mass to 20 parts by mass with respect to 100 parts by mass of the electrode material.
- the solvent used for the electrode forming paint or electrode forming paste can be arbitrarily selected. Specifically, water, methanol, ethanol, 1-propanol, 2-propanol (isopropyl alcohol: IPA), butanol, pentanol, hexanol, octanol, diacetone alcohol and other alcohols, ethyl acetate, butyl acetate, ethyl lactate , Propylene glycol monomethyl ether acetate, propylene glycol monoethyl ether acetate, esters such as ⁇ -butyrolactone, diethyl ether, ethylene glycol monomethyl ether (methyl cellosolve), ethylene glycol monoethyl ether (ethyl cellosolve), ethylene glycol mono Ethers such as butyl ether (butyl cellosolve), diethylene glycol monomethyl ether, diethylene glycol monoethyl ether, acetone Ketones such as
- the electrode-forming paint or electrode-forming paste is applied to one surface of a member such as a metal selected arbitrarily, for example, a metal foil. Thereafter, by drying, a metal foil in which a coating film made of a mixture of the electrode material and the binder resin is formed on one surface is obtained. Next, this coating film is pressure-bonded and dried to produce a current collector (electrode) having an electrode material layer on one surface of the metal foil.
- a current collector electrode capable of improving the electronic conductivity can be produced without impairing the lithium ion conductivity of the present embodiment.
- a lithium ion battery can be obtained by using the current collector (electrode) as a positive electrode.
- the internal resistance of the current collector (electrode) can be reduced by producing the current collector (electrode) using the electrode material of the present embodiment. Therefore, the internal resistance of the battery can be kept low, and as a result, it is possible to provide a lithium ion battery that can perform high-speed charge / discharge without fear of a significant voltage drop.
- the electrode active material particles having a carbonaceous film formed on the surface thereof are aggregated to form an aggregate.
- the volume density is 50% by volume or more and 80% by volume or less of the actual volume density.
- the coverage of the carbonaceous film on the surface of the electrode active material particles is 80% or more. It was set to 1.0 nm or more and 7.0 nm or less. Therefore, unevenness of the amount of the carbonaceous film formed on the surface of the electrode active material particles can be reduced, and the electron conductivity can be improved without impairing the lithium ion conductivity.
- the present invention by controlling the carbon loading, the thickness of the carbonaceous film, the density of the carbonaceous film, the specific surface area of the electrode active material particles, and the mass percentage of the carbon component constituting the carbonaceous film,
- the electrode material is used for a lithium ion battery
- the internal resistance of the battery is reduced, and the lithium ion battery can be used as a high output power source.
- metal Li is used for the negative electrode in order to reflect the behavior of the electrode material itself in the data, but a negative electrode material such as a carbon material, Li alloy, Li 4 Ti 5 O 12 may be used for the negative electrode. It doesn't matter.
- a solid electrolyte may be used instead of the electrolytic solution and the separator.
- Example 1 (Production of electrode material) 4 mol of lithium acetate (LiCH 3 COO), 2 mol of iron (II) sulfate (FeSO 4 ), and 2 mol of phosphoric acid (H 3 PO 4 ) are added to 2 L (liter) of water, and the total amount becomes 4 L. In this way, water was added and mixed to prepare a uniform slurry mixture. Subsequently, this mixture was accommodated in a pressure-resistant sealed container having a capacity of 8 L, and hydrothermal synthesis was performed at 120 ° C. for 1 hour. Next, the obtained precipitate was washed with water to obtain a cake-like electrode active material precursor.
- 150 g of the precursor of this electrode active material in terms of solid content
- an aqueous polyvinyl alcohol solution (2.0% by mass in terms of carbon content, obtained by dissolving 20 g of polyvinyl alcohol (PVA) as an organic compound in 100 g of water) were obtained.
- the material is measured with a carbon analyzer), and 500 g of zirconia balls having a diameter of 5 mm are introduced as medium particles into a ball mill, and the particle size distribution D90 / D10 of the precursor particles of the electrode active material in the slurry is 7.
- the ball mill stirring time was adjusted so that the specific surface area of the electrode active material particles having the carbonaceous film formed on the surface to be obtained was 5.0 m 2 / g, and the dispersion treatment was performed.
- the stirring time of the ball mill at this time was about 30 minutes.
- the particle size distributions D90 and D10 of the precursor particles of the electrode active material were measured by stopping the ball mill several times and taking samples. Whether or not the specific surface area of the electrode active material particles was 5.0 m 2 / g was confirmed by a specific surface area meter. The reason why the amount of carbon was 2.0% by mass is considered that only a part of the amount of carbon added as PVA at the time of firing remained in the electrode material, while a certain amount of carbon was blown away.
- Example 1 The volume density of this aggregate (when the volume density when the aggregate is solid is 100% by volume) was 64% by volume. The volume density was measured using a mercury porosimeter (trade name: PoreMaster GT 60, manufactured by Quanta chrome Co.).
- Electrode active material having a carbonaceous film formed on the surface by measuring an electrode material using a specific surface area meter (product name: BELSORP-mini II, Nippon Bell Co., Ltd.) The specific surface area of the particles was determined.
- Lithium metal was disposed as a negative electrode with respect to the positive electrode of the lithium ion battery, and a separator made of porous polypropylene was disposed between the positive electrode and the negative electrode to obtain a battery member.
- ethylene carbonate and diethyl carbonate were mixed at a ratio of 1: 1 (mass ratio), and LiPF 6 was further added to a concentration of 1M to prepare an electrolyte solution having lithium ion conductivity.
- the battery member was immersed in the electrolyte solution and stored in a coin cell container to produce a lithium ion battery of Example 1.
- Example 2 The stirring time of the ball mill is adjusted so that the specific surface area of the electrode active material particles having a carbonaceous film formed on the surface is 8.1 m 2 / g, the firing temperature in a nitrogen atmosphere is 700 ° C., and the carbon content is 1.
- the electrode material and lithium ion battery positive electrode of Example 2 were produced and evaluated in the same manner as Example 1 except that the content was 0% by mass. The evaluation results are shown in Tables 1 and 2.
- the stirring time of Example 2 is about 120 minutes.
- the volume density of this aggregate (when the volume density when the aggregate is solid is 100% by volume) was 62% by volume.
- Example 3 The stirring time of the ball mill is adjusted so that the specific surface area of the electrode active material particles having a carbonaceous film formed on the surface is 10.7 m 2 / g, the firing temperature in a nitrogen atmosphere is 800 ° C., and the carbon content is 1.
- the electrode material and lithium ion battery positive electrode of Example 3 were produced and evaluated in the same manner as in Example 1 except that the content was 2% by mass. The evaluation results are shown in Tables 1 and 2.
- the stirring time of Example 3 is about 240 minutes.
- the volume density of this aggregate (when the volume density when the aggregate is solid is 100% by volume) was 60% by volume.
- Example 4 The stirring time of the ball mill is adjusted so that the specific surface area of the electrode active material particles having a carbonaceous film formed on the surface is 12.3 m 2 / g, the firing temperature in a nitrogen atmosphere is 700 ° C., and the carbon content is 1.
- the electrode material and lithium ion battery positive electrode of Example 4 were produced and evaluated in the same manner as in Example 1 except that the amount was 6% by mass. The evaluation results are shown in Tables 1 and 2.
- the stirring time in Example 4 is about 480 minutes.
- the volume density of this aggregate (when the volume density when the aggregate is solid is 100% by volume) was 60% by volume.
- Example 5 Except for adjusting the ball mill stirring time so that the specific surface area of the electrode active material particles having the carbonaceous film formed on the surface is 14.0 m 2 / g and setting the carbon amount to 1.4% by mass, in the same manner as in Example 1, the electrode material of Example 5 and the positive electrode of the lithium ion battery were prepared and evaluated. The evaluation results are shown in Tables 1 and 2.
- the stirring time in Example 5 is about 960 minutes.
- the volume density of the aggregate (when the volume density when the aggregate is solid is 100% by volume) was 58% by volume.
- Example 6 The agitation time of the ball mill is adjusted so that the specific surface area of the electrode active material particles having a carbonaceous film formed on the surface is 14.0 m 2 / g, the firing temperature in a nitrogen atmosphere is 900 ° C., and the carbon content is 2.
- the electrode material and lithium ion battery positive electrode of Example 6 were prepared and evaluated in the same manner as Example 1 except that the content was 0% by mass. The evaluation results are shown in Tables 1 and 2.
- the stirring time in Example 6 is about 960 minutes.
- the volume density of the aggregate (when the volume density when the aggregate is solid is 100% by volume) was 58% by volume.
- Example 7 The stirring time of the ball mill is adjusted so that the specific surface area of the electrode active material particles having a carbonaceous film formed on the surface is 14.0 m 2 / g, the firing temperature in a nitrogen atmosphere is 950 ° C., and the carbon content is 2.
- the electrode material and lithium ion battery positive electrode of Example 7 were produced and evaluated in the same manner as Example 1 except that the content was 0% by mass. The evaluation results are shown in Tables 1 and 2.
- the stirring time in Example 7 is about 960 minutes.
- the volume density of the aggregate (when the volume density when the aggregate is solid is 100% by volume) was 58% by volume.
- Example 8 The stirring time of the ball mill is adjusted so that the specific surface area of the electrode active material particles having a carbonaceous film formed on the surface is 14.0 m 2 / g, the firing temperature in a nitrogen atmosphere is 1000 ° C., and the carbon content is 2.
- the electrode material and lithium ion battery positive electrode of Example 8 were produced and evaluated in the same manner as in Example 1 except that the content was 0% by mass. The evaluation results are shown in Tables 1 and 2.
- the stirring time in Example 8 is about 960 minutes.
- the volume density of the aggregate (when the volume density when the aggregate is solid is 100% by volume) was 58% by volume.
- Example 9 The agitation time of the ball mill is adjusted so that the specific surface area of the electrode active material particles having a carbonaceous film formed on the surface is 14.7 m 2 / g, the firing temperature in a nitrogen atmosphere is 800 ° C., and the carbon content is 2.
- the electrode material and lithium ion battery positive electrode of Example 9 were prepared and evaluated in the same manner as Example 1 except that the content was 0% by mass. The evaluation results are shown in Tables 1 and 2.
- the stirring time in Example 9 is about 960 minutes.
- the volume density of the aggregate (when the volume density when the aggregate is solid is 100% by volume) was 58% by volume.
- Example 10 The agitation time of the ball mill was adjusted so that the specific surface area of the electrode active material particles having the carbonaceous film formed on the surface was 20.0 m 2 / g, the firing temperature in a nitrogen atmosphere was 700 ° C., and the carbon amount was 0.1.
- the electrode material and lithium ion battery positive electrode of Example 10 were prepared and evaluated in the same manner as in Example 1 except that the amount was 6% by mass. The evaluation results are shown in Tables 1 and 2.
- the stirring time in Example 10 is about 1440 minutes.
- the volume density of this aggregate (when the volume density when the aggregate is solid is 100 volume%) was 55 volume%.
- Comparative Example 1 The agitation time of the ball mill was adjusted so that the specific surface area of the electrode active material particles having a carbonaceous film formed on the surface was 17.0 m 2 / g, the firing temperature in a nitrogen atmosphere was 700 ° C., and the carbon amount was 0.1.
- the electrode material of Comparative Example 1 and the lithium ion battery positive electrode were prepared and evaluated in the same manner as in Example 1 except that the content was 5% by mass. The evaluation results are shown in Tables 1 and 2.
- the stirring time of the comparative example 1 is about 1200 minutes.
- the volume density of this aggregate (when the volume density when the aggregate is solid is 100% by volume) was 56% by volume.
- Comparative Example 2 The stirring time of the ball mill is adjusted so that the specific surface area of the electrode active material particles having the carbonaceous film formed on the surface is 8.5 m 2 / g, the firing temperature in the nitrogen atmosphere is 700 ° C., and the carbon content is 2.
- An electrode material and a lithium ion battery positive electrode of Comparative Example 2 were produced and evaluated in the same manner as in Example 1 except that the content was 0% by mass. The evaluation results are shown in Tables 1 and 2.
- the stirring time in Comparative Example 2 is about 130 minutes. The volume density of this aggregate (when the volume density when the aggregate is solid is 100% by volume) was 62% by volume.
- Comparative Example 3 The stirring time of the ball mill is adjusted so that the specific surface area of the electrode active material particles having a carbonaceous film formed on the surface is 4.5 m 2 / g, the firing temperature in a nitrogen atmosphere is 700 ° C., and the carbon content is 1.
- the electrode material and lithium ion battery positive electrode of Comparative Example 3 were prepared and evaluated in the same manner as in Example 1 except that the content was 2% by mass. The evaluation results are shown in Tables 1 and 2.
- the stirring time of the comparison 31 is about 25 minutes.
- the volume density of this aggregate (when the volume density when the aggregate is solid is 100% by volume) was 64% by volume.
- Comparative Example 4 The stirring time of the ball mill is adjusted so that the specific surface area of the electrode active material particles having a carbonaceous film formed on the surface is 22.0 m 2 / g, the firing temperature in a nitrogen atmosphere is 700 ° C., and the carbon content is 1.
- An electrode material and a lithium ion battery positive electrode of Comparative Example 4 were produced and evaluated in the same manner as in Example 1 except that the content was 0% by mass. The evaluation results are shown in Tables 1 and 2.
- the stirring time of the comparative example 4 is about 1600 minutes. The volume density of this aggregate (when the volume density when the aggregate is solid is 100% by volume) was 52% by volume.
- the film thickness of the carbonaceous film is in the range of 1.0 nm to 7.0 nm, and the density of the carbonaceous film is 0.3 g / cm 3 to 1. It was found to be in the range of 0.5 g / cm 3 and the internal resistance to be in the range of 9.5 ⁇ to 12.5 ⁇ . In addition, it was found that these electrode materials have a lower internal resistance than the electrode materials of Comparative Examples 1 to 4, and can reduce the internal resistance when used as an electrode material for a lithium ion battery.
- the electrode material of the present invention has a volume density of an aggregate formed by agglomerating electrode active material particles having a carbonaceous film formed on the surface. 50% by volume or more and 80% by volume or less, and further, the coverage of the carbonaceous film on the surface of the electrode active material particles is 80% or more, and the average film thickness of the carbonaceous film is 1.0 nm or more and 7.0 nm or less. It was.
- the unevenness of the loading amount of the carbonaceous film formed on the surface of the electrode active material particles can be reduced.
- the loading amount of carbon, the film thickness of the carbonaceous film, the density of the carbonaceous film, the electrode The specific surface area of the active material and the mass fraction of the carbon component constituting the carbonaceous film could be controlled.
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Abstract
Description
本願は、2012年3月30日に、日本に出願された特願2012-078860号に基づき優先権を主張し、その内容をここに援用する。
リチウムイオン電池の負極材料としては、負極活物質として、炭素系材料またはチタン酸リチウム(Li4Ti5O12)等の、リチウムイオンを可逆的に脱挿入可能な性質を有するLi含有金属酸化物が、一般に用いられている。
一方、リチウムイオン電池の正極材料としては、正極活物質として、鉄リン酸リチウム(LiFePO4)等の、リチウムイオンを可逆的に脱挿入可能な性質を有するLi含有金属酸化物や、バインダー等を含む電極材料合剤が、用いられている。そして、この電極材料合剤を集電体と称される金属箔の表面に塗布することにより、リチウムイオン電池の正極が形成されている。
また、近年、リチウムイオン電池は、プラグインハイブリッド自動車、ハイブリッド自動車、及び電動工具等の高出力電源としても検討されている。これらの高出力電源として用いられる電池には、高速の充放電特性が求められている。
電極材料の電子伝導性を高めるために、電極活物質の粒子表面を、炭素源である有機化合物で覆い、その後、有機化合物を炭化することにより、電極活物質の表面に炭素質被膜を形成した、すなわち、この炭素質被膜の炭素を電子伝導性物質として介在させた、電極材料が提案されている(特許文献1)。
しかしながら、一方で、この炭素質被膜はリチウムイオンが拡散する際の障壁となる。すなわち、炭素質被膜の膜厚が厚ければ厚い程、また、炭素質被膜の結晶性が高ければ高い程、リチウムイオンの伝導性が損なわれる。その結果、炭素質被膜に起因して電池内部の抵抗が上昇し、特に高速の充放電を行った際に、電圧が著しく低下することとなる。
そこで、本発明者等は、電極活物質の炭素質被膜の膜厚のムラを低減する目的で、これまで、表面に炭素質被膜が形成された電極活物質粒子を凝集して、平均粒子径が0.5μm以上かつ100μm以下の凝集体を形成し、この凝集体の体積密度を、前記凝集体を中実とした場合の体積密度の50体積%以上かつ80体積%以下とすることにより、電極活物質の炭素質被膜の膜厚のムラを軽減した電極材料を提案している(特願2010-282353号)。しかしながら、この電極材料においても、電子伝導性は改善されているものの、リチウムイオンの伝導性の達成は十分ではなかった。
前記凝集体の体積密度は、前記凝集体を中実とした場合の体積密度に対して、50体積%以上かつ80体積%以下であり、
前記電極活物質粒子の表面の前記炭素質被膜の被覆率は80%以上であり、前記炭素質被膜の平均膜厚は1.0nm以上かつ7.0nm以下であることを特徴とする。
前記炭素質被膜中に占める炭素成分の質量は、前記炭素質被膜の全質量に対して、50質量%以上であり、前記炭素質被膜の炭素成分から求められる密度は0.3g/cm3以上かつ1.5g/cm3以下であることが好ましい。
さらに、表面に炭素質被膜が形成された電極活物質粒子を凝集してなる凝集体の体積密度を、この凝集体を中実とした場合の体積密度の50体積%以上かつ80体積%以下としたので、電極活物質粒子の表面に形成された炭素質被膜の担持量のムラを小さくすることができ、よって、電極活物質の電子導電性のムラを低減することができる。そして、この電子導電性のムラが低減した電極活物質をリチウムイオン電池の電極材料として用いることにより、リチウムイオンの脱挿入に関わる反応を電極活物質の表面全体にて均一に行うことができ、よって、電極の内部抵抗を小さくすることができる。
本発明の電極材料を実施するための形態について以下に説明する。
なお、この形態は、発明の趣旨をより良く理解させるために具体的に説明するものであり、特に指定のない限り、本発明を限定するものではない。発明の範囲を逸脱しない範囲で、特に問題の無い限り、数、量、種類及び比率などの、省略及び変更などを行っても良い。
本実施形態の電極材料は、表面に炭素質被膜が形成された電極活物質粒子を凝集した凝集体からなる。すなわち電極材料は1つ以上の凝集体を含んで構成される。この凝集体の体積密度は、この凝集体を中実とした場合の体積密度の50体積%以上かつ80体積%以下であり、この電極活物質粒子の表面における炭素質被膜の被覆率は80%以上であり、この炭素質被膜の平均膜厚は1.0nm以上かつ7.0nm以下である。炭素質被膜は、有機化合物が熱分解して生成した膜であり、電極活物質上に位置しており、かつ電極活物質同士を接続する膜である。
ここで、中実な凝集体とは、空隙が全く存在しない凝集体のことを意味し、この中実な凝集体の密度は電極活物質の理論密度に等しい密度とする。
ここで、希土類元素とは、ランタン系列であるLa、Ce、Pr、Nd、Pm、Sm、Eu、Gd、Tb、Dy、Ho、Er、Tm、Yb、Luの15元素のことである。
炭素質被膜の被覆率は、透過電子顕微鏡(TEM)、エネルギー分散型X線分光器(EDX)を用いて測定することができる。具体的には、電極活物質粒子に形成された炭素質被膜は、透過型電子顕微鏡(TEM)、及び、エネルギー分散型X線分光器(EDX)を用いて100個の電極活物質粒子を観察し、電極活物質粒子の表面のうち炭素質被膜が覆っている部分の割合を算出し、被覆率とする。
炭素質被膜の被覆率が80%未満では、炭素質被膜の被覆効果が不十分となり、リチウムイオンの脱挿入反応が電極活物質表面にて行なわれる際に、炭素質被膜が形成されていない箇所においてリチウムイオンの脱挿入に関わる反応抵抗が高くなり、放電末期の電圧降下が顕著になる可能性があるので、好ましくない。なお電極活物質粒子の表面の炭素質被膜による被覆率の上限は任意で選択でき、例えば、上限を100%、すなわち範囲の上限を100%以下と設定することができる。必要に応じて、例えば、98%以下、96%以下、93%以下、90%以下などから、選択できる。
ここで、炭素質被膜中の炭素の質量を上記の範囲に限定した理由は、炭素量が0.6質量%未満では、電池を形成した場合に高速充放電レートにおける放電容量が低くなり、充分な充放電レート性能を実現することが困難となる可能性があるからである。一方、炭素量が2.0質量%を超えると、リチウムイオンが炭素質被膜中を拡散する際に立体障害によってリチウムイオン移動抵抗が高くなり、その結果として電池の内部抵抗が上昇し、高速充放電レートにおける電圧低下が著しくなる可能性があるからである。
ここで、炭素質被膜の平均膜厚を上記の範囲に限定した理由は、平均膜厚が1.0nm未満であると、炭素質被膜中の電荷移動抵抗が高くなり、その結果として電池の内部抵抗が上昇し、高速充放電レートにおける電圧低下が著しくなる可能性があるからである。一方、炭素質被膜の平均膜厚が7.0nmを超えると、リチウムイオンが炭素質被膜中を拡散する際に立体障害によってリチウムイオン移動抵抗が高くなり、その結果として電池の内部抵抗が上昇し、高速充放電レートにおける電圧低下が著しくなる可能性があるからである。
この内部抵抗の評価方法としては、例えば、電流休止法等が用いられる。この電流休止法では、内部抵抗は、配線抵抗、接触抵抗、電荷移動抵抗、リチウムイオン移動抵抗、正負電極におけるリチウム反応抵抗、正負極間距離によって定まる極間抵抗、リチウムイオンの溶媒和、脱溶媒和に関わる抵抗、およびリチウムイオンのSEI(Solid ElectrolyteInterface)移動抵抗の総和として測定される。
ここで、炭素質被膜中に占める炭素成分の質量を上記の範囲に限定した理由は、得られた炭素質被膜中に占める炭素成分の質量が50質量%を下回ると、炭素質被膜の電荷移動抵抗が高くなり、その結果として電池の内部抵抗が上昇し、高速充放電レートにおける電圧低下が著しくなる可能性があるからである。
電極材料の炭素質被膜は、炭素の前駆体である有機化合物の熱分解によって生成したものである。よって、この炭素質被膜は、必然的に炭素の他に水素、酸素等の元素を含んでいる。それ故に例えば、500℃以下の温度範囲で焼成した場合には、得られた炭素質被膜中に占める炭素成分の質量が50質量%を下回る可能性がある。その場合、炭素質被膜の電荷移動抵抗が高くなり、その結果として電池の内部抵抗が上昇し、高速充放電レートにおける電圧低下が著しくなる可能性がある。
ここで、炭素質被膜の炭素成分から求められる密度を上記の範囲に限定した理由は、密度が0.3g/cm3未満であると、炭素質被膜の電子伝導性が不足する可能性があるからである。一方、1.5g/cm3を超えると、炭素質被膜中に層状構造からなる黒鉛の微結晶が多数発生してしまう可能性がある。そして、リチウムイオンが炭素質被膜中を拡散する際に黒鉛の微結晶が立体障害を引き起こしてリチウムイオン移動抵抗が高くなり、結果として電池の内部抵抗が上昇し、高速充放電レートにおける電圧低下が著しくなる可能性があるからである。
ここで、表面に炭素質被膜が形成された電極活物質粒子の比表面積を上記の範囲に限定した理由は、比表面積が5m2/g未満であると、炭素質被膜中の炭素量が2.0質量%またはそれ以上であった場合に、炭素質被膜の平均膜厚が7nmを超えてしまう可能性があるからである。一方、比表面積が20m2/gを超えると、炭素質被膜中の炭素量が0.6%未満の場合に炭素質被膜の平均膜厚が1.0nmを下回る可能性があるからである。すなわち上記範囲外であると、適切な炭素量を維持できない可能性があるからである。
本発明の電極材料の好ましい製造方法を以下に述べる。本実施形態の電極材料の製造方法では、電極活物質またはその前駆体と、有機化合物と、水とを含む、前記成分が混合された、スラリーを用意する。スラリー中において、この電極活物質またはその前駆体は、その粒度分布における、累積体積百分率が90%のときの粒子径(D90)の、累積体積百分率が10%のときの粒子径(D10)に対する比(D90/D10)が、5以上かつ30以下であることが好ましい。より好ましくは10~25である。値が上記範囲にあると、凝集体の体積密度の望ましいコントロールができる点で有利である。そしてこのスラリーを乾燥する。次いで、得られた乾燥物を、500℃以上かつ1000℃以下の非酸化性雰囲気下にて焼成する。
なお前記電極活物質またはその前駆体の粒子径や粒度分布は、粒度分布計などによって測定することができる。
ここで、希土類元素とは、ランタン系列であるLa、Ce、Pr、Nd、Pm、Sm、Eu、Gd、Tb、Dy、Ho、Er、Tm、Yb、Luの15元素のことである。
この化合物(LixAyDzPO4粉体)は、任意に選択できる。例えば、Li源と2価の鉄塩とリン酸化合物と水とを混合して得られるスラリー状の混合物を、耐圧密閉容器を用いて水熱合成し、得られた沈殿物を水洗してケーキ状の前駆体物質を生成し、このケーキ状の前駆体物質を焼成して得られた化合物(LixAyDzPO4粉体)等を好適に用いることができる。
具体的には、酢酸リチウム(LiCH3COO)、及び、塩化リチウム(LiCl)等のリチウム塩、あるいは水酸化リチウム(LiOH)からなる群から選択されたLi源と、塩化鉄(II)(FeCl2)、酢酸鉄(II)(Fe(CH3COO)2)、及び硫酸鉄(II)(FeSO4)等の2価の鉄塩と、リン酸(H3PO4)、リン酸二水素アンモニウム(NH4H2PO4)、及びリン酸水素二アンモニウム((NH4)2HPO4)等のリン酸化合物と、水と、を混合して得られるスラリー状の混合物を得て、上記の合成や処理を行い、化合物(LixAyDzPO4粉体)(0<x<2、0<y<1.5、0≦z<1.5)を得て、これを好適に用いることができる。
ここで、電極活物質の1次粒子の平均粒径を上記の範囲に限定した理由は、1次粒子の平均粒径が0.01μm未満では、1次粒子の表面を薄膜状の炭素で充分に被覆することが困難となり、高速充放電レートにおける放電容量が低くなり、充分な充放電レート性能を実現することが困難となる可能性があり、好ましくないからである。一方、1次粒子の平均粒径が20μmを超えると、1次粒子の内部抵抗が大きくなり、したがって、高速充放電レートにおける放電容量が不充分となる可能性があるので、好ましくないからである。
ここで、電極活物質の形状が球状であることが好ましい理由は、電極活物質と、バインダー樹脂(結着剤)と、溶媒とを混合して正電極用ペーストを調製する際の溶媒量を低減させることができると共に、この正電極用ペーストの集電体への塗工も容易となるからである。
さらに、電極活物質が最密充填し易いので、単位体積あたりの正極材料の充填量が多くなり、よって、電極密度を高くすることができる。その結果、リチウムイオン電池の高容量化を図ることができるので、好ましい。
ここで、有機化合物の炭素量換算の配合比が0.6質量部未満では、電池を形成した場合に高速充放電レートにおける放電容量が低くなり、充分な充放電レート性能を実現することが困難となる可能性がある。一方、有機化合物の炭素量換算の配合比が2.0質量部を超えると、炭素質被膜の平均膜厚が7nmを超え、リチウムイオンが炭素質被膜中を拡散する際に立体障害によってリチウムイオン移動抵抗が高くなる傾向がある。その結果、電池を形成した場合に電池の内部抵抗が上昇し、高速充放電レートにおける電圧低下が無視できなくなる程度になる可能性がある。
電極活物質と有機化合物とを水に溶解あるいは分散させる方法としては、電極活物質が分散し、有機化合物が溶解または分散する方法であれば、特に限定されない。例えば、遊星ボールミル、振動ボールミル、ビーズミル、ペイントシェーカー、アトライタ等の媒体粒子を高速で攪拌する媒体攪拌型分散装置を用いることが好ましい。
スラリー中の電極活物質及び有機化合物の濃度は任意で選択できるが、例えばスラリー固形分率として20~70質量%や、30~60質量%が好ましい例として挙げられる。攪拌時間も任意で選択できるが、例えば、20~7000分や、30~4000分などが好ましい例として挙げられる。
次いで、この乾燥物を、非酸化性雰囲気下で、焼成する。例えば、500℃以上かつ1000℃以下、好ましくは550℃以上かつ950℃以下、より好ましくは600℃以上かつ900℃以下の範囲内の温度にて、0.1時間以上かつ40時間以下の間、焼成する。焼成温度は任意に選択でき、700~1000℃の範囲であることも好ましい。焼成時間も任意に選択でき、例えば0.5時間以上15時間以下や、0.5時間以上3時間以下なども好ましく使用できる。
以上に述べた工程により、乾燥物中の有機化合物が熱分解して生成した炭素によって、電極活物質の1次粒子の表面が被覆される。よって、この電極活物質の1次粒子の間に炭素が介在した、2次粒子からなる凝集体が得られる。すなわち2次粒子には、炭素質によって結合された複数の一次粒子が含まれる。
この凝集体が、本実施形態における電極材料となる。電極材料には複数の凝集体が含まれる。凝集体のサイズは任意で選択可能であるが、好ましくは平均粒径が0.05μm~100μmであり、より好ましくは、0.1μm~50μm であり、さらに好ましくは1.0μm~20μmである。前記サイズは、走査型電子顕微鏡で撮影した写真判定により求めることができる。
本実施形態の電極は、本実施形態の電極材料を含有する電極である。
本実施形態の電極を作製する例を以下に述べる。まず、上記の電極材料と、バインダー樹脂である結着剤と、溶媒とを混合して、電極形成用塗料または電極形成用ペーストを調整する。この際、必要に応じてカーボンブラック等の導電助剤を添加してもよい。
上記の結着剤、すなわちバインダー樹脂は任意に選択できる。例えば、ポリテトラフルオロエチレン(PTFE)樹脂、ポリフッ化ビニリデン(PVdF)樹脂、フッ素ゴム等が好適に用いられる。
上記の電極材料とバインダー樹脂との配合比は、特に限定されない。例えば、電極材料100質量部に対して、バインダー樹脂を1質量部以上かつ30質量部以下、好ましくは3質量部以上かつ20質量部以下の比率で、混合することができる。
次いで、この塗膜を加圧圧着し、乾燥して、金属箔の一方の面に電極材料層を有する集電体(電極)を作製する。
このようにして、本実施形態のリチウムイオン伝導性を損なうことなく、電子伝導性を向上させることができる電極を作製することができる。
このリチウムイオン電池は、本実施形態の電極材料を用いて集電体(電極)を作製していることにより、集電体(電極)の内部抵抗を小さくすることができる。したがって、電池の内部抵抗を低く抑えることができ、その結果、電圧が著しく低下する虞もなく、高速の充放電を行うことができるリチウムイオン電池を提供することができる。
例えば、本実施例では、電極材料自体の挙動をデータに反映させるために負極に金属Liを用いたが、炭素材料、Li合金、Li4Ti5O12等の負極材料を負極に用いてもかまわない。また電解液とセパレータの代わりに固体電解質を用いても良い。
(電極材料の作製)
水2L(リットル)に、4molの酢酸リチウム(LiCH3COO)、2molの硫酸鉄(II)(FeSO4)、及び2molのリン酸(H3PO4)を加え、更に全体量が4Lになるように水を加え混合し、均一なスラリー状の混合物を調製した。
次いで、この混合物を、容量8Lの耐圧密閉容器に収容し、120℃にて1時間、水熱合成を行った。
次いで、得られた沈殿物を水洗し、ケーキ状の電極活物質の前駆体を得た。
なお電極活物質の前駆体粒子の粒度分布のD90及びD10は、ボールミルを途中で何度か止めてサンプルをとり、測定を行なった。なお電極活物質粒子の比表面積が5.0m2/gとなるかどうかは比表面積計によって確認した。
また炭素量が2.0質量%になったのは、焼成時にPVAとして加えた炭素量の一部のみが電極材料中に残り、一方である程度の炭素分は飛んで行ったと考えられる。
次いで、得られた乾燥物を850℃の窒素雰囲気下にて1時間焼成し、平均粒子径が6μmの凝集体を得て、この凝集体を実施例1の電極材料とした。この凝集体の体積密度(凝集体を中実とした場合の体積密度を100体積%とした場合)は64体積%であった。体積密度は水銀ポロシメーター(商品名: PoreMaster GT 60、Quanta chrome Co.製)を用いて測定を行なった。
この電極材料の電極活物質粒子の比表面積、炭素質被膜の膜厚、炭素質被膜の密度、炭素質被膜の炭素成分の質量分率(炭素分率)、及び炭素質被膜の被覆率の、それぞれの評価を行った。
評価方法は下記のとおりである。
(1)電極活物質粒子の比表面積
比表面積計(製品名: BELSORP-mini II、日本ベル株式会社)を用いて電極材料を測定することにより、表面に炭素質被膜が形成された電極活物質粒子の比表面積を求めた。
凝集体の炭素質被膜を透過型電子顕微鏡(TEM)、エネルギー分散型X線分光器(EDX)を用いて100個の電極活物質粒子を無作為に選択し、これを観察し、電極活物質粒子の表面のうち炭素質被膜が覆っている部分の割合を算出し、被覆率(平均値)とした。
(3) 炭素質被膜の膜厚
電極材料の表面の炭素質被膜を透過型電子顕微鏡(TEM)を用いて100個の電極活物質粒子を観察し、この透過型電子顕微鏡(TEM)像を基に炭素質被膜の膜厚(平均値)を算出した。
電極材料100gを、2000ccの酸性水溶液(3規定塩酸水溶液)に浸漬し、溶解後、残渣である炭素質被膜のみを分離した。この後、これを乾燥し、乾式密度計を用いて炭素質被膜の密度を測定した。
(5) 炭素質被膜の炭素成分の質量分率(炭素分率)
電極材料100gを、2000ccの酸性水溶液(3規定塩酸水溶液)に浸漬し、溶解後、残渣である炭素質被膜のみを分離した。この後、分離した炭素質被膜を使用して、炭素分析計を用いて炭素質被膜の炭素分率を測定した。
上記評価の結果を表1に示す。
上記の電極材料と、バインダーとしてポリフッ化ビニリデン(PVdF)と、導電助剤としてアセチレンブラック(AB)とを、質量比が90:5:5となるように混合した。この混合物2gに、さらに溶媒として3gのN-メチル-2-ピロリジノン(NMP)を加えて流動性を付与し、スラリーを作製した。
次いで、このスラリーを厚み15μmのアルミニウム(Al)箔上に塗布し、乾燥した。その後、600kgf/cm2の圧力にて加圧し、実施例1のリチウムイオン電池の正極を作製した。
一方、炭酸エチレンと炭酸ジエチルとを1:1(質量比)にて混合し、さらにLiPF6を濃度が1Mとなるように加えて、リチウムイオン伝導性を有する電解質溶液を作製した。
次いで、上記の電池用部材を上記の電解質溶液に浸漬し、コインセル容器内に格納して実施例1のリチウムイオン電池を作製した。
このリチウムイオン電池の内部抵抗、充放電特性それぞれの評価を行った。
評価方法は下記のとおりである。
上記のリチウムイオン電池の充放電試験を、室温(25℃)にて、カットオフ電圧2~4.5V、充放電レート1Cの定電流(1時間充電の後、1時間放電)下にて実施した。1C放電容量を表2に示す。
(2)内部抵抗
電極面積が2平方センチメートルの上記正極とリチウム金属からなる負極とを、ポリプロピレンからなる、厚さ25ミクロンのセパレーターを介して対向させ、直径2cm、厚み3.2mmのコインセル容器内に配置した。放電深度50%で、1C放電時に電流休止法により測定される電圧上昇と、1C放電電流とから、内部抵抗を算出した。内部抵抗を表2に示す。
表面に炭素質被膜が形成された電極活物質粒子の比表面積が8.1m2/gとなるようにボールミルの撹拌時間を調整し、窒素雰囲気中の焼成温度を700℃、炭素量を1.0質量%とした他は、実施例1と同様にして実施例2の電極材料及びリチウムイオン電池正電極を作製し、評価を行った。評価結果を表1及び表2に示す。なお実施例2の攪拌時間は約120分である。
またこの凝集体の体積密度(凝集体を中実とした場合の体積密度を100体積%とした場合)は62体積%であった。
表面に炭素質被膜が形成された電極活物質粒子の比表面積が10.7m2/gとなるようにボールミルの撹拌時間を調整し、窒素雰囲気中の焼成温度を800℃、炭素量を1.2質量%とした他は、実施例1と同様にして実施例3の電極材料及びリチウムイオン電池正電極を作製し、評価を行った。評価結果を表1及び表2に示す。なお実施例3の攪拌時間は約240分である。またこの凝集体の体積密度(凝集体を中実とした場合の体積密度を100体積%とした場合)は60体積%であった。
表面に炭素質被膜が形成された電極活物質粒子の比表面積が12.3m2/gとなるようにボールミルの撹拌時間を調整し、窒素雰囲気中の焼成温度を700℃、炭素量を1.6質量%とした他は、実施例1と同様にして実施例4の電極材料及びリチウムイオン電池正電極を作製し、評価を行った。評価結果を表1及び表2に示す。なお実施例4の攪拌時間は約480分である。またこの凝集体の体積密度(凝集体を中実とした場合の体積密度を100体積%とした場合)は60体積%であった。
表面に炭素質被膜が形成された電極活物質粒子の比表面積が14.0m2/gとなるようにボールミルの撹拌時間を調整し、炭素量を1.4質量%とした他は、実施例1と同様にして実施例5の電極材料及びリチウムイオン電池正電極を作製し、評価を行った。評価結果を表1及び表2に示す。
なお実施例5の攪拌時間は約960分である。またこの凝集体の体積密度(凝集体を中実とした場合の体積密度を100体積%とした場合)は58体積%であった。
表面に炭素質被膜が形成された電極活物質粒子の比表面積が14.0m2/gとなるようにボールミルの撹拌時間を調整し、窒素雰囲気中の焼成温度を900℃、炭素量を2.0質量%とした他は、実施例1と同様にして実施例6の電極材料及びリチウムイオン電池正電極を作製し、評価を行った。評価結果を表1及び表2に示す。なお実施例6の攪拌時間は約960分である。またこの凝集体の体積密度(凝集体を中実とした場合の体積密度を100体積%とした場合)は58体積%であった。
表面に炭素質被膜が形成された電極活物質粒子の比表面積が14.0m2/gとなるようにボールミルの撹拌時間を調整し、窒素雰囲気中の焼成温度を950℃、炭素量を2.0質量%とした他は、実施例1と同様にして実施例7の電極材料及びリチウムイオン電池正電極を作製し、評価を行った。評価結果を表1及び表2に示す。なお実施例7の攪拌時間は約960分である。またこの凝集体の体積密度(凝集体を中実とした場合の体積密度を100体積%とした場合)は58体積%であった。
表面に炭素質被膜が形成された電極活物質粒子の比表面積が14.0m2/gとなるようにボールミルの撹拌時間を調整し、窒素雰囲気中の焼成温度を1000℃、炭素量を2.0質量%とした他は、実施例1と同様にして実施例8の電極材料及びリチウムイオン電池正電極を作製し、評価を行った。評価結果を表1及び表2に示す。なお実施例8の攪拌時間は約960分である。
またこの凝集体の体積密度(凝集体を中実とした場合の体積密度を100体積%とした場合)は58体積%であった。
表面に炭素質被膜が形成された電極活物質粒子の比表面積が14.7m2/gとなるようにボールミルの撹拌時間を調整し、窒素雰囲気中の焼成温度を800℃、炭素量を2.0質量%とした他は、実施例1と同様にして実施例9の電極材料及びリチウムイオン電池正電極を作製し、評価を行った。評価結果を表1及び表2に示す。なお実施例9の攪拌時間は約960分である。またこの凝集体の体積密度(凝集体を中実とした場合の体積密度を100体積%とした場合)は58体積%であった。
表面に炭素質被膜が形成された電極活物質粒子の比表面積が20.0m2/gとなるようにボールミルの撹拌時間を調整し、窒素雰囲気中の焼成温度を700℃、炭素量を0.6質量%とした他は、実施例1と同様にして実施例10の電極材料及びリチウムイオン電池正電極を作製し、評価を行った。評価結果を表1及び表2に示す。なお実施例10の攪拌時間は約1440分である。またこの凝集体の体積密度(凝集体を中実とした場合の体積密度を100体積%とした場合)は55体積%であった。
表面に炭素質被膜が形成された電極活物質粒子の比表面積が17.0m2/gとなるようにボールミルの撹拌時間を調整し、窒素雰囲気中の焼成温度を700℃、炭素量を0.5質量%とした他は、実施例1と同様にして比較例1の電極材料及びリチウムイオン電池正電極を作製し、評価を行った。評価結果を表1及び表2に示す。なお比較例1の攪拌時間は約1200分である。またこの凝集体の体積密度(凝集体を中実とした場合の体積密度を100体積%とした場合)は56体積%であった。
表面に炭素質被膜が形成された電極活物質粒子の比表面積が8.5m2/gとなるようにボールミルの撹拌時間を調整し、窒素雰囲気中の焼成温度を700℃、炭素量を2.0質量%とした他は、実施例1と同様にして比較例2の電極材料及びリチウムイオン電池正電極を作製し、評価を行った。評価結果を表1及び表2に示す。なお比較例2の攪拌時間は約130分である。またこの凝集体の体積密度(凝集体を中実とした場合の体積密度を100体積%とした場合)は62体積%であった。
表面に炭素質被膜が形成された電極活物質粒子の比表面積が4.5m2/gとなるようにボールミルの撹拌時間を調整し、窒素雰囲気中の焼成温度を700℃、炭素量を1.2質量%とした他は、実施例1と同様にして比較例3の電極材料及びリチウムイオン電池正電極を作製し、評価を行った。評価結果を表1及び表2に示す。なお比較31の攪拌時間は約25分である。またこの凝集体の体積密度(凝集体を中実とした場合の体積密度を100体積%とした場合)は64体積%であった。
表面に炭素質被膜が形成された電極活物質粒子の比表面積が22.0m2/gとなるようにボールミルの撹拌時間を調整し、窒素雰囲気中の焼成温度を700℃、炭素量を1.0質量%とした他は、実施例1と同様にして比較例4の電極材料及びリチウムイオン電池正電極を作製し、評価を行った。評価結果を表1及び表2に示す。なお比較例4の攪拌時間は約1600分である。またこの凝集体の体積密度(凝集体を中実とした場合の体積密度を100体積%とした場合)は52体積%であった。
具体的には、本発明の電極材料は、表面に炭素質被膜が形成された電極活物質粒子を凝集してなる凝集体の体積密度を、この凝集体を中実とした場合の体積密度の50体積%以上かつ80体積%以下とし、さらに、この電極活物質粒子の表面における炭素質被膜の被覆率を80%以上、この炭素質被膜の平均膜厚を1.0nm以上かつ7.0nm以下とした。このことにより、電極活物質粒子の表面に形成された炭素質被膜の担持量のムラを小さくすることができ、さらには炭素の担持量、炭素質被膜の膜厚、炭素質被膜の密度、電極活物質の比表面積、炭素質被膜を構成する炭素成分の質量分率を制御することができた。この電極材料をリチウムイオン電池に用いた場合、電池の内部抵抗を低減し、リチウムイオン電池を高出力電源用途に適用することができる。よって、より小型化、軽量化、高容量化が期待される次世代の二次電池に対しても前記電極材料が適用されることが可能であり、次世代の二次電池の場合、その効果は非常に大きなものである。
Claims (10)
- 表面に炭素質被膜が形成された電極活物質粒子が凝集された凝集体からなり、
前記凝集体の体積密度は、前記凝集体を中実とした場合の体積密度に対して、50体積%以上かつ80体積%以下であり、
前記電極活物質粒子の表面の前記炭素質被膜の被覆率は80%以上であり、
前記炭素質被膜の平均膜厚は1.0nm以上かつ7.0nm以下であることを特徴とする電極材料。 - 前記炭素質被膜中の炭素の質量は、前記電極活物質粒子の質量に対して、0.6質量%以上かつ2.0質量%以下であり、
表面に前記炭素質被膜が形成された電極活物質粒子の比表面積は5m2/g以上かつ20m2/g以下であることを特徴とする請求項1記載の電極材料。 - 前記炭素質被膜中に占める炭素成分の質量は、前記炭素質被膜の全質量に対して、50質量%以上であり、
前記炭素質被膜の炭素成分から求められる密度は0.3g/cm3以上かつ1.5g/cm3以下であることを特徴とする請求項1または2記載の電極材料。 - 前記電極活物質粒子は、コバルト酸リチウム、ニッケル酸リチウム、マンガン酸リチウム、チタン酸リチウム及びLixAyDzPO4(但し、AはCo、Mn、Ni、Fe、Cu、Crの群から選択される1種または2種以上、DはMg、Ca、S、Sr、Ba、Ti、Zn、B、Al、Ga、In、Si、Ge、Sc、Y、希土類元素の群から選択される1種または2種以上であり、0<x<2、0<y<1.5、0≦z<1.5)の群から選択される1種を主成分とすることを特徴とする請求項1ないし3のいずれか1項記載の電極材料。
- 前記電極活物質の平均粒径が、0.01μm以上かつ20μm以下である、請求項1記載の電極材料。
- 前記炭素質被膜が、有機化合物が熱分解して生成した、電極活物質上に位置し、かつ電極活物質同士を接続する、炭素質被膜であって、
前記炭素質被膜は、
電極活物質またはその前駆体と、水と、ポリビニルアルコール、ポリビニルピロリドン、セルロース、デンプン、ゼラチン、カルボキシメチルセルロース、メチルセルロース、ヒドロキシメチルセルロース、ヒドロキシエチルセルロース、ポリアクリル酸、ポリスチレンスルホン酸、ポリアクリルアミド、ポリ酢酸ビニル、グルコース、フルクトース、ガラクトース、マンノース、マルトース、スクロース、ラクトース、グリコーゲン、ペクチン、アルギン酸、グルコマンナン、キチン、ヒアルロン酸、コンドロイチン、アガロース、ポリエーテル、2価アルコール、及び、3価アルコールからなる群から選択される少なくとも1種である有機化合物と、を混合し、この混合物を、70℃以上かつ250℃以下の大気中に噴霧し乾燥させ、その後、500℃以上かつ1000℃以下の非酸化性雰囲気下で焼成することによって得られた膜である、請求項1記載の電極材料。 - 請求項1の電極材料とバインダー樹脂を含む電極材料層を有し、
前記電極材料100質量部に対してバインダー樹脂が1質量部以上かつ30質量部以下の範囲で含まれる、電極。 - 正極電極である、請求項7に記載の電極。
- 請求項7に記載の電極を含む、電池。
- 前記電極が正極電極である、請求項9に記載の電池。
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