WO2016051934A1 - 層状複水酸化物を用いた電池 - Google Patents
層状複水酸化物を用いた電池 Download PDFInfo
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- WO2016051934A1 WO2016051934A1 PCT/JP2015/070714 JP2015070714W WO2016051934A1 WO 2016051934 A1 WO2016051934 A1 WO 2016051934A1 JP 2015070714 W JP2015070714 W JP 2015070714W WO 2016051934 A1 WO2016051934 A1 WO 2016051934A1
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- H—ELECTRICITY
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- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M10/00—Secondary cells; Manufacture thereof
- H01M10/24—Alkaline accumulators
- H01M10/26—Selection of materials as electrolytes
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- 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
- H01M10/34—Gastight accumulators
- H01M10/345—Gastight metal hydride accumulators
- H01M10/347—Gastight metal hydride accumulators with solid electrolyte
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M12/00—Hybrid cells; Manufacture thereof
- H01M12/04—Hybrid cells; Manufacture thereof composed of a half-cell of the fuel-cell type and of a half-cell of the primary-cell type
- H01M12/06—Hybrid cells; Manufacture thereof composed of a half-cell of the fuel-cell type and of a half-cell of the primary-cell type with one metallic and one gaseous electrode
- H01M12/065—Hybrid cells; Manufacture thereof composed of a half-cell of the fuel-cell type and of a half-cell of the primary-cell type with one metallic and one gaseous electrode with plate-like electrodes or stacks of plate-like electrodes
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- 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
- H01M4/24—Electrodes for alkaline accumulators
- H01M4/244—Zinc electrodes
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- 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
- H01M4/24—Electrodes for alkaline accumulators
- H01M4/32—Nickel oxide or hydroxide electrodes
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M4/00—Electrodes
- H01M4/02—Electrodes composed of, or comprising, active material
- H01M4/36—Selection of substances as active materials, active masses, active liquids
- H01M4/38—Selection of substances as active materials, active masses, active liquids of elements or alloys
- H01M4/42—Alloys based on zinc
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M4/00—Electrodes
- H01M4/02—Electrodes composed of, or comprising, active material
- H01M4/36—Selection of substances as active materials, active masses, active liquids
- H01M4/48—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides
- H01M4/52—Selection of substances as active materials, active masses, active liquids of inorganic oxides or hydroxides of nickel, cobalt or iron
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M50/00—Constructional details or processes of manufacture of the non-active parts of electrochemical cells other than fuel cells, e.g. hybrid cells
- H01M50/40—Separators; Membranes; Diaphragms; Spacing elements inside cells
- H01M50/409—Separators, membranes or diaphragms characterised by the material
- H01M50/431—Inorganic material
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M50/00—Constructional details or processes of manufacture of the non-active parts of electrochemical cells other than fuel cells, e.g. hybrid cells
- H01M50/40—Separators; Membranes; Diaphragms; Spacing elements inside cells
- H01M50/409—Separators, membranes or diaphragms characterised by the material
- H01M50/431—Inorganic material
- H01M50/434—Ceramics
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M50/00—Constructional details or processes of manufacture of the non-active parts of electrochemical cells other than fuel cells, e.g. hybrid cells
- H01M50/40—Separators; Membranes; Diaphragms; Spacing elements inside cells
- H01M50/409—Separators, membranes or diaphragms characterised by the material
- H01M50/446—Composite material consisting of a mixture of organic and inorganic materials
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M50/00—Constructional details or processes of manufacture of the non-active parts of electrochemical cells other than fuel cells, e.g. hybrid cells
- H01M50/40—Separators; Membranes; Diaphragms; Spacing elements inside cells
- H01M50/409—Separators, membranes or diaphragms characterised by the material
- H01M50/449—Separators, membranes or diaphragms characterised by the material having a layered structure
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- 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
- H01M2300/0002—Aqueous electrolytes
- H01M2300/0014—Alkaline electrolytes
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M50/00—Constructional details or processes of manufacture of the non-active parts of electrochemical cells other than fuel cells, e.g. hybrid cells
- H01M50/40—Separators; Membranes; Diaphragms; Spacing elements inside cells
- H01M50/489—Separators, membranes, diaphragms or spacing elements inside the cells, characterised by their physical properties, e.g. swelling degree, hydrophilicity or shut down properties
- H01M50/491—Porosity
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- 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
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P70/00—Climate change mitigation technologies in the production process for final industrial or consumer products
- Y02P70/50—Manufacturing or production processes characterised by the final manufactured product
Definitions
- the present invention relates to a battery using layered double hydroxide (LDH).
- LDH layered double hydroxide
- zinc secondary batteries such as nickel zinc secondary batteries and zinc-air secondary batteries have been developed and studied for a long time, they have not yet been put into practical use. This is because the zinc constituting the negative electrode produces dendritic crystals called dendrite during charging, and this dendrite breaks through the separator and causes a short circuit with the positive electrode. Therefore, a technique for preventing a short circuit due to zinc dendrite in a zinc secondary battery such as a nickel zinc secondary battery or a zinc-air secondary battery is strongly desired.
- Patent Document 1 International Publication No. 2013/118561 discloses a separator made of a hydroxide ion conductive LDH-containing solid electrolyte for the purpose of preventing a short circuit caused by zinc dendrite in a nickel zinc secondary battery.
- an aqueous potassium hydroxide (KOH) solution is used as an electrolytic solution, and improvements thereof have been proposed.
- the electrolyte in contact with the zinc negative electrode is composed of an aqueous KOH solution having an initial concentration of 4 to 8 M in which 70 to 100 g of aluminum is dissolved.
- An alkaline storage battery is disclosed, and the solubility of zinc in the electrolyte is limited by the addition of aluminum.
- the ion exchange membrane used in the examples of this document is a hydrocarbon-based ion exchange membrane, not a ceramic separator.
- the present applicant has succeeded in developing an LDH separator (layered double hydroxide separator) that has hydroxide ion conductivity but is highly densified to such an extent that it does not have water permeability and air permeability.
- a separator or a separator with a porous substrate
- a short circuit due to zinc dendrite (especially in the case of a metal-air secondary battery) (Problem) carbon dioxide contamination can be prevented.
- a battery using a layered double hydroxide is provided so as to be in contact with a positive electrode, a negative electrode, an electrolyte solution that is an alkali metal hydroxide aqueous solution, and the electrolyte solution.
- a battery configured such that a metal compound containing a metal element corresponding to M 2+ and / or M 3+ is dissolved in the electrolytic solution, whereby erosion of the layered double hydroxide by the electrolytic solution is suppressed.
- the battery includes the layered double hydroxide as a separator having hydroxide ion conductivity, and the separator can separate the positive electrode and the negative electrode.
- the positive electrode is an air electrode
- the negative electrode is immersed in the electrolyte
- the battery includes a container for storing the negative electrode and the electrolyte, and the container has an opening.
- the separator closes the opening so as to be in contact with the electrolytic solution to form the container and a negative electrode side sealed space, thereby isolating the air electrode and the electrolytic solution so as to conduct hydroxide ions, thereby
- the battery may be a zinc air secondary battery.
- FIG. 3B is a perspective view of the zinc-air secondary battery shown in FIG. 3A. It is a schematic cross section showing one mode of a separator with a porous substrate. It is a schematic cross section which shows the other one aspect
- LDH layered double hydroxide
- 4 is an SEM image obtained by observing the microstructure of an LDH dense body before being immersed in a KOH aqueous solution in Example 2.
- 4 is an SEM image obtained by observing the microstructure of an LDH dense body after being immersed in an aqueous KOH solution having an Al concentration of 0.7 mol / L for 1 week at 30 ° C. in Example 2.
- FIG. 4 is an SEM image obtained by observing the microstructure of an LDH dense body after being immersed in an aqueous KOH solution with an Al concentration of 0.7 mol / L at 70 ° C. for one week in Example 2.
- FIG. 6 is a schematic cross-sectional view of a denseness discrimination measurement system used in Example 3.
- FIG. 6 is an exploded perspective view of a measurement sealed container used in a denseness determination test II of Example 3.
- FIG. 6 is a schematic cross-sectional view of a measurement system used in a denseness determination test II of Example 3.
- FIG. 6 is a schematic cross-sectional view of a measurement system used in a denseness determination test II of Example 3.
- the battery of the present invention is a battery using layered double hydroxide (LDH).
- LDH layered double hydroxide
- the constituent member containing LDH include a separator, an electrolyte, an electrode protective agent (for example, a negative electrode protective agent), and the like.
- desirable characteristics such as hydroxide ion conductivity of LDH can be exhibited to improve battery performance.
- the separator may be composed of LDH alone, or may be a composite separator including LDH and another material (for example, a polymer) combined.
- LDH may be used for various battery constituent members. In such battery constituent members, LDH may be used alone or in combination with LDH and other materials (for example, polymer). Good.
- the battery may be either a primary battery or a secondary battery, but a secondary battery is preferable.
- a nickel zinc secondary battery and a zinc-air secondary battery are preferable. Accordingly, in the following general description, reference may be made to FIG. 1 relating to a nickel zinc secondary battery and FIGS. 3A and 3B relating to a zinc air secondary battery, but the battery of the present invention may be referred to as a nickel zinc secondary battery and a zinc air secondary battery. It should not be limited to the secondary battery, but conceptually includes various types of batteries as described above that can employ LDH.
- a battery according to one embodiment of the present invention includes a positive electrode, a negative electrode, an electrolytic solution, and a layered double hydroxide (LDH).
- a separator is provided in contact with the electrolyte and capable of separating the positive electrode and the negative electrode.
- the LDH is provided so as to be in contact with the electrolytic solution, and may be any battery constituent member such as a separator as described above.
- LDH is, M 2+ 1-x M 3+ x (OH) 2 A n- x / n ⁇ mH 2 O (wherein, M 2+ is a divalent cation, M 3+ is trivalent cation , A n ⁇ is an n-valent anion, n is an integer of 1 or more, and x is 0.1 to 0.4.
- the electrolytic solution is an alkali metal hydroxide (KOH) aqueous solution. That is, as described above, a high hydroxide ion conductivity is required for the electrolyte solution of a battery to which LDH is applied (for example, a metal-air battery or a nickel-zinc battery). It is desirable to use a KOH aqueous solution.
- LDH is desired to have a high alkali resistance that hardly deteriorates even in such a strong alkaline electrolyte.
- the present inventors have now obtained the knowledge that degradation of LDH due to an alkaline electrolyte can be significantly reduced by intentionally dissolving a predetermined metal compound in the alkaline electrolyte.
- the battery of the present invention includes a metal element corresponding to M 2+ and / or M 3+ in the general formula of LDH: M 2+ 1-x M 3+ x (OH) 2 A n ⁇ x / n ⁇ mH 2 O
- the battery is configured such that the metal compound is dissolved in the electrolytic solution, thereby preventing erosion of the layered double hydroxide by the electrolytic solution.
- the excellent hydroxide ion conductivity inherent in the layered double hydroxide and the excellent denseness that the LDH-containing member can have for a long period of time. Can be desirably maintained over time. That is, according to the present invention, it is possible to provide a highly reliable secondary battery capable of significantly reducing deterioration of the layered double hydroxide (LDH) contained in the battery due to the alkaline electrolyte.
- LDH layered double hydroxide
- LDH is a general formula: M 2+ 1-x M 3+ x (OH) 2 A n ⁇ x / n ⁇ mH 2 O (where M 2+ is a divalent cation and M 3+ is a trivalent cation) A n ⁇ is an n-valent anion, n is an integer of 1 or more, x is 0.1 to 0.4, and m is an arbitrary real number).
- M 2+ may be any divalent cation, and preferred examples include Mg 2+ , Ca 2+ and Zn 2+ , and more preferably Mg 2+ .
- M 3+ may be any trivalent cation, but preferred examples include Al 3+ or Cr 3+ , and more preferred is Al 3+ .
- a n- can be any anion, but preferred examples include OH - and CO 3 2- . Therefore, in the general formula, M 2+ comprises Mg 2+, M 3+ comprises Al 3+, A n-is OH - and / or CO preferably contains 3 2-.
- n is an integer of 1 or more, preferably 1 or 2.
- x is 0.1 to 0.4, preferably 0.2 to 0.35.
- m is an arbitrary real number. More specifically, m is a real number or an integer of 0 or more, typically more than 0 or 1 or more.
- LDH may be combined with other materials and used for battery components.
- examples of other materials include polymers, zinc-containing compounds, alumina, silica, polymers, conductive carbon, conductive ceramics, and the like, and polymers are particularly preferable.
- polymer examples include hydrocarbon moiety-containing polymers such as polyethylene and polypropylene, aromatic group-containing polymers typified by polystyrene, etc .; ether group-containing polymers typified by alkylene glycol, etc .; polyvinyl alcohol and poly ( ⁇ - Hydroxymethyl acrylate) and other hydroxyl group-containing polymers; polyamide, nylon, polyacrylamide, polyvinylpyrrolidone, N-substituted polyacrylamide and other amide bond-containing polymers; polymaleimide and other imide bond-containing polymers Polymer; carboxyl group-containing polymer represented by poly (meth) acrylic acid, polymaleic acid, polyitaconic acid, polymethyleneglutaric acid, etc .; poly (meth) acrylate, polymaleate, polyitaconate, polymethyleneglu Carboxylate-containing polymers such as oxalates; Halogen-containing polymers such as polyvinyl chloride, polyvinylidene fluoride,
- the electrolytic solution may be any alkaline electrolytic solution that can be used in a battery as long as it is an aqueous alkali metal hydroxide solution.
- an alkali metal hydroxide aqueous solution is preferably used as the positive electrode electrolyte 14 and the negative electrode electrolyte 18.
- the alkali metal hydroxide include potassium hydroxide, sodium hydroxide, lithium hydroxide, ammonium hydroxide and the like, and potassium hydroxide is more preferable.
- a zinc compound such as zinc oxide or zinc hydroxide may be added to the electrolytic solution in order to suppress self-dissolution of the zinc alloy.
- the alkaline electrolyte may be mixed with the positive electrode and / or the negative electrode to be present in the form of a positive electrode mixture and / or a negative electrode mixture.
- the electrolytic solution may be gelled in order to prevent leakage of the electrolytic solution.
- the gelling agent it is desirable to use a polymer that swells by absorbing the solvent of the electrolytic solution, and polymers such as polyethylene oxide, polyvinyl alcohol, and polyacrylamide, and starch are used.
- the electrolytic solution corresponds to the general formula of the layered double hydroxide: M 2+ 1-x M 3+ x (OH) 2 A n ⁇ x / n ⁇ mH 2 O, M 2+ and / or M 3+ .
- a metal compound containing a metal element is dissolved.
- the metal compound is intentionally dissolved in the electrolytic solution, and is preferably dissolved in advance in the electrolytic solution. For example, it may be dissolved at the time of manufacturing the battery or the electrolytic solution or before using the battery. Of course, the metal compound may be dissolved in the electrolytic solution afterwards (for example, when the battery is used). In this case, the metal compound may be gradually dissolved as the battery is used.
- the metal element only needs to be dissolved in the electrolyte solution in some form, and can typically be dissolved in the electrolyte solution in the form of metal ions, hydroxides and / or hydroxy complexes.
- metal ions for example, Al 3+ , Al (OH) 2+ , Al (OH) 2 + , Al (OH) 3 0 , Al (OH) 4 ⁇ , Al (OH) 5 2 ⁇ and the like are dissolved in the form of Al.
- the metal compound preferably contains a metal element corresponding to M 3+ , and preferred examples of such a metal element include Al and Cr, and most preferably Al.
- the upper limit of the concentration of Al in the electrolytic solution is not particularly limited, and may reach the saturation solubility of the Al compound, but is, for example, 20 mol / L or less or 10 mol / L or less.
- the air electrode 32 (positive electrode) does not need to be completely accommodated in the container 46, and is simply attached so as to close the opening 46a of the container 46 (for example, in the form of a lid).
- the positive electrode and the alkaline electrolyte need not necessarily be separated, and may be configured as a positive electrode mixture in which the positive electrode and the alkaline electrolyte are mixed. No liquid is required.
- the negative electrode and the alkaline electrolyte need not necessarily be separated, and may be configured as a negative electrode mixture in which the negative electrode and the alkaline electrolyte are mixed.
- a positive electrode current collector may be provided in contact with the positive electrode.
- a negative electrode current collector may be provided in contact with the negative electrode.
- the battery is preferably provided with LDH as a separator having hydroxide ion conductivity, and the separator separates the positive electrode and the negative electrode.
- the separator 20 contains a positive electrode chamber 24 containing the positive electrode 12 and the positive electrode electrolyte solution 14, and a negative electrode 16 and a negative electrode electrolyte solution 18 in the container 22.
- the separator 40 may block the opening 46a of the container 46 so as to be in contact with the electrolytic solution 36, as in the zinc-air secondary battery 30 shown in FIG. 3A.
- the container 46 and the negative electrode side sealed space may be formed.
- the separator preferably has a hydroxide ion conductivity but is so dense that it does not have water permeability and air permeability. That is, the fact that the separator does not have water permeability and air permeability means that the separator has a high degree of denseness that does not allow water and gas to pass through. It means not a porous material. For this reason, in the case of a zinc secondary battery, it has a very effective configuration for physically preventing penetration of the separator by zinc dendrite generated during charging and preventing a short circuit between the positive and negative electrodes.
- the separator is made of a solid electrolyte body containing LDH (hereinafter referred to as an LDH-containing solid electrolyte body) and thereby has hydroxide ion conductivity.
- LDH-containing solid electrolyte body a solid electrolyte body containing LDH
- the separator or the LDH-containing solid electrolyte body may be composed of LDH, or may further include another material (for example, a polymer) in addition to LDH.
- the other material that can be used together with LDH may be a material that itself has hydroxide ion conductivity, or may be a material that does not have hydroxide ion conductivity.
- Such a dense and hard LDH-containing solid electrolyte body can be produced through hydrothermal treatment. Accordingly, a simple green compact that has not been subjected to hydrothermal treatment is not preferable as the LDH-containing solid electrolyte of the present invention because it is not dense and is brittle in solution. However, any manufacturing method can be adopted as long as a dense and hard LDH-containing solid electrolyte body can be obtained, even if it has not undergone hydrothermal treatment.
- the separator or the LDH-containing solid electrolyte body may be a composite of a particle group including LDH and an auxiliary component that assists densification and curing of the particle group.
- the separator may be a composite of an open-pore porous material as a base material and LDH deposited and grown in the pores so as to fill the pores of the porous material.
- the substance constituting the porous body include ceramics such as alumina and zirconia, and insulating substances such as a porous sheet made of a foamed resin or a fibrous substance.
- the separator or LDH-containing solid electrolyte body is preferably densified by hydrothermal treatment.
- Hydrothermal treatment is extremely effective for the densification of layered double hydroxides, especially Mg—Al type layered double hydroxides. Densification by hydrothermal treatment is performed, for example, as described in Patent Document 1 (International Publication No. 2013/118561), in which pure water and a plate-shaped green compact are placed in a pressure vessel, and 120 to 250 ° C., preferably The reaction can be carried out at a temperature of 180 to 250 ° C., 2 to 24 hours, preferably 3 to 10 hours. However, a more preferable production method using hydrothermal treatment will be described later.
- the separator or the LDH-containing solid electrolyte body may be in any form of a plate, film, or layer.
- the film-like or layered LDH-containing solid electrolyte is a porous substrate. It is preferably formed on or in the material.
- the plate-like form is used, sufficient hardness can be secured and penetration of zinc dendrites can be more effectively prevented.
- the film or layer form is thinner than the plate, there is an advantage that the resistance of the separator can be significantly reduced while ensuring the minimum necessary hardness to prevent the penetration of zinc dendrite. is there.
- a preferable thickness of the plate-like LDH-containing solid electrolyte body is 0.01 to 0.5 mm, more preferably 0.02 to 0.2 mm, and still more preferably 0.05 to 0.1 mm.
- the hydroxide ion conductivity of the LDH-containing solid electrolyte body is preferably as high as possible, but typically has a conductivity of 10 ⁇ 4 to 10 ⁇ 1 S / m.
- the thickness is preferably 100 ⁇ m or less, more preferably 75 ⁇ m or less, still more preferably 50 ⁇ m or less, particularly preferably 25 ⁇ m or less, and most preferably 5 ⁇ m or less.
- the resistance of the separator can be reduced by being thin.
- the lower limit of the thickness is not particularly limited because it varies depending on the application, but in order to ensure a certain degree of rigidity desired as a separator film or layer, the thickness is preferably 1 ⁇ m or more, more preferably 2 ⁇ m or more. is there.
- a porous substrate may be provided on one side or both sides of the separator. It goes without saying that the porous substrate 28 has water permeability, and therefore, the alkaline electrolyte can reach the separator. However, the presence of the porous substrate allows hydroxide ions to be more stably formed on the separator. It can also be held. In addition, since the strength can be imparted by the porous base material, the resistance can be reduced by thinning the separator. In addition, a dense film or a dense layer of an LDH-containing solid electrolyte (preferably LDH) can be formed on or in the porous substrate.
- LDH-containing solid electrolyte preferably LDH
- a method of preparing a porous substrate and depositing an inorganic solid electrolyte on the porous substrate can be considered (this method will be described later).
- a porous base material on both surfaces of a separator it can be considered that densification is performed by sandwiching a raw material powder of an inorganic solid electrolyte between two porous base materials.
- the porous substrate 28 is provided over the entire surface of one side of the separator 20, but may be provided only on a part of one side of the separator 20 (for example, a region involved in the charge / discharge reaction).
- the porous substrate is provided over the entire surface of one side of the separator derived from the manufacturing method. It is typical.
- the porous base material is provided only on a part of one side of the separator (for example, a region involved in the charge / discharge reaction). It may be retrofitted or a porous substrate may be retrofitted over the entire surface of one side.
- the positive electrode 12 may further contain an additional element in addition to the nickel hydroxide compound and the different element that can be dissolved therein.
- additional elements include scandium (Sc), lanthanum (La), cerium (Ce), praseodymium (Pr), neodymium (Nd), promethium (Pm), samarium (Sm), europium (Eu), Gadolinium (Gd), terbium (Tb), dysprosium (Dy), holmium (Ho), elpium (Er), thulium (Tm), lutetium (Lu), hafnium (Hf), tantalum (Ta), tungsten (W), Examples include rhenium (Re), osmium (Os), iridium (Ir), platinum (Pt), gold (Au) and mercury (Hg), and any combination thereof.
- the air electrode catalyst is not particularly limited as long as it functions as a positive electrode in a metal-air battery, and various air electrode catalysts that can use oxygen as a positive electrode active material can be used.
- Preferred examples of the air electrode catalyst include carbon-based materials having a redox catalyst function such as graphite, metals having a redox catalyst function such as platinum and nickel, perovskite oxides, manganese dioxide, nickel oxide, cobalt oxide, spinel. Examples thereof include inorganic oxides having a redox catalyst function such as oxides.
- the shape of the air electrode catalyst is not particularly limited, but is preferably a particle shape.
- the content of the air electrode catalyst in the air electrode 12 is not particularly limited, but is preferably 5 to 70% by volume, more preferably 5 to 60% by volume, and still more preferably 5 to 50% by volume with respect to the total amount of the air electrode 12. %.
- the shape of the electron conductive material may be a particle shape or other shapes, but is used in a form that provides a continuous phase in the thickness direction (that is, an electron conductive phase) in the air electrode 32.
- the electron conductive material may be a porous material.
- the electron conductive material may be in the form of a mixture or complex with an air electrode catalyst (for example, platinum-supported carbon).
- an air electrode catalyst for example, a transition metal
- Perovskite-type compounds may be used in a form that provides a continuous phase in the thickness direction (that is, an electron conductive phase) in the air electrode 32.
- the electron conductive material may be a porous material.
- the electron conductive material may be in the form of a mixture or complex with an air electrode catalyst (for example, platinum-supported carbon).
- an air electrode catalyst for example, a transition metal
- Perovskite-type compounds for example, a transition metal
- the air electrode catalyst and the electron conductive material but also the hydroxide ion conductive material is contained in the air electrode 32, so that the electron conductive phase (electron conductive material), the gas phase (air),
- the three-phase interface consisting of is present not only in the interface between the separator 40 (or the intermediate layer, if applicable) and the air electrode 32 but also in the air electrode 32, and exchange of hydroxide ions contributing to the battery reaction.
- the reaction resistance of the air electrode is considered to be reduced in the metal-air battery.
- the content of the hydroxide ion conductive material in the air electrode 32 is not particularly limited, but is preferably 0 to 95% by volume, more preferably 5 to 85% by volume, and still more preferably based on the total amount of the air electrode 32. 10 to 80% by volume.
- the third electrode 38 may be provided so as to be in contact with the electrolytic solution 36 but not to be in contact with the negative electrode 34.
- the third electrode 38 is connected to the air electrode 32 through an external circuit.
- the third electrode 38 is in contact with the electrolytic solution 36, but it is desirable that the third electrode 38 be disposed at a place not directly related to the normal charge / discharge reaction. In this case, even when the electrolyte solution is reduced by disposing a water-holding member made of a water-absorbing resin such as a nonwoven fabric or a liquid-retaining resin so as to be in contact with the third electrode 38 in the negative electrode side sealed space, the electrolytic solution 36 is reduced. Is preferably configured to be held in contact with the third electrode 38 at all times.
- a commercially available battery separator can also be used as the water retaining member.
- Preferable examples of the water absorbent resin or the liquid retaining resin include polyolefin resins.
- the third electrode 38 does not necessarily need to be impregnated with a large amount of electrolytic solution 36, and can exhibit a desired function even when wet with a small amount or a small amount of electrolytic solution 36. As long as the water retaining member has.
- the porous substrate is preferably one that can form an LDH-containing separator layer on and / or in the porous substrate, and the material and porous structure are not particularly limited.
- an LDH-containing separator layer is formed on and / or in a porous substrate, but an LDH-containing separator layer is formed on a non-porous substrate and then non-porous by various known techniques.
- the porous substrate may be made porous.
- the porous base material has a porous structure having water permeability in that the electrolyte solution can reach the separator layer when incorporated into the battery as a battery separator.
- the magnification of the electron microscope (SEM) image used for this measurement is 20000 times, and all obtained pore diameters are arranged in order of size, and the top 15 points and the bottom 15 points from the average value, with 30 points per field of view in total.
- the average pore diameter can be obtained by calculating an average value for two visual fields.
- a length measurement function of SEM software, image analysis software (for example, Photoshop, manufactured by Adobe) or the like can be used.
- the surface of the porous substrate preferably has a porosity of 10 to 60%, more preferably 15 to 55%, still more preferably 20 to 50%. By setting it within these ranges, it is possible to form an LDH-containing separator layer that is so dense that it does not have water permeability while ensuring desired water permeability in the porous substrate.
- the porosity of the surface of the porous substrate is adopted because it is easy to measure the porosity using the image processing described below, and the porosity of the surface of the porous substrate. This is because it can be said that it generally represents the porosity inside the porous substrate. That is, if the surface of the porous substrate is dense, the inside of the porous substrate can be said to be dense as well.
- the porosity of the surface of the porous substrate can be measured as follows by a technique using image processing. That is, 1) An electron microscope (SEM) image of the surface of the porous substrate (acquisition of 10,000 times or more) is obtained, and 2) a grayscale SEM image is read using image analysis software such as Photoshop (manufactured by Adobe). 3) Create a black-and-white binary image by the procedure of [Image] ⁇ [Tonal Correction] ⁇ [Turn Tone], and 4) The value obtained by dividing the number of pixels occupied by the black part by the total number of pixels in the image Rate (%).
- the porosity measurement by this image processing is preferably performed for a 6 ⁇ m ⁇ 6 ⁇ m region on the surface of the porous substrate. In order to obtain a more objective index, three arbitrarily selected regions are used. It is more preferable to employ the average value of the obtained porosity.
- the porosity of the surface of the separator layer is adopted because it is easy to measure the porosity using the image processing described below, and the porosity of the surface of the separator layer is determined inside the separator layer. It is because it can be said that the porosity of is generally expressed. That is, if the surface of the separator layer is dense, it can be said that the inside of the separator layer is also dense.
- the porosity of the surface of the separator layer can be measured as follows by a technique using image processing. That is, 1) An electron microscope (SEM) image (10,000 times or more magnification) of the surface of the separator layer is acquired, and 2) a gray-scale SEM image is read using image analysis software such as Photoshop (manufactured by Adobe).
- the LDH crystal is known to have the form of a plate-like particle having a layered structure as shown in FIG. 6, but the above-mentioned substantially vertical or oblique orientation is obtained by using an LDH-containing separator layer (for example, an LDH dense film).
- an LDH-containing separator layer for example, an LDH dense film
- the hydroxide ion conductivity in the direction in which the LDH plate-like particles are oriented is perpendicular to this. This is because there is a conductivity anisotropy that is much higher than the conductivity in the direction.
- the present applicant has obtained knowledge that the conductivity (S / cm) in the alignment direction is one order of magnitude higher than the conductivity (S / cm) in the direction perpendicular to the alignment direction in the LDH oriented bulk body.
- the substantially vertical or oblique orientation in the LDH-containing separator layer of the present embodiment indicates the conductivity anisotropy that the LDH oriented body can have in the layer thickness direction (that is, the direction perpendicular to the surface of the separator layer or the porous substrate).
- the conductivity in the layer thickness direction can be maximized or significantly increased.
- the LDH-containing separator layer has a layer form, lower resistance can be realized than a bulk form LDH.
- An LDH-containing separator layer having such an orientation is easy to conduct hydroxide ions in the layer thickness direction.
- it since it is densified, it is extremely suitable for a separator that requires high conductivity and denseness in the layer thickness direction.
- the LDH plate-like particles are highly oriented in a substantially vertical direction in the LDH-containing separator layer (typically an LDH dense film).
- LDH-containing separator layer typically an LDH dense film.
- This high degree of orientation is confirmed by the fact that when the surface of the separator layer is measured by an X-ray diffraction method, the peak of the (003) plane is not substantially detected or smaller than the peak of the (012) plane. (However, when a porous substrate in which a diffraction peak is observed at the same position as the peak due to the (012) plane is used, the peak of the (012) plane due to the LDH plate-like particle is used. This is not the case).
- the c-axis direction (00l) plane (l is 3 and 6) to which the (003) plane belongs is a plane parallel to the layered structure of the LDH plate-like particles.
- the LDH layered structure also faces in a substantially vertical direction.
- the separator layer surface is measured by an X-ray diffraction method, the (00l) plane (l is 3 and 6).
- the peak of) does not appear or becomes difficult to appear.
- the peak of the (003) plane tends to be stronger than the peak of the (006) plane when it is present. I can say that. Therefore, in the oriented LDH-containing separator layer, the (003) plane peak is substantially not detected or smaller than the (012) plane peak, suggesting a high degree of vertical orientation. It can be said that it is preferable.
- the thickness of the LDH alignment film is not particularly limited because it varies depending on the application, but in order to ensure a certain degree of hardness desired as a functional film such as a separator, the thickness is preferably 1 ⁇ m or more. Preferably it is 2 micrometers or more.
- the LDH separator with a porous substrate described above is (1) a porous substrate is prepared, and (2) a total of 0.20 to 0.40 mol / L of magnesium ions (Mg 2+ ) and aluminum ions (Al 3+ ).
- a separator comprising a layered double hydroxide by immersing the porous substrate in a raw material aqueous solution containing urea at a concentration and (3) hydrothermally treating the porous substrate in the raw material aqueous solution It can be produced by forming a layer on and / or in a porous substrate.
- the density of the LDH-containing separator layer tends to be improved.
- the porous substrate is immersed in the raw material aqueous solution in a desired direction (for example, horizontally or vertically).
- a desired direction for example, horizontally or vertically.
- the porous substrate may be suspended, floated, or disposed so as to be in contact with the bottom of the container.
- the porous substrate is suspended from the bottom of the container in the raw material aqueous solution.
- the material may be fixed.
- a jig that can set the porous substrate vertically on the bottom of the container may be placed.
- LDH is substantially perpendicular to or close to the porous substrate (that is, the LDH plate-like particles have their plate surfaces intersecting the surface (substrate surface) of the porous substrate substantially perpendicularly or obliquely. It is preferable to adopt a configuration or arrangement in which growth is performed in such a direction.
- the raw material aqueous solution contains magnesium ions (Mg 2+ ) and aluminum ions (Al 3+ ) at a predetermined total concentration, and contains urea. By the presence of urea, ammonia is generated in the solution by utilizing hydrolysis of urea, so that the pH value increases, and the coexisting metal ions form hydroxides to obtain LDH.
- the total concentration (Mg 2+ + Al 3+ ) of magnesium ions and aluminum ions contained in the raw material aqueous solution is preferably 0.20 to 0.40 mol / L, more preferably 0.22 to 0.38 mol / L, still more preferably The amount is 0.24 to 0.36 mol / L, particularly preferably 0.26 to 0.34 mol / L.
- concentration is within such a range, nucleation and crystal growth can proceed in a well-balanced manner, and an LDH-containing separator layer that is excellent not only in orientation but also in denseness can be obtained. That is, when the total concentration of magnesium ions and aluminum ions is low, crystal growth becomes dominant compared to nucleation, and the number of particles decreases and particle size increases. It is considered that the generation becomes dominant, the number of particles increases, and the particle size decreases.
- the porous substrate After the hydrothermal treatment, it is preferable to take out the porous substrate from the sealed container and wash it with ion-exchanged water.
- the LDH-containing separator layer in the LDH-containing composite material produced as described above is one in which LDH plate-like particles are highly densified and are oriented in a substantially vertical direction advantageous for conduction. Therefore, it can be said that it is extremely suitable for a nickel-zinc battery in which the progress of zinc dendrite has become a major barrier to practical use.
- the LDH containing separator layer obtained by the said manufacturing method can be formed in both surfaces of a porous base material. For this reason, in order to make the LDH-containing composite material suitable for use as a separator, the LDH-containing separator layer on one side of the porous substrate is mechanically scraped after film formation, or on one side during film formation. It is desirable to take measures so that the LDH-containing separator layer cannot be formed.
- LDH dense body is a layered double hydroxide (LDH) dense body.
- LDH dense body may be produced by any method, an embodiment of a preferable production method will be described below. This production method is carried out by forming and firing LDH raw material powder typified by hydrotalcite to form an oxide fired body, regenerating it into a layered double hydroxide, and then removing excess water. . According to this method, a high-quality layered double hydroxide dense body having a relative density of 88% or more can be provided and produced easily and stably.
- the raw material powder may be calcined to obtain an oxide powder.
- the calcining temperature at this time is somewhat different depending on the constituent M 2+ and M 3+ , but is preferably 500 ° C. or less, more preferably 380 to 460 ° C., and in a region where the raw material particle size does not change greatly.
- a molded body after molding and before firing (hereinafter referred to as a molded body) has a relative density of 43 to 65%, more preferably 45 to 60%, and still more preferably 47% to 58%. For example, it is preferably performed by pressure molding.
- the relative density of the molded body is calculated by calculating the density from the size and weight of the molded body and dividing by the theoretical density, but the weight of the molded body is affected by the adsorbed moisture.
- the pressure forming described as an example may be performed by a uniaxial press of a mold, or may be performed by cold isostatic pressing (CIP).
- CIP cold isostatic pressing
- mold by well-known methods, such as slip casting and extrusion molding, and it does not specifically limit about a shaping
- the raw material powder is calcined to obtain an oxide powder, it is limited to the dry molding method.
- the relative density of these compacts not only affects the strength of the resulting compact, but also affects the degree of orientation of the layered double hydroxides that usually have a plate shape.
- the relative density is preferably set within the above range.
- the molded body obtained in the above step is fired to obtain an oxide fired body.
- This firing is preferably carried out so that the oxide fired body has a weight of 57 to 65% of the weight of the compact and / or a volume of 70 to 76% or less of the volume of the compact.
- it is 57% or more of the weight of the molded product, it is difficult to generate a heterogeneous phase that cannot be regenerated during regeneration to a layered double hydroxide in the subsequent step, and when it is 65% or less, sufficient firing is performed in the subsequent step. Densify.
- the raw material powder is calcined to obtain an oxide powder
- the firing is preferably performed so that the oxide fired body has a relative density of 20 to 40% in terms of oxide, more preferably 20 to 35. %, More preferably 20-30%.
- the relative density in terms of oxide means that each metal element constituting the layered double hydroxide is changed to an oxide by firing, and the converted density obtained as a mixture of each oxide is used as the denominator. It is the obtained relative density.
- a preferable baking temperature for obtaining the oxide fired body is 400 to 850 ° C., more preferably 700 to 800 ° C. It is preferable to hold at a firing temperature within this range for 1 hour or more, and a more preferable holding time is 3 to 10 hours. Further, in order to prevent moisture and carbon dioxide from being released due to rapid temperature rise and cracking the molded body, the temperature rise for reaching the firing temperature is preferably performed at a rate of 100 ° C./h or less.
- the total firing time from the temperature rise to the temperature fall (100 ° C. or less) is preferably secured for 20 hours or more, more preferably 30 to 70 hours, and further preferably 35 to 65 hours.
- the layered double hydroxide is obtained by holding the calcined oxide obtained in the above step in the aqueous solution containing the n-valent anion (A n ⁇ ) or just above it. It regenerates into a product, thereby obtaining a layered double hydroxide solidified body rich in moisture. That is, the layered double hydroxide solidified body obtained by this production method inevitably contains excess moisture.
- the anion contained in the aqueous solution may be the same kind of anion as that contained in the raw material powder, or may be a different kind of anion.
- the oxide sintered body is preferably held for 1 hour or more at such a layered double hydroxide formation temperature, more preferably 2 to 50 hours, and further preferably 5 to 20 hours. With such a holding time, it is possible to avoid or reduce the occurrence of a heterogeneous phase by sufficiently regenerating the layered double hydroxide.
- the holding time is not particularly problematic if it is too long, but it may be set in a timely manner with emphasis on efficiency.
- the fired oxide body may be submerged in the aqueous solution, or the treatment may be performed in a state where at least one surface is in contact with the aqueous solution using a jig.
- the amount of excess water is small compared to complete submergence, so that the subsequent steps may be completed in a short time.
- the amount of the aqueous solution is too small, cracks are likely to occur. Therefore, it is preferable to use moisture equal to or greater than the weight of the fired body.
- the layered double hydroxide dense body of the present invention is obtained.
- the step of removing excess water is preferably performed in an environment of 300 ° C. or lower and an estimated relative humidity of 25% or higher at the maximum temperature of the removal step.
- the preferred temperature is 50 to 250 ° C., more preferably 100 to 200 ° C.
- a more preferable relative humidity at the time of dehydration is 25 to 70%, and further preferably 40 to 60%. Dehydration may be performed at room temperature, and there is no problem as long as the relative humidity is within a range of 40 to 70% in a normal indoor environment.
- the relative density was measured on a molded article stored at room temperature and a relative humidity of 20% or less for 24 hours.
- the obtained molded body was fired in an alumina sheath. This firing is performed at a rate of 100 ° C./h or less to prevent moisture and carbon dioxide from being released due to a sudden rise in temperature, and when the temperature reaches a maximum temperature of 750 ° C., 5 After holding for a period of time, cooling was performed.
- the total firing time from the temperature increase to the temperature decrease (100 ° C. or less) was 62 hours, and the weight, volume and relative density of the obtained sintered body were 59% by weight, 72% by volume and 23%, respectively. It was.
- Example 2 Alkali resistance test of LDH dense bodies in various electrolyte solutions Alkali resistance (especially whether or not Al is eluted and its degree) is as follows by immersing LDH dense bodies in electrolyte solutions (KOH aqueous solution) of various Al concentrations. Examined. Prior to immersion in the electrolytic solution, the surface microstructure of the LDH dense sample prepared in Example 1 was measured at an acceleration voltage of 10 to 20 kV using a scanning electron microscope (SEM, JSM-6610LV, manufactured by JEOL). Observed. The SEM image of the surface microstructure of the obtained LDH dense sample was as shown in FIG. Moreover, when the composition of the LDH dense body sample produced in Example 1 was analyzed by energy dispersive X-ray analysis prior to immersion in the electrolytic solution, the Al / Mg ratio shown in Table 1 was obtained.
- SEM scanning electron microscope
- the electrolytic solution samples 1 to 4 were evaluated in the same manner as described above when the immersion temperature was set to 70 ° C. as an accelerated test.
- the Al / Mg ratio of the LDH dense body after immersion was as shown in Table 1. From the results shown in Table 1, by intentionally pre-dissolving Al in the electrolyte (KOH aqueous solution), the change in the Al / Mg ratio of the LDH dense body is significantly suppressed (that is, the Al content from the LDH dense body). As a result, it can be seen that the alkali resistance of LDH is significantly improved.
- Example 3 Production and Evaluation of LDH Separator with Porous Substrate (1) Production of Porous Substrate Boehmite (manufactured by Sasol, DISPAL 18N4-80), methylcellulose, and ion-exchanged water (boehmite): (methylcellulose) : (Ion-exchanged water) mass ratio was 10: 1: 5, and then kneaded. The obtained kneaded product was subjected to extrusion molding using a hand press and molded into a plate shape having a size sufficiently exceeding 5 cm ⁇ 8 cm and a thickness of 0.5 cm. The obtained molded body was dried at 80 ° C. for 12 hours and then calcined at 1150 ° C. for 3 hours to obtain an alumina porous substrate. The porous substrate thus obtained was cut into a size of 5 cm ⁇ 8 cm.
- the porosity of the surface of the porous substrate was measured by a technique using image processing, and it was 24.6%.
- the porosity is measured by 1) observing the surface microstructure with an accelerating voltage of 10 to 20 kV using a scanning electron microscope (SEM, JSM-6610LV, manufactured by JEOL Co., Ltd.). SEM) image (magnification of 10,000 times or more) is obtained, 2) a grayscale SEM image is read using image analysis software such as Photoshop (manufactured by Adobe), etc.
- magnesium nitrate hexahydrate (Mg (NO 3) 2 ⁇ 6H 2 O, manufactured by Kanto Chemical Co., Inc.), aluminum nitrate nonahydrate (Al (NO 3) 3 ⁇ 9H 2 O, manufactured by Kanto Chemical Co., Ltd.) and urea ((NH 2 ) 2 CO, manufactured by Sigma-Aldrich) were prepared.
- Mg (NO 3) 2 ⁇ 6H 2 O manufactured by Kanto Chemical Co., Inc.
- Al (NO 3) 3 ⁇ 9H 2 O manufactured by Kanto Chemical Co., Ltd.
- urea ((NH 2 ) 2 CO, manufactured by Sigma-Aldrich)
- the substrate is taken out from the sealed container, washed with ion-exchanged water, dried at 70 ° C. for 10 hours, and a dense layer of layered double hydroxide (hereinafter referred to as LDH) (hereinafter referred to as a membrane sample). ) was obtained on a substrate.
- LDH layered double hydroxide
- the thickness of the obtained film sample was about 1.5 ⁇ m.
- a composite material sample was obtained.
- the LDH film was formed on both surfaces of the porous substrate, the LDH film on one surface of the porous substrate was mechanically scraped to give the composite material a form as a separator.
- FIG. 13 shows an SEM image (secondary electron image) of the surface microstructure of the obtained film sample.
- FIG. 14 shows an SEM image of the polished cross-sectional microstructure of the composite material sample thus obtained.
- the porosity of the surface of the membrane was measured for the membrane sample by a technique using image processing.
- the porosity is measured by 1) observing the surface microstructure with a scanning electron microscope (SEM, JSM-6610LV, manufactured by JEOL) at an acceleration voltage of 10 to 20 kV, and observing an electron microscope (SEM) on the surface of the film.
- SEM scanning electron microscope
- the porosity of the polished cross section of the film sample was also measured.
- the measurement of the porosity of the polished cross section is the same as that described above except that an electron microscope (SEM) image (magnification of 10,000 times or more) of the cross-section polished surface in the thickness direction of the film was obtained according to the procedure shown in (5b) above. It carried out similarly to the porosity of the film
- the measurement of the porosity was performed on the film portion of the alignment film cross section.
- the porosity calculated from the cross-sectional polished surface of the film sample is 3.5% on average (average value of the three cross-sectional polished surfaces), and a very high-density film is formed on the porous substrate. It was confirmed that
- the composite material sample 120 obtained in the above (1) has a 0.5 cm ⁇ 0.5 cm square at the center on the film sample side.
- the silicon rubber 122 provided with the opening 122a was adhered, and the obtained laminate was adhered between two acrylic containers 124 and 126.
- the bottom of the acrylic container 124 disposed on the silicon rubber 122 side is pulled out, whereby the silicon rubber 122 is bonded to the acrylic container 124 with the opening 122a open.
- An epoxy adhesive 134 was applied to the depression 132 b of the alumina jig 132, and the film sample 136 b side of the composite material sample 136 was placed in the depression 132 b and adhered to the alumina jig 132 in an air-tight and liquid-tight manner. Then, the alumina jig 132 to which the composite material sample 136 is bonded is adhered to the upper end of the acrylic container 130 in a gas-tight and liquid-tight manner using a silicone adhesive 138 so as to completely close the open portion of the acrylic container 130. A measurement sealed container 140 was obtained.
- the measurement sealed container 140 was placed in a water tank 142, and the gas supply port 130 a of the acrylic container 130 was connected to a pressure gauge 144 and a flow meter 146 so that helium gas could be supplied into the acrylic container 130.
- Water 143 was put into the water tank 142 and the measurement sealed container 140 was completely submerged.
- the inside of the measurement sealed container 140 is sufficiently airtight and liquid tight, and the membrane sample 136b side of the composite material sample 136 is exposed to the internal space of the measurement sealed container 140, while the composite material sample
- the porous substrate 136 a side of 136 is in contact with the water in the water tank 142.
- helium gas was introduced into the measurement sealed container 140 into the acrylic container 130 via the gas supply port 130a.
- the pressure gauge 144 and the flow meter 146 are controlled so that the differential pressure inside and outside the membrane sample 136a is 0.5 atm (that is, the pressure applied to the side in contact with the helium gas is 0.5 atm higher than the water pressure applied to the opposite side). Whether or not helium gas bubbles were generated in the water from the composite material sample 136 was observed. As a result, generation of bubbles due to helium gas was not observed. Therefore, it was confirmed that the membrane sample 136b has high density so as not to have air permeability.
- Example 4 (Reference): Preparation and Evaluation of Nickel-Zinc Battery (1) Preparation of Separator with Porous Substrate Hydrotalcite membrane on alumina substrate (size) as a separator with porous substrate by the same procedure as Example 1. : 5 cm ⁇ 8 cm).
- a rectangular parallelepiped case body made of ABS resin with the case top lid removed was prepared.
- a separator with a porous substrate (a hydrotalcite film on an alumina substrate) was inserted near the center of the case body, and three sides thereof were fixed to the inner wall of the case body using a commercially available adhesive.
- the positive electrode plate and the negative electrode plate were inserted into the positive electrode chamber and the negative electrode chamber, respectively.
- the positive electrode plate and the negative electrode plate were arranged so that the positive electrode current collector and the negative electrode current collector were in contact with the inner wall of the case body.
- a 6 mol / L aqueous KOH solution in an amount that sufficiently hides the positive electrode active material coating portion was injected into the positive electrode chamber as an electrolyte.
- the liquid level in the positive electrode chamber was about 5.2 cm from the case bottom.
- the negative electrode chamber not only the negative electrode active material coating part was sufficiently hidden, but also an excessive amount of 6 mol / L KOH aqueous solution was injected as an electrolyte considering the amount of water expected to decrease during charging. .
- the liquid level in the negative electrode chamber was about 6.5 cm from the case bottom.
- the terminal portions of the positive electrode current collector and the negative electrode current collector were connected to external terminals at the top of the case.
- the case upper lid was fixed to the case body by heat sealing, and the battery case container was sealed. Thus, a nickel zinc battery was obtained.
- the positive electrode chamber and the negative electrode The space equivalent to 3 cm above the chamber can be said to be the positive electrode side excess space and the negative electrode side excess space.
- the manufactured nickel zinc battery was subjected to constant current charging for 10 hours at a current of 0.4 mA corresponding to 0.1 C with a design capacity of 4 Ah. After charging, no deformation of the case or leakage of the electrolyte was observed. When the amount of the electrolyte after charging was observed, the electrolyte level in the positive electrode chamber was about 7.5 cm from the bottom of the case, and the electrolyte level in the negative electrode chamber was about 5.2 cm from the bottom of the case. It was. Although the positive electrode chamber electrolyte increased and the negative electrode chamber electrolyte decreased due to charging, there was sufficient electrolyte in the negative electrode active material coating part, and the applied positive electrode active material and negative electrode active material were charged and discharged. The electrolyte that causes a sufficient charge / discharge reaction could be held in the case.
- Example 5 (Reference): Preparation of a zinc-air secondary battery (1) Preparation of separator with porous substrate An alumina substrate as a separator with a porous substrate (hereinafter simply referred to as a separator) by the same procedure as in Example 1 An upper hydrotalcite membrane was prepared.
- the ⁇ -MnO 2 particles and LDH particles obtained above and carbon black (product number VXC72, manufactured by Cabot Co., Ltd.) as an electron conductive material are weighed so as to have a predetermined blending ratio, and in the presence of an ethanol solvent. Wet mixed. The resulting mixture is dried at 70 ° C. and then crushed. The obtained pulverized powder was mixed with a binder (PTFE, manufactured by Electrochem, product number EC-TEF-500ML) and water for fibrillation. At this time, the amount of water added was 1% by mass with respect to the air electrode.
- PTFE manufactured by Electrochem, product number EC-TEF-500ML
- the fibrillar mixture thus obtained was pressure-bonded to a current collector (carbon cloth (manufactured by Electrochem, product number EC-CC1-060T)) so as to have a thickness of 50 ⁇ m, and the air electrode layer / current collector A laminated sheet was obtained.
- the air electrode layer thus obtained has an electron conductive phase (carbon black) of 20% by volume, a catalyst layer ( ⁇ -MnO 2 particles) of 5% by volume, a hydroxide ion conductive phase (LDH particles) of 70% by volume and It contained 5% by volume of a binder phase (PTFE).
- Negative Electrode Plate A mixture of 80 parts by weight of zinc oxide powder, 20 parts by weight of zinc powder and 3 parts by weight of polytetrafluoroethylene particles was applied onto a current collector made of copper punching metal, and the porosity was about A negative electrode plate coated with an active material portion at 50% is obtained.
- a zinc-air secondary battery having a horizontal structure as shown in FIG. 3A is produced by the following procedure. .
- a container without a lid (hereinafter referred to as a resin container) made of ABS resin and having a rectangular parallelepiped shape is prepared.
- the negative electrode plate is placed on the bottom of the resin container so that the side on which the negative electrode active material is coated faces upward.
- the negative electrode current collector is in contact with the bottom of the resin container, and the end of the negative electrode current collector is connected to an external terminal provided through the side surface of the resin container.
- a third electrode is provided at a position higher than the upper surface of the negative electrode plate on the inner wall of the resin container (that is, a position that does not contact the negative electrode plate and does not participate in the charge / discharge reaction), and the nonwoven fabric separator contacts the third electrode.
- Deploy. Seal the opening of the resin container with an air electrode with a separator so that the air electrode side is on the outside, and apply a commercially available adhesive to the outer periphery of the opening to provide air tightness and liquid tightness. Stop and bond.
- a 6 mol / L aqueous solution of KOH is injected as an electrolyte into the resin container through a small inlet provided near the upper end of the resin container.
- the separator comes into contact with the electrolyte solution, and the electrolyte solution can always contact the third electrode regardless of the increase or decrease of the electrolyte solution due to the liquid retaining property of the nonwoven fabric separator.
- the amount of electrolyte to be injected is the amount of water expected not only to sufficiently hide the negative electrode active material coating part in the resin container but also to decrease during charging in order to produce a battery in a discharged state. Use an excess amount in consideration. Therefore, the resin container is designed so as to accommodate the excessive amount of the electrolytic solution. Finally, the inlet of the resin container is sealed. Thus, the internal space defined by the resin container and the separator is hermetically and liquid-tightly sealed. Finally, the third electrode and the current collecting layer of the air electrode are connected via an external circuit. In this way, a zinc-air secondary battery is obtained.
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Abstract
Description
M2+及び/又はM3+に対応する金属元素を含む金属化合物が前記電解液に溶解され、それにより前記層状複水酸化物の前記電解液による浸食が抑制されるように構成されてなる、電池が提供される。
前記電解液が、前記正極が浸漬される正極電解液と、前記負極が浸漬される負極電解液から構成され、
前記電池が、前記正極、前記正極電解液、前記負極、及び前記負極電解液を収容する容器を備え、
前記セパレータが、前記容器内に、前記正極及び前記正極電解液を収容する正極室と、前記負極及び前記負極電解液を収容する負極室とを区画するように設けられ、それにより該電池がニッケル亜鉛二次電池とされうる。
前記負極が前記電解液に浸漬され、
前記電池が、前記負極及び前記電解液を収容する容器を備え、該容器が開口部を有してなり、
前記セパレータが、前記開口部を前記電解液と接触可能に塞いで前記容器と負極側密閉空間を形成し、それにより前記空気極と前記電解液を水酸化物イオン伝導可能に隔離し、それにより該電池が亜鉛空気二次電池とされうる。
本発明の電池は、層状複水酸化物(LDH)を用いた電池である。LDHは何らかの電池構成部材として電池内において含まれていればよく、電解液に接触しうる箇所に設けられるかぎり、その構成部位や存在形態は限定されない。LDHが含まれる構成部材の好ましい例としては、セパレータ、電解質、電極用保護剤(例えば負極用保護剤)等が挙げられる。これらの構成部材においてはLDHの有する水酸化物イオン伝導性等の望ましい特性を発揮させて電池性能の向上を図ることができる。特に好ましくは、セパレータである。この場合、セパレータはLDH単体で構成されてもよいし、LDHと他の材料(例えばポリマー)を複合して含む複合セパレータとしてもよい。また、負極(例えば亜鉛及び/又は酸化亜鉛を含む負極)等の電極がLDHで被覆されてなる構成も好ましい。いずれにしてもLDHは各種電池構成部材に用いられてよく、かかる電池構成部材において、LDHは単体で用いられてもよいし、LDHと他の材料(例えばポリマー)を複合して用いられてもよい。なお、電池は一次電池及び二次電池のいずれであってもよいが、二次電池が好ましく、例えば、ニッケル亜鉛二次電池、酸化銀亜鉛二次電池、酸化マンガン亜鉛二次電池、亜鉛空気二次電池、及びその他各種のアルカリ亜鉛二次電池、並びにリチウム空気二次電池等、LDHを適用可能な各種二次電池であることができる。特に、ニッケル亜鉛二次電池及び亜鉛空気二次電池が好ましい。したがって、以下の一般的説明において、ニッケル亜鉛二次電池に関する図1及び亜鉛空気二次電池に関する図3A及び3Bに言及することがあるが、本発明の電池はニッケル亜鉛二次電池及び亜鉛空気二次電池に限定されるべきではなく、LDHを採用可能な上述したような各種電池を概念的に包含するものである。
本発明の好ましい態様によれば、ニッケル亜鉛二次電池が提供される。図1に、本態様によるニッケル亜鉛電池の一例を模式的に示す。図1に示されるニッケル亜鉛電池は充電が行われる前の初期状態を示しており、放電末状態に相当する。もっとも、本態様のニッケル亜鉛電池は満充電状態で構成されてもよいのはいうまでもない。図1に示されるように、本態様によるニッケル亜鉛電池10は、正極12、正極電解液14、負極16、負極電解液18、及びセパレータ20を容器22内に備えてなる。正極12は、水酸化ニッケル及び/又はオキシ水酸化ニッケルを含んでなる。正極電解液14はアルカリ金属水酸化物を含んでなるアルカリ電解液であり、正極12が浸漬される。負極16は亜鉛及び/又は酸化亜鉛を含んでなる。負極電解液18はアルカリ金属水酸化物を含んでなるアルカリ電解液であり、負極16が浸漬される。容器22は、正極12、正極電解液14、負極16、及び負極電解液18を収容する。正極12及び正極電解液14は必ずしも分離している必要はなく、正極12と正極電解液14が混合された正極合材として構成されてもよい。同様に、負極16及び負極電解液18は必ずしも分離している必要はなく、負極16と負極電解液18が混合された負極合材として構成されてもよい。所望により、正極集電体13が正極12に接触して設けられる。また、所望により、負極集電体17が負極16に接触して設けられる。
‐ 正極: Ni(OH)2+OH-→NiOOH+H2O+e-
‐ 負極: ZnO+H2O+2e-→Zn+2OH-
‐ ZnOの溶解反応: ZnO+H2O+2OH-→Zn(OH)4 2-
‐ Znの析出反応: Zn(OH)4 2-+2e-→Zn+4OH-
本発明の別の好ましい態様によれば、亜鉛空気二次電池が提供される。図3A及び3Bに、本態様による亜鉛空気二次電池の一例を模式的に示す。図3A及び3Bに示されるように、本態様による亜鉛空気二次電池30は、空気極32、負極34、アルカリ電解液36、セパレータ40、容器46、及び所望により第三電極38を備えてなる。空気極32は正極として機能する。負極34は亜鉛、亜鉛合金及び/又は亜鉛化合物を含んでなる。電解液36は、負極34が浸漬される水系電解液である。容器46は、開口部46aを有し、負極34、電解液36及び第三電極38を収容する。セパレータ40は開口部46aを電解液36と接触可能に塞いで容器46と負極側密閉空間を形成し、それにより空気極32と電解液36を水酸化物イオン伝導可能に隔離する。所望により、正極集電体42が空気極32に接触して設けられてよい。また、所望により、負極集電体44が負極34に接触して設けられてよく、その場合、負極集電体44も容器46内に収容されうる。
第三電極: H2+2OH-→2H2O+2e-
正極放電: O2+2H2O+4e-→4OH-により水に戻すことができる。別の表現をすれば、負極34で発生した水素ガスが第三電極38で吸収され自己放電をすることになる。これにより、水素ガスの発生による負極側密閉空間における内圧の上昇及びそれに伴う不具合を抑制又は回避できるとともに、(放電反応に伴い上記反応式に従い減少することになる)水を発生させて負極側密閉空間内での水不足を抑制又は回避することができる。すなわち、負極から発生した水素ガスを負極側密閉空間内で水に戻して再利用することができる。その結果、亜鉛デンドライトによる短絡及び二酸化炭素の混入の両方を防止するのに極めて効果的な構成を有しながら、水素ガス発生の問題にも対処可能な、信頼性の高い亜鉛空気二次電池を提供することができる。
前述のとおり、本発明においてセパレータを構成するLDH含有固体電解質体は膜状又は層状の形態であることができる。この場合、膜状又は層状のLDH含有固体電解質体が多孔質基材上又はその中に形成されてなる、多孔質基材付きセパレータとするのが好ましい。特に好ましい多孔質基材付きセパレータは、多孔質基材と、この多孔質基材上及び/又は多孔質基材中に形成されるセパレータ層とを備えてなり、セパレータ層が前述したような層状複水酸化物(LDH)を含んでなるものである。セパレータ層は透水性及び通気性を有しないのが好ましい。すなわち、多孔質材料は孔の存在により透水性及び通気性を有しうるが、セパレータ層は透水性及び通気性を有しない程にまでLDHで緻密化されているのが好ましい。セパレータ層は多孔質基材上に形成されるのが好ましい。例えば、図4に示されるように、多孔質基材28上にセパレータ層20がLDH緻密膜として形成されるのが好ましい。この場合、多孔質基材28の性質上、図4に示されるように多孔質基材28の表面及びその近傍の孔内にもLDHが形成されてよいのはいうまでもない。あるいは、図5に示されるように、多孔質基材28中(例えば多孔質基材28の表面及びその近傍の孔内)にLDHが緻密に形成され、それにより多孔質基材28の少なくとも一部がセパレータ層20’を構成するものであってもよい。この点、図5に示される態様は図4に示される態様のセパレータ層20における膜相当部分を除去した構成となっているが、これに限定されず、多孔質基材28の表面と平行にセパレータ層が存在していればよい。いずれにしても、セパレータ層は透水性及び通気性を有しない程にまでLDHで緻密化されているため、水酸化物イオン伝導性を有するが透水性及び通気性を有しない(すなわち基本的に水酸化物イオンのみを通す)という特有の機能を有することができる。
多孔質基材は、前述したとおりであり、セラミックス材料、金属材料、及び高分子材料からなる群から選択される少なくとも1種で構成されるのが好ましい。多孔質基材は、セラミックス材料で構成されるのがより好ましい。この場合、セラミックス材料の好ましい例としては、アルミナ、ジルコニア、チタニア、マグネシア、スピネル、カルシア、コージライト、ゼオライト、ムライト、フェライト、酸化亜鉛、炭化ケイ素、窒化アルミニウム、窒化ケイ素、及びそれらの任意の組合せが挙げられ、より好ましくは、アルミナ、ジルコニア、チタニア、及びそれらの任意の組合せであり、特に好ましくはアルミナ及びジルコニアであり、最も好ましくはアルミナである。これらの多孔質セラミックスを用いるとLDH含有セパレータ層の緻密性を向上しやすい傾向がある。セラミックス材料製の多孔質基材を用いる場合、超音波洗浄、イオン交換水での洗浄等を多孔質基材に施すのが好ましい。
次に、多孔質基材を原料水溶液に所望の向きで(例えば水平又は垂直に)浸漬させる。多孔質基材を水平に保持する場合は、吊るす、浮かせる、容器の底に接するように多孔質基材を配置すればよく、例えば、容器の底から原料水溶液中に浮かせた状態で多孔質基材を固定としてもよい。多孔質基材を垂直に保持する場合は、容器の底に多孔質基材を垂直に設置できるような冶具を置けばよい。いずれにしても、多孔質基材にLDHを略垂直方向又はそれに近い方向(すなわちLDH板状粒子がそれらの板面が多孔質基材の表面(基材面)と略垂直に又は斜めに交差するような向きに)に成長させる構成ないし配置とするのが好ましい。原料水溶液は、マグネシウムイオン(Mg2+)及びアルミニウムイオン(Al3+)を所定の合計濃度で含み、かつ、尿素を含んでなる。尿素が存在することで尿素の加水分解を利用してアンモニアが溶液中に発生することによりpH値が上昇し、共存する金属イオンが水酸化物を形成することによりLDHを得ることができる。また、加水分解に二酸化炭素の発生を伴うため、陰イオンが炭酸イオン型のLDHを得ることができる。原料水溶液に含まれるマグネシウムイオン及びアルミニウムイオンの合計濃度(Mg2++Al3+)は0.20~0.40mol/Lが好ましく、より好ましくは0.22~0.38mol/Lであり、さらに好ましくは0.24~0.36mol/L、特に好ましくは0.26~0.34mol/Lである。このような範囲内の濃度であると核生成と結晶成長をバランスよく進行させることができ、配向性のみならず緻密性にも優れたLDH含有セパレータ層を得ることが可能となる。すなわち、マグネシウムイオン及びアルミニウムイオンの合計濃度が低いと核生成に比べて結晶成長が支配的となり、粒子数が減少して粒子サイズが増大する一方、この合計濃度が高いと結晶成長に比べて核生成が支配的となり、粒子数が増大して粒子サイズが減少するものと考えられる。
そして、原料水溶液中で多孔質基材を水熱処理して、LDHを含んでなるセパレータ層を多孔質基材上及び/又は多孔質基材中に形成させる。この水熱処理は密閉容器中、60~150℃で行われるのが好ましく、より好ましくは65~120℃であり、さらに好ましくは65~100℃であり、特に好ましくは70~90℃である。水熱処理の上限温度は多孔質基材(例えば高分子基材)が熱で変形しない程度の温度を選択すればよい。水熱処理時の昇温速度は特に限定されず、例えば10~200℃/hであってよいが、好ましくは100~200℃/hである、より好ましくは100~150℃/hである。水熱処理の時間はLDH含有セパレータ層の目的とする密度と厚さに応じて適宜決定すればよい。
板状の無機固体電解質の好ましい形態として、層状複水酸化物(LDH)緻密体が挙げられる。LDH緻密体はあらゆる方法によって作製されたものであってもよいが、以下に好ましい製造方法の一態様を説明する。この製造方法は、ハイドロタルサイトに代表されるLDHの原料粉末を成形及び焼成して酸化物焼成体とし、これを層状複水酸化物へ再生した後、余剰の水分を除去することにより行われる。この方法によれば、88%以上の相対密度を有する高品位な層状複水酸化物緻密体を簡便に且つ安定的に提供及び製造することができる。
原料粉末として、一般式:M2+ 1-xM3+ x(OH)2An- x/n・mH2O(式中、M2+は2価の陽イオン、M3+は3価の陽イオンであり、An-はn価の陰イオン、nは1以上の整数、xは0.1~0.4であり、mは任意の実数である)で表される層状複水酸化物の粉末を用意する。上記一般式において、M2+は任意の2価の陽イオンでありうるが、好ましい例としてはMg2+、Ca2+及びZn2+が挙げられ、より好ましくはMg2+である。M3+は任意の3価の陽イオンでありうるが、好ましい例としてはAl3+又はCr3+が挙げられ、より好ましくはAl3+である。An-は任意の陰イオンでありうるが、好ましい例としてはOH-及びCO3 2-が挙げられる。したがって、上記一般式は、少なくともM2+がMg2+を、M3+がAl3+を含み、An-がOH-及び/又はCO3 2-を含むのが好ましい。nは1以上の整数であるが、好ましくは1又は2である。xは0.1~0.4であるが、好ましくは0.2~0.35である。このような原料粉末は市販の層状複水酸化物製品であってもよいし、硝酸塩や塩化物を用いた液相合成法等の公知の方法にて作製した原料であってもよい。原料粉末の粒径は、所望の層状複水酸化物緻密体が得られる限り限定されないが、体積基準D50平均粒径が0.1~1.0μmであるのが好ましく、より好ましくは0.3~0.8μmである。原料粉末の粒径が細かすぎると粉末が凝集しやすく、成形時に気孔が残留する可能性が高く、大きすぎると成形性が悪くなるためである。
原料粉末を成形して成形体を得る。この成形は、成形後且つ焼成前の成形体(以下、成形体という)が、43~65%、より好ましくは45~60%であり、さらに好ましくは47%~58%の相対密度を有するように、例えば加圧成形により行われるのが好ましい。成形体の相対密度は、成形体の寸法及び重量から密度を算出し、理論密度で除して求められるが、成形体の重量は吸着水分の影響を受けるため、一義的な値を得るために、室温、相対湿度20%以下のデシケータ内で24時間以上保管した原料粉末を用いた成形体か、もしくは成形体を前記条件下で保管した後に相対密度を測定するのが好ましい。ただし、原料粉末を仮焼して酸化物粉末とした場合は、成形体の相対密度が26~40%であるのが好ましく、より好ましくは29~36%である。なお、酸化物粉末を用いる場合の相対密度は、層状複水酸化物を構成する各金属元素が仮焼により各々酸化物に変化したと仮定し、各酸化物の混合物として求めた換算密度を分母として求めた。一例に挙げた加圧成形は、金型一軸プレスにより行ってもよいし、冷間等方圧加圧(CIP)により行ってもよい。冷間等方圧加圧(CIP)を用いる場合は原料粉末をゴム製容器中に入れて真空封じするか、あるいは予備成形したものを用いるのが好ましい。その他、スリップキャストや押出成形など、公知の方法で成形してもよく、成形方法については特に限定されない。ただし、原料粉末を仮焼して酸化物粉末とした場合は、乾式成形法に限られる。これらの成形体の相対密度は、得られる緻密体の強度だけではなく、通常板状形状を有する層状複水酸化物の配向度への影響もあることから、その用途等を考慮して成形時の相対密度を上記の範囲で適宜設定するのが好ましい。
上記工程で得られた成形体を焼成して酸化物焼成体を得る。この焼成は、酸化物焼成体が、成形体の重量の57~65%の重量となり、且つ/又は、成形体の体積の70~76%以下の体積となるように行われるのが好ましい。成形体の重量の57%以上であると、後工程の層状複水酸化物への再生時に再生できない異相が生成しにくくなり、65%以下であると焼成が十分に行われて後工程で十分に緻密化する。また、成形体の体積の70%以上であると、後工程の層状複水酸化物への再生時に異相が生成にくくなるとともに、クラックも生じにくくなり、76%以下であると、焼成が十分に行われて後工程で十分に緻密化する。原料粉末を仮焼して酸化物粉末とした場合は、成形体の重量の85~95%、及び/又は成形体の体積の90%以上の酸化物焼成体を得るのが好ましい。原料粉末が仮焼されるか否かに関わらず、焼成は、酸化物焼成体が、酸化物換算で20~40%の相対密度を有するように行われるのが好ましく、より好ましくは20~35%であり、さらに好ましくは20~30%である。ここで、酸化物換算での相対密度とは、層状複水酸化物を構成する各金属元素が焼成により各々酸化物に変化したと仮定し、各酸化物の混合物として求めた換算密度を分母として求めた相対密度である。酸化物焼成体を得るための好ましい焼成温度は400~850℃であり、より好ましくは700~800℃である。この範囲内の焼成温度で1時間以上保持されるのが好ましく、より好ましい保持時間は3~10時間である。また、急激な昇温により水分や二酸化炭素が放出して成形体が割れるのを防ぐため、上記焼成温度に到達させるための昇温は100℃/h以下の速度で行われるのが好ましく、より好ましくは5~75℃/hであり、さらに好ましくは10~50℃/hである。したがって、昇温から降温(100℃以下)に至るまでの全焼成時間は20時間以上確保するのが好ましく、より好ましくは30~70時間、さらに好ましくは35~65時間である。
上記工程で得られた酸化物焼成体を上述したn価の陰イオン(An-)を含む水溶液中又はその直上に保持して層状複水酸化物へと再生し、それにより水分に富む層状複水酸化物固化体を得る。すなわち、この製法により得られる層状複水酸化物固化体は必然的に余分な水分を含んでいる。なお、水溶液中に含まれる陰イオンは原料粉末中に含まれる陰イオンと同種の陰イオンとしてよいし、異なる種類の陰イオンとしてもよい。酸化物焼成体の水溶液中又は水溶液直上での保持は密閉容器内で水熱合成の手法により行われるのが好ましく、そのような密閉容器の例としてはテフロン(登録商標)製の密閉容器が挙げられ、より好ましくはその外側にステンレス製等のジャケットを備えた密閉容器である。層状複水酸化物化は、酸化物焼成体を20℃以上200℃未満で、少なくとも酸化物焼成体の一面が水溶液に接する状態に保持することにより行われるのが好ましく、より好ましい温度は50~180℃であり、さらに好ましい温度は100~150℃である。このような層状複水酸化物化温度で酸化物焼結体が1時間以上保持されるのが好ましく、より好ましくは2~50時間であり、さらに好ましくは5~20時間である。このような保持時間であると十分に層状複水酸化物への再生を進行させて異相が残るのを回避又は低減できる。なお、この保持時間は、長すぎても特に問題はないが、効率性を重視して適時設定すればよい。
上記工程で得られた水分に富む層状複水酸化物固化体から余剰の水分を除去する。こうして本発明の層状複水酸化物緻密体が得られる。この余剰の水分を除去する工程は、300℃以下、除去工程の最高温度での推定相対湿度25%以上の環境下で行われるのが好ましい。層状複水酸化物固化体からの急激な水分の蒸発を防ぐため、室温より高い温度で脱水する場合は層状複水酸化物への再生工程で使用した密閉容器中に再び封入して行うことが好ましい。その場合の好ましい温度は50~250℃であり、さらに好ましくは100~200℃である。また、脱水時のより好ましい相対湿度は25~70%であり、さらに好ましくは40~60%である。脱水を室温で行ってもよく、その場合の相対湿度は通常の室内環境における40~70%の範囲内であれば問題はない。
(1)LDH緻密体の作製
原料粉末として、市販の層状複水酸化物であるハイドロタルサイト粉末(DHT-4H、協和化学工業株式会社製)粉末を用意した。この原料粉末の組成はMg2+ 0.68Al3+ 0.32(OH)2CO3 2- 0.16・mH2Oであった。原料粉末を直径16mmの金型に充填して500kgf・cm2の成形圧で一軸プレス成形して、相対密度53%、厚さ約2mmの成形体を得た。なお、この相対密度の測定は、室温、相対湿度20%以下で24時間保管した成形体について行った。得られた成形体をアルミナ鞘中で焼成した。この焼成は、急激な昇温により水分や二酸化炭素が放出して成形体が割れるのを防ぐため、100℃/h以下の速度で昇温を行い、750℃の最高温度に達した時点で5時間保持した後、冷却することにより行った。この昇温から降温(100℃以下)に至るまでの全焼成時間は62時間であり、得られた焼結体の重量、体積及び相対密度はそれぞれ59重量%、72体積%、23%であった。なお、上記「重量」及び「体積」は焼成前の成形体を100%とした算出された相対値(%)であり、「相対密度」はハイドロタルサイトの構成金属元素であるMg及びAlを酸化物として算出した理論密度を用いて得た、酸化物換算での相対密度である。こうして得られた焼成体を、外側にステンレス製ジャケットを備えたテフロン(登録商標)製の密閉容器に大気中でイオン交換水と共に封入し、100℃で5時間保持する再生条件(温度及びその温度での保持時間)で水熱処理を施して、試料を得た。室温まで冷めた試料は余分な水分を含んでいるため、ろ紙等で軽く表面の水分を拭き取った。こうして得られた試料を25℃、相対湿度が50%程度の室内で自然脱水(乾燥)してLDH緻密体試料を得た。
LDH緻密体試料の寸法及び重量から密度を算出し、この密度を理論密度で除することにより決定したところ、91%であった。なお、理論密度の算出にあたり、Mg/Al=2のハイドロタルサイトの理論密度としてJCPDSカードNo.70-2151に記載される2.09g/cm3とを用いた。
LDH緻密体試料を目視にて観察したところ、クラックは観察されなかった。
X線回折装置(D8 ADVANCE、Bulker AXS社製)により、電圧:40kV、電流値:40mA、測定範囲:5~70°の測定条件で、LDH緻密体試料の結晶相を測定し、JCPDSカードNO.35-0965に記載されるハイドロタルサイトの回折ピークを用いて同定した。その結果、ハイドロタルサイトに起因するピークのみが観察された。
LDH緻密体を各種Al濃度の電解液(KOH水溶液)に浸漬して耐アルカリ性(特にAl溶出の有無及びその程度)を以下のようにして調べた。なお、電解液への浸漬に先立ち、例1で作製されたLDH緻密体試料の表面微構造を走査型電子顕微鏡(SEM、JSM-6610LV、JEOL社製)を用いて10~20kVの加速電圧で観察した。得られたLDH緻密体試料の表面微構造のSEM画像は図7に示されるとおりであった。また、電解液への浸漬に先立ち、例1で作製されたLDH緻密体試料の組成をエネルギー分散型X線分析にて分析したところ、表1に示されるAl/Mg比が得られた。
(1)多孔質基材の作製
ベーマイト(サソール社製、DISPAL 18N4-80)、メチルセルロース、及びイオン交換水を、(ベーマイト):(メチルセルロース):(イオン交換水)の質量比が10:1:5となるように秤量した後、混練した。得られた混練物を、ハンドプレスを用いた押出成形に付し、5cm×8cmを十分に超える大きさで且つ厚さ0.5cmの板状に成形した。得られた成形体を80℃で12時間乾燥した後、1150℃で3時間焼成して、アルミナ製多孔質基材を得た。こうして得られた多孔質基材を5cm×8cmの大きさに切断加工した。
得られた多孔質基材をアセトン中で5分間超音波洗浄し、エタノール中で2分間超音波洗浄、その後、イオン交換水中で1分間超音波洗浄した。
原料として、硝酸マグネシウム六水和物(Mg(NO3)2・6H2O、関東化学株式会社製)、硝酸アルミニウム九水和物(Al(NO3)3・9H2O、関東化学株式会社製)、及び尿素((NH2)2CO、シグマアルドリッチ製)を用意した。カチオン比(Mg2+/Al3+)が2となり且つ全金属イオンモル濃度(Mg2++Al3+)が0.320mol/Lとなるように、硝酸マグネシウム六水和物と硝酸アルミニウム九水和物を秤量してビーカーに入れ、そこにイオン交換水を加えて全量を600mlとした。得られた溶液を攪拌した後、溶液中に尿素/NO3 -=4の割合で秤量した尿素を加え、更に攪拌して原料水溶液を得た。
テフロン(登録商標)製密閉容器(内容量800ml、外側がステンレス製ジャケット)に上記(3)で作製した原料水溶液と上記(2)で洗浄した多孔質基材を共に封入した。このとき、基材はテフロン(登録商標)製密閉容器の底から浮かせて固定し、基材両面に溶液が接するように水平に設置した。その後、水熱温度70℃で168時間(7日間)水熱処理を施すことにより基材表面に層状複水酸化物配向膜(セパレータ層)の形成を行った。所定時間の経過後、基材を密閉容器から取り出し、イオン交換水で洗浄し、70℃で10時間乾燥させて、層状複水酸化物(以下、LDHという)の緻密膜(以下、膜試料という)を基材上に得た。得られた膜試料の厚さは約1.5μmであった。こうして、層状複水酸化物含有複合材料試料(以下、複合材料試料という)を得た。なお、LDH膜は多孔質基材の両面に形成されていたが、セパレータとして形態を複合材料に付与するため、多孔質基材の片面のLDH膜を機械的に削り取った。
(5a)膜試料の同定
X線回折装置(リガク社製 RINT TTR III)にて、電圧:50kV、電流値:300mA、測定範囲:10~70°の測定条件で、膜試料の結晶相を測定したところ、図12に示されるXRDプロファイルが得られた。得られたXRDプロファイルについて、JCPDSカードNO.35-0964に記載される層状複水酸化物(ハイドロタルサイト類化合物)の回折ピークを用いて同定した。その結果、膜試料は層状複水酸化物(LDH、ハイドロタルサイト類化合物)であることが確認された。なお、図12に示されるXRDプロファイルにおいては、膜試料が形成されている多孔質基材を構成するアルミナに起因するピーク(図中で○印が付されたピーク)も併せて観察されている。
膜試料の表面微構造を走査型電子顕微鏡(SEM、JSM-6610LV、JEOL社製)を用いて10~20kVの加速電圧で観察した。得られた膜試料の表面微構造のSEM画像(二次電子像)を図13に示す。
膜試料について、画像処理を用いた手法により、膜の表面の気孔率を測定した。この気孔率の測定は、1)表面微構造を走査型電子顕微鏡(SEM、JSM-6610LV、JEOL社製)を用いて10~20kVの加速電圧で観察して膜の表面の電子顕微鏡(SEM)画像(倍率10000倍以上)を取得し、2)Photoshop(Adobe社製)等の画像解析ソフトを用いてグレースケールのSEM画像を読み込み、3)[イメージ]→[色調補正]→[2階調化]の手順で白黒の2値画像を作成し、4)黒い部分が占めるピクセル数を画像の全ピクセル数で割った値を気孔率(%)とすることにより行った。この気孔率の測定は配向膜表面の6μm×6μmの領域について行われた。その結果、膜の表面の気孔率は19.0%であった。また、この膜表面の気孔率を用いて、膜表面から見たときの密度D(以下、表面膜密度という)をD=100%-(膜表面の気孔率)により算出したところ、81.0%であった。
膜試料が透水性を有しない程の緻密性を有することを確認すべく、緻密性判定試験を以下のとおり行った。まず、図15Aに示されるように、上記(1)において得られた複合材料試料120(1cm×1cm平方に切り出されたもの)の膜試料側に、中央に0.5cm×0.5cm平方の開口部122aを備えたシリコンゴム122を接着し、得られた積層物を2つのアクリル製容器124,126で挟んで接着した。シリコンゴム122側に配置されるアクリル製容器124は底が抜けており、それによりシリコンゴム122はその開口部122aが開放された状態でアクリル製容器124と接着される。一方、複合材料試料120の多孔質基材側に配置されるアクリル製容器126は底を有しており、その容器126内にはイオン交換水128が入っている。このとき、イオン交換水にAl及び/又はMgを溶解させておいてもよい。すなわち、組み立て後に上下逆さにすることで、複合材料試料120の多孔質基材側にイオン交換水128が接するように各構成部材が配置されてなる。これらの構成部材等を組み立て後、総重量を測定した。なお、容器126には閉栓された通気穴(図示せず)が形成されており、上下逆さにした後に開栓されることはいうまでもない。図15Bに示されるように組み立て体を上下逆さに配置して25℃で1週間保持した後、総重量を再度測定した。このとき、アクリル製容器124の内側側面に水滴が付着している場合には、その水滴を拭き取った。そして、試験前後の総重量の差を算出することにより緻密度を判定した。その結果、25℃で1週間保持した後においても、イオン交換水の重量に変化は見られなかった。このことから、膜試料(すなわち機能膜)は透水性を有しない程に高い緻密性を有することが確認された。
膜試料が通気性を有しない程の緻密性を有することを確認すべく、緻密性判定試験を以下のとおり行った。まず、図16A及び16Bに示されるように、蓋の無いアクリル容器130と、このアクリル容器130の蓋として機能しうる形状及びサイズのアルミナ治具132とを用意した。アクリル容器130にはその中にガスを供給するためのガス供給口130aが形成されている。また、アルミナ治具132には直径5mmの開口部132aが形成されており、この開口部132aの外周に沿って膜試料載置用の窪み132bが形成されてなる。アルミナ治具132の窪み132bにエポキシ接着剤134を塗布し、この窪み132bに複合材料試料136の膜試料136b側を載置してアルミナ治具132に気密かつ液密に接着させた。そして、複合材料試料136が接合されたアルミナ治具132を、アクリル容器130の開放部を完全に塞ぐようにシリコーン接着剤138を用いて気密かつ液密にアクリル容器130の上端に接着させて、測定用密閉容器140を得た。この測定用密閉容器140を水槽142に入れ、アクリル容器130のガス供給口130aを圧力計144及び流量計146に接続して、ヘリウムガスをアクリル容器130内に供給可能に構成した。水槽142に水143を入れて測定用密閉容器140を完全に水没させた。このとき、測定用密閉容器140の内部は気密性及び液密性が十分に確保されており、複合材料試料136の膜試料136b側が測定用密閉容器140の内部空間に露出する一方、複合材料試料136の多孔質基材136a側が水槽142内の水に接触している。この状態で、アクリル容器130内にガス供給口130aを介してヘリウムガスを測定用密閉容器140内に導入した。圧力計144及び流量計146を制御して膜試料136a内外の差圧が0.5atmとなる(すなわちヘリウムガスに接する側に加わる圧力が反対側に加わる水圧よりも0.5atm高くなる)ようにして、複合材料試料136から水中にヘリウムガスの泡が発生するか否かを観察した。その結果、ヘリウムガスに起因する泡の発生は観察されなかった。よって、膜試料136bは通気性を有しない程に高い緻密性を有することが確認された。
(1)多孔質基材付きセパレータの用意
例1と同様の手順により、多孔質基材付きセパレータとして、アルミナ基材上ハイドロタルサイト膜(サイズ:5cm×8cm)を用意した。
亜鉛及びコバルトを固溶体となるように添加した水酸化ニッケル粒子を用意した。この水酸化ニッケル粒子を水酸化コバルトで被覆して正極活物質を得た。得られた正極活物質と、カルボキシメチルセルロースの2%水溶液とを混合してペーストを調製した。正極活物質の多孔度が50%となるように、多孔度が約95%のニッケル金属多孔質基板からなる集電体に上記得られたペーストを均一に塗布して乾燥し、活物質部分が5cm×5cmの領域にわたって塗工された正極板を得た。このとき、4Ah相当の水酸化ニッケル粒子が活物質中に含まれるように塗工量を調整した。
銅パンチングメタルからなる集電体上に、酸化亜鉛粉末80重量部、亜鉛粉末20重量部及びポリテトラフルオロエチレン粒子3重量部からなる混合物を塗布して、多孔度約50%で、活物質部分が5cm×5cmの領域にわたって塗工された負極板を得た。このとき、正極板容量の4Ah相当の酸化亜鉛粉末が活物質中に含まれるように塗工量を調整した。
上記得られた正極板、負極板、及び多孔質基材付きセパレータを用いて、図1に示されるようなニッケル亜鉛電池を以下のような手順で組み立てた。
作製したニッケル亜鉛電池に対して、設計容量4Ahの0.1C相当の0.4mAの電流で10時間定電流充電を実施した。充電後、ケースの変形や電解液の漏れは観察されなかった。充電後の電解液量を観察したところ、正極室の電解液の液面高さはケース底より約7.5cm、負極室の電解液の液面高さはケース底より約5.2cmであった。充電により、正極室電解液が増加し、負極室電解液が減少したものの、負極活物質塗工部分には十分な電解液があり、充放電を通して、塗工した正極活物質及び負極活物質が、十分な充放電反応を起こす電解液をケース内に保持できていた。
(1)多孔質基材付きセパレータの用意
例1と同様の手順により、多孔質基材付きセパレータ(以下、単にセパレータという)として、アルミナ基材上ハイドロタルサイト膜を用意した。
空気極触媒としてのα-MnO2粒子を次のようにして作製した。まず、Mn(SO4)・5H2O及びKMnO4を5:13のモル比で脱イオン水に溶かして混合した。得られた混合液をテフロン(登録商標)が内貼りされたステンレス製密閉容器に入れ、140℃で水熱合成を2時間行う。水熱合成により得られた沈殿物をろ過し、蒸留水で洗浄した後、80℃で6時間乾燥した。こうしてα-MnO2の粉末を得た。
アニオン交換膜(アストム社、ネオセプタAHA)を1MのNaOH水溶液に一晩浸漬させた。このアニオン交換膜をセパレータのハイドロタルサイト膜上に中間層として積層して、セパレータ/中間層積層体を得る。中間層の厚さは30μmである。得られたセパレータ/中間層積層体に、先に作製した空気極層/集電体の積層シートを、空気極層側が中間層と接するように圧着して、セパレータ付き空気極試料を得る。
銅パンチングメタルからなる集電体上に、酸化亜鉛粉末80重量部、亜鉛粉末20重量部及びポリテトラフルオロエチレン粒子3重量部からなる混合物を塗布して、多孔度約50%で活物質部分が塗工された負極板を得る。
ニッケルメッシュからなる集電体上に白金ペーストを塗布して、第三電極を得る。
上記得られたセパレータ付き空気極、負極板、及び第三電極を用いて、図3Aに示されるような横型構造の亜鉛空気二次電池を以下のような手順で作製する。まず、ABS樹脂製で直方体形状を有する蓋の無い容器(以下、樹脂容器という)を用意する。この樹脂容器の底に負極板を、負極活物質が塗工された側が上を向くように載置する。このとき、負極集電体が樹脂容器の底部に接しており、負極集電体の端部が樹脂容器側面に貫通して設けられる外部端子と接続する。次に、樹脂容器内壁の負極板の上面よりも高い位置に(すなわち負極板と接触せず充放電反応に関与しない位置)に第三電極を設け、不織布セパレータを第三電極と接触するように配置する。樹脂容器の開口部をセパレータ付き空気極で空気極側が外側になるように塞ぎ、その際、開口部の外周部分に市販の接着剤を塗工して気密性及び液密性を与えるように封止して接着する。樹脂容器の上端近傍に設けられた小さな注入口を介して樹脂容器内に6mol/LのKOH水溶液を電解液として注入する。こうして、セパレータが電解液と接触するとともに、不織布セパレータの保液性により電解液の増減に関わらず電解液が第三電極に常時接触可能な状態とされる。このとき、注入する電解液の量は、放電末状態で電池を作製すべく、樹脂容器内で負極活物質塗工部分が十分に隠れるだけでなく、充電時に減少することが見込まれる水分量を考慮した過剰量とする。したがって、樹脂容器は上記過剰量の電解液を収容できるように設計されている。最後に、樹脂容器の注入口を封止する。こうして樹脂容器及びセパレータで区画された内部空間は気密且つ液密に密閉されている。最後に第三電極と空気極の集電層とを外部回路を介して接続する。こうして亜鉛空気二次電池を得る。
Claims (16)
- 層状複水酸化物を用いた電池であって、正極と、負極と、アルカリ金属水酸化物水溶液である電解液と、該電解液に接触可能に設けられる、M2+ 1-xM3+ x(OH)2An- x/n・mH2O(式中、M2+は2価の陽イオンであり、M3+は3価の陽イオンであり、An-はn価の陰イオンであり、nは1以上の整数であり、xは0.1~0.4であり、mは任意の実数である)の基本組成を有する層状複水酸化物とを備えてなり、
M2+及び/又はM3+に対応する金属元素を含む金属化合物が前記電解液に溶解され、それにより前記層状複水酸化物の前記電解液による浸食が抑制されるように構成されてなる、電池。 - 前記アルカリ金属水酸化物水溶液が水酸化カリウム水溶液である、請求項1に記載の電池。
- 前記金属元素が、金属イオン、水酸化物及び/又はヒドロキシ錯体の形態で前記電解液に溶解されてなる、請求項1又は2に記載の電池。
- 前記金属化合物が前記電解液に予め溶解されてなる、請求項1~3のいずれか一項に記載の電池。
- 前記一般式において、M2+がMg2+を含み、M3+がAl3+を含み、An-がOH-及び/又はCO3 2-を含む、請求項1~4のいずれか一項に記載の電池。
- 前記金属化合物がM3+に対応する金属元素を含む、請求項1~5のいずれか一項に記載の電池。
- 前記金属化合物がAlを含む、請求項1~6のいずれか一項に記載の電池。
- 前記金属化合物が、水酸化アルミニウム及び/又はγアルミナである、請求項1~7のいずれか一項に記載の電池。
- 前記電解液におけるAlの濃度が0.1mol/L以上である、請求項7又は8に記載の電池。
- 前記電解液におけるAlの濃度が2.0mol/L以上である、請求項7~9のいずれか一項に記載の電池。
- 前記電池が、前記層状複水酸化物を、水酸化物イオン伝導性を有するセパレータとして備えてなり、該セパレータが前記正極と前記負極を隔離する、請求項1~10のいずれか一項に記載の電池。
- 前記セパレータが、前記層状複水酸化物に加え、他の材料をさらに含んでなる、請求項11に記載の電池。
- 前記他の材料がポリマーである、請求項12に記載の電池。
- 前記セパレータが透水性及び通気性を有しない程に緻密化されたものである、請求項11~13のいずれか一項に記載の電池。
- 前記セパレータの片面又は両面に多孔質基材をさらに備えた、請求項11~14のいずれか一項に記載の電池。
- 前記負極が前記層状複水酸化物で被覆されてなる、請求項1~15のいずれか一項に記載の電池。
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JP7017445B2 (ja) | 2017-12-27 | 2022-02-08 | 日本碍子株式会社 | 亜鉛二次電池用負極構造体 |
JP7037002B1 (ja) * | 2020-11-30 | 2022-03-15 | 日本碍子株式会社 | 層状複水酸化物様化合物を用いた電池 |
WO2022113433A1 (ja) * | 2020-11-30 | 2022-06-02 | 日本碍子株式会社 | 層状複水酸化物様化合物を用いた電池 |
DE112021005259T5 (de) | 2020-11-30 | 2023-07-20 | Ngk Insulators, Ltd. | Batterie, die eine Verbindung nach Art eines geschichteten Doppelhydroxids verwendet |
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US20170200981A1 (en) | 2017-07-13 |
JPWO2016051934A1 (ja) | 2017-04-27 |
JP6001198B2 (ja) | 2016-10-05 |
CN106716679A (zh) | 2017-05-24 |
CN106716679B (zh) | 2020-08-11 |
US10700385B2 (en) | 2020-06-30 |
EP3203546A1 (en) | 2017-08-09 |
EP3203546A4 (en) | 2018-04-11 |
EP3203546B1 (en) | 2019-06-19 |
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