WO2014020654A1 - All-solid ion secondary cell - Google Patents

All-solid ion secondary cell Download PDF

Info

Publication number
WO2014020654A1
WO2014020654A1 PCT/JP2012/069284 JP2012069284W WO2014020654A1 WO 2014020654 A1 WO2014020654 A1 WO 2014020654A1 JP 2012069284 W JP2012069284 W JP 2012069284W WO 2014020654 A1 WO2014020654 A1 WO 2014020654A1
Authority
WO
WIPO (PCT)
Prior art keywords
active material
solid electrolyte
electrode active
negative electrode
positive electrode
Prior art date
Application number
PCT/JP2012/069284
Other languages
French (fr)
Japanese (ja)
Inventor
正 藤枝
拓也 青柳
内藤　孝
純 川治
尚貴 木村
良幸 高森
心 高橋
Original Assignee
株式会社 日立製作所
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 株式会社 日立製作所 filed Critical 株式会社 日立製作所
Priority to PCT/JP2012/069284 priority Critical patent/WO2014020654A1/en
Priority to JP2014527829A priority patent/JPWO2014020654A1/en
Publication of WO2014020654A1 publication Critical patent/WO2014020654A1/en

Links

Images

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
    • H01M4/13—Electrodes for accumulators with non-aqueous electrolyte, e.g. for lithium-accumulators; Processes of manufacture thereof
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M10/00—Secondary cells; Manufacture thereof
    • H01M10/05—Accumulators with non-aqueous electrolyte
    • H01M10/052—Li-accumulators
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M10/00—Secondary cells; Manufacture thereof
    • H01M10/05—Accumulators with non-aqueous electrolyte
    • H01M10/056—Accumulators with non-aqueous electrolyte characterised by the materials used as electrolytes, e.g. mixed inorganic/organic electrolytes
    • H01M10/0561—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
    • 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
    • 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 all solid ion secondary battery.
  • the contact area between the active material particles and the solid electrolyte particles is small and the ion conduction resistance between the two is large, sufficient output density and energy density cannot be obtained.
  • the positive electrode active material and the solid electrolyte are hardly sinterable ceramics, and it is difficult to completely sinter them at a low temperature where they do not react.
  • Patent Document 1 in order to increase the contact area between the active material particles and the solid electrolyte, a unipolar electrode composed of a porous structure of the active material particles and the particle binding material, and voids of the porous structure are disclosed.
  • a solid electrolyte battery having a solid electrolyte layer made of an ion conductive material deposited on the surface of the part, another active material filled in the void of the porous structure, and another polar side electrode made of the filled material It is disclosed.
  • An object of the present invention is to improve the energy density and output density of an all-solid ion secondary battery.
  • the present invention is characterized in that in the all-solid-state ion secondary battery in which a solid electrolyte layer is bonded between a positive electrode active material layer and a negative electrode active material layer, the positive electrode active material layer includes a positive electrode
  • the active material particles and the solid electrolyte particles are formed by binding with vanadium oxide glass having ion conductivity
  • the negative electrode active material layer is formed by vanadium oxidation in which the negative electrode active material particles and the solid electrolyte particles have ion conductivity. This is because it is formed by binding with glass.
  • the energy density of the all solid state ion secondary battery can be improved.
  • Example 1 Sectional drawing of the positive electrode / solid electrolyte layer / negative electrode laminated body in Example 1 Sectional drawing of the positive electrode / vanadium oxide glass layer / negative electrode laminated body in Example 3 Sectional drawing of the positive electrode / solid electrolyte layer / negative electrode laminated body in Example 4
  • the positive electrode active material layer is formed by mixing the positive electrode active material particles and the solid electrolyte particles and then binding the both with the vanadium oxide glass.
  • the negative electrode active material layer the negative electrode active material particles and the solid electrolyte particles are bound by vanadium oxide glass.
  • Ions move between the active material particles and the vanadium oxide glass using the surface of the active material particles in contact with the vanadium oxide glass as an ion conduction path. Further, ions move between the vanadium oxide glass and the solid electrolyte particles using the surface of the solid electrolyte particles in contact with the vanadium oxide glass as an ion conduction path. Thereby, a sufficient ion conduction path can be secured between the active material particles and the solid electrolyte particles, and the ion conductivity can be improved. Further, since vanadium oxide glass softens and flows at a low temperature of 500 ° C. or less so that the active material particles and the solid electrolyte particles do not react, a dense sintered body can be easily formed.
  • FIG. 1 shows a cross-sectional view of a main part of an all solid state ion secondary battery according to a first embodiment of the present invention.
  • a positive electrode active material layer 107 formed on the positive electrode current collector 101 and a negative electrode active material layer 109 formed on the negative electrode current collector 106 are joined via a solid electrolyte layer 108.
  • the positive electrode active material layer and the negative electrode active material layer are completely electrically insulated by a solid electrolyte layer.
  • a conductive support agent in order to improve the electroconductivity in the active material layer of each electrode.
  • the conductive auxiliary agent can be omitted.
  • Conductive aids include carbon materials such as graphite, acetylene black, ketjen black, metal powders such as gold, silver, copper, nickel, aluminum, titanium, indium / tin oxide (ITO), titanium oxide, tin oxide And conductive oxides such as zinc oxide and tungsten oxide are preferred.
  • the vanadium oxide glass contains vanadium and at least one of tellurium and phosphorus which are vitrification components. In addition, water resistance can be remarkably improved by adding iron or tungsten. In order to prevent the reaction between the active material particles and the solid electrolyte particles, the softening point of the vanadium oxide glass is preferably 500 ° C. or lower.
  • the amount of vanadium oxide glass added to the active material or solid electrolyte is preferably 10% by volume or more and 40% by volume or less in terms of volume.
  • the volume is 5% by volume or more, the space between the active material particles and the solid electrolyte particles can be sufficiently filled.
  • the volume is 40% by volume or less, the charge / discharge capacity and the charge / discharge rate associated with the decrease in the amount of the active material and the solid electrolytic mass are reduced. Decline can be prevented.
  • the vanadium oxide glass in the positive and negative electrode active material layers.
  • the solid electrolyte layer is formed by binding the solid electrolyte particles with glass, it is necessary to ensure electrical insulation, so the vanadium oxide glass must be amorphous. For this reason, it is effective to apply different types of vanadium oxide glasses to the positive electrode active material layer, the negative electrode active material layer, and the solid electrolyte layer.
  • the positive electrode active material layer and the negative electrode active material layer contain a crystallization component such as lithium or copper, apply a glass that crystallizes after softening, and are a vitrification component to the solid electrolyte layer.
  • the positive electrode active material a known positive electrode active material capable of occluding and releasing lithium ions can be used.
  • a known positive electrode active material capable of occluding and releasing lithium ions can be used.
  • spinel system, olivine system, layered oxide system, solid solution system, silicate system and the like can be mentioned.
  • Vanadium oxide glass can be used as the positive electrode active material, and ionic conductivity and electronic conductivity can be improved by crystallizing at least a part of the glass.
  • a known negative electrode active material capable of occluding and releasing lithium ions can be used.
  • a carbon material typified by graphite an alloy material such as a TiSn alloy or a TiSi alloy, a nitride such as LiCoN, or an oxide such as Li 4 Ti 5 O 12 or LiTiO 4 can be used.
  • Vanadium oxide glass can be used as the negative electrode active material, and ionic conductivity and electronic conductivity can be improved by crystallizing at least a part of the glass.
  • the solid electrolyte is not particularly limited as long as it is a solid and a reforming material that conducts lithium ions, but an incombustible inorganic solid electrolyte is preferable from the viewpoint of safety.
  • lithium halides such as LiCl and LiI
  • sulfide glasses represented by Li 2 S—SiS 2 , Li 3 PO 4 —Li 2 S—SiS 2 , Li 1.4 Al 0.4 Ti 1.6 (PO 4 ) 3
  • An oxide glass typified by Li 3.4 V 0.6 Si 0.4 O 4 , Li 2 P 2 O 6 or the like, or a perovskite oxide typified by Li 0.34 La 0.51 TiO 2.94 or the like can be used.
  • the said ion conductive vanadium oxide glass can also be used as a solid electrolyte.
  • the said ion conductive vanadium oxide glass can also be used as a solid electrolyte.
  • the said oxide-type material about a solid electrolyte.
  • vanadium oxide glass Two types of ion-conductive vanadium oxide glasses having different softening points were produced.
  • raw materials vanadium pentoxide (V 2 O 5 ), phosphorus pentoxide (P 2 O 5 ), tellurium dioxide (TeO 2 ) powder, and ferric oxide (Fe 2 O 3 ) were used.
  • V 2 O 5 vanadium pentoxide
  • P 2 O 5 phosphorus pentoxide
  • TeO 2 tellurium dioxide
  • Fe 2 O 3 ferric oxide
  • These raw material powders were put into a platinum crucible and heated and held at 1100 ° C. for 1 hour using an electric furnace. During heating, stirring was performed so that the raw materials in the platinum crucible were uniform. Thereafter, the platinum crucible was taken out from the electric furnace, poured onto a stainless steel plate heated to 150 ° C. in advance, and naturally cooled to obtain vanadium oxide glass.
  • the softening points of Glass A and Glass B measured by differential thermal analysis were 356 ° C. and 345 ° C., respectively. Further, the produced glass was mechanically pulverized so that the average particle size was about 3 ⁇ m.
  • LATP solid electrolyte
  • ethyl cellulose or nitrocellulose was used as the resin binder, and butyl carbitol acetate was used as the solvent.
  • This positive electrode paste was applied to an aluminum foil having a thickness of 20 ⁇ m, and after heat treatment for removing the solvent and removing the binder, the positive electrode paste was fired at 360 ° C. ⁇ 1 hr in the atmosphere to obtain a positive electrode sheet having a positive electrode active material layer thickness of 10 ⁇ m. This was punched out into a disk shape having a diameter of 14 mm to obtain a positive electrode.
  • This negative electrode paste was applied to an aluminum foil having a thickness of 20 ⁇ m, and after heat treatment for removing the solvent and removing the binder, the negative electrode paste was fired in the atmosphere at 360 ° C. ⁇ 1 hr to obtain a negative electrode sheet having a negative electrode active material layer thickness of 10 ⁇ m. This was punched out into a disk shape having a diameter of 14 mm to obtain a negative electrode.
  • the vanadium oxide glass used for the positive electrode active material layer and the vanadium oxide glass used for the negative electrode active material layer are the same, but both are the same as long as the vanadium oxide glass has ion conductivity. It does not have to be of composition. The same applies to the following embodiments.
  • ⁇ Solid electrolyte layer> LATP with an average particle diameter of 3 ⁇ m, which is a solid electrolyte, and the prepared glass B powder were prepared so that the volume ratio was 70:30, and a proper amount of resin binder and solvent was added to the mixed powder to obtain a solid.
  • An electrolyte paste was prepared. After applying this solid electrolyte paste to either the positive electrode layer or the negative electrode layer, and after heat treatment for removing the solvent and removing the binder, the temperature is higher than the softening point of the glass B, 350 ° C. ⁇ 1 hr. Firing was performed in the air to form a solid electrolyte layer having a thickness of 15 ⁇ m. This was punched into a disk shape having a diameter of 15 mm.
  • the solid electrolyte layer is not limited to a solid electrolyte layer formed of a particulate solid electrolyte as in the present embodiment as long as it allows ions to pass therethrough and does not pass electrons. The same applies to the following embodiments.
  • the mixed powder is allowed to collide with the base material in a solid state in supersonic flow with an inert gas without melting or gasifying.
  • AD aerosol deposition method for forming a film by spraying an aerosol obtained by mixing a mixed powder with a gas through a nozzle to the substrate through a nozzle.
  • CS Cold spray
  • AD aerosol deposition
  • a battery manufacturing method by the CS method will be described below.
  • a mixed powder of the same LiCoO 2 powder, glass A powder, LATP powder, and conductive titanium oxide was sprayed onto an aluminum foil having a thickness of 20 ⁇ m to form a positive electrode active material layer having a thickness of 10 ⁇ m.
  • Each powder may be put into a separate feeder and sprayed at the same time.
  • a mixed powder of the same LATP powder and the produced glass A powder or glass B powder was sprayed onto the positive electrode active material layer to form a solid electrolyte layer having a thickness of 15 ⁇ m.
  • the platinum crucible was taken out from the electric furnace, poured onto a stainless steel plate heated to 150 ° C. in advance, and naturally cooled to obtain vanadium oxide glass.
  • the softening point of glass C measured by differential thermal analysis was 390 ° C., and the crystallization start temperature was 434 ° C. Further, the produced glass was mechanically pulverized so that the average particle size was about 3 ⁇ m.
  • ethyl cellulose or nitrocellulose was used as the resin binder, and butyl carbitol acetate was used as the solvent.
  • This positive electrode paste is applied to an aluminum foil having a thickness of 20 ⁇ m, heat-treated for removal of the solvent and binder, fired at 400 ° C. ⁇ 1 hr in the atmosphere, and further subjected to heat treatment at 430 ° C. ⁇ 0.5 hr.
  • a positive electrode sheet having a positive electrode active material layer thickness of 10 ⁇ m was obtained.
  • the vanadium oxide glass may be crystallized only partially or entirely. This was punched out into a disk shape having a diameter of 14 mm to obtain a positive electrode.
  • This negative electrode paste is applied to an aluminum foil having a thickness of 20 ⁇ m, heat-treated for removal of the solvent and binder, fired at 400 ° C. ⁇ 1 hr in the air, and further subjected to heat treatment at 430 ° C. ⁇ 0.5 hr to produce crystals.
  • a negative electrode sheet having a negative electrode active material layer thickness of 10 ⁇ m was obtained. This was punched out into a disk shape having a diameter of 14 mm to obtain a negative electrode.
  • ⁇ Solid electrolyte layer> LATP with an average particle diameter of 3 ⁇ m, which is a solid electrolyte, and the prepared glass B powder were prepared so that the volume ratio was 70:30, and a proper amount of resin binder and solvent was added to the mixed powder to obtain a solid.
  • An electrolyte paste was prepared. After applying this solid electrolyte paste to either the positive electrode layer or the negative electrode layer, and after heat treatment for removing the solvent and removing the binder, the temperature is higher than the softening point of the glass B, 350 ° C. ⁇ 1 hr. Firing was performed in the air to form a solid electrolyte layer having a thickness of 15 ⁇ m. This was punched into a disk shape having a diameter of 14 mm.
  • This positive electrode paste was applied to an aluminum foil having a thickness of 20 ⁇ m, and after heat treatment for removing the solvent and removing the binder, the positive electrode paste was fired at 360 ° C. ⁇ 1 hr in the atmosphere to obtain a positive electrode sheet having a positive electrode active material layer thickness of 10 ⁇ m. This was punched out into a disk shape having a diameter of 14 mm to obtain a positive electrode.
  • titanium oxide a rutile titanium oxide base material coated with SnO 2
  • a paste prepared by adding appropriate amounts of the resin binder and solvent to glass B powder is applied to either the positive electrode layer or the negative electrode layer, and after heat treatment for removal of the solvent and debinding, 350 ° C. in the atmosphere.
  • the glass B layer was formed by firing at x 1 hr. Then, in order to improve the adhesion at the interface of the positive electrode layer / glass B layer / negative electrode layer, the temperature is higher than the softening point of glass B and lower than the softening point of glass A while pressing this laminate. Firing was performed in the air at 350 ° C. ⁇ 1 hr to sufficiently adhere the interfaces of the layers.
  • FIG. 2 is a cross-sectional view of this laminate, and an amorphous glass layer 207 having a thickness of several ⁇ m is formed between the positive electrode active material layer 204 and the negative electrode active material layer 208, so that The electrical insulation is maintained. That is, instead of the solid electrolyte layer, vanadium oxide glass having ionic conductivity and being amorphous is used.
  • the positive electrode active material particles 202 are bound by vanadium oxide glass 203
  • the negative electrode active material particles 205 are bound by vanadium oxide glass 203.
  • the side surface of the obtained laminate was masked with an insulator, and this was incorporated into a CR2025 type coin battery to produce an all-solid battery.
  • vanadium oxide glass (glass D) to be crystallized was produced.
  • vanadium pentoxide (V 2 O 5 ), lithium oxide (Li 2 O), phosphorus pentoxide (P 2 O 5 ), and ferric oxide (Fe 2 O 3 ) were used.
  • the platinum crucible was taken out from the electric furnace, poured onto a stainless steel plate heated to 150 ° C. in advance, and naturally cooled to obtain vanadium oxide glass.
  • Glass D measured by differential thermal analysis had a first crystallization onset temperature of 315 ° C. and a second crystallization onset temperature of 428 ° C., but no clear softening point was observed. Further, the produced glass was mechanically pulverized so that the average particle size was about 3 ⁇ m.
  • ⁇ Positive electrode> As the positive electrode active material, glass D powder having an average particle diameter of 3 ⁇ m, glass A powder, LATP having an average particle diameter of 3 ⁇ m which is a solid electrolyte, and aciculars which are conductive assistants (short axis: 0.13 ⁇ m, long axis: the conductive titanium oxide (rutile type titanium oxide 1.68) maternal ones coated with SnO 2 conductive layer doped with Sb) and at each volume ratio, 53: 30: 10: 7 become so formulated A proper amount of a resin binder and a solvent was added to the mixed powder to prepare a positive electrode paste.
  • ethyl cellulose or nitrocellulose was used as the resin binder, and butyl carbitol acetate was used as the solvent.
  • This positive electrode paste is applied to an aluminum foil having a thickness of 20 ⁇ m, and after the heat treatment for removing the solvent and removing the binder, the second crystallization of the glass D is started at the softening point of the glass A and the first crystallization start temperature of the glass D. Firing was performed in the air at 375 ° C. below the temperature for 2 hours to obtain a positive electrode sheet having a positive electrode active material layer thickness of 10 ⁇ m. This was punched out into a disk shape having a diameter of 14 mm to obtain a positive electrode.
  • ⁇ Negative electrode> As the negative electrode, a lithium metal foil punched into a disk shape having a diameter of 14 mm was used instead of the negative electrode active material layer in the above examples. An alloy of lithium metal and another metal may be used.
  • ⁇ Solid electrolyte layer> LATP with an average particle diameter of 3 ⁇ m, which is a solid electrolyte, and the prepared glass B powder were prepared so that the volume ratio was 70:30, and a proper amount of resin binder and solvent was added to the mixed powder to obtain a solid.
  • An electrolyte paste was prepared. After applying this solid electrolyte paste to either the positive electrode layer or the negative electrode layer, and after heat treatment for removing the solvent and removing the binder, the temperature is higher than the softening point of the glass B, 350 ° C. ⁇ 1 hr. Baking in air. This was punched into a disk shape having a diameter of 14 mm.
  • this laminate is added. While pressing, firing was performed in an inert gas atmosphere at 350 ° C. ⁇ 1 hr, which is higher than the softening point of glass B and lower than the softening point of glass A, to sufficiently adhere the interfaces of the layers.
  • FIG. 3 shows a cross-sectional view of this laminate.
  • a lithium metal negative electrode 305 is used instead of the negative electrode current collector, and a positive electrode active material layer 306 and a solid electrolyte layer 307 are formed between the positive electrode current collector 301 and the lithium metal negative electrode 305.
  • the positive electrode active material particles 302 are bound by vanadium oxide glass 303.
  • the side surface of the obtained laminate was masked with an insulator, and this was incorporated into a CR2025 type coin battery to produce an all-solid battery.
  • LiCoO 2 powder having an average particle diameter of 5 ⁇ m as a positive electrode active material, and polyvinylidene fluoride as a binder, and LATP an average particle diameter of 3 ⁇ m is a solid electrolyte, conductive additive and a needle (minor axis: 0.13 [mu] m,
  • the volume ratio of conductive titanium oxide (major axis: 1.68 ⁇ m) with rutile-type titanium oxide coated with SnO 2 conductive layer doped with Sb is 53: 30: 10: 7, respectively.
  • NMP N-methyl-2-pyrodrine
  • This positive electrode paste was applied to an aluminum foil having a thickness of 20 ⁇ m, dried by heating in the atmosphere of 90 ° C. ⁇ 1 hr, and then pressed to obtain a positive electrode sheet having a positive electrode active material layer thickness of 10 ⁇ m. This was punched into a disk shape having a diameter of 14 mm.
  • This negative electrode paste was applied to an aluminum foil having a thickness of 20 ⁇ m, dried by heating in the atmosphere of 90 ° C. ⁇ 1 hr, and then pressed to obtain a negative electrode sheet having a negative electrode active material layer thickness of 10 ⁇ m. This was punched into a disk shape having a diameter of 14 mm.
  • This paste was applied to a polyimide sheet having a thickness of 50 ⁇ m, dried by heating in the atmosphere of 90 ° C. ⁇ 1 hr, and then pressed to obtain a solid electrolyte sheet having a thickness of 15 ⁇ m. This was punched out into a disk shape having a diameter of 14 mm and separated from the polyimide sheet to obtain a solid electrolyte layer.
  • ⁇ Battery> In order to laminate the positive electrode, the solid electrolyte layer, and the negative electrode and improve the adhesion at the interface of the positive electrode layer / solid electrolyte layer / negative electrode layer, a heat treatment in vacuum of 120 ° C. ⁇ 1 hr is performed while pressing the laminate. Thus, the interface of each layer was sufficiently adhered.
  • the side surface of the obtained laminate was masked with an insulator, and this was incorporated into a CR2025 type coin battery to produce an all-solid battery.
  • the all-solid lithium ion secondary battery of this example is superior to the comparative example in the rate characteristics and cycle retention rate of the discharge capacity of the battery. This is because a sufficient ion conduction path is secured between the active material particles and the solid electrolyte particles by filling the gap between the active material particles and the solid electrolyte particles with vanadium oxide glass having ion conductivity.
  • the battery of Example 4 has a particularly large discharge capacity because the capacity of the vanadium oxide glass used as the positive electrode active material is large.

Abstract

The purpose of the present invention is to improve the energy density and output density of an all-solid ion secondary cell. In order to achieve the purpose, the present invention is an all-solid ion secondary cell in which a solid electrolyte layer is joined between a positive electrode active material layer and a negative electrode active material layer, the all-solid ion secondary cell being characterized in that the positive electrode active material layer is formed by binding positive electrode active material particles and solid electrolyte particles together using vanadium oxide glass having ionic conductivity, and the negative electrode active material layer is formed by binding negative electrode active material particles and solid electrolyte particles together using vanadium oxide glass having ionic conductivity.

Description

全固体イオン二次電池All solid ion secondary battery
　本発明は、全固体イオン二次電池に関する。 The present invention relates to an all solid ion secondary battery.
　近年、携帯情報端末、携帯電子機器、家庭用小型電力貯蔵装置、電気自動車、ハイブリッド電気自動車等に、不燃性又は難燃性の無機固体電解質を用いた全固体イオン二次電池が用いられている。 In recent years, all solid-state ion secondary batteries using non-flammable or flame-retardant inorganic solid electrolytes are used in personal digital assistants, portable electronic devices, small household power storage devices, electric vehicles, hybrid electric vehicles, and the like. .
　しかし、固体電池においては、活物質粒子と固体電解質粒子との接触面積が小さく、両者間でのイオン伝導抵抗が大きいため、十分な出力密度やエネルギー密度が得られない。また、正極活物質や固体電解質は難焼結性のセラミックスであり、これらが反応しないような低温下で完全に焼結させることは困難である。 However, in a solid battery, since the contact area between the active material particles and the solid electrolyte particles is small and the ion conduction resistance between the two is large, sufficient output density and energy density cannot be obtained. Further, the positive electrode active material and the solid electrolyte are hardly sinterable ceramics, and it is difficult to completely sinter them at a low temperature where they do not react.
　特許文献１では、活物質粒子と固体電解質との接触面積を増大させるために、活物質粒子と粒子結着物質との多孔質構造体から成る一極性側電極と、この多孔質構造体の空隙部表面に被着したイオン伝導性物質から成る固体電解質層と、この多孔質構造体の空隙部に充填された他の活物質と充填物質から成る他の極性側電極とを有する固体電解質電池が開示されている。 In Patent Document 1, in order to increase the contact area between the active material particles and the solid electrolyte, a unipolar electrode composed of a porous structure of the active material particles and the particle binding material, and voids of the porous structure are disclosed. A solid electrolyte battery having a solid electrolyte layer made of an ion conductive material deposited on the surface of the part, another active material filled in the void of the porous structure, and another polar side electrode made of the filled material It is disclosed.
特開２００１－２４３９８４号公報JP 2001-243984 A
　しかし、上記特許文献のものは、活物質粒子と固体電解質層との接触面積を増大させることについて、更なる改善の余地がある。 However, the above-mentioned patent document has room for further improvement in increasing the contact area between the active material particles and the solid electrolyte layer.
　本発明の目的は、全固体イオン二次電池のエネルギー密度および出力密度を向上させることにある。 An object of the present invention is to improve the energy density and output density of an all-solid ion secondary battery.
　前記課題を解決するために、本発明の特徴は、正極活物質層と負極活物質層との間に固体電解質層が接合された全固体イオン二次電池において、前記正極活物質層は、正極活物質粒子と固体電解質粒子とがイオン電導性を有するバナジウム酸化物ガラスで結着されて形成され、前記負極活物質層は、負極活物質粒子と固体電解質粒子とがイオン電導性を有するバナジウム酸化物ガラスで結着されて形成されていることにある。 In order to solve the above problems, the present invention is characterized in that in the all-solid-state ion secondary battery in which a solid electrolyte layer is bonded between a positive electrode active material layer and a negative electrode active material layer, the positive electrode active material layer includes a positive electrode The active material particles and the solid electrolyte particles are formed by binding with vanadium oxide glass having ion conductivity, and the negative electrode active material layer is formed by vanadium oxidation in which the negative electrode active material particles and the solid electrolyte particles have ion conductivity. This is because it is formed by binding with glass.
　本発明によれば、全固体イオン二次電池のエネルギー密度を向上させることができる。 According to the present invention, the energy density of the all solid state ion secondary battery can be improved.
実施例１における正極/固体電解質層/負極積層体の断面図Sectional drawing of the positive electrode / solid electrolyte layer / negative electrode laminated body in Example 1 実施例３における正極/バナジウム酸化物ガラス層/負極積層体の断面図Sectional drawing of the positive electrode / vanadium oxide glass layer / negative electrode laminated body in Example 3 実施例４における正極/固体電解質層/負極積層体の断面図Sectional drawing of the positive electrode / solid electrolyte layer / negative electrode laminated body in Example 4
　次に、本発明の実施形態（実施例）について、適宜図面を参照しながら詳細に説明する。なお、本発明は、ここで取り上げた複数の実施形態（実施例）の個々に限定されることはなく、適宜組み合わせてもよい。 Next, embodiments (examples) of the present invention will be described in detail with reference to the drawings as appropriate. In addition, this invention is not limited to each of several embodiment (Example) taken up here, You may combine suitably.
　全固体電池の出力密度やエネルギー密度向上のためには、正極活物質粒子と固体電解質粒子との間、負極活物質粒子と固体電解質粒子との間において、十分なイオン伝導経路を確保し、イオン伝導性を向上させることが必要である。そこで、活物質粒子と固体電解質粒子とを混合し、イオン伝導性を有するバナジウム酸化物ガラスにより両者の間隙を充たすことを考えた。つまり、正極活物質粒子と固体電解質粒子とを混在させた上で、両者をバナジウム酸化物ガラスで結着することで、正極活物質層が形成されている。また、負極活物質層は、負極活物質粒子と固体電解質粒子とがバナジウム酸化物ガラスで結着されている。バナジウム酸化物ガラスと接触している活物質粒子の表面をイオン伝導経路として、その活物質粒子とバナジウム酸化物ガラスとの間でイオンが移動する。更に、バナジウム酸化物ガラスと接触している固体電解質粒子の表面をイオン伝導経路として、バナジウム酸化物ガラスと固体電解質粒子との間でイオンが移動する。これにより、活物質粒子と固体電解質粒子との間におけるイオン伝導経路を十分確保でき、イオン伝導性を向上させることができる。また、バナジウム酸化物ガラスは活物質粒子と固体電解質粒子とが反応しないような５００℃以下の低温で軟化流動するため、緻密な焼結体を容易に形成することができる。 In order to improve the output density and energy density of all-solid-state batteries, a sufficient ion conduction path is secured between the positive electrode active material particles and the solid electrolyte particles and between the negative electrode active material particles and the solid electrolyte particles, It is necessary to improve conductivity. Therefore, it was considered that active material particles and solid electrolyte particles were mixed and the gap between the two was filled with vanadium oxide glass having ion conductivity. That is, the positive electrode active material layer is formed by mixing the positive electrode active material particles and the solid electrolyte particles and then binding the both with the vanadium oxide glass. In the negative electrode active material layer, the negative electrode active material particles and the solid electrolyte particles are bound by vanadium oxide glass. Ions move between the active material particles and the vanadium oxide glass using the surface of the active material particles in contact with the vanadium oxide glass as an ion conduction path. Further, ions move between the vanadium oxide glass and the solid electrolyte particles using the surface of the solid electrolyte particles in contact with the vanadium oxide glass as an ion conduction path. Thereby, a sufficient ion conduction path can be secured between the active material particles and the solid electrolyte particles, and the ion conductivity can be improved. Further, since vanadium oxide glass softens and flows at a low temperature of 500 ° C. or less so that the active material particles and the solid electrolyte particles do not react, a dense sintered body can be easily formed.
　図１に、本発明の第１の実施形態に係る全固体イオン二次電池の要部の断面図を示す。正極集電体１０１上に形成された正極活物質層１０７と、負極集電体１０６上に形成された負極活物質層１０９とが、固体電解質層１０８を介して接合されている。 FIG. 1 shows a cross-sectional view of a main part of an all solid state ion secondary battery according to a first embodiment of the present invention. A positive electrode active material layer 107 formed on the positive electrode current collector 101 and a negative electrode active material layer 109 formed on the negative electrode current collector 106 are joined via a solid electrolyte layer 108.
　なお、正極活物質層と負極活物質層とは固体電解質層により、完全に電気絶縁されている。 Note that the positive electrode active material layer and the negative electrode active material layer are completely electrically insulated by a solid electrolyte layer.
　なお、各極の活物質層における導電性向上のために、導電助剤を添加してもよい。しかし、活物質粒子と固体電解質粒子との結着材であるバナジウム酸化物ガラスを結晶化させ、活物質層の導電性を向上させた場合には、導電助剤を省略することも可能である。導電助剤としては、黒鉛、アセチレンブラック、ケッチェンブラック等の炭素材料や金、銀、銅、ニッケル、アルミニウム、チタン等の金属粉、インジウム・錫酸化物（ＩＴＯ）、チタン酸化物、錫酸化物、亜鉛酸化物、タングステン酸化物等の導電性酸化物等が好ましい。 In addition, you may add a conductive support agent in order to improve the electroconductivity in the active material layer of each electrode. However, when the vanadium oxide glass, which is a binder between the active material particles and the solid electrolyte particles, is crystallized to improve the conductivity of the active material layer, the conductive auxiliary agent can be omitted. . Conductive aids include carbon materials such as graphite, acetylene black, ketjen black, metal powders such as gold, silver, copper, nickel, aluminum, titanium, indium / tin oxide (ITO), titanium oxide, tin oxide And conductive oxides such as zinc oxide and tungsten oxide are preferred.
　バナジウム酸化物ガラスは、バナジウム、及び、ガラス化成分であるテルルと燐の少なくとも１種を含む。この他に鉄やタングステンを添加することにより、耐水性を著しく向上させることができる。また、活物質粒子と固体電解質粒子との反応を防止するために、バナジウム酸化物ガラスの軟化点を５００℃以下にすることが好ましい。 The vanadium oxide glass contains vanadium and at least one of tellurium and phosphorus which are vitrification components. In addition, water resistance can be remarkably improved by adding iron or tungsten. In order to prevent the reaction between the active material particles and the solid electrolyte particles, the softening point of the vanadium oxide glass is preferably 500 ° C. or lower.
　活物質あるいは固体電解質に対するバナジウム酸化物ガラスの添加量は、体積換算で１０体積％以上、４０体積％以下であることが望ましい。５体積％以上にすると、活物質粒子と固体電解質粒子の間を十分に埋めることができ、４０体積％以下にすると、活物質量や固体電解質量の減少に伴う充放電容量や充放電レートの低下を防止できる。 The amount of vanadium oxide glass added to the active material or solid electrolyte is preferably 10% by volume or more and 40% by volume or less in terms of volume. When the volume is 5% by volume or more, the space between the active material particles and the solid electrolyte particles can be sufficiently filled. When the volume is 40% by volume or less, the charge / discharge capacity and the charge / discharge rate associated with the decrease in the amount of the active material and the solid electrolytic mass are reduced. Decline can be prevented.
　また、正負極活物質層におけるバナジウム酸化物ガラスの少なくとも一部を結晶化させることにより、イオン伝導性や電子伝導性を向上させることが可能である。しかし、固体電解質粒子をガラスで結着させて固体電解質層を形成する場合は、電気絶縁性を確保する必要があるため、バナジウム酸化物ガラスは非晶質でなければならない。このため、正極活物質層、負極活物質層、固体電解質層の各々に異なる種類のバナジウム酸化物ガラスを適用することが有効である。具体的には、正極活物質層と負極活物質層は、リチウムや銅等の結晶化成分を含有し、軟化後、結晶化するガラスを適用し、固体電解質層へは、ガラス化成分であるテルルや燐の含有量を増加させ、結晶化し難くしたガラスを適用するのが好ましい。なお、バナジウム酸化物ガラスのイオン伝導性を向上させるために、バナジウムガラスにリチウムイオンをプレドープしておくことがより好ましい。 Also, it is possible to improve ion conductivity and electronic conductivity by crystallizing at least part of the vanadium oxide glass in the positive and negative electrode active material layers. However, when the solid electrolyte layer is formed by binding the solid electrolyte particles with glass, it is necessary to ensure electrical insulation, so the vanadium oxide glass must be amorphous. For this reason, it is effective to apply different types of vanadium oxide glasses to the positive electrode active material layer, the negative electrode active material layer, and the solid electrolyte layer. Specifically, the positive electrode active material layer and the negative electrode active material layer contain a crystallization component such as lithium or copper, apply a glass that crystallizes after softening, and are a vitrification component to the solid electrolyte layer. It is preferable to apply a glass in which the content of tellurium or phosphorus is increased to make it difficult to crystallize. In order to improve the ionic conductivity of the vanadium oxide glass, it is more preferable to pre-dope lithium ions into the vanadium glass.
　正極活物質としては、リチウムイオンを吸蔵・放出可能である既知の正極活物質を使用することができる。例えば、スピネル系、オリビン系、層状酸化物系、固溶体系、ケイ酸塩系等が挙げられる。また、バナジウム酸化物ガラスを正極活物質として使用することができ、そのガラスの少なくとも一部を結晶化させることでイオン伝導性や電子伝導性を向上させることができる。 As the positive electrode active material, a known positive electrode active material capable of occluding and releasing lithium ions can be used. For example, spinel system, olivine system, layered oxide system, solid solution system, silicate system and the like can be mentioned. Vanadium oxide glass can be used as the positive electrode active material, and ionic conductivity and electronic conductivity can be improved by crystallizing at least a part of the glass.
　負極活物質としては、リチウムイオンを吸蔵・放出可能である既知の負極活物質を使用することができる。たとえば、黒鉛に代表される炭素材料や、ＴｉＳｎ合金、ＴｉＳｉ合金などの合金材料、ＬｉＣｏＮなどの窒化物、Ｌｉ4Ｔｉ5Ｏ12、ＬｉＴｉＯ4などの酸化物を用いることができる。また、リチウム金属箔を用いてもよい。また、バナジウム酸化物ガラスを負極活物質として使用することができ、そのガラスの少なくとも一部を結晶化させることでイオン伝導性や電子伝導性を向上させることができる。 As the negative electrode active material, a known negative electrode active material capable of occluding and releasing lithium ions can be used. For example, a carbon material typified by graphite, an alloy material such as a TiSn alloy or a TiSi alloy, a nitride such as LiCoN, or an oxide such as Li 4 Ti 5 O 12 or LiTiO 4 can be used. Moreover, you may use lithium metal foil. Vanadium oxide glass can be used as the negative electrode active material, and ionic conductivity and electronic conductivity can be improved by crystallizing at least a part of the glass.
　固体電解質については、リチウムイオンを伝導する固体で改質材料であれば、特に限定する必要はないが、安全性の観点から不燃性の無機固体電解質が好ましい。例えば、ＬｉＣｌ、ＬｉＩなどのハロゲン化リチウム、Ｌｉ2Ｓ－ＳｉＳ2、Ｌｉ3ＰＯ4－Ｌｉ2Ｓ－ＳｉＳ2などに代表される硫化物ガラス、Ｌｉ1.4Ａｌ0.4Ｔｉ1.6（ＰＯ4）3、Ｌｉ3.4Ｖ0.6Ｓｉ0.4Ｏ4、Ｌｉ2Ｐ2Ｏ6などで代表される酸化物ガラス、Ｌｉ0.34Ｌａ0.51ＴｉＯ2.94などで代表されるペロブスカイト型酸化物などが使用できる。また、前記イオン伝導性のバナジウム酸化物ガラスも固体電解質として使用することができる。なお、ハロゲン化リチウムや硫化物ガラスについては、水や酸素に対する安定性が低いことなどから、固体電解質については、酸化物系の材料を使用するのがより好ましい。 The solid electrolyte is not particularly limited as long as it is a solid and a reforming material that conducts lithium ions, but an incombustible inorganic solid electrolyte is preferable from the viewpoint of safety. For example, lithium halides such as LiCl and LiI, sulfide glasses represented by Li 2 S—SiS 2 , Li 3 PO 4 —Li 2 S—SiS 2 , Li 1.4 Al 0.4 Ti 1.6 (PO 4 ) 3 , An oxide glass typified by Li 3.4 V 0.6 Si 0.4 O 4 , Li 2 P 2 O 6 or the like, or a perovskite oxide typified by Li 0.34 La 0.51 TiO 2.94 or the like can be used. Moreover, the said ion conductive vanadium oxide glass can also be used as a solid electrolyte. In addition, about lithium halide and sulfide glass, since stability with respect to water or oxygen is low etc., it is more preferable to use an oxide-type material about a solid electrolyte.
　以下、実施例にて本発明を具体的に説明する。 Hereinafter, the present invention will be specifically described with reference to examples.
　＜バナジウム酸化物ガラスの作製＞
　軟化点の異なる２種類のイオン伝導性のバナジウム酸化物ガラスを作製した。原料として、五酸化バナジウム（Ｖ2Ｏ5）、五酸化リン（Ｐ2Ｏ5）、二酸化テルル（ＴｅＯ2）粉末、酸化第二鉄（Ｆｅ2Ｏ3）を用いた。軟化点の高いガラスＡの原料組成としては、それぞれの原料をモル比でＶ2Ｏ5：Ｐ2Ｏ5：ＴｅＯ2：Ｆｅ2Ｏ3＝４７：１３：３０：１０とした。また、軟化点の低いガラスＢの原料組成としては、モル比でＶ2Ｏ5：Ｐ2Ｏ5：ＴｅＯ2：Ｆｅ2Ｏ3＝５５：１４：２２：９とした。これらの原料粉末を白金るつぼに投入し、電気炉を用いて１１００℃、１時間加熱保持した。なお、加熱中は、白金るつぼ内の原材料が均一になるように攪拌した。その後、白金るつぼを電気炉から取り出し、あらかじめ１５０℃に加熱しておいたステンレス板上に流し、これを自然冷却することでバナジウム酸化物ガラスを得た。示差熱分析法により測定したガラスＡ、ガラスＢの軟化点はそれぞれ、３５６℃、３４５℃であった。また、作製したガラスを平均粒径が３μｍ程度になるように機械的に粉砕した。 <Production of vanadium oxide glass>
Two types of ion-conductive vanadium oxide glasses having different softening points were produced. As raw materials, vanadium pentoxide (V 2 O 5 ), phosphorus pentoxide (P 2 O 5 ), tellurium dioxide (TeO 2 ) powder, and ferric oxide (Fe 2 O 3 ) were used. As a raw material composition of the glass A having a high softening point, each raw material was set to have a molar ratio of V 2 O 5 : P 2 O 5 : TeO 2 : Fe 2 O 3 = 47: 13: 30: 10. In addition, the raw material composition of the glass B having a low softening point was V 2 O 5 : P 2 O 5 : TeO 2 : Fe 2 O 3 = 55: 14: 22: 9 in terms of molar ratio. These raw material powders were put into a platinum crucible and heated and held at 1100 ° C. for 1 hour using an electric furnace. During heating, stirring was performed so that the raw materials in the platinum crucible were uniform. Thereafter, the platinum crucible was taken out from the electric furnace, poured onto a stainless steel plate heated to 150 ° C. in advance, and naturally cooled to obtain vanadium oxide glass. The softening points of Glass A and Glass B measured by differential thermal analysis were 356 ° C. and 345 ° C., respectively. Further, the produced glass was mechanically pulverized so that the average particle size was about 3 μm.
　＜正極＞
　正極活物質である平均粒径５μｍのＬｉＣｏＯ2粉末と、作製したガラスＡ粉末と、固体電解質である平均粒径３μｍのＬｉ1.5Ａｌ0.5Ｔｉ1.5（ＰＯ4）3粉末（以下ＬＡＴＰと記述する）と、導電助材である針状（短軸：０．１３μｍ、長軸：１．６８μｍ）の導電性酸化チタン（ルチル型酸化チタンを母体にＳｂをドープしたＳｎＯ２導電層を被覆したもの）とをそれぞれ体積比で、５３：３０：１０：７となるように調合し、この混合粉末に、樹脂バインダーと溶剤とを適量添加して正極ペーストを作製した。なお、樹脂バインダーとしては、エチルセルロースやニトロセルロース、溶剤としてはブチルカルビトールアセテートを用いた。この正極ペーストを厚さ２０μｍのアルミニウム箔に塗布し、脱媒、脱バインダーのための熱処理後に、大気中３６０℃×１ｈｒで焼成し、正極活物質層厚さが１０μｍの正極シートを得た。これを直径１４ｍｍの円盤状に打ち抜き、正極とした。 <Positive electrode>
LiCoO 2 powder having an average particle diameter of 5 μm as a positive electrode active material, the produced glass A powder, and Li 1.5 Al 0.5 Ti 1.5 (PO 4 ) 3 powder having an average particle diameter of 3 μm as a solid electrolyte (hereinafter referred to as LATP) And a conductive titanium oxide (short axis: 0.13 μm, long axis: 1.68 μm) conductive titanium oxide (rutile titanium oxide based on a SnO 2 conductive layer coated with Sb) Were mixed at a volume ratio of 53: 30: 10: 7, and a proper amount of a resin binder and a solvent were added to the mixed powder to prepare a positive electrode paste. In addition, ethyl cellulose or nitrocellulose was used as the resin binder, and butyl carbitol acetate was used as the solvent. This positive electrode paste was applied to an aluminum foil having a thickness of 20 μm, and after heat treatment for removing the solvent and removing the binder, the positive electrode paste was fired at 360 ° C. × 1 hr in the atmosphere to obtain a positive electrode sheet having a positive electrode active material layer thickness of 10 μm. This was punched out into a disk shape having a diameter of 14 mm to obtain a positive electrode.
　＜負極＞
　負極活物質である平均粒径５μｍのＬｉ4Ｔｉ5Ｏ12粉末と、作製したガラスＡ粉末と、固体電解質である平均粒径３μｍのＬＡＴＰと、導電助材である針状（短軸：０．１３μｍ、長軸：１．６８μｍ）の導電性酸化チタン（ルチル型酸化チタンを母体にＳｂをドープしたＳｎＯ２導電層を被覆したもの）とをそれぞれ体積比で、５３：３０：１０：７となるように調合し、この混合粉末に、樹脂バインダーと溶剤とを適量添加して負極ペーストを作製した。この負極ペーストを厚さ２０μｍのアルミニウム箔に塗布し、脱媒、脱バインダーのための熱処理後に、大気中３６０℃×１ｈｒで焼成し、負極活物質層厚さが１０μｍの負極シートを得た。これを直径１４ｍｍの円盤状に打ち抜き、負極とした。 <Negative electrode>
Li 4 Ti 5 O 12 powder having an average particle diameter of 5 μm as a negative electrode active material, produced glass A powder, LATP having an average particle diameter of 3 μm as a solid electrolyte, and needle-like (short axis: 0) as a conductive aid .13 μm, long axis: 1.68 μm) conductive titanium oxide (a rutile-type titanium oxide base material coated with SnO 2 conductive layer doped with Sb) in a volume ratio of 53: 30: 10: 7 An appropriate amount of a resin binder and a solvent was added to the mixed powder to prepare a negative electrode paste. This negative electrode paste was applied to an aluminum foil having a thickness of 20 μm, and after heat treatment for removing the solvent and removing the binder, the negative electrode paste was fired in the atmosphere at 360 ° C. × 1 hr to obtain a negative electrode sheet having a negative electrode active material layer thickness of 10 μm. This was punched out into a disk shape having a diameter of 14 mm to obtain a negative electrode.
　なお、本実施例では正極活物質層に用いるバナジウム酸化物ガラスと負極活物質層に用いるバナジウム酸化物ガラスを同じ物としたが、イオン電導性のあるバナジウム酸化物ガラスであれば、両者は同一組成のものでなくてもよい。以下の実施例についても同様である。 In this example, the vanadium oxide glass used for the positive electrode active material layer and the vanadium oxide glass used for the negative electrode active material layer are the same, but both are the same as long as the vanadium oxide glass has ion conductivity. It does not have to be of composition. The same applies to the following embodiments.
　＜固体電解質層＞ 
　固体電解質である平均粒径３μｍのＬＡＴＰと、作製したガラスＢ粉末とをそれぞれ体積比で、７０：３０となるように調合し、この混合粉末に、樹脂バインダーと溶剤とを適量添加して固体電解質ペーストを作製した。この固体電解質ペーストを正極あるいは負極の電極層のいずれかに塗布した後、脱媒、脱バインダーのための熱処理を施した後、ガラスＢの軟化点よりも高い温度である、３５０℃×１ｈｒで大気中焼成し、厚さ１５μｍの固体電解質層を形成した。これを直径１５ｍｍの円盤状に打ち抜いた。 <Solid electrolyte layer>
LATP with an average particle diameter of 3 μm, which is a solid electrolyte, and the prepared glass B powder were prepared so that the volume ratio was 70:30, and a proper amount of resin binder and solvent was added to the mixed powder to obtain a solid. An electrolyte paste was prepared. After applying this solid electrolyte paste to either the positive electrode layer or the negative electrode layer, and after heat treatment for removing the solvent and removing the binder, the temperature is higher than the softening point of the glass B, 350 ° C. × 1 hr. Firing was performed in the air to form a solid electrolyte layer having a thickness of 15 μm. This was punched into a disk shape having a diameter of 15 mm.
　固体電解質層は、イオンを通し電子を通さないものであればよく、本実施例のような粒子状の固体電解質で固体電解質層を形成するものに限られない。以下の実施例についても同様である。 The solid electrolyte layer is not limited to a solid electrolyte layer formed of a particulate solid electrolyte as in the present embodiment as long as it allows ions to pass therethrough and does not pass electrons. The same applies to the following embodiments.
　＜電池化＞
　上記の固体電解質層が形成された電極層と、もう一方の電極層を積層し、正極活物質層／固体電解質層／負極活物質層の界面の密着性を向上させるため、この積層体を加圧しながら、ガラスＢの軟化点よりも高く、ガラスＡの軟化点よりも低い温度である、３５０℃×１ｈｒで大気中焼成し、各層の界面を十分密着させた。得られた積層体の側面を絶縁物でマスキングし、これをＣＲ２０２５型のコイン電池に組み込み全固体電池を作製した。 <Battery>
In order to improve the adhesion at the interface of the positive electrode active material layer / solid electrolyte layer / negative electrode active material layer by laminating the electrode layer on which the solid electrolyte layer is formed and the other electrode layer, this laminate is added. While being pressed, the glass B was fired in air at 350 ° C. × 1 hr, which is higher than the softening point of the glass B and lower than the softening point of the glass A, and the interfaces of the layers were sufficiently adhered. The side surface of the obtained laminate was masked with an insulator, and this was incorporated into a CR2025 type coin battery to produce an all-solid battery.
　なお、上記した混合粉末ペーストの塗布、焼成による各層の形成法の代わりに、混合粉末を溶融またはガス化させること無く、不活性ガスと共に超音速流で固相状態のまま基材に衝突させて皮膜を形成するコールドスプレー（ＣＳ）法や、混合粉末をガスと混合したエアロゾルを圧力差により生じるガスの流れを利用し、ノズルを通して基板に噴射して皮膜を形成するエアロゾルデポジション（ＡＤ）法を適用することもできる。 Instead of the above-mentioned method of forming each layer by applying and baking the mixed powder paste, the mixed powder is allowed to collide with the base material in a solid state in supersonic flow with an inert gas without melting or gasifying. Cold spray (CS) method for forming a film, and aerosol deposition (AD) method for forming a film by spraying an aerosol obtained by mixing a mixed powder with a gas through a nozzle to the substrate through a nozzle. Can also be applied.
　ＣＳ法による電池作製方法について以下に説明する。上記同様のＬｉＣｏＯ2粉末と、ガラスＡ粉末と、ＬＡＴＰ粉末と、前記導電性酸化チタンとの混合粉末を厚さ２０μｍのアルミニウム箔上に噴射し、厚さ１０μｍの正極活物質層を形成させた。なお、各粉末をそれぞれ別のフィーダーに投入し、同時に噴射させてもよい。 A battery manufacturing method by the CS method will be described below. A mixed powder of the same LiCoO 2 powder, glass A powder, LATP powder, and conductive titanium oxide was sprayed onto an aluminum foil having a thickness of 20 μm to form a positive electrode active material layer having a thickness of 10 μm. . Each powder may be put into a separate feeder and sprayed at the same time.
　上記同様のＬＡＴＰ粉末と、作製したガラスＡ粉末あるいはガラスＢ粉末との混合粉末を正極活物質層上に噴射し、厚さ15μｍの固体電解質層を形成させた。 A mixed powder of the same LATP powder and the produced glass A powder or glass B powder was sprayed onto the positive electrode active material layer to form a solid electrolyte layer having a thickness of 15 μm.
　次に、上記同様のＬｉ4Ｔｉ5Ｏ12粉末と、ガラスＡ粉末と、ＬＡＴＰ粉末と、前記導電性酸化チタンとの混合粉末を固体電解質層上に噴射し、厚さ１０μｍの負極活物質層を形成させた。 Next, the above same of Li 4 Ti 5 O 12 powder, and glass powder A, and LATP powder, a mixed powder of the conductive titanium oxide was sprayed onto the solid electrolyte layer, the negative electrode active material layer having a thickness of 10μm Formed.
　さらに、負極電解質層の上に、アルミニウム粉末を噴射し、厚さ２０μｍの負極集電体層を形成した。 Further, aluminum powder was sprayed on the negative electrode electrolyte layer to form a negative electrode current collector layer having a thickness of 20 μm.
　＜バナジウム酸化物ガラスの作製＞
　軟化点を有し、結晶化するイオン伝導性のバナジウム酸化物ガラス（ガラスＣ）を作製した。原料として、五酸化バナジウム（Ｖ2Ｏ5）、五酸化リン（Ｐ2Ｏ5）、酸化第二鉄（Ｆｅ2Ｏ3）を用いた。それぞれの原料をモル比でＶ2Ｏ5：Ｐ2Ｏ5：Ｆｅ2Ｏ3＝６０：２０：２０で混合した原料粉末を白金るつぼに投入し、電気炉を用いて１１００℃、１時間加熱保持した。なお、加熱中は、白金るつぼ内の原材料が均一になるように攪拌した。その後、白金るつぼを電気炉から取り出し、あらかじめ１５０℃に加熱しておいたステンレス板上に流し、これを自然冷却することでバナジウム酸化物ガラスを得た。示差熱分析法により測定したガラスＣの軟化点は３９０℃、結晶化開始温度は４３４℃であった。また、作製したガラスを平均粒径が３μｍ程度になるように機械的に粉砕した。 <Production of vanadium oxide glass>
An ion conductive vanadium oxide glass (glass C) having a softening point and crystallizing was produced. As raw materials, vanadium pentoxide (V 2 O 5 ), phosphorus pentoxide (P 2 O 5 ), and ferric oxide (Fe 2 O 3 ) were used. Raw materials mixed with each raw material in a molar ratio of V 2 O 5 : P 2 O 5 : Fe 2 O 3 = 60: 20: 20 are put into a platinum crucible and heated at 1100 ° C. for 1 hour using an electric furnace. Retained. During heating, stirring was performed so that the raw materials in the platinum crucible were uniform. Thereafter, the platinum crucible was taken out from the electric furnace, poured onto a stainless steel plate heated to 150 ° C. in advance, and naturally cooled to obtain vanadium oxide glass. The softening point of glass C measured by differential thermal analysis was 390 ° C., and the crystallization start temperature was 434 ° C. Further, the produced glass was mechanically pulverized so that the average particle size was about 3 μm.
　＜正極＞
　正極活物質である平均粒径５μｍのＬｉＣｏＯ2粉末と、作製したガラスＣ粉末と、固体電解質である平均粒径３μｍのＬＡＴＰと、導電助材である針状（短軸：０．１３μｍ、長軸：１．６８μｍ）の導電性酸化チタン（ルチル型酸化チタンを母体にＳｂをドープしたＳｎＯ２導電層を被覆したもの）とをそれぞれ体積比で、５３：３０：１０：７となるように調合し、この混合粉末に、樹脂バインダーと溶剤とを適量添加して正極ペーストを作製した。なお、樹脂バインダーとしては、エチルセルロースやニトロセルロース、溶剤としてはブチルカルビトールアセテートを用いた。この正極ペーストを厚さ２０μｍのアルミニウム箔に塗布し、脱媒、脱バインダーのための熱処理後に、大気中４００℃×１ｈｒで焼成後、さらに、４３０℃×０．５ｈｒの熱処理を施すことにより結晶化させ、正極活物質層厚さが１０μｍの正極シートを得た。このときバナジウム酸化物ガラスを一部だけ結晶化させても、全て結晶化させてもよい。これを直径１４ｍｍの円盤状に打ち抜き、正極とした。 <Positive electrode>
LiCoO 2 powder with an average particle diameter of 5 μm as a positive electrode active material, the produced glass C powder, LATP with an average particle diameter of 3 μm as a solid electrolyte, and needle-like material as a conductive auxiliary (short axis: 0.13 μm, long Axis: 1.68 μm) conductive titanium oxide (rutile titanium oxide coated with SnO 2 conductive layer doped with Sb) and volume ratio of 53: 30: 10: 7 An appropriate amount of a resin binder and a solvent was added to the mixed powder to prepare a positive electrode paste. In addition, ethyl cellulose or nitrocellulose was used as the resin binder, and butyl carbitol acetate was used as the solvent. This positive electrode paste is applied to an aluminum foil having a thickness of 20 μm, heat-treated for removal of the solvent and binder, fired at 400 ° C. × 1 hr in the atmosphere, and further subjected to heat treatment at 430 ° C. × 0.5 hr. Thus, a positive electrode sheet having a positive electrode active material layer thickness of 10 μm was obtained. At this time, the vanadium oxide glass may be crystallized only partially or entirely. This was punched out into a disk shape having a diameter of 14 mm to obtain a positive electrode.
　＜負極＞
　負極活物質である平均粒径５μｍのＬｉ4Ｔｉ5Ｏ12粉末と、作製したガラスＣ粉末と、固体電解質である平均粒径３μｍのＬＡＴＰと、導電助材である針状（短軸：０．１３μｍ、長軸：１．６８μｍ）の導電性酸化チタン（ルチル型酸化チタンを母体にＳｂをドープしたＳｎＯ２導電層を被覆したもの）とをそれぞれ体積比で、５３：３０：１０：７となるように調合し、この混合粉末に、樹脂バインダーと溶剤とを適量添加して負極ペーストを作製した。この負極ペーストを厚さ２０μｍのアルミニウム箔に塗布し、脱媒、脱バインダーのための熱処理後に、大気中４００℃×１ｈｒで焼成後、さらに、４３０℃×０．５ｈｒの熱処理を施すことにより結晶化させ、負極活物質層厚さが１０μｍの負極シートを得た。これを直径１４ｍｍの円盤状に打ち抜き、負極とした。 <Negative electrode>
Li 4 Ti 5 O 12 powder having an average particle diameter of 5 μm as a negative electrode active material, the produced glass C powder, LATP having an average particle diameter of 3 μm as a solid electrolyte, and acicular (short axis: 0) as a conductive aid. .13 μm, long axis: 1.68 μm) conductive titanium oxide (a rutile-type titanium oxide base material coated with SnO 2 conductive layer doped with Sb) in a volume ratio of 53: 30: 10: 7 An appropriate amount of a resin binder and a solvent was added to the mixed powder to prepare a negative electrode paste. This negative electrode paste is applied to an aluminum foil having a thickness of 20 μm, heat-treated for removal of the solvent and binder, fired at 400 ° C. × 1 hr in the air, and further subjected to heat treatment at 430 ° C. × 0.5 hr to produce crystals. Thus, a negative electrode sheet having a negative electrode active material layer thickness of 10 μm was obtained. This was punched out into a disk shape having a diameter of 14 mm to obtain a negative electrode.
　＜固体電解質層＞ 
　固体電解質である平均粒径３μｍのＬＡＴＰと、作製したガラスＢ粉末とをそれぞれ体積比で、７０：３０となるように調合し、この混合粉末に、樹脂バインダーと溶剤とを適量添加して固体電解質ペーストを作製した。この固体電解質ペーストを正極あるいは負極の電極層のいずれかに塗布した後、脱媒、脱バインダーのための熱処理を施した後、ガラスＢの軟化点よりも高い温度である、３５０℃×１ｈｒで大気中焼成し、厚さ１５μｍの固体電解質層を形成した。これを直径１４ｍｍの円盤状に打ち抜いた。 <Solid electrolyte layer>
LATP with an average particle diameter of 3 μm, which is a solid electrolyte, and the prepared glass B powder were prepared so that the volume ratio was 70:30, and a proper amount of resin binder and solvent was added to the mixed powder to obtain a solid. An electrolyte paste was prepared. After applying this solid electrolyte paste to either the positive electrode layer or the negative electrode layer, and after heat treatment for removing the solvent and removing the binder, the temperature is higher than the softening point of the glass B, 350 ° C. × 1 hr. Firing was performed in the air to form a solid electrolyte layer having a thickness of 15 μm. This was punched into a disk shape having a diameter of 14 mm.
　＜電池化＞
　上記の固体電解質層が形成された電極層と、もう一方の電極層を積層し、正極活物質層／固体電解質層／負極活物質層の界面の密着性を向上させるため、この積層体を加圧しながら、ガラスＢの軟化点よりも高く、ガラスＣの軟化点よりも低い温度である、３５０℃×１ｈｒで大気中焼成し、各層の界面を十分密着させた。得られた積層体の側面を絶縁物でマスキングし、これをＣＲ２０２５型のコイン電池に組み込み全固体電池を作製した。 <Battery>
In order to improve the adhesion at the interface of the positive electrode active material layer / solid electrolyte layer / negative electrode active material layer by laminating the electrode layer on which the solid electrolyte layer is formed and the other electrode layer, this laminate is added. While being pressed, the glass B was fired in air at 350 ° C. × 1 hr, which is higher than the softening point of the glass B and lower than the softening point of the glass C, so that the interfaces of the layers were sufficiently adhered. The side surface of the obtained laminate was masked with an insulator, and this was incorporated into a CR2025 type coin battery to produce an all-solid battery.
　＜電池特性評価＞
　０．１Ｃ、１Ｃレートでの放電容量を実施例１と比較した結果、０．１Ｃレートではほぼ同等であったが、１Ｃレートのものに関しては、若干の放電容量が向上した。これは、バナジウム酸化物ガラスの結晶化に伴い、活物質層の導電性が向上したためである。 <Battery characteristics evaluation>
As a result of comparing the discharge capacities at 0.1 C and 1 C rates with Example 1, the discharge capacities were almost the same at the 0.1 C rates, but the discharge capacities were slightly improved for the 1 C rates. This is because the conductivity of the active material layer has improved with the crystallization of the vanadium oxide glass.
　＜正極＞
　正極活物質である平均粒径５μｍのＬｉＣｏＯ2粉末と、作製したガラスＡ粉末と、導電助材である針状（短軸：０．１３μｍ、長軸：１．６８μｍ）の導電性酸化チタン（ルチル型酸化チタンを母体にＳｂをドープしたＳｎＯ２導電層を被覆したもの）とをそれぞれ体積比で、６３：３０：７となるように調合し、この混合粉末に、樹脂バインダーと溶剤とを適量添加して正極ペーストを作製した。なお、樹脂バインダーとしては、エチルセルロースやニトロセルロース、溶剤としてはブチルカルビトールアセテートを用いた。この正極ペーストを厚さ２０μｍのアルミニウム箔に塗布し、脱媒、脱バインダーのための熱処理後に、大気中３６０℃×１ｈｒで焼成し、正極活物質層厚さが１０μｍの正極シートを得た。これを直径１４ｍｍの円盤状に打ち抜き、正極とした。 <Positive electrode>
LiCoO 2 powder having an average particle diameter of 5 μm as a positive electrode active material, the produced glass A powder, and acicular conductive titanium oxide (short axis: 0.13 μm, long axis: 1.68 μm) as a conductive additive ( Rutile-type titanium oxide based on Sb-doped SnO 2 conductive layer) and a volume ratio of 63: 30: 7, and the mixed powder is mixed with a resin binder and a solvent. An appropriate amount was added to prepare a positive electrode paste. In addition, ethyl cellulose or nitrocellulose was used as the resin binder, and butyl carbitol acetate was used as the solvent. This positive electrode paste was applied to an aluminum foil having a thickness of 20 μm, and after heat treatment for removing the solvent and removing the binder, the positive electrode paste was fired at 360 ° C. × 1 hr in the atmosphere to obtain a positive electrode sheet having a positive electrode active material layer thickness of 10 μm. This was punched out into a disk shape having a diameter of 14 mm to obtain a positive electrode.
　＜負極＞
　負極活物質である平均粒径５μｍのＬｉ4Ｔｉ5Ｏ12粉末と、作製したガラスＡ粉末と、導電助材である針状（短軸：０．１３μｍ、長軸：１．６８μｍ）の導電性酸化チタン（ルチル型酸化チタンを母体にＳｂをドープしたＳｎＯ２導電層を被覆したもの）とをそれぞれ体積比で、６３：３０：７となるように調合し、この混合粉末に、樹脂バインダーと溶剤とを適量添加して負極ペーストを作製した。この負極ペーストを厚さ２０μｍのアルミニウム箔に塗布し、脱媒、脱バインダーのための熱処理後に、大気中３６０℃×１ｈｒで焼成し、負極活物質層厚さが１０μｍの負極シートを得た。これを直径１４ｍｍの円盤状に打ち抜き、負極とした。 <Negative electrode>
Li 4 Ti 5 O 12 powder having an average particle diameter of 5 μm as a negative electrode active material, the produced glass A powder, and needle-like (short axis: 0.13 μm, long axis: 1.68 μm) conductive additive And titanium oxide (a rutile titanium oxide base material coated with SnO 2 conductive layer doped with Sb) was prepared so as to have a volume ratio of 63: 30: 7. An appropriate amount of and a solvent were added to prepare a negative electrode paste. This negative electrode paste was applied to an aluminum foil having a thickness of 20 μm, and after heat treatment for removing the solvent and removing the binder, the negative electrode paste was fired in the atmosphere at 360 ° C. × 1 hr to obtain a negative electrode sheet having a negative electrode active material layer thickness of 10 μm. This was punched out into a disk shape having a diameter of 14 mm to obtain a negative electrode.
　＜電池化＞
　上記の正極あるいは負極の電極層のいずれかに、ガラスＢ粉末に前記樹脂バインダーと溶剤とを適量添加して作製したペーストを塗布し、脱媒、脱バインダーのための熱処理後に、大気中３５０℃×１ｈｒで焼成しガラスＢ層を形成した。その後、正極層／ガラスＢ層／負極層の界面の密着性を向上させるため、この積層体を加圧しながら、ガラスＢの軟化点よりも高く、ガラスＡの軟化点よりも低い温度である、３５０℃×１ｈｒで大気中焼成し、各層の界面を十分密着させた。図２はこの積層体の断面図であるが、正極活物質層２０４と負極活物質層２０８との間に、厚さ数μｍの非晶質のガラス層２０７が形成することで、正負極間の電気絶縁性は保たれている。即ち、固体電解質層の替わりにイオン電導性を有し、非晶質であるバナジウム酸化物ガラスを用いている。正極活物質粒子２０２はバナジウム酸化物ガラス２０３で結着され、負極活物質粒子２０５はバナジウム酸化物ガラス２０３で結着されている。得られた積層体の側面を絶縁物でマスキングし、これをＣＲ２０２５型のコイン電池に組み込み全固体電池を作製した。 <Battery>
A paste prepared by adding appropriate amounts of the resin binder and solvent to glass B powder is applied to either the positive electrode layer or the negative electrode layer, and after heat treatment for removal of the solvent and debinding, 350 ° C. in the atmosphere. The glass B layer was formed by firing at x 1 hr. Then, in order to improve the adhesion at the interface of the positive electrode layer / glass B layer / negative electrode layer, the temperature is higher than the softening point of glass B and lower than the softening point of glass A while pressing this laminate. Firing was performed in the air at 350 ° C. × 1 hr to sufficiently adhere the interfaces of the layers. FIG. 2 is a cross-sectional view of this laminate, and an amorphous glass layer 207 having a thickness of several μm is formed between the positive electrode active material layer 204 and the negative electrode active material layer 208, so that The electrical insulation is maintained. That is, instead of the solid electrolyte layer, vanadium oxide glass having ionic conductivity and being amorphous is used. The positive electrode active material particles 202 are bound by vanadium oxide glass 203, and the negative electrode active material particles 205 are bound by vanadium oxide glass 203. The side surface of the obtained laminate was masked with an insulator, and this was incorporated into a CR2025 type coin battery to produce an all-solid battery.
　＜電池特性評価＞
　０．１Ｃ、１Ｃレートでの放電容量を実施例１と比較した結果、０．１Ｃレートでは若干、容量が向上したが、１Ｃレートではほぼ同等の容量が得られた。 <Battery characteristics evaluation>
As a result of comparing the discharge capacity at the 0.1 C and 1 C rates with that of Example 1, the capacity was slightly improved at the 0.1 C rate, but almost the same capacity was obtained at the 1 C rate.
　＜バナジウム酸化物ガラスの作製＞
　結晶化するイオン伝導性のバナジウム酸化物ガラス（ガラスＤ）を作製した。原料として、五酸化バナジウム（Ｖ2Ｏ5）、酸化リチウム（Ｌｉ2Ｏ）、五酸化リン（Ｐ2Ｏ5）、酸化第二鉄（Ｆｅ2Ｏ3）を用いた。それぞれの原料をモル比でＶ2Ｏ5：Ｌｉ2Ｏ：Ｐ2Ｏ5：Ｆｅ2Ｏ3＝７０．３：１０．７：９：１０で混合した原料粉末を白金るつぼに投入し、電気炉を用いて１１００℃、１時間加熱保持した。なお、加熱中は、白金るつぼ内の原材料が均一になるように攪拌した。その後、白金るつぼを電気炉から取り出し、あらかじめ１５０℃に加熱しておいたステンレス板上に流し、これを自然冷却することでバナジウム酸化物ガラスを得た。示差熱分析法により測定したガラスＤの第一結晶化開始温度は３１５℃、第二結晶化開始温度は４２８℃であったが、明瞭な軟化点は認められなかった。また、作製したガラスを平均粒径が３μｍ程度になるように機械的に粉砕した。 <Production of vanadium oxide glass>
An ion conductive vanadium oxide glass (glass D) to be crystallized was produced. As raw materials, vanadium pentoxide (V 2 O 5 ), lithium oxide (Li 2 O), phosphorus pentoxide (P 2 O 5 ), and ferric oxide (Fe 2 O 3 ) were used. A raw material powder in which each raw material was mixed at a molar ratio of V 2 O 5 : Li 2 O: P 2 O 5 : Fe 2 O 3 = 70.3: 10.7: 9: 10 was charged into a platinum crucible, It was heated and held at 1100 ° C. for 1 hour using a furnace. During heating, stirring was performed so that the raw materials in the platinum crucible were uniform. Thereafter, the platinum crucible was taken out from the electric furnace, poured onto a stainless steel plate heated to 150 ° C. in advance, and naturally cooled to obtain vanadium oxide glass. Glass D measured by differential thermal analysis had a first crystallization onset temperature of 315 ° C. and a second crystallization onset temperature of 428 ° C., but no clear softening point was observed. Further, the produced glass was mechanically pulverized so that the average particle size was about 3 μm.
　＜正極＞
　正極活物質として、平均粒径３μｍのガラスＤ粉末と、ガラスＡ粉末と、固体電解質である平均粒径３μｍのＬＡＴＰと、導電助材である針状（短軸：０．１３μｍ、長軸：１．６８μｍ）の導電性酸化チタン（ルチル型酸化チタンを母体にＳｂをドープしたＳｎＯ２導電層を被覆したもの）とをそれぞれ体積比で、５３：３０：１０：７となるように調合し、この混合粉末に、樹脂バインダーと溶剤とを適量添加して正極ペーストを作製した。なお、樹脂バインダーとしては、エチルセルロースやニトロセルロース、溶剤としてはブチルカルビトールアセテートを用いた。この正極ペーストを厚さ２０μｍのアルミニウム箔に塗布し、脱媒、脱バインダーのための熱処理後に、ガラスＡの軟化点およびガラスＤの第一結晶化開始温度以上、ガラスＤの第二結晶化開始温度未満の３７５℃で２時間大気中で焼成し、正極活物質層厚さが１０μｍの正極シートを得た。これを直径１４ｍｍの円盤状に打ち抜き、正極とした。 <Positive electrode>
As the positive electrode active material, glass D powder having an average particle diameter of 3 μm, glass A powder, LATP having an average particle diameter of 3 μm which is a solid electrolyte, and aciculars which are conductive assistants (short axis: 0.13 μm, long axis: the conductive titanium oxide (rutile type titanium oxide 1.68) maternal ones coated with SnO 2 conductive layer doped with Sb) and at each volume ratio, 53: 30: 10: 7 become so formulated A proper amount of a resin binder and a solvent was added to the mixed powder to prepare a positive electrode paste. In addition, ethyl cellulose or nitrocellulose was used as the resin binder, and butyl carbitol acetate was used as the solvent. This positive electrode paste is applied to an aluminum foil having a thickness of 20 μm, and after the heat treatment for removing the solvent and removing the binder, the second crystallization of the glass D is started at the softening point of the glass A and the first crystallization start temperature of the glass D. Firing was performed in the air at 375 ° C. below the temperature for 2 hours to obtain a positive electrode sheet having a positive electrode active material layer thickness of 10 μm. This was punched out into a disk shape having a diameter of 14 mm to obtain a positive electrode.
　＜負極＞
　負極としては、上記実施例における負極活物質層に替えて、直径１４ｍｍの円盤状に打ち抜いたリチウム金属箔を用いた。リチウム金属と他の金属との合金を用いてもよい。 <Negative electrode>
As the negative electrode, a lithium metal foil punched into a disk shape having a diameter of 14 mm was used instead of the negative electrode active material layer in the above examples. An alloy of lithium metal and another metal may be used.
　＜固体電解質層＞ 
　固体電解質である平均粒径３μｍのＬＡＴＰと、作製したガラスＢ粉末とをそれぞれ体積比で、７０：３０となるように調合し、この混合粉末に、樹脂バインダーと溶剤とを適量添加して固体電解質ペーストを作製した。この固体電解質ペーストを正極あるいは負極の電極層のいずれかに塗布した後、脱媒、脱バインダーのための熱処理を施した後、ガラスＢの軟化点よりも高い温度である、３５０℃×１ｈｒで大気中焼成した。これを直径１４ｍｍの円盤状に打ち抜いた。 <Solid electrolyte layer>
LATP with an average particle diameter of 3 μm, which is a solid electrolyte, and the prepared glass B powder were prepared so that the volume ratio was 70:30, and a proper amount of resin binder and solvent was added to the mixed powder to obtain a solid. An electrolyte paste was prepared. After applying this solid electrolyte paste to either the positive electrode layer or the negative electrode layer, and after heat treatment for removing the solvent and removing the binder, the temperature is higher than the softening point of the glass B, 350 ° C. × 1 hr. Baking in air. This was punched into a disk shape having a diameter of 14 mm.
　＜電池化＞
　上記の固体電解質層が形成された電極層と、もう一方の電極層を積層し、正極活物質層／固体電解質層／負極活物質層の界面の密着性を向上させるため、この積層体を加圧しながら、ガラスＢの軟化点よりも高く、ガラスＡの軟化点よりも低い温度である、３５０℃×１ｈｒで不活性ガス雰囲気中で焼成し、各層の界面を十分密着させた。図３にこの積層体の断面図を示す。負極集電体の替わりにリチウム金属負極３０５とし、正極集電体３０１とリチウム金属負極３０５との間に、正極活物質層３０６と固体電解質層３０７とが形成されている。正極活物質粒子３０２はバナジウム酸化物ガラス３０３で結着されている。得られた積層体の側面を絶縁物でマスキングし、これをＣＲ２０２５型のコイン電池に組み込み全固体電池を作製した。 <Battery>
In order to improve the adhesion at the interface of the positive electrode active material layer / solid electrolyte layer / negative electrode active material layer by laminating the electrode layer on which the solid electrolyte layer is formed and the other electrode layer, this laminate is added. While pressing, firing was performed in an inert gas atmosphere at 350 ° C. × 1 hr, which is higher than the softening point of glass B and lower than the softening point of glass A, to sufficiently adhere the interfaces of the layers. FIG. 3 shows a cross-sectional view of this laminate. A lithium metal negative electrode 305 is used instead of the negative electrode current collector, and a positive electrode active material layer 306 and a solid electrolyte layer 307 are formed between the positive electrode current collector 301 and the lithium metal negative electrode 305. The positive electrode active material particles 302 are bound by vanadium oxide glass 303. The side surface of the obtained laminate was masked with an insulator, and this was incorporated into a CR2025 type coin battery to produce an all-solid battery.
［比較例］
　＜正極＞
　正極活物質である平均粒径５μｍのＬｉＣｏＯ2粉末と、バインダーであるポリフッ化ビニリデンと、固体電解質である平均粒径３μｍのＬＡＴＰと、導電助材である針状（短軸：０．１３μｍ、長軸：１．６８μｍ）の導電性酸化チタン（ルチル型酸化チタンを母体にＳｂをドープしたＳｎＯ２導電層を被覆したもの）とをそれぞれ体積比で、５３：３０：１０：７となるように調合し、さらに、Ｎ－メチル－２－ピロドリン（ＮＭＰ）を適量添加して正極ペーストを作製した。この正極ペーストを厚さ２０μｍのアルミニウム箔に塗布し、９０℃×１ｈｒの大気中加熱による乾燥後、プレスし、正極活物質層厚さが１０μｍの正極シートを得た。これを直径１４ｍｍの円盤状に打ち抜いた。 [Comparative example]
<Positive electrode>
And LiCoO 2 powder having an average particle diameter of 5μm as a positive electrode active material, and polyvinylidene fluoride as a binder, and LATP an average particle diameter of 3μm is a solid electrolyte, conductive additive and a needle (minor axis: 0.13 [mu] m, The volume ratio of conductive titanium oxide (major axis: 1.68 μm) with rutile-type titanium oxide coated with SnO 2 conductive layer doped with Sb is 53: 30: 10: 7, respectively. In addition, an appropriate amount of N-methyl-2-pyrodrine (NMP) was added to prepare a positive electrode paste. This positive electrode paste was applied to an aluminum foil having a thickness of 20 μm, dried by heating in the atmosphere of 90 ° C. × 1 hr, and then pressed to obtain a positive electrode sheet having a positive electrode active material layer thickness of 10 μm. This was punched into a disk shape having a diameter of 14 mm.
　＜負極層＞
　負極活物質である平均粒径５μｍのＬｉ4Ｔｉ5Ｏ12粉末と、バインダーであるポリフッ化ビニリデンと、固体電解質である平均粒径３μｍのＬＡＴＰと、導電助材である針状（短軸：０．１３μｍ、長軸：１．６８μｍ）の導電性酸化チタン（ルチル型酸化チタンを母体にＳｂをドープしたＳｎＯ２導電層を被覆したもの）とをそれぞれ体積比で、五三：３０：１０：７となるように調合し、さらに、ＮＭＰを適量添加して負極ペーストを作製した。この負極ペーストを厚さ２０μｍのアルミニウム箔に塗布し、９０℃×１ｈｒの大気中加熱による乾燥後、プレスし、負極活物質層厚さが１０μｍの負極シートを得た。これを直径１４mmの円盤状に打ち抜いた。 <Negative electrode layer>
Li 4 Ti 5 O 12 powder having an average particle diameter of 5 μm as a negative electrode active material, polyvinylidene fluoride as a binder, LATP having an average particle diameter of 3 μm as a solid electrolyte, and needle-like (short axis: conductive aid) 0.13 μm, long axis: 1.68 μm) conductive titanium oxide (a rutile-type titanium oxide base material coated with SnO 2 conductive layer doped with Sb) in a volume ratio of 5: 30: 30: 10 : A negative electrode paste was prepared by adding an appropriate amount of NMP. This negative electrode paste was applied to an aluminum foil having a thickness of 20 μm, dried by heating in the atmosphere of 90 ° C. × 1 hr, and then pressed to obtain a negative electrode sheet having a negative electrode active material layer thickness of 10 μm. This was punched into a disk shape having a diameter of 14 mm.
　＜固体電解質層＞
　固体電解質である平均粒径３μｍのＬＡＴＰと、バインダーであるポリフッ化ビニリデンとをそれぞれ体積比で、７０：３０となるように調合し、さらに、NMPを適量添加して固体電解質ペーストを作製した。このペーストを厚さ５０μｍのポリイミドシートに塗布し、９０℃×１ｈｒの大気中加熱による乾燥後、プレスし、厚さ１５μｍの固体電解質シートを得た。これを直径１４ｍｍの円盤状に打ち抜き、ポリイミドシートから分離して固体電解質層とした。 <Solid electrolyte layer>
LATP having an average particle diameter of 3 μm as a solid electrolyte and polyvinylidene fluoride as a binder were mixed in a volume ratio of 70:30, and an appropriate amount of NMP was added to prepare a solid electrolyte paste. This paste was applied to a polyimide sheet having a thickness of 50 μm, dried by heating in the atmosphere of 90 ° C. × 1 hr, and then pressed to obtain a solid electrolyte sheet having a thickness of 15 μm. This was punched out into a disk shape having a diameter of 14 mm and separated from the polyimide sheet to obtain a solid electrolyte layer.
　＜電池化＞
　上記の正極、固体電解質層、負極を積層し、正極層／固体電解質層／負極層の界面の密着性を向上させるため、この積層体を加圧しながら、１２０℃×１ｈｒの真空中熱処理をして各層の界面を十分密着させた。得られた積層体の側面を絶縁物でマスキングし、これをＣＲ２０２５型のコイン電池に組み込み全固体電池を作製した。 <Battery>
In order to laminate the positive electrode, the solid electrolyte layer, and the negative electrode and improve the adhesion at the interface of the positive electrode layer / solid electrolyte layer / negative electrode layer, a heat treatment in vacuum of 120 ° C. × 1 hr is performed while pressing the laminate. Thus, the interface of each layer was sufficiently adhered. The side surface of the obtained laminate was masked with an insulator, and this was incorporated into a CR2025 type coin battery to produce an all-solid battery.
　＜電池特性評価＞
　実施例１、実施例４、比較例で作製した電池について、０．１Ｃ、１Ｃレートでの放電容量を測定した。その結果を表１に示す。 <Battery characteristics evaluation>
About the battery produced by Example 1, Example 4, and the comparative example, the discharge capacity in 0.1C and 1C rate was measured. The results are shown in Table 1.
　電池の放電容量のレート特性およびサイクル維持率において、本実施例の全固体リチウムイオン二次電池の方が比較例よりも優れていることが明らかになった。これはイオン伝導性を有するバナジウム酸化物ガラスで活物質粒子と固体電解質粒子との間隙を充たすことによって、両者間で十分なイオン伝導経路が確保されたことに起因している。また実施例４の電池では特に放電容量が大きいが、正極活物質として用いたバナジウム酸化物ガラスの容量が大きいためである。 It has been clarified that the all-solid lithium ion secondary battery of this example is superior to the comparative example in the rate characteristics and cycle retention rate of the discharge capacity of the battery. This is because a sufficient ion conduction path is secured between the active material particles and the solid electrolyte particles by filling the gap between the active material particles and the solid electrolyte particles with vanadium oxide glass having ion conductivity. The battery of Example 4 has a particularly large discharge capacity because the capacity of the vanadium oxide glass used as the positive electrode active material is large.
Figure JPOXMLDOC01-appb-T000001
Figure JPOXMLDOC01-appb-T000001
　１０１、２０１、３０１　正極集電体
　１０２、２０２、３０２　正極活物質粒子
　１０３、２０３、３０３　バナジウム酸化物ガラス
　１０４、３０４　固体電解質粒子
　１０５、２０５　負極活物質粒子
　１０６、２０６　負極集電体
　１０７、２０４、３０６　正極活物質層
　１０８、３０７　固体電解質層
　１０９、２０８　負極活物質層
　２０７　ガラス層
　３０５　リチウム金属負極 101, 201, 301 Positive electrode current collector 102, 202, 302 Positive electrode active material particles 103, 203, 303 Vanadium oxide glass 104, 304 Solid electrolyte particles 105, 205 Negative electrode active material particles 106, 206 Negative electrode current collectors 107, 204 , 306 Positive electrode active material layer 108, 307 Solid electrolyte layer 109, 208 Negative electrode active material layer 207 Glass layer 305 Lithium metal negative electrode

Claims (9)

  1. 　正極活物質層と負極活物質層との間に固体電解質層が接合された全固体イオン二次電池において、
    　前記正極活物質層は、正極活物質粒子と固体電解質粒子とがイオン電導性を有するバナジウム酸化物ガラスで結着されて形成され、
    　前記負極活物質層は、負極活物質粒子と固体電解質粒子とがイオン電導性を有するバナジウム酸化物ガラスで結着されて形成されていることを特徴とする全固体イオン二次電池。     In an all solid ion secondary battery in which a solid electrolyte layer is bonded between a positive electrode active material layer and a negative electrode active material layer,
    The positive electrode active material layer is formed by binding positive electrode active material particles and solid electrolyte particles with vanadium oxide glass having ion conductivity,
    The negative electrode active material layer is formed by binding negative electrode active material particles and solid electrolyte particles with vanadium oxide glass having ionic conductivity.
  2. 　請求項１において、前記固体電解質層は、固体電解質粒子が非晶質のイオン電導性を有するバナジウム酸化物ガラスで結着されて形成されていることを特徴とする全固体イオン二次電池。 2. The all-solid ion secondary battery according to claim 1, wherein the solid electrolyte layer is formed by binding solid electrolyte particles with vanadium oxide glass having amorphous ion conductivity.
  3. 　請求項１において、前記固体電解質層および前記固体電解質粒子は、非晶質のイオン電導性を有するバナジウム酸化物ガラスで形成されていることを特徴とする全固体イオン二次電池。 2. The all solid ion secondary battery according to claim 1, wherein the solid electrolyte layer and the solid electrolyte particles are formed of vanadium oxide glass having amorphous ion conductivity.
  4. 　請求項１において、前記イオン伝導性を有するバナジウム酸化物ガラスはテルルと燐の少なくとも１種を含むことを特徴とする全固体イオン二次電池。 2. The all-solid ion secondary battery according to claim 1, wherein the ion conductive vanadium oxide glass contains at least one of tellurium and phosphorus.
  5. 　請求項１において、前記イオン伝導性を有するバナジウム酸化物ガラスは軟化点が５００℃以下であることを特徴とする全固体イオン二次電池。 2. The all-solid-ion secondary battery according to claim 1, wherein the vanadium oxide glass having ion conductivity has a softening point of 500 ° C. or lower.
  6. 　請求項１において、前記イオン伝導性を有するバナジウム酸化物ガラスの少なくとも一部が結晶化していることを特徴とする全固体イオン二次電池。 2. The all-solid-ion secondary battery according to claim 1, wherein at least part of the vanadium oxide glass having ion conductivity is crystallized.
  7. 　請求項１において、前記活物質粒子がイオン電導性を有するバナジウム酸化物ガラスで形成されることを特徴とする全固体イオン二次電池。 2. The all solid state ion secondary battery according to claim 1, wherein the active material particles are formed of vanadium oxide glass having ion conductivity.
  8. 　請求項７において、前記活物質粒子の少なくとも一部が結晶化していることを特徴とする全固体イオン二次電池。 8. The all-solid-ion secondary battery according to claim 7, wherein at least a part of the active material particles are crystallized.
  9. 　請求項１において、前記負極活物質層に替えてリチウム金属またはリチウム合金である負極を用いることを特徴とするイオン二次電池。 2. The ion secondary battery according to claim 1, wherein a negative electrode made of lithium metal or a lithium alloy is used instead of the negative electrode active material layer.
PCT/JP2012/069284 2012-07-30 2012-07-30 All-solid ion secondary cell WO2014020654A1 (en)

Priority Applications (2)

Application Number Priority Date Filing Date Title
PCT/JP2012/069284 WO2014020654A1 (en) 2012-07-30 2012-07-30 All-solid ion secondary cell
JP2014527829A JPWO2014020654A1 (en) 2012-07-30 2012-07-30 All solid ion secondary battery

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/JP2012/069284 WO2014020654A1 (en) 2012-07-30 2012-07-30 All-solid ion secondary cell

Publications (1)

Publication Number Publication Date
WO2014020654A1 true WO2014020654A1 (en) 2014-02-06

Family

ID=50027387

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2012/069284 WO2014020654A1 (en) 2012-07-30 2012-07-30 All-solid ion secondary cell

Country Status (2)

Country Link
JP (1) JPWO2014020654A1 (en)
WO (1) WO2014020654A1 (en)

Cited By (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2015132845A1 (en) * 2014-03-03 2015-09-11 株式会社日立製作所 All-solid-state battery
WO2015147279A1 (en) * 2014-03-28 2015-10-01 富士フイルム株式会社 All-solid secondary cell, solid electrolyte composition and cell electrode sheet used for same, and method for manufacturing cell electrode sheet and all-solid secondary cell
JP2015204179A (en) * 2014-04-14 2015-11-16 株式会社日立製作所 Method for manufacturing electrode for all-solid battery, and method for manufacturing all-solid battery
JP2015220011A (en) * 2014-05-15 2015-12-07 富士通株式会社 Solid electrolyte structure, method for manufacturing the same, and all-solid battery
JP2016066584A (en) * 2014-05-09 2016-04-28 ソニー株式会社 Electrode, method of producing the same, battery, and electronic device
WO2017104405A1 (en) * 2015-12-16 2017-06-22 富士フイルム株式会社 Material for electrodes, electrode sheet for all-solid-state secondary batteries, all-solid-state secondary battery, method for producing electrode sheet for all-solid-state secondary batteries, and method for producing all-solid-state secondary battery
WO2018092434A1 (en) * 2016-11-17 2018-05-24 株式会社村田製作所 All-solid-state battery, electronic device, electronic card, wearable device, and electric vehicle
WO2018123479A1 (en) * 2016-12-27 2018-07-05 日本碍子株式会社 Lithium ion cell and method for manufacturing same
JP2018142439A (en) * 2017-02-27 2018-09-13 富士通株式会社 All-solid battery and manufacturing method of the same, and joint material
CN113471517A (en) * 2020-03-31 2021-10-01 本田技研工业株式会社 All-solid-state battery and method for manufacturing same
US20220115661A1 (en) * 2019-01-25 2022-04-14 Semiconductor Energy Laboratory Co., Ltd. All-solid-state battery and manufacturing method thereof

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2000277119A (en) * 1999-03-26 2000-10-06 Kyocera Corp Lithium battery
JP2000340261A (en) * 1999-04-07 2000-12-08 Hydro Quebec COMPLEX TREATMENT WITH LiPO3
JP2001126757A (en) * 1999-10-25 2001-05-11 Kyocera Corp Lithium battery
JP2011014373A (en) * 2009-07-02 2011-01-20 Hitachi Powdered Metals Co Ltd Conductive material and positive electrode material for lithium ion secondary battery using the same
JP2011119263A (en) * 2009-12-04 2011-06-16 Schott Ag Material for battery electrode, battery electrode containing the same, battery equipped with the electrodes, preparation method of the material for battery electrode
JP2011119141A (en) * 2009-12-04 2011-06-16 Sumitomo Electric Ind Ltd Positive electrode for nonaqueous electrolyte battery, method for manufacturing the same, and nonaqueous electrolyte battery
JP2011241133A (en) * 2010-05-21 2011-12-01 Hitachi Ltd Crystallized glass and method for producing the same

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3854985B2 (en) * 2001-07-18 2006-12-06 財団法人北九州産業学術推進機構 Vanadate glass and method for producing vanadate glass

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2000277119A (en) * 1999-03-26 2000-10-06 Kyocera Corp Lithium battery
JP2000340261A (en) * 1999-04-07 2000-12-08 Hydro Quebec COMPLEX TREATMENT WITH LiPO3
JP2001126757A (en) * 1999-10-25 2001-05-11 Kyocera Corp Lithium battery
JP2011014373A (en) * 2009-07-02 2011-01-20 Hitachi Powdered Metals Co Ltd Conductive material and positive electrode material for lithium ion secondary battery using the same
JP2011119263A (en) * 2009-12-04 2011-06-16 Schott Ag Material for battery electrode, battery electrode containing the same, battery equipped with the electrodes, preparation method of the material for battery electrode
JP2011119141A (en) * 2009-12-04 2011-06-16 Sumitomo Electric Ind Ltd Positive electrode for nonaqueous electrolyte battery, method for manufacturing the same, and nonaqueous electrolyte battery
JP2011241133A (en) * 2010-05-21 2011-12-01 Hitachi Ltd Crystallized glass and method for producing the same

Cited By (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2015132845A1 (en) * 2014-03-03 2015-09-11 株式会社日立製作所 All-solid-state battery
US10297859B2 (en) 2014-03-28 2019-05-21 Fujifilm Corporation All-solid-state secondary battery, solid electrolyte composition and electrode sheet for batteries used in the same, and manufacturing method of electrode sheet for batteries and all-solid-state secondary battery
WO2015147279A1 (en) * 2014-03-28 2015-10-01 富士フイルム株式会社 All-solid secondary cell, solid electrolyte composition and cell electrode sheet used for same, and method for manufacturing cell electrode sheet and all-solid secondary cell
JP2015191864A (en) * 2014-03-28 2015-11-02 富士フイルム株式会社 All-solid type secondary battery, solid electrolytic composition used therefor, electrode sheet for batteries, and method for manufacturing all-solid type secondary battery
JP2015204179A (en) * 2014-04-14 2015-11-16 株式会社日立製作所 Method for manufacturing electrode for all-solid battery, and method for manufacturing all-solid battery
JP2016066584A (en) * 2014-05-09 2016-04-28 ソニー株式会社 Electrode, method of producing the same, battery, and electronic device
JP2015220011A (en) * 2014-05-15 2015-12-07 富士通株式会社 Solid electrolyte structure, method for manufacturing the same, and all-solid battery
WO2017104405A1 (en) * 2015-12-16 2017-06-22 富士フイルム株式会社 Material for electrodes, electrode sheet for all-solid-state secondary batteries, all-solid-state secondary battery, method for producing electrode sheet for all-solid-state secondary batteries, and method for producing all-solid-state secondary battery
US10693190B2 (en) 2015-12-16 2020-06-23 Fujifilm Corporation Material for electrode, electrode sheet for all-solid state secondary battery, all-solid state secondary battery, and methods for manufacturing electrode sheet for all-solid state secondary battery and all-solid state secondary battery
JPWO2017104405A1 (en) * 2015-12-16 2018-09-20 富士フイルム株式会社 Electrode material, electrode sheet for all-solid-state secondary battery, all-solid-state secondary battery, electrode sheet for all-solid-state secondary battery, and method for producing all-solid-state secondary battery
WO2018092434A1 (en) * 2016-11-17 2018-05-24 株式会社村田製作所 All-solid-state battery, electronic device, electronic card, wearable device, and electric vehicle
WO2018123479A1 (en) * 2016-12-27 2018-07-05 日本碍子株式会社 Lithium ion cell and method for manufacturing same
JPWO2018123479A1 (en) * 2016-12-27 2019-10-31 日本碍子株式会社 Lithium ion battery and manufacturing method thereof
JP7009390B2 (en) 2016-12-27 2022-01-25 日本碍子株式会社 Lithium-ion battery and its manufacturing method
JP2018142439A (en) * 2017-02-27 2018-09-13 富士通株式会社 All-solid battery and manufacturing method of the same, and joint material
US20220115661A1 (en) * 2019-01-25 2022-04-14 Semiconductor Energy Laboratory Co., Ltd. All-solid-state battery and manufacturing method thereof
CN113471517A (en) * 2020-03-31 2021-10-01 本田技研工业株式会社 All-solid-state battery and method for manufacturing same
JP2021163579A (en) * 2020-03-31 2021-10-11 本田技研工業株式会社 All-solid battery and manufacturing method therefor
US11817549B2 (en) 2020-03-31 2023-11-14 Honda Motor Co., Ltd. All-solid-state battery and method for manufacturing same

Also Published As

Publication number Publication date
JPWO2014020654A1 (en) 2016-07-11

Similar Documents

Publication Publication Date Title
WO2014020654A1 (en) All-solid ion secondary cell
JP5987103B2 (en) All solid ion secondary battery
JP6085370B2 (en) All solid state battery, electrode for all solid state battery and method for producing the same
WO2014141456A1 (en) Solid electrolyte, and all-solid ion secondary cell using same
US8808407B2 (en) Method of manufacturing a solid lithium ion secondary battery with an electrolyte layer and/or positive electrode layer containing a crystallite having a lithium ion conducting property
JP5484928B2 (en) All solid battery
JP6240306B2 (en) Lithium secondary battery
JP5312969B2 (en) Method for producing lithium ion secondary battery
US10530015B2 (en) All-solid-state lithium secondary battery and method for producing the same
JP5731278B2 (en) All-solid-state lithium ion battery
JP5551542B2 (en) All-solid battery and method for producing all-solid battery
TWI453973B (en) Lithium ion secondary battery and manufacturing method thereof
WO2015037270A1 (en) Solid electrolyte, and all-solid ion secondary battery using same
JP2016201310A (en) All-solid-state lithium secondary battery
JP2011165410A (en) All solid lithium ion secondary battery and method for manufacturing the same
JPWO2008059987A1 (en) Solid electrolyte structure for all solid state battery, all solid state battery, and manufacturing method thereof
JP4575487B2 (en) Lithium ion secondary battery and manufacturing method thereof
JP6259704B2 (en) Method for producing electrode for all solid state battery and method for producing all solid state battery
JP2020184407A (en) All-solid battery
WO2014170998A1 (en) All-solid-state lithium-ion secondary battery
JPWO2018225494A1 (en) All solid sodium ion secondary battery
JP2018170189A (en) All-solid type secondary battery
JP6578743B2 (en) Electrode manufacturing method
JP2017168282A (en) Electrode composite, battery, method for manufacturing electrode composite, and method for manufacturing battery
JP6102615B2 (en) Negative electrode active material and secondary battery using the same

Legal Events

Date Code Title Description
121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 12882200

Country of ref document: EP

Kind code of ref document: A1

ENP Entry into the national phase

Ref document number: 2014527829

Country of ref document: JP

Kind code of ref document: A

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 12882200

Country of ref document: EP

Kind code of ref document: A1