WO2017203954A1 - 低対称ガーネット関連型構造固体電解質およびリチウムイオン二次電池 - Google Patents
低対称ガーネット関連型構造固体電解質およびリチウムイオン二次電池 Download PDFInfo
- Publication number
- WO2017203954A1 WO2017203954A1 PCT/JP2017/017233 JP2017017233W WO2017203954A1 WO 2017203954 A1 WO2017203954 A1 WO 2017203954A1 JP 2017017233 W JP2017017233 W JP 2017017233W WO 2017203954 A1 WO2017203954 A1 WO 2017203954A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- crystal
- garnet
- lithium
- solid electrolyte
- raw material
- Prior art date
Links
Images
Classifications
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
- C01G33/00—Compounds of niobium
- C01G33/006—Compounds containing, besides niobium, two or more other elements, with the exception of oxygen or hydrogen
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
- C01G25/00—Compounds of zirconium
- C01G25/006—Compounds containing, besides zirconium, two or more other elements, with the exception of oxygen or hydrogen
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01G—COMPOUNDS CONTAINING METALS NOT COVERED BY SUBCLASSES C01D OR C01F
- C01G35/00—Compounds of tantalum
- C01G35/006—Compounds containing, besides tantalum, two or more other elements, with the exception of oxygen or hydrogen
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/01—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics
- C04B35/48—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on oxide ceramics based on zirconium or hafnium oxides, zirconates, zircon or hafnates
- C04B35/486—Fine ceramics
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/626—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B
- C04B35/62605—Treating the starting powders individually or as mixtures
- C04B35/6261—Milling
- C04B35/6262—Milling of calcined, sintered clinker or ceramics
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
- C04B35/626—Preparing or treating the powders individually or as batches ; preparing or treating macroscopic reinforcing agents for ceramic products, e.g. fibres; mechanical aspects section B
- C04B35/62605—Treating the starting powders individually or as mixtures
- C04B35/62645—Thermal treatment of powders or mixtures thereof other than sintering
-
- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B13/00—Single-crystal growth by zone-melting; Refining by zone-melting
- C30B13/28—Controlling or regulating
-
- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B29/00—Single crystals or homogeneous polycrystalline material with defined structure characterised by the material or by their shape
- C30B29/10—Inorganic compounds or compositions
- C30B29/16—Oxides
- C30B29/22—Complex oxides
-
- C—CHEMISTRY; METALLURGY
- C30—CRYSTAL GROWTH
- C30B—SINGLE-CRYSTAL GROWTH; UNIDIRECTIONAL SOLIDIFICATION OF EUTECTIC MATERIAL OR UNIDIRECTIONAL DEMIXING OF EUTECTOID MATERIAL; REFINING BY ZONE-MELTING OF MATERIAL; PRODUCTION OF A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; SINGLE CRYSTALS OR HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; AFTER-TREATMENT OF SINGLE CRYSTALS OR A HOMOGENEOUS POLYCRYSTALLINE MATERIAL WITH DEFINED STRUCTURE; APPARATUS THEREFOR
- C30B29/00—Single crystals or homogeneous polycrystalline material with defined structure characterised by the material or by their shape
- C30B29/10—Inorganic compounds or compositions
- C30B29/16—Oxides
- C30B29/22—Complex oxides
- C30B29/30—Niobates; Vanadates; Tantalates
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B1/00—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors
- H01B1/06—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors mainly consisting of other non-metallic substances
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B1/00—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors
- H01B1/06—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors mainly consisting of other non-metallic substances
- H01B1/08—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors mainly consisting of other non-metallic substances oxides
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B13/00—Apparatus or processes specially adapted for manufacturing conductors or cables
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M10/00—Secondary cells; Manufacture thereof
- H01M10/05—Accumulators with non-aqueous electrolyte
- H01M10/052—Li-accumulators
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M10/00—Secondary cells; Manufacture thereof
- H01M10/05—Accumulators with non-aqueous electrolyte
- H01M10/052—Li-accumulators
- H01M10/0525—Rocking-chair batteries, i.e. batteries with lithium insertion or intercalation in both electrodes; Lithium-ion batteries
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- 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
- H01M10/0561—Accumulators with non-aqueous electrolyte characterised by the materials used as electrolytes, e.g. mixed inorganic/organic electrolytes the electrolyte being constituted of inorganic materials only
- H01M10/0562—Solid materials
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2002/00—Crystal-structural characteristics
- C01P2002/30—Three-dimensional structures
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2002/00—Crystal-structural characteristics
- C01P2002/50—Solid solutions
- C01P2002/52—Solid solutions containing elements as dopants
- C01P2002/54—Solid solutions containing elements as dopants one element only
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2002/00—Crystal-structural characteristics
- C01P2002/70—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data
- C01P2002/72—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data by d-values or two theta-values, e.g. as X-ray diagram
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2002/00—Crystal-structural characteristics
- C01P2002/70—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data
- C01P2002/74—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data by peak-intensities or a ratio thereof only
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2002/00—Crystal-structural characteristics
- C01P2002/70—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data
- C01P2002/76—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data by a space-group or by other symmetry indications
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2002/00—Crystal-structural characteristics
- C01P2002/70—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data
- C01P2002/77—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data by unit-cell parameters, atom positions or structure diagrams
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2002/00—Crystal-structural characteristics
- C01P2002/70—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data
- C01P2002/78—Crystal-structural characteristics defined by measured X-ray, neutron or electron diffraction data by stacking-plane distances or stacking sequences
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2002/00—Crystal-structural characteristics
- C01P2002/80—Crystal-structural characteristics defined by measured data other than those specified in group C01P2002/70
- C01P2002/88—Crystal-structural characteristics defined by measured data other than those specified in group C01P2002/70 by thermal analysis data, e.g. TGA, DTA, DSC
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2006/00—Physical properties of inorganic compounds
- C01P2006/10—Solid density
-
- C—CHEMISTRY; METALLURGY
- C01—INORGANIC CHEMISTRY
- C01P—INDEXING SCHEME RELATING TO STRUCTURAL AND PHYSICAL ASPECTS OF SOLID INORGANIC COMPOUNDS
- C01P2006/00—Physical properties of inorganic compounds
- C01P2006/40—Electric properties
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3201—Alkali metal oxides or oxide-forming salts thereof
- C04B2235/3203—Lithium oxide or oxide-forming salts thereof
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3224—Rare earth oxide or oxide forming salts thereof, e.g. scandium oxide
- C04B2235/3227—Lanthanum oxide or oxide-forming salts thereof
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
- C04B2235/30—Constituents and secondary phases not being of a fibrous nature
- C04B2235/32—Metal oxides, mixed metal oxides, or oxide-forming salts thereof, e.g. carbonates, nitrates, (oxy)hydroxides, chlorides
- C04B2235/3231—Refractory metal oxides, their mixed metal oxides, or oxide-forming salts thereof
- C04B2235/3251—Niobium oxides, niobates, tantalum oxides, tantalates, or oxide-forming salts thereof
-
- C—CHEMISTRY; METALLURGY
- C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
- C04B—LIME, MAGNESIA; SLAG; CEMENTS; COMPOSITIONS THEREOF, e.g. MORTARS, CONCRETE OR LIKE BUILDING MATERIALS; ARTIFICIAL STONE; CERAMICS; REFRACTORIES; TREATMENT OF NATURAL STONE
- C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
- C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
- C04B2235/74—Physical characteristics
- C04B2235/76—Crystal structural characteristics, e.g. symmetry
- C04B2235/762—Cubic symmetry, e.g. beta-SiC
- C04B2235/764—Garnet structure A3B2(CO4)3
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M2300/00—Electrolytes
- H01M2300/0017—Non-aqueous electrolytes
- H01M2300/0065—Solid electrolytes
- H01M2300/0068—Solid electrolytes inorganic
- H01M2300/0071—Oxides
- H01M2300/0074—Ion conductive at high temperature
- H01M2300/0077—Ion conductive at high temperature based on zirconium oxide
-
- 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 a solid electrolyte material containing a low-symmetric garnet-related structural crystal and an all-solid lithium ion secondary battery using this solid electrolyte material.
- Lithium ion secondary batteries have a higher energy density than secondary batteries such as nickel-cadmium batteries and nickel metal hydride batteries, and can be operated at high potentials, so they are widely used in small information devices such as mobile phones and laptop computers. It has been. In recent years, since it is easy to reduce the size and weight, there is an increasing demand for secondary batteries for hybrid vehicles and electric vehicles. Since high safety is required for applications such as automobiles, all-solid-state lithium ion secondary batteries that do not use flammable electrolytes are being researched and developed in consideration of safety. High ion conductivity is required for a solid electrolyte used in an all-solid lithium ion secondary battery.
- the solid material which is a high-density molded body, can prevent short-circuiting between the positive and negative electrodes during the charge and discharge process, and can be made into thin pieces, thus giving the possibility of downsizing all-solid-state lithium ion secondary batteries.
- materials having these garnet-related structures are difficult to sinter and it is difficult to produce a high-density molded body.
- the present invention has been made in view of such circumstances, and a high-density lithium-containing garnet-related structure crystal having lower symmetry than cubic and tetragonal crystals, and a high-density lithium-containing garnet-related structure. It aims at providing a sintered compact.
- the present inventors have devised a manufacturing method to provide a high density Li 7-xy La 3 Zr 2 -xy Ta x Nb y O 12 (0.05 ⁇ x + y ⁇ 0) where there is no grain boundary. .2, x.gtoreq.0, y.gtoreq.0) crystals were obtained, and it was considered that the above problems could be solved. However, when the lithium-containing garnet-related structural crystal is heated at a high temperature, the lithium volatilizes and becomes lithium deficient and decomposes into lanthanum zirconium oxide.
- the inventors of the present invention have prepared Li 7-xy La 3 Zr 2 -xy Ta x Nb y O 12 (0.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, which melts and cools the raw material at a high temperature. y ⁇ 0)
- the method for producing the crystal was studied earnestly. As a result, by combining the appropriate amount of lithium and the crystal growth rate, the production of lanthanum zirconium oxide due to the volatilization of lithium is suppressed, and the raw material is rotated at a high speed so that the volatile gas does not stagnate in the melting part. It was found that the single crystal growth can be stabilized by releasing it early from the melting part.
- Li 7-x-y La 3 Zr 2-x-y Ta x Nb y O 12 with high density garnet related structure (0.05 ⁇ x + y ⁇ 0.2 , x ⁇ 0, y ⁇ 0) It was confirmed that the crystal can be grown. It was also confirmed that the garnet-related structural crystal can be thinned mechanically.
- this garnet-related structure crystal is a novel garnet-related structure
- the present inventors examined whether a sintered body having the same composition can be produced. As a result, it was confirmed that a crystal body in which the volatilization of lithium was suppressed could be produced by applying an embedding method in which the green compact of the sintered body raw material was covered with the mother powder. Further, at least one of the amount of niobium (x) and the amount of tantalum (y) of Li 7-xy La 3 Zr 2 -xy Ta x Nb y O 12 is changed to satisfy 0.2 ⁇ x + y ⁇ 0.6. Confirms that it is possible to produce a sintered body that has the characteristics of both orthorhombic garnet-related structural crystals with low activation energy and cubic garnet-related structural crystals with high ionic conductivity. did.
- the present inventors also made Li (7-xy) z La 3 Zr 2 -xy Ta x Nb y O 12 (0.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, y ⁇ 0, 1 ⁇ z ⁇ 2) After a polycrystalline body is formed into a rod shape, the polycrystalline body is melted and rapidly cooled by an FZ method using infrared focused heating to obtain a high density Li 7-xy La It was found that a rod of 3 Zr 2 -xy Ta x Nb y O 12 (0.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, y ⁇ 0) crystal can be produced. Moreover, since this high-density rod has high strength, it can be easily cut with a diamond cutter without causing unintentional breakage, etc., and a thin piece having a thickness of about 0.1 mm can be produced by cutting. I found it.
- the garnet-related structure crystal of the present invention has a chemical composition of Li 7-xy La 3 Zr 2 -xy Ta x Nb y O 12 (0.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, y ⁇ 0) and the crystal structure is orthorhombic.
- the garnet-related structural sintered body of the present invention is composed of the garnet-related structural crystal of the present invention and the chemical composition of Li 7-xy La 3 Zr 2-xy Ta x Nb y O 12 (0.2 ⁇ x + y ⁇ 0.6, x ⁇ 0, y ⁇ 0), and a crystal body having a cubic garnet-related structure.
- the all solid lithium ion secondary battery of the present invention has a positive electrode, a negative electrode, and a solid electrolyte material containing the garnet-related structural crystal of the present invention or the garnet-related structural sintered body of the present invention.
- the chemical composition is Li 7-xy La 3 Zr 2-xy Ta x Nb y O 12 (0.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, y ⁇ 0), and a method for producing an orthorhombic garnet-related structural crystal having a chemical composition of Li (7-xy) z La 3 Zr 2-xy Ta x Nb y O 12 form a (0.05 ⁇ x + y ⁇ 0.2 , x ⁇ 0, y ⁇ 0,1 ⁇ z ⁇ 2) melting unit for crystal growth by melting at least part of the raw material represented by Then, the melted portion where the crystal is grown at a moving speed of 8 mm / h or more is moved to the uncrystallized raw material for crystal growth.
- a solid electrolyte material having high ionic conductivity and low activation energy can be obtained.
- Example 4 is a powder X-ray diffraction pattern of the Li 6.8 La 3 Zr 1.8 Ta 0.20 O 12 sintered body obtained in Example 4.
- FIG. The Arrhenius plot of the Li 6.8 La 3 Zr 1.8 Ta 0.20 O 12 sintered body obtained in Example 4.
- FIG. 9 is an exploded view of an all solid lithium ion secondary battery produced in Example 8.
- the crystal body, the sintered body, the solid electrolyte material, the all-solid lithium ion secondary battery, and the method for producing the crystal body of the present invention will be described in detail based on the embodiments and examples.
- duplication description is abbreviate
- the garnet-related structural crystal according to the embodiment of the present invention has a chemical composition of Li 7-xy La 3 Zr 2-xy Ta x Nb y O 12 (0.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, y ⁇ 0), and the crystal structure is orthorhombic.
- the space group showing the symmetry of the crystal structure belongs to Ibca.
- the structure of the garnet-related structural crystal of the present embodiment is such that the B site that takes tetrahedral coordination with oxygen in the garnet structure represented by the general formula C 3 A 2 B 3 O 12 represented by YAG or the like.
- the crystal structure is non-occupied and voids, and Li is occupied by the voids.
- the A site is occupied by La
- the C site is occupied by at least one of Zr, Nb, and Ta
- the void is occupied by Li.
- the garnet-related structural crystal of this embodiment belongs to an orthorhombic crystal having a lower symmetry than a cubic crystal, there are three types of independent sites at the A site, two types of independent sites at the C site, and independent oxygen. There are 6 types of sites.
- the crystal system of the garnet-related structure crystal of the present embodiment, the space group of the crystal structure, and the arrangement of lithium ions are different from the garnet-related structures reported so far.
- the conventionally reported garnet-related structure is cubic or tetragonal, and the space group showing symmetry of the crystal structure is Ia-3d in the case of cubic and I41 / acd in the case of tetragonal. It is.
- the A site, the C site, and the oxygen ion are each one type of independent site.
- the A site is the 24c site
- the C site is the 16a site
- the oxygen ions are the 96h site.
- there are two types of Li ions, and the occupied sites of lithium ions are one type of 24d site and one type of 96h site.
- the crystal system is orthorhombic, and the space group showing the symmetry of the crystal structure is Ibca.
- the A site occupies three types of independent sites 8c, 8d, and 8e
- the C site occupies two types of independent sites 8a and 8b
- oxygen ions occupy six types of 16f sites.
- Lithium ions occupy three types of 16f sites and one type of 8d sites.
- the Wyckoff position is a notation that represents a set of equivalent positions of the crystal structure, and is composed of the number of equivalent points in the crystal structure called multiplicity and the Wyckoff symbols assigned alphabetically from the highest symmetry position. Yes.
- the Li ion site is different from the conventional garnet-related structure, and the occupation ratio of lithium ions is different.
- lithium ions are likely to diffuse if there are appropriate voids at the lithium ion occupation sites. As a result, the activation energy is reduced, and an improvement in lithium ion conductivity can be expected.
- the molten part of the raw material is lowered at a moving speed of 8 mm / h or higher, and the molten part is cooled at high speed.
- the resulting high density Li 7-xy La 3 Zr 2-xy Ta x Nb y O 12 (0.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, y ⁇ 0) crystalline rod is Can be cut to any thickness with a diamond cutter.
- the garnet-related structure crystal of the present embodiment has a chemical composition of Li 7-xy La 3 Zr 2-xy Ta x Nb y O 12 (0) in consideration of the volatilization of lithium at a high temperature. (.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, y ⁇ 0), it is preferable to manufacture by melting a mixed raw material in which the amount of lithium is increased from the stoichiometric ratio of each metal.
- the garnet-related structure crystal of the present embodiment has a chemical composition of Li (7-xy) z La 3 Zr 2 -xy Ta x Nb y O 12 (0.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, y ⁇ 0, 1 ⁇ z ⁇ 2), melting at least part of the raw material to form a crystal growth, and crystal growth at a moving speed of 8 mm / h or more It can be manufactured by moving the molten part to an uncrystallized raw material and crystal growth.
- the melting part for crystal growth can move at a moving speed of 8 mm / h or more
- the CZochralski (CZ) method, the Bridgeman method, the pedestal method, etc. can be used in addition to the FZ method described above.
- the garnet-related structural crystal of the embodiment can be grown.
- Li 7-x-y La 3 Zr 2-x-y Ta x Nb y O 12 (0.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, y ⁇ 0) to be produced according to the size and shape of the crystal body From these, an appropriate production method may be selected.
- the garnet-related structural crystal of this embodiment preferably has a relative density of 99% or more.
- the relative density is calculated by measuring the outer shape of the manufactured flakes, calculating the apparent volume, and dividing the apparent density calculated from the measured mass by the true density obtained from the single crystal X-ray structural analysis result. .
- the higher the relative density the more preferable the garnet-related structural crystal of this embodiment.
- the Nyquist plot based on AC impedance measurement shows two resistance components, ie, a resistance component due to a grain boundary and a resistance component due to the material itself (Non-Patent Document). 1).
- the Nyquist plot of the garnet-related structure crystal of the present embodiment does not show the resistance component due to the grain boundary, but shows only the resistance component of the material itself, as shown in FIG.
- diffraction spots may appear in a ring shape in a diffraction pattern in X-ray diffraction measurement, neutron diffraction measurement, or electron diffraction measurement using a single crystal.
- the present inventors have found that a garnet-related structural crystal belonging to the orthorhombic system. It is found that a single crystal of Li 7-xy La 3 Zr 2 -xy Ta x Nb y O 12 (0.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, y ⁇ 0) can be produced. It was confirmed that the single crystal can be thinned mechanically.
- the sample rod When growing a garnet-related structure single crystal belonging to the orthorhombic system by the FZ method, the sample rod is usually rotated at a speed of 20 rpm or less and lowered at a descending speed of about 2 mm / h.
- Li 7-xy La 3 Zr 2 -xy Ta x Nb y O 12 (0.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, y ⁇ 0) has voids and high Density crystals cannot be produced.
- the garnet-related structure crystal of this embodiment has a high density, it can be easily cut to an arbitrary thickness with a diamond cutter or the like.
- the garnet-related structural crystal of this embodiment has high ionic conductivity. Specifically, at 25 ° C., the lithium ion conductivity is 1.0 ⁇ 10 ⁇ 4 S / cm or more and the activation energy is 0.4 eV or less.
- the garnet-related structural crystal of this embodiment is manufactured by the FZ method
- the raw material is melted while rotating the rod-shaped raw material on a plane perpendicular to the longitudinal direction at a rotation speed of 30 rpm or more, and the molten part is elongated. It is preferable to grow the crystal by moving in the direction.
- the moving speed of the melted part is preferably 8 mm / h or more and 19 mm / h or less.
- bubbles are generated in the molten part as lithium is volatilized, the bubbles can be removed by increasing the rotation speed of the rod-shaped raw material to 30 rpm or more.
- the rotation speed of the raw material is preferably 30 rpm or more and 60 rpm or less.
- the melting of the raw material and the movement of the molten part are preferably performed in a dry air atmosphere.
- Li 7-xy La 3 Zr 2 -xy Ta x Nb y O 12 (0.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, y ⁇ 0) crystal having a relative density of 99% or more.
- the body can be manufactured.
- Li 7-xy La 3 Zr 2 -xy Ta x Nb y O 12 (0.05 ⁇ x + y ⁇ 0. 2, x ⁇ 0, y ⁇ 0)
- the method for producing the garnet-related structure crystal of the present embodiment will be described by taking the growth of the crystal as an example.
- a rod-shaped raw material is produced as follows. First, considering that lithium is volatilized at a high temperature, a lithium compound, a lanthanum compound, a zirconium compound, a niobium compound, and / or a tantalum compound is converted into Li: La: Zr: Nb: Ta (7-xy) z. : 3: 2-xy: Weigh so that x: y (0.05 ⁇ x + y ⁇ 2, x ⁇ 0, y ⁇ 0, 1 ⁇ z ⁇ 2).
- the lithium compound is not particularly limited as long as it contains lithium, and examples thereof include oxides such as Li 2 O and carbonates such as Li 2 CO 3 .
- the lanthanum compound is not particularly limited as long as it contains lanthanum, and examples thereof include oxides such as La 2 O 3 and hydroxides such as La (OH) 3 .
- the zirconium compound is not particularly limited as long as it contains zirconium, and examples thereof include oxides such as ZrO 2 and chlorides such as ZrCl 4 .
- the niobium compound is not particularly limited as long as it contains niobium, and examples thereof include oxides such as Nb 2 O 5 and chlorides such as NbCl 5 .
- the tantalum compound is not particularly limited as long as it contains tantalum, and examples thereof include oxides such as Ta 2 O 5 and chlorides such as TaCl 5 .
- Li: La: Zr: Nb: Ta is (7-xy) z: 3: 2-x-y: x: y (0.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, y ⁇ 0, 1 ⁇ z ⁇ 2) may be weighed.
- the compound containing two or more of these include lanthanum zirconium oxide such as La 2 Zr 2 O 7 , lanthanum niobium oxide such as LaNbO 4 , lithium niobium oxide such as LiNbO 3, and lithium such as Li 2 ZrO 3.
- zirconium oxide and lithium tantalum oxide such as LiTaO 3 .
- each weighed compound is mixed.
- the mixing method is not particularly limited as long as these compounds can be uniformly mixed, and may be mixed by a wet method or a dry method using a mixer such as a mixer. Then, after filling the obtained mixture into a crucible with a lid, a powder as a raw material is obtained by calcining at 600 ° C. to 900 ° C., preferably 850 ° C. In addition, it is more preferable to repeat pulverizing, mixing, and firing the raw material once temporarily fired.
- the obtained raw material powder is pulverized to reduce the particle size.
- the pulverization method is not particularly limited as long as the powder can be refined.
- the pulverization method may be wet or dry using a pulverizer such as a planetary ball mill, pot mill, or bead mill.
- a pulverizer such as a planetary ball mill, pot mill, or bead mill.
- the obtained ground material in a rubber tube, it hydrostatically presses and shape
- the obtained rod-shaped molded body is fired at about 700 ° C. to 1300 ° C., preferably at 800 ° C. to 1150 ° C. for about 4 hours, to obtain a rod-shaped raw material.
- the chemical composition of the raw material is Li (7-xy) z La 3 Zr 2-xy Nb x Ta y O 12 (0.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, y ⁇ 0 1 ⁇ z ⁇ 2). In this way, a rod-shaped raw material can be manufactured.
- the rod-shaped raw material is melted in an infrared condensing heating furnace while rotating at a rotation speed of 30 rpm or more, and then rapidly cooled at a moving speed of 8 mm / h or more and 19 mm / h or less, whereby the relative density is 99% or more.
- Li 7-xy La 3 Zr 2-xy Ta x Nb y O 12 (0.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, y ⁇ 0) is produced.
- high density Li 7-xy La 3 Zr 2-xy Ta x Nb y O 12 (0.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, y ⁇ 0) crystal is produced by CZ method To do so, follow the procedure below. First, the raw material is put in a crucible and heated to melt. Next, the seed crystal is put on the raw material melt and pulled up while rotating.
- the garnet-related structural crystal of this embodiment has a chemical composition of Li (7-xy) z La 3 Zr 2 -xy Ta x Nb y O 12 (0.05 ⁇ x + y ⁇ 0.2, x ⁇ 0, y ⁇ 0, 1 ⁇ z ⁇ 2)
- the mixed powder (hereinafter sometimes referred to as “mother powder”) obtained by temporary firing is mixed into a green compact. After being molded into a compact, it can be manufactured by firing at 1000 ° C. or higher by applying a burying method in which the green compact is covered with a mother powder.
- Non-patent Document 2 Non-patent Document 3
- crystals with orthorhombic garnet-related structures or sintered bodies with orthorhombic garnet-related structures and cubic garnet-related structures can be obtained. It was.
- the garnet-related structural sintered body according to the embodiment of the present invention includes the garnet-related structural sintered body of the present embodiment and the chemical composition of Li 7-xy La 3 Zr 2-xy Ta x Nb y O. 12 (0.2 ⁇ x + y ⁇ 0.6, x ⁇ 0, y ⁇ 0), and a crystal having a cubic garnet-related structure.
- Zr: Nb: Ta in the raw material is adjusted to 2-xy: x: y (0.2 ⁇ x + y ⁇ 0.6, x ⁇ 0, y ⁇ 0). It is obtained by manufacturing a sintered body.
- This garnet-related structural sintered body is a mixture of two phases of an orthorhombic garnet-related structural crystal and a cubic garnet-related structural crystal.
- x + y 0.4
- a garnet-related structure sintered body with low activation energy and high lithium ion conductivity is obtained.
- the garnet-related structural crystal body and the garnet-related structural sintered body of this embodiment are excellent in lithium ion conductivity, they are also used in solid electrolytes of all solid lithium ion secondary batteries, lithium air batteries, and lithium sulfur batteries. Can be used. That is, the all-solid-state lithium ion secondary battery according to the embodiment of the present invention includes a positive electrode, a negative electrode, and a solid electrolyte material containing the garnet-related structural crystal or the garnet-related structural sintered body of the present embodiment. Have. When this solid electrolyte material is used for a lithium-air battery, it also functions as a separator for preventing the lithium metal used on the negative electrode side and the air present on the positive electrode side from coming into direct contact.
- the solid electrolyte material of the present embodiment is useful as a high-density solid electrolyte. Further, in the lithium-sulfur battery, sulfur used for the positive electrode during discharge is easily dissolved in the electrolytic solution, and thus a solid electrolyte having high ionic conductivity is required as in the case of the all-solid lithium ion secondary battery.
- Example 1 Production of Li 6.95 La 3 Zr 1.95 Nb 0.05 O 12 crystal by FZ method> (Mixing of raw materials) First, lithium carbonate Li 2 CO 3 (rare metallic, purity 99.99%) 7.972 g, lanthanum oxide La 2 O 3 (rare metallic, purity 99.99%) 12.620 g, zirconium oxide ZrO 2 6.22 g (rare metallic, purity 99.99%) 6.22 g and niobium oxide Nb 2 O 5 (rare metallic, purity 99.99%) 0.172 g are placed in an agate mortar and wet using ethanol To mix evenly. The lanthanum oxide used was pre-baked at 900 ° C. in advance.
- the metal molar ratio Li: La: Zr: Nb in this mixture is 20 mol% more lithium than the stoichiometric ratio of the target product Li 6.95 La 3 Zr 1.95 Nb 0.05 O 12. . That is, the chemical composition is an amount corresponding to Li 8.34 La 3 Zr 1.95 Nb 0.05 O 12 .
- a rod-shaped raw material was produced by the following procedure. First, a rubber mold was filled with 20.497 g of this powder and deaerated. Next, this mold was put in water in a sealed state and maintained at 40 MPa for 5 minutes. And after reducing the pressure of water, the molded object was taken out from the type
- the rod-shaped raw material obtained in the above process was installed in a four-elliptical infrared condensing heating furnace (FZ furnace) (Crystal System FZ-T-10000H type) equipped with a 1 kW halogen lamp. The atmosphere was dry air.
- FZ furnace Cirptical infrared condensing heating furnace
- the rod-shaped raw material was heated at an output of 25.9% while rotating at 40 rpm on a plane perpendicular to the longitudinal direction. After a while, a part of the raw material melted to form a melted part.
- sample 1 a high density Li 6.95 La 3 Zr 1.95 Nb 0.05 O 12 crystal
- sample 1 a high density Li 6.95 La 3 Zr 1.95 Nb 0.05 O 12 crystal
- FIG. 1 a high-density Li 6.95 La 3 Zr 1.95 Nb 0.05 O 12 crystal having a length of 5 cm could be produced.
- Sample 1 was cut with a diamond cutter to produce four thin pieces having a thickness of 0.1 mm, and their relative densities were calculated by the method described above. As a result, their relative densities were 99.8%, 99.2%, 100%, and 99.5%, respectively.
- FIG. 3 schematically shows the crystal structure of Sample 1.
- the garnet-related structural crystals reported so far are cubic or tetragonal, and the space groups showing the symmetry of the crystal structure are Ia-3d for cubic and I41 / acd for tetragonal. is there.
- It has one kind of oxygen ion seat (96h seat) and two kinds of lithium ion seats (24d seat, 96h seat).
- At least one cation seat selected from two kinds of lanthanum ion seats (8b seat, 16e seat), one kind of zirconium ion seat, niobium ion seat, and tantalum ion seat in the crystal structure.
- (16c seats) There are three types of oxygen ion seats (three types of 32g seats) and three types of lithium ion seats (8a seats, 16f seats, 32g seats).
- the sample 1 has an orthorhombic crystal system, a space group of Ibca, and three types of lanthanum ion seats (8c seat, 8d seat, 8e seat), two types of zirconium ion seats in the crystal structure, At least one of the niobium ion seat and the tantalum ion seat (8a seat, 8b seat), six oxygen ion seats (six types of 16f seats), four two types of lithium ion seats (three seats) 16f seats and one 8d seat).
- Li (x, y, z) is (0.0857, 0.1955, 0.0816), (0.1669, 0.5569, 0.1627), and (0 0.0689, 0.1288, 0.6811) and (0.25, 0.1270, 0). Since the R factor indicating the reliability of the crystal structure analysis was 1.76%, it can be said that the crystal structure analysis result is appropriate.
- the lattice constant of Sample 1 is 1.311 nm ⁇ a ⁇ 1.312 nm, 1.2676 nm ⁇ b ⁇ 1.25767 nm, 1.311 nm ⁇ b ⁇ 1.312 nm.
- Example 2 Production of Li 6.95 La 3 Zr 1.95 Ta 0.05 O 12 crystal by FZ method>
- the obtained crystal was a lithium composite oxide having the same orthorhombic garnet-related structure as in Example 1.
- FIG. 9 schematically shows the crystal structure of Sample 2. Since the R factor indicating the reliability of the crystal structure analysis was 4.09%, it can be said that the crystal structure analysis result is appropriate.
- the lattice constant of sample 1 is 1.310 nm ⁇ a ⁇ 1.311 nm, 1.268 nm ⁇ b ⁇ 1.274 nm, 1.309 nm ⁇ b. ⁇ 1.312 nm.
- Example 3 Production of Li 6.95 La 3 Zr 1.90 Ta 0.025 Nb 0.025 O 12 crystal by FZ method>
- a lithium-containing garnet crystal was manufactured and evaluated in the same manner as in Example 1 except that zirconium oxide ZrO 2 , tantalum oxide Ta 2 O 5 and niobium oxide Nb 2 O 5 were mixed.
- the obtained crystal was a lithium composite oxide having an orthorhombic garnet-related structure.
- a plate-shaped raw material was produced by the following procedure using this mixed powder that was passed through a sieve.
- 0.7532 g of this powder was filled in a tablet molding machine, and maintained at 60 MPa for 5 minutes with a hydraulic press. And the molded object was taken out from the type
- the molded body had a plate shape with a diameter of 1.30 cm and a height of 0.15 cm.
- the plate-like molded body was fired at 1200 ° C. for 4 hours.
- the taken-out sintered body (hereinafter sometimes referred to as “sample 3”) had a plate shape with a diameter of 1.20 cm and a height of 0.12 cm.
- the chemical composition of Sample 2 was Li 6.81 La 3 Zr 1.81 Ta 0.19 O 12 .
- the result of pulverizing Sample 3 and performing powder X-ray diffraction measurement is shown in FIG.
- the powder X-ray diffraction pattern of Sample 3 was different from the diffraction pattern of the solid electrolyte, which is a garnet-related structural crystal, reported so far.
- This also shows that Sample 3 is a crystal having a novel crystal structure.
- the lithium ion conductivity was 2.87 ⁇ 10 ⁇ 4 S / cm at 25 ° C. Further, by obtaining the ionic conductivity in the range from ⁇ 20 ° C. to 40 ° C., an Arrhenius plot as shown in FIG. 14 was obtained, and the activation energy was 0.44 eV.
- Example 5 Production of Li 6.6 La 3 Zr 1.60 Ta 0.40 O 12 sintered body by burying method>
- a sintered body hereinafter sometimes referred to as “sample 4” was prepared and evaluated in the same manner as in Example 3. From the powder X-ray diffraction pattern, Sample 4 was a sintered body having two phases of an orthorhombic garnet-related structure and a cubic garnet-related structure.
- the result of pulverizing Sample 4 and performing powder X-ray diffraction measurement is shown in FIG.
- the sintered body had a lithium ion conductivity of 7.5 ⁇ 10 ⁇ 4 S / cm at 25 ° C. Further, by obtaining the ionic conductivity in the range from ⁇ 20 ° C. to 40 ° C., an Arrhenius plot as shown in FIG. 16 is obtained, and the activation energy is 0.42 eV, and the high ionic conductivity and the low activation energy are obtained. It was a mixture that had both.
- Example 6 Production of Li 6.4 La 3 Zr 1.40 Ta 0.60 O 12 sintered body by burying method>
- a sintered body (hereinafter sometimes referred to as “sample 5”) was produced and evaluated in the same manner as in Example 4 except for the above points. From the powder X-ray diffraction pattern, Sample 5 was a sintered body having two phases of an orthorhombic garnet-related structure and a cubic garnet-related structure.
- Example 7 Production of Li 6.75 La 3 Zr 1.75 Nb 0.25 O 12 sintered body by burying method>
- a sintered body hereinafter sometimes referred to as “sample 6” was prepared and evaluated in the same manner as in Example 3. From the powder X-ray diffraction pattern, Sample 6 was a sintered body having two phases of an orthorhombic garnet-related structure and a cubic garnet-related structure.
- the result of pulverizing Sample 6 and performing powder X-ray diffraction measurement is shown in FIG.
- the powder X-ray diffraction pattern of Sample 6 was different from the diffraction pattern of the solid electrolyte, which is a garnet-related structural crystal, reported so far. This also indicates that Sample 5 is a crystal having a new crystal structure.
- As a result of detailed powder X-ray structural analysis it was found that most of them were orthorhombic garnet-related structures, and a small amount of cubic garnet-related structures were mixed.
- orthorhombic 97: 3.
- the sintered body had a lithium ion conductivity of 3.6 ⁇ 10 ⁇ 4 S / cm at 25 ° C. Further, by obtaining the ionic conductivity in the range from ⁇ 20 ° C. to 40 ° C., an Arrhenius plot as shown in FIG. 20 is obtained, the activation energy is 0.41 eV, and the high ionic conductivity and the low activation energy are obtained. It was a mixture that had both.
- Example 8 Production of all solid lithium ion secondary battery> 0.0105 mol of lithium acetate dihydrate (manufactured by Sigma Aldrich) and 0.01 mol of cobalt acetate tetrahydrate (manufactured by Wako Pure Chemical Industries) were dissolved in 100 g of ethylene glycol (manufactured by Wako Pure Chemical Industries). Next, 10 mol of polyvinyl pyrrolidone (manufactured by Wako Pure Chemical Industries, K-30) was added and dissolved to prepare a 0.1 mol / kg lithium cobaltate precursor solution. The reason why the amount of lithium acetate was increased by 5 mol% from the amount of cobalt acetate is that the amount of lithium evaporated during firing was taken into account.
- sample 1 was cut to produce a thin piece having a diameter of about 0.8 cm and a thickness of about 0.10 cm.
- 10 ⁇ L of the precursor solution was dropped onto the flakes and calcined at 400 ° C. for 20 minutes, and then calcined at 850 ° C. for 10 minutes to form lithium cobaltate as a positive electrode on the surface of the sample 1 (hereinafter referred to as “sample”).
- sample 7 In a glove box, a sample 7 and metallic lithium punched into a circle having a diameter of 4 mm are placed in a commercially available HS cell for battery evaluation (made by Hosen Co., Ltd.) as shown in FIG. A secondary battery was produced. This all solid lithium ion secondary battery exhibited an open circuit voltage of 2.53 V, confirming that it functions as a battery.
- the sintered body is an all solid lithium ion secondary battery. It can be used as a solid electrolyte material for lithium-air batteries, lithium-sulfur batteries, separators, and the like.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Organic Chemistry (AREA)
- Inorganic Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Materials Engineering (AREA)
- General Chemical & Material Sciences (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Crystallography & Structural Chemistry (AREA)
- Metallurgy (AREA)
- Electrochemistry (AREA)
- Ceramic Engineering (AREA)
- Physics & Mathematics (AREA)
- Condensed Matter Physics & Semiconductors (AREA)
- General Physics & Mathematics (AREA)
- Structural Engineering (AREA)
- Composite Materials (AREA)
- Thermal Sciences (AREA)
- Secondary Cells (AREA)
- Conductive Materials (AREA)
- Inorganic Compounds Of Heavy Metals (AREA)
- Crystals, And After-Treatments Of Crystals (AREA)
Abstract
Description
(原料の混合)
まず、炭酸リチウムLi2CO3(レアメタリック製、純度99.99%)7.972gと、酸化ランタンLa2O3(レアメタリック製、純度99.99%)12.620gと、酸化ジルコニウムZrO2(レアメタリック製、純度99.99%)6.22gと、酸化ニオブNb2O5(レアメタリック製、純度99.99%)0.172gをメノウ製乳鉢に入れて、エタノールを使用した湿式法によって均一に混合した。なお、酸化ランタンは、あらかじめ900℃で仮焼成したものを使用した。この混合物の金属のモル比Li:La:Zr:Nbは、目的物であるLi6.95La3Zr1.95Nb0.05O12の化学量論比よりもリチウムが20mol%過剰である。すなわち、化学組成がLi8.34La3Zr1.95Nb0.05O12に相当する分量である。
上記工程でふるいを通過した粉末を用いて、以下の手順で棒形状の原料を作製した。まず、ゴム製の型にこの粉末20.497gを充填して脱気した。つぎに、この型を密閉した状態で水中に入れて、40MPaで5分間維持した。そして、水の圧力を下げた後、成形体を型から取り出した。成形体は、直径1.0cm、高さ9.6cmの円柱形状をしていた。つぎに、箱型電気炉(デンケン製、型番KDF009)を用いて、この円柱状の成形体を1150℃で焼成した。取り出した成形体は、直径0.94cm、高さ9.2cmの円柱形状をしていた。
まず、1kWのハロゲンランプを装備した四楕円型赤外線集光加熱炉(FZ炉)(Crystal System社製、FZ-T-10000H型)に、上記工程で得られた棒形状の原料を設置して、乾燥空気雰囲気にした。つぎに、棒形状の原料を長手方向と垂直な面で40rpmで回転させながら、出力25.9%で加熱した。しばらくすると、原料の一部が溶融して溶融部を形成した。そして、棒形状の原料の設置台を10mm/hの移動速度で下降させて高密度のLi6.95La3Zr1.95Nb0.05O12結晶体(以下「試料1」ということがある)を育成した。なお、試料1の化学組成はX線結晶構造解析によって分析した。試料1の外観を図1に示す。図1に示すように、長さ5cmの高密度のLi6.95La3Zr1.95Nb0.05O12結晶体が作製できた。
二次元IP検出器および検出器にシンチレーションカウンターを有する単結晶X線回折装置(リガク社製、R-AXIS RAPID-II)を用いて、試料1の構造を調べた。試料1のX線回折パターンを図2に示す。図2に示すように、明瞭な回折点が測定できた。また、試料1の回折強度データを収集し、結晶構造解析プログラムJana2006によって結晶構造を調べたところ、試料1が斜方晶に属することがわかった。試料1をダイヤモンドカッターで切断して厚さ0.1mmの薄片を4枚作製し、上述の方法でこれらの相対密度を算出した。その結果、これらの相対密度はそれぞれ99.8%、99.2%、100%、99.5%であった。
金属のモル比Li:La:Ta:Zrが8.3:3.0:0.05:1.95となるように、すなわち原料のLi(7-x)zLa3Zr2-xTaxO12がx=0.05、z=1.2となるように、炭酸リチウムLi2CO3と、酸化ランタンLa2O3と、酸化ジルコニウムZrO2と、酸化タンタルTa2O5を混合した点を除いて、実施例1と同様にしてリチウム含有ガーネット結晶体を製造し、評価した。試料2の外観を図7に示す。また試料2のX線回折パターンを図8に示す。図8に示すように、明瞭な回折点が測定できた。得られた結晶体は、実施例1と同じ、新規斜方晶ガーネット関連型構造を有するリチウム複合酸化物であった。この結晶体の格子定数a=1.31073nm±0.0006nm、b=1.26803nm±0.0006nm、c=1.30982nm±0.0008nmであり、化学組成はLi6.92La3Zr1.952Ta0.048O12であった。図9は試料2の結晶構造を模式的に示している。この結晶構造解析の信頼度を示すR因子は4.09%であったため、結晶構造解析結果は妥当であると言える。
金属のモル比Li:La:Ta:Nb:Zrが8.3:3.0:0.025:0.025:1.95となるように、すなわち原料のLi(7-x+y)zLa3Zr2-x―yTaxNbyO12がx=0.025、y=0.025、z=1.2となるように、炭酸リチウムLi2CO3と、酸化ランタンLa2O3と、酸化ジルコニウムZrO2と、酸化タンタルTa2O5と、酸化ニオブNb2O5を混合した点を除いて、実施例1と同様にしてリチウム含有ガーネット結晶体を製造し、評価した。得られた結晶体は、斜方晶ガーネット関連型構造を有するリチウム複合酸化物であった。この結晶体の格子定数a=1.31091nm±0.0004nm、b=1.26763nm±0.0003nm、c=1.31082nm±0.0008nmであり、化学組成はLi6.91La3Zr1.953Ta0.022Nb0.025O12であった。この結晶構造解析の信頼度を示すR因子は2.11%であったため、結晶構造解析結果は妥当であると言える。
金属のモル比Li:La:Ta:Zrが10.2:3.0:0.20:1.8となるように、すなわち原料のLi(7-x)zLa3Zr2-xTaxO12がx=0.20、z=1.5となるように、炭酸リチウムLi2CO3と、酸化ランタンLa2O3と、酸化ジルコニウムZrO2と、酸化タンタルTa2O5を混合した点を除いて、実施例1の原料の混合と同様にして混合粉末を調製した。
金属のモル比Li:La:Zr:Taが9.9:3.0:1.60:0.40となるように、すなわち原料のLi(7-x)zLa3Zr2-xTaxO12がx=0.40、z=1.5となるように、炭酸リチウムLi2CO3と、酸化ランタンLa2O3と、酸化ジルコニウムZrO2と、酸化タンタルTa2O5を混合した点を除いて、実施例3と同様に焼結体(以下「試料4」ということがある)を作製し評価した。粉末X線回折パターンから、試料4は、斜方晶ガーネット関連型構造と立方晶ガーネット関連型構造の二相からなる焼結体であった。
金属のモル比Li:La:Zr:Taが9.6:3.0:1.40:0.60となるように、すなわち原料のLi(7-x)zLa3Zr2-xTaxO12がx=0.60、z=1.5となるように、炭酸リチウムLi2CO3と、酸化ランタンLa2O3と、酸化ジルコニウムZrO2と、酸化タンタルTa2O5を混合した点を除いて、実施例4と同様にして焼結体(以下「試料5」ということがある)を作製し評価した。粉末X線回折パターンから、試料5は、斜方晶ガーネット関連型構造と立方晶ガーネット関連型構造の二相からなる焼結体であった。
金属のモル比Li:La:Zr:Nbが10.125:3.0:1.75:0.25となるように、すなわち原料のLi(7-x)zLa3Zr2-xNbxO12がx=0.25、z=1.5となるように、炭酸リチウムLi2CO3と、酸化ランタンLa2O3と、酸化ジルコニウムZrO2と、酸化ニオブNb2O5を混合した点を除いて、実施例3と同様に焼結体(以下「試料6」ということがある)を作製し評価した。粉末X線回折パターンから、試料6は、斜方晶ガーネット関連型構造と立方晶ガーネット関連型構造の二相からなる焼結体であった。
酢酸リチウム2水和物(シグマアルドリッチ製)0.0105モルと、酢酸コバルト4水和物(和光純薬工業製)0.01モルを、エチレングリコール(和光純薬工業製)100gに溶解した。つぎに、ポリビニルピロリドン(和光純薬工業製、K-30)10gを加えて溶解させることで0.1モル/kgのコバルト酸リチウム前駆体溶液を調製した。酢酸リチウム量を酢酸コバルト量より5モル%多くしたのは、焼成時のリチウム蒸発分を加味したためである。
Claims (10)
- 化学組成がLi7―x―yLa3Zr2―x―yTaxNbyO12(0.05≦x+y≦0.2、x≧0、y≧0)で表され、結晶構造が斜方晶系であるガーネット関連型構造結晶体。
- 結晶構造の対称性を示す空間群がIbcaに属する請求項1に記載のガーネット関連型構造結晶体。
- 結晶構造の格子定数a、b、c、が、それぞれ1.29nm≦a≦1.32nm、1.26nm≦b≦1.29nm、1.29nm≦c≦1.32nmである請求項1または2に記載のガーネット関連型構造結晶体。
- 結晶構造中に4つ以上のリチウムイオンが占有する席が存在する請求項1から3のいずれかに記載のガーネット関連型構造結晶体。
- リチウムイオン伝導率が、25℃で1.0×10-4S/cm以上である請求項1から4のいずれかに記載のガーネット関連型構造結晶体。
- 相対密度が99%以上である請求項1から5のいずれかに記載のガーネット関連型構造結晶体。
- 前記相対密度が100%である請求項6に記載のガーネット関連型構造結晶体。
- 請求項1から7のいずれかに記載の結晶体と、化学組成がLi7―x―yLa3Zr2―x―yTaxNbyO12(0.2<x+y≦0.6、x≧0、y≧0)で表され、立方晶ガーネット関連型構造を有する結晶体とを含有するガーネット関連型構造焼結体。
- 正極と、負極と、請求項1から7のいずれかに記載の結晶体または請求項8に記載の焼結体を含有する固体電解質材料とを有する全固体リチウムイオン二次電池。
- 化学組成がLi(7―x―y)zLa3Zr2―x―yTaxNbyO12(0.05≦x+y≦0.2、x≧0、y≧0、1<z≦2)で表される原料の少なくとも一部を溶融して結晶成長させる溶融部を形成し、移動速度8mm/h以上で前記結晶成長させる溶融部を未結晶化原料へ移動して結晶成長させ、化学組成がLi7―x―yLa3Zr2―x―yTaxNbyO12(0.05≦x+y≦0.2、x≧0、y≧0)で表され、斜方晶系に属するガーネット関連型構造結晶体の製造方法。
Priority Applications (5)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US16/304,231 US10763544B1 (en) | 2016-05-26 | 2017-05-02 | Solid electrolyte with low-symmetry garnet-related structure and lithium-ion secondary battery |
KR1020187034916A KR102137801B1 (ko) | 2016-05-26 | 2017-05-02 | 저대칭 가닛 관련형 구조 고체 전해질 및 리튬 이온 이차 전지 |
CN201780032600.8A CN109195918B (zh) | 2016-05-26 | 2017-05-02 | 低对称石榴子石关联型结构固体电解质以及锂离子二次电池 |
EP17802551.6A EP3466888B1 (en) | 2016-05-26 | 2017-05-02 | Lowly symmetric garnet-related structured solid electrolyte and lithium secondary battery |
JP2018519168A JP6667182B2 (ja) | 2016-05-26 | 2017-05-02 | 低対称ガーネット関連型構造固体電解質およびリチウムイオン二次電池 |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2016-104874 | 2016-05-26 | ||
JP2016104874 | 2016-05-26 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2017203954A1 true WO2017203954A1 (ja) | 2017-11-30 |
Family
ID=60412761
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2017/017233 WO2017203954A1 (ja) | 2016-05-26 | 2017-05-02 | 低対称ガーネット関連型構造固体電解質およびリチウムイオン二次電池 |
Country Status (7)
Country | Link |
---|---|
US (1) | US10763544B1 (ja) |
EP (1) | EP3466888B1 (ja) |
JP (1) | JP6667182B2 (ja) |
KR (1) | KR102137801B1 (ja) |
CN (1) | CN109195918B (ja) |
TW (1) | TWI623496B (ja) |
WO (1) | WO2017203954A1 (ja) |
Cited By (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2020174785A1 (ja) * | 2019-02-26 | 2020-09-03 | セイコーエプソン株式会社 | 固体電解質の前駆体組成物、二次電池の製造方法 |
WO2020183805A1 (ja) * | 2019-03-14 | 2020-09-17 | セイコーエプソン株式会社 | 固体電解質の前駆体溶液 |
WO2020189705A1 (ja) * | 2019-03-21 | 2020-09-24 | アダマンド並木精密宝石株式会社 | リチウム含有酸化物結晶、電池およびリチウム含有酸化物結晶の製造方法 |
JP7495743B2 (ja) | 2018-12-28 | 2024-06-05 | キュイ、イ | 低純度供給源からの高純度リチウムの電解製造 |
Families Citing this family (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US20220077459A1 (en) * | 2018-12-28 | 2022-03-10 | Yi Cui | High energy density molten lithium-sulfur and lithium-selenium batteries with solid electrolyte |
EP3902941A4 (en) * | 2018-12-28 | 2022-11-23 | Yi Cui | ELECTROLYTIC PRODUCTION OF HIGH PURITY LITHIUM FROM LOW PURITY SOURCES |
JP2021138571A (ja) * | 2020-03-05 | 2021-09-16 | セイコーエプソン株式会社 | 固体組成物の製造方法および固体電解質の製造方法 |
FR3112431B1 (fr) * | 2020-07-09 | 2024-04-19 | Saint Gobain Ct Recherches | Membrane en un produit polycristallin de llzo |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2016068040A1 (ja) * | 2014-10-27 | 2016-05-06 | 国立研究開発法人産業技術総合研究所 | リチウム含有ガーネット結晶体および全固体リチウムイオン二次電池 |
JP2016072210A (ja) * | 2014-09-30 | 2016-05-09 | セイコーエプソン株式会社 | 耐リチウム還元層形成用組成物、耐リチウム還元層の成膜方法およびリチウム二次電池 |
Family Cites Families (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP5649033B2 (ja) | 2010-03-19 | 2015-01-07 | 独立行政法人産業技術総合研究所 | リチウムイオン伝導性酸化物及びその製造方法、並びにそれを部材として使用した電気化学デバイス |
KR101596947B1 (ko) * | 2014-04-30 | 2016-02-25 | 한국전기연구원 | 리튬 이차전지용 리튬 산화물-고분자 복합 전해질 및 그를 포함하는 이차전지 |
JP6524089B2 (ja) * | 2014-07-31 | 2019-06-05 | 国立研究開発法人産業技術総合研究所 | リチウム含有ガーネット単結晶体の製造方法 |
US20160093915A1 (en) * | 2014-09-30 | 2016-03-31 | Seiko Epson Corporation | Composition for forming lithium reduction resistant layer, method for forming lithium reduction resistant layer, and lithium secondary battery |
-
2017
- 2017-05-02 EP EP17802551.6A patent/EP3466888B1/en active Active
- 2017-05-02 JP JP2018519168A patent/JP6667182B2/ja active Active
- 2017-05-02 CN CN201780032600.8A patent/CN109195918B/zh active Active
- 2017-05-02 TW TW106114545A patent/TWI623496B/zh active
- 2017-05-02 KR KR1020187034916A patent/KR102137801B1/ko active IP Right Grant
- 2017-05-02 WO PCT/JP2017/017233 patent/WO2017203954A1/ja unknown
- 2017-05-02 US US16/304,231 patent/US10763544B1/en active Active
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2016072210A (ja) * | 2014-09-30 | 2016-05-09 | セイコーエプソン株式会社 | 耐リチウム還元層形成用組成物、耐リチウム還元層の成膜方法およびリチウム二次電池 |
WO2016068040A1 (ja) * | 2014-10-27 | 2016-05-06 | 国立研究開発法人産業技術総合研究所 | リチウム含有ガーネット結晶体および全固体リチウムイオン二次電池 |
Non-Patent Citations (1)
Title |
---|
WANG, YUXING ET AL.: "High Ionic Conductivity Lithium Garnet Oxides of Li7-xLa3Zr2-xTaxO12 Compositions", ELECTROCHEMICAL AND SOLID-STATE LETTERS, vol. 15, no. 5, 29 February 2012 (2012-02-29), pages A68 - A71, XP055203215, DOI: doi:10.1149/2.024205esl * |
Cited By (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP7495743B2 (ja) | 2018-12-28 | 2024-06-05 | キュイ、イ | 低純度供給源からの高純度リチウムの電解製造 |
WO2020174785A1 (ja) * | 2019-02-26 | 2020-09-03 | セイコーエプソン株式会社 | 固体電解質の前駆体組成物、二次電池の製造方法 |
JPWO2020174785A1 (ja) * | 2019-02-26 | 2021-11-04 | セイコーエプソン株式会社 | 固体電解質の前駆体組成物、二次電池の製造方法 |
JP7115626B2 (ja) | 2019-02-26 | 2022-08-09 | セイコーエプソン株式会社 | 固体電解質の前駆体組成物、二次電池の製造方法 |
WO2020183805A1 (ja) * | 2019-03-14 | 2020-09-17 | セイコーエプソン株式会社 | 固体電解質の前駆体溶液 |
JPWO2020183805A1 (ja) * | 2019-03-14 | 2021-12-02 | セイコーエプソン株式会社 | 固体電解質の前駆体溶液 |
WO2020189705A1 (ja) * | 2019-03-21 | 2020-09-24 | アダマンド並木精密宝石株式会社 | リチウム含有酸化物結晶、電池およびリチウム含有酸化物結晶の製造方法 |
Also Published As
Publication number | Publication date |
---|---|
KR102137801B1 (ko) | 2020-07-24 |
EP3466888B1 (en) | 2020-09-23 |
CN109195918B (zh) | 2020-12-08 |
US20200274193A1 (en) | 2020-08-27 |
US10763544B1 (en) | 2020-09-01 |
KR20190002660A (ko) | 2019-01-08 |
EP3466888A4 (en) | 2020-01-29 |
TWI623496B (zh) | 2018-05-11 |
JP6667182B2 (ja) | 2020-03-18 |
CN109195918A (zh) | 2019-01-11 |
TW201741243A (zh) | 2017-12-01 |
EP3466888A1 (en) | 2019-04-10 |
JPWO2017203954A1 (ja) | 2019-03-14 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP6278433B2 (ja) | リチウム含有ガーネット結晶体および全固体リチウムイオン二次電池 | |
WO2017203954A1 (ja) | 低対称ガーネット関連型構造固体電解質およびリチウムイオン二次電池 | |
JP6120346B2 (ja) | リチウム含有ガーネット結晶体および全固体リチウムイオン二次電池 | |
KR101969657B1 (ko) | 리튬 함유 가닛 결정체, 그의 제조 방법 및 전고체 리튬 이온 이차 전지 | |
US20200303771A1 (en) | Lithium ion conductive crystal body and all-solid state lithium ion secondary battery | |
WO2021053923A1 (ja) | ガリウム置換型固体電解質材料および全固体リチウムイオン二次電池 | |
JP7442878B2 (ja) | 新規結晶構造を備える複合酸化物と、この複合酸化物を固体電解質とする全固体リチウムイオン二次電池 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
ENP | Entry into the national phase |
Ref document number: 2018519168 Country of ref document: JP Kind code of ref document: A |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 17802551 Country of ref document: EP Kind code of ref document: A1 |
|
ENP | Entry into the national phase |
Ref document number: 20187034916 Country of ref document: KR Kind code of ref document: A |
|
ENP | Entry into the national phase |
Ref document number: 2017802551 Country of ref document: EP Effective date: 20190102 |