WO2011065349A1 - 多孔質電極基材およびその製造方法 - Google Patents
多孔質電極基材およびその製造方法 Download PDFInfo
- Publication number
- WO2011065349A1 WO2011065349A1 PCT/JP2010/070862 JP2010070862W WO2011065349A1 WO 2011065349 A1 WO2011065349 A1 WO 2011065349A1 JP 2010070862 W JP2010070862 W JP 2010070862W WO 2011065349 A1 WO2011065349 A1 WO 2011065349A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- porous electrode
- fibers
- electrode substrate
- fiber
- carbon
- Prior art date
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
- H01M8/00—Fuel cells; Manufacture thereof
- H01M8/02—Details
- H01M8/0202—Collectors; Separators, e.g. bipolar separators; Interconnectors
- H01M8/023—Porous and characterised by the material
- H01M8/0241—Composites
- H01M8/0243—Composites in the form of mixtures
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
- B01J23/00—Catalysts comprising metals or metal oxides or hydroxides, not provided for in group B01J21/00
- B01J23/38—Catalysts comprising metals or metal oxides or hydroxides, not provided for in group B01J21/00 of noble metals
- B01J23/40—Catalysts comprising metals or metal oxides or hydroxides, not provided for in group B01J21/00 of noble metals of the platinum group metals
- B01J23/42—Platinum
-
- D—TEXTILES; PAPER
- D04—BRAIDING; LACE-MAKING; KNITTING; TRIMMINGS; NON-WOVEN FABRICS
- D04H—MAKING TEXTILE FABRICS, e.g. FROM FIBRES OR FILAMENTARY MATERIAL; FABRICS MADE BY SUCH PROCESSES OR APPARATUS, e.g. FELTS, NON-WOVEN FABRICS; COTTON-WOOL; WADDING ; NON-WOVEN FABRICS FROM STAPLE FIBRES, FILAMENTS OR YARNS, BONDED WITH AT LEAST ONE WEB-LIKE MATERIAL DURING THEIR CONSOLIDATION
- D04H1/00—Non-woven fabrics formed wholly or mainly of staple fibres or like relatively short fibres
- D04H1/40—Non-woven fabrics formed wholly or mainly of staple fibres or like relatively short fibres from fleeces or layers composed of fibres without existing or potential cohesive properties
- D04H1/42—Non-woven fabrics formed wholly or mainly of staple fibres or like relatively short fibres from fleeces or layers composed of fibres without existing or potential cohesive properties characterised by the use of certain kinds of fibres insofar as this use has no preponderant influence on the consolidation of the fleece
- D04H1/4209—Inorganic fibres
- D04H1/4242—Carbon fibres
-
- D—TEXTILES; PAPER
- D04—BRAIDING; LACE-MAKING; KNITTING; TRIMMINGS; NON-WOVEN FABRICS
- D04H—MAKING TEXTILE FABRICS, e.g. FROM FIBRES OR FILAMENTARY MATERIAL; FABRICS MADE BY SUCH PROCESSES OR APPARATUS, e.g. FELTS, NON-WOVEN FABRICS; COTTON-WOOL; WADDING ; NON-WOVEN FABRICS FROM STAPLE FIBRES, FILAMENTS OR YARNS, BONDED WITH AT LEAST ONE WEB-LIKE MATERIAL DURING THEIR CONSOLIDATION
- D04H1/00—Non-woven fabrics formed wholly or mainly of staple fibres or like relatively short fibres
- D04H1/40—Non-woven fabrics formed wholly or mainly of staple fibres or like relatively short fibres from fleeces or layers composed of fibres without existing or potential cohesive properties
- D04H1/44—Non-woven fabrics formed wholly or mainly of staple fibres or like relatively short fibres from fleeces or layers composed of fibres without existing or potential cohesive properties the fleeces or layers being consolidated by mechanical means, e.g. by rolling
- D04H1/46—Non-woven fabrics formed wholly or mainly of staple fibres or like relatively short fibres from fleeces or layers composed of fibres without existing or potential cohesive properties the fleeces or layers being consolidated by mechanical means, e.g. by rolling by needling or like operations to cause entanglement of fibres
-
- D—TEXTILES; PAPER
- D04—BRAIDING; LACE-MAKING; KNITTING; TRIMMINGS; NON-WOVEN FABRICS
- D04H—MAKING TEXTILE FABRICS, e.g. FROM FIBRES OR FILAMENTARY MATERIAL; FABRICS MADE BY SUCH PROCESSES OR APPARATUS, e.g. FELTS, NON-WOVEN FABRICS; COTTON-WOOL; WADDING ; NON-WOVEN FABRICS FROM STAPLE FIBRES, FILAMENTS OR YARNS, BONDED WITH AT LEAST ONE WEB-LIKE MATERIAL DURING THEIR CONSOLIDATION
- D04H1/00—Non-woven fabrics formed wholly or mainly of staple fibres or like relatively short fibres
- D04H1/40—Non-woven fabrics formed wholly or mainly of staple fibres or like relatively short fibres from fleeces or layers composed of fibres without existing or potential cohesive properties
- D04H1/44—Non-woven fabrics formed wholly or mainly of staple fibres or like relatively short fibres from fleeces or layers composed of fibres without existing or potential cohesive properties the fleeces or layers being consolidated by mechanical means, e.g. by rolling
- D04H1/46—Non-woven fabrics formed wholly or mainly of staple fibres or like relatively short fibres from fleeces or layers composed of fibres without existing or potential cohesive properties the fleeces or layers being consolidated by mechanical means, e.g. by rolling by needling or like operations to cause entanglement of fibres
- D04H1/48—Non-woven fabrics formed wholly or mainly of staple fibres or like relatively short fibres from fleeces or layers composed of fibres without existing or potential cohesive properties the fleeces or layers being consolidated by mechanical means, e.g. by rolling by needling or like operations to cause entanglement of fibres in combination with at least one other method of consolidation
- D04H1/488—Non-woven fabrics formed wholly or mainly of staple fibres or like relatively short fibres from fleeces or layers composed of fibres without existing or potential cohesive properties the fleeces or layers being consolidated by mechanical means, e.g. by rolling by needling or like operations to cause entanglement of fibres in combination with at least one other method of consolidation in combination with bonding agents
-
- D—TEXTILES; PAPER
- D21—PAPER-MAKING; PRODUCTION OF CELLULOSE
- D21H—PULP COMPOSITIONS; PREPARATION THEREOF NOT COVERED BY SUBCLASSES D21C OR D21D; IMPREGNATING OR COATING OF PAPER; TREATMENT OF FINISHED PAPER NOT COVERED BY CLASS B31 OR SUBCLASS D21G; PAPER NOT OTHERWISE PROVIDED FOR
- D21H13/00—Pulp or paper, comprising synthetic cellulose or non-cellulose fibres or web-forming material
- D21H13/10—Organic non-cellulose fibres
- D21H13/12—Organic non-cellulose fibres from macromolecular compounds obtained by reactions only involving carbon-to-carbon unsaturated bonds
-
- D—TEXTILES; PAPER
- D21—PAPER-MAKING; PRODUCTION OF CELLULOSE
- D21H—PULP COMPOSITIONS; PREPARATION THEREOF NOT COVERED BY SUBCLASSES D21C OR D21D; IMPREGNATING OR COATING OF PAPER; TREATMENT OF FINISHED PAPER NOT COVERED BY CLASS B31 OR SUBCLASS D21G; PAPER NOT OTHERWISE PROVIDED FOR
- D21H13/00—Pulp or paper, comprising synthetic cellulose or non-cellulose fibres or web-forming material
- D21H13/36—Inorganic fibres or flakes
- D21H13/46—Non-siliceous fibres, e.g. from metal oxides
- D21H13/50—Carbon fibres
-
- D—TEXTILES; PAPER
- D21—PAPER-MAKING; PRODUCTION OF CELLULOSE
- D21H—PULP COMPOSITIONS; PREPARATION THEREOF NOT COVERED BY SUBCLASSES D21C OR D21D; IMPREGNATING OR COATING OF PAPER; TREATMENT OF FINISHED PAPER NOT COVERED BY CLASS B31 OR SUBCLASS D21G; PAPER NOT OTHERWISE PROVIDED FOR
- D21H15/00—Pulp or paper, comprising fibres or web-forming material characterised by features other than their chemical constitution
- D21H15/02—Pulp or paper, comprising fibres or web-forming material characterised by features other than their chemical constitution characterised by configuration
- D21H15/10—Composite fibres
-
- 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
- H01M4/86—Inert electrodes with catalytic activity, e.g. for fuel cells
- H01M4/8605—Porous electrodes
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M4/00—Electrodes
- H01M4/86—Inert electrodes with catalytic activity, e.g. for fuel cells
- H01M4/88—Processes of manufacture
- H01M4/8817—Treatment of supports before application of the catalytic active composition
-
- 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
- H01M4/86—Inert electrodes with catalytic activity, e.g. for fuel cells
- H01M4/90—Selection of catalytic material
- H01M4/92—Metals of platinum group
- H01M4/925—Metals of platinum group supported on carriers, e.g. powder carriers
- H01M4/926—Metals of platinum group supported on carriers, e.g. powder carriers on carbon or graphite
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M4/00—Electrodes
- H01M4/86—Inert electrodes with catalytic activity, e.g. for fuel cells
- H01M4/96—Carbon-based electrodes
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M8/00—Fuel cells; Manufacture thereof
- H01M8/02—Details
- H01M8/0202—Collectors; Separators, e.g. bipolar separators; Interconnectors
- H01M8/023—Porous and characterised by the material
- H01M8/0234—Carbonaceous material
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M8/00—Fuel cells; Manufacture thereof
- H01M8/10—Fuel cells with solid electrolytes
- H01M8/1007—Fuel cells with solid electrolytes with both reactants being gaseous or vaporised
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M8/00—Fuel cells; Manufacture thereof
- H01M8/10—Fuel cells with solid electrolytes
- H01M2008/1095—Fuel cells with polymeric electrolytes
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M8/00—Fuel cells; Manufacture thereof
- H01M8/02—Details
- H01M8/0202—Collectors; Separators, e.g. bipolar separators; Interconnectors
- H01M8/023—Porous and characterised by the material
- H01M8/0239—Organic resins; Organic polymers
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/30—Hydrogen technology
- Y02E60/50—Fuel cells
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P70/00—Climate change mitigation technologies in the production process for final industrial or consumer products
- Y02P70/50—Manufacturing or production processes characterised by the final manufactured product
Definitions
- the content of the carbon powder in the porous electrode substrate is preferably 10 to 100 parts by mass when the total of the short carbon fibers (A) and the oxidized fibers (B) is 100 parts by mass from the viewpoint of conductivity expression. More preferred is 15 to 60 parts by mass.
- the content of the fluororesin in the porous electrode base material is 100 parts by mass with the total of the short carbon fibers (A) and the oxidized fibers (B) from the viewpoint of the expression of conductivity and the strength of the porous electrode base material.
- 10 to 100 parts by mass is preferable, and 10 to 40 parts by mass is more preferable.
- the concentration of carbon powder in the dispersion is preferably 4% by mass or more in order to form a conductive path made of carbon powder, and is preferably 8% by mass or less in order to obtain a dispersion having a low viscosity and high impregnation. 8 mass% is more preferable.
- the concentration of the fluororesin in the dispersion is preferably 2% by mass or more for imparting water repellency to the porous electrode substrate, and preferably 6% by mass or less, so as not to impair the conductivity. Is more preferable.
- the second production method is a method of further performing the step (5) of heat-pressing the precursor sheet at a temperature of less than 200 ° C. after the step (2) in the first production method and before the step (3). It is.
- the third production method is a step of drying the precursor sheet at a temperature of 70 ° C. or more and less than 150 ° C. after the step (3) in the first production method or the second production method and before the step (4). This is a method of further performing (6).
- the residual mass in the heat treatment step (4) is preferably 20% by mass or more.
- the polymer having a residual mass of 20% by mass or more in the heat treatment step (4) include acrylic polymers, cellulose polymers, and phenolic polymers.
- Methacrylic acid esters acrylic acid, methacrylic acid, maleic acid, itaconic acid, acrylamide, N-methylol acrylamide, diacetone acrylamide, styrene, vinyl toluene, vinyl acetate, vinyl chloride, vinylidene chloride, vinylidene bromide, vinyl fluoride, And vinylidene fluoride.
- the short carbon fibers (A) can be bonded to each other from low to high temperatures, the residual mass during heat treatment is large, and the fiber elasticity and fiber strength when performing the entanglement treatment described below, acrylonitrile It is preferable to use an acrylic polymer containing 50% by mass or more of units.
- One type of oxidized fiber precursor short fiber (b) may be used, or two or more types of oxidized fiber precursor short fibers (b) having different fiber diameters and polymer types may be used.
- the porous electrode substrate finally obtained by the type of these oxidized fiber precursor short fibers (b), the type of fibrillated oxidized fiber precursor fibers (b ′) described later, and the mixing ratio with the carbon short fibers (A) Since the ratios remaining as oxidized fibers (B) are different, the blending amount may be adjusted as appropriate so as to achieve the target content of oxidized fibers (B).
- one or two or more kinds of oxidized fiber precursor fibers having a structure in which the degree of freeness, the fiber diameter, or the polymer type are different and the fibrils are branched may be used.
- One kind or two or more kinds of oxidized fiber precursor short fibers which are different in freeness, fiber diameter or polymer type and fibrillate by beating can be used, or a combination of these can be used.
- the acrylic polymer used for the oxidized fiber precursor fiber having a structure in which a large number of fibrils are branched may be an acrylonitrile homopolymer or a copolymer of acrylonitrile and other monomers.
- the monomer copolymerized with acrylonitrile is not particularly limited as long as it is an unsaturated monomer constituting a general acrylic fiber.
- the method for producing the oxidized fiber precursor fiber having a structure in which a large number of fibrils are branched is not particularly limited, but it is preferable to use a jet coagulation method in which the freeness can be easily controlled.
- those having a residual mass of 20% by mass or more in the heat treatment step (4) include acrylic polymers, cellulose polymers, and phenol polymers.
- Methacrylic acid esters acrylic acid, methacrylic acid, maleic acid, itaconic acid, acrylamide, N-methylol acrylamide, diacetone acrylamide, styrene, vinyl toluene, vinyl acetate, vinyl chloride, vinylidene chloride, vinylidene bromide, vinyl fluoride, And vinylidene fluoride.
- acrylic acid, methacrylic acid, maleic acid, itaconic acid acrylamide, N-methylol acrylamide, diacetone acrylamide, styrene, vinyl toluene, vinyl acetate, vinyl chloride, vinylidene chloride, vinylidene bromide, vinyl fluoride, And vinylidene fluoride.
- acrylic polymer containing 50% by mass or more of acrylonitrile units.
- the weight average molecular weight of the acrylonitrile-based polymer used for the easily split sea-island composite fiber is not particularly limited, but is preferably 50,000 to 1,000,000. When the weight average molecular weight is 50,000 or more, the spinnability is improved and the yarn quality of the fiber tends to be good. When the weight average molecular weight is 1,000,000 or less, the polymer concentration that gives the optimum viscosity of the spinning dope increases, and the productivity tends to improve.
- the polymers used for the easily splittable sea-island composite fibers when the above-mentioned acrylic polymer is used as the residual mass in the heat treatment step (4) is 20% by mass or more, It must be stable when dissolved in the same solvent as the acrylonitrile polymer and used as a spinning dope. That is, in the spinning dope, if the degree of incompatibility of the two types of polymers is large, the fibers become inhomogeneous and may cause yarn breakage during spinning, so the fibers may not be shaped. . Therefore, other polymers are incompatible with acrylonitrile polymers when dissolved in the same solvent as acrylonitrile polymers, but they must be miscible enough to form a sea-island structure during spinning. . In addition, when wet spinning is performed, if another polymer is dissolved in water in the coagulation tank and the washing tank, the polymer falls off and is a manufacturing problem. Therefore, the other polymer needs to be hardly soluble in water.
- Examples of other polymers that satisfy these requirements include polyvinyl chloride, polyvinylidene chloride, polyvinylidene fluoride, polyvinyl pyrrolidone, cellulose acetate, acrylic resin, methacrylic resin, and phenol resin. Resin and methacrylic resin can be preferably used in terms of the balance of the above-mentioned requirements.
- the other polymer may be one type or two or more types.
- the easily splittable sea-island composite fiber used as the oxidized fiber precursor short fiber that fibrillates by beating can be produced by a normal wet spinning method.
- an acrylonitrile-based polymer is used assuming that the residual mass in the carbonization process is 20% by mass or more, the polymer is mixed with another polymer, dissolved in a solvent, and then an easily splittable sea-island composite fiber.
- a spinning stock solution obtained by dissolving an acrylonitrile-based polymer in a solvent and a spinning stock solution obtained by dissolving another polymer in a solvent are mixed with a static mixer or the like, and a spinning stock solution of an easily splittable sea-island composite fiber. It is good.
- organic solvents such as dimethylamide, dimethylformamide, dimethyl sulfoxide and the like can be used.
- These split spinning solutions are spun from a nozzle and subjected to wet heat drawing, washing, drying and dry heat drawing, whereby an easily split sea-island composite fiber can be obtained.
- the cross-sectional shape of the oxidized fiber precursor short fiber that is fibrillated by beating is not particularly limited.
- the fineness of the oxidized fiber precursor short fibers that are fibrillated by beating is preferably 1 to 10 dtex.
- the average fiber length of the oxidized fiber precursor short fibers fibrillated by beating is preferably 1 to 20 mm from the viewpoint of dispersibility.
- Oxidized fiber precursor short fibers fibrillated by beating are beaten by peeling of the phase separation interface by mechanical external force, and at least a part thereof is split and fibrillated.
- the beating method is not particularly limited, and examples thereof include a refiner, a pulper, a beater, or a method of fibrillation by jetting a pressurized water stream (water jet punching).
- the state of fibrillation varies depending on the beating method and beating time when the oxidized fiber precursor short fibers fibrillated by beating are beaten by peeling of the phase separation interface by mechanical external force.
- freeness evaluation JIS P8121 (pulp freeness test method: Canadian standard type)
- the freeness of the oxidized fiber precursor short fiber fibrillated by beating is not particularly limited, but as the freeness decreases, the oxidized fiber (B) having a three-dimensional network structure is likely to be formed.
- oxidized fibers (B) having a fiber structure are easily formed.
- a wet method in which (b ') is dispersed and made into paper; in the air, the carbon short fibers (A), one or more kinds of oxidized fiber precursor short fibers (b) and / or one or more kinds of fibrillated oxidized fibers A paper making method such as a dry method in which the precursor fibers (b ′) are dispersed and deposited is applicable, but a wet method is preferred.
- the short carbon fibers (A) to open into single fibers, prevents the opened single fibers from re-converging, and further reduces the short carbon fibers (A) and one or more oxidized fiber precursor short fibers ( It is preferable to use one or more fibrillated oxidized fiber precursor fibers (b ′) and to make wet paper making in order to improve sheet strength by entanglement with b) and make the binder substantially free.
- Examples of the medium in which the carbon short fibers (A) and one or more kinds of oxidized fiber precursor short fibers (b) and / or one or more kinds of fibrillated oxidized fiber precursor fibers (b ′) are dispersed include, for example, water From the viewpoint of productivity, a medium in which one or more kinds of oxidized fiber precursor short fibers (b) and / or one or more kinds of fibrillated oxidized fiber precursor fibers (b ′), such as alcohol, is not dissolved. Water is preferred.
- the precursor sheet can be produced by either a continuous method or a batch method, but it is preferably produced by a continuous method from the viewpoint of the productivity and mechanical strength of the precursor sheet.
- the basis weight of the precursor sheet is preferably about 10 to 200 g / m 2 .
- the thickness of the precursor sheet is preferably about 20 to 400 ⁇ m.
- the entanglement process for entanglement is not particularly limited as long as a three-dimensional entangled structure is formed, such as a mechanical entanglement method such as a needle punching method, a high-pressure liquid injection method such as a water jet punching method, a steam jet punching method, etc.
- the high-pressure gas injection method or a combination thereof can be used.
- the high-pressure liquid injection method is preferable in that the breakage of the short carbon fibers (A) in the entanglement treatment step can be suppressed and sufficient entanglement can be obtained.
- the entanglement process by high-pressure liquid injection of the precursor sheet may be repeated a plurality of times. That is, after performing the high-pressure liquid injection treatment of the precursor sheet, the precursor sheets may be further laminated, and the high-pressure liquid injection treatment may be performed. Alternatively, high-pressure liquid injection processing may be performed. These operations may be repeated.
- a dense structure of sheets is formed in the sheeting direction by vibrating a high-pressure liquid jet nozzle having one or more rows of nozzle holes in the width direction of the sheet.
- the streak-like locus pattern derived from can be suppressed.
- the mechanical strength in the sheet width direction can be expressed.
- three-dimensional confounding is performed by controlling the frequency and the phase difference that vibrate the number of high-pressure liquid jet nozzles in the width direction of the sheet. It is also possible to suppress the pattern periodically appearing on the structural precursor sheet.
- the number of impregnations is not particularly limited, but it is preferable to reduce the number of impregnations from the viewpoint of reducing the production cost.
- the number of impregnations is multiple, the same carbon powder and fluororesin slurry may be used, or slurry having different slurry concentrations, types of carbon powder and fluororesin, and mixing ratios may be used. .
- the impregnation amount of the carbon powder and the fluororesin in the thickness direction of the three-dimensional entangled structure precursor sheet may be uniform or may have a concentration gradient.
- the carbon fiber (A) is favorably fused with one or more kinds of oxidized fiber precursor short fibers (b) and / or one or more kinds of fibrillated oxidized fiber precursor fibers (b ′), and a binder component
- the precursor sheet impregnated with the carbon powder and the fluororesin is not less than 150 ° C. from the viewpoint that the fluororesin is sintered and the short carbon fiber (A) and the oxidized fiber (B) are bonded well.
- Heat treatment is performed at a temperature of less than 400 ° C.
- the heat treatment temperature is preferably 200 ° C. or higher for softening and melting the fluororesin, preferably less than 400 ° C., more preferably 300 to 370 ° C. for suppressing thermal decomposition of the fluororesin.
- the heat treatment method is not particularly limited, and a heat treatment method using a high-temperature atmosphere furnace or a far-infrared heating furnace, a direct heat treatment method using a hot plate, a hot roll, or the like can be applied.
- the heat treatment time can be, for example, 1 minute to 2 hours.
- the carbon short fiber (A) is fused with one or more kinds of oxidized fiber precursor short fibers (b) and / or one or more kinds of fibrillated oxidized fiber precursor fibers (b ′), and the porous electrode substrate
- the carbon short fibers (A) and the one or more kinds of oxidized fiber precursor short fibers (b) and / or one or more kinds of fibrillar oxidation which have been reduced in thickness unevenness and become fluffy on the sheet surface by the entanglement treatment From the viewpoint of suppressing the fluffing in the vicinity of the sheet surface with the fiber precursor fiber (b ′) and suppressing short circuit current and gas leak when incorporated as a fuel cell, before the impregnation treatment with the carbon powder, the fluororesin, It is preferable to heat and press mold the precursor sheet at a temperature of less than 200 ° C.
- Any method can be applied as a method of heat and pressure molding as long as it is a technology capable of uniformly heating and pressing the precursor sheet.
- a method of hot pressing a flat rigid plate on both sides of the precursor sheet a method of using a hot roll press device or a continuous belt press device can be mentioned.
- a method using a hot roll press device or a continuous belt press device is preferable. Thereby, heat processing can be performed continuously.
- the heating temperature in the heat and pressure molding is preferably less than 200 ° C. and more preferably 120 to 190 ° C. in order to effectively smooth the surface of the precursor sheet.
- the time for heat and pressure molding can be, for example, 30 seconds to 10 minutes.
- the molding pressure is not particularly limited, but when the content ratio of one or more kinds of oxidized fiber precursor short fibers (b) and / or one or more kinds of fibrillated oxidized fiber precursor fibers (b ′) in the precursor sheet is large. Can easily smooth the surface of the precursor sheet even when the molding pressure is low. If the press pressure is increased more than necessary at this time, there may be a problem that the short carbon fibers (A) are destroyed at the time of heat and pressure molding, a problem that the structure of the porous electrode substrate is too dense, or the like. is there.
- the molding pressure is preferably about 20 kPa to 10 MPa.
- oxidized fiber precursor short fibers ( b) When a precursor sheet is sandwiched between two rigid plates, or when heated and pressed with a hot roll press device or a continuous belt press device, one or more oxidized fiber precursor short fibers ( b) and / or applying a release agent in advance so that one or more kinds of fibrillated oxidized fiber precursor fibers (b ′) do not adhere, or between the precursor sheet and the rigid plate, the heat roll, or the belt. It is preferable to sandwich the release paper.
- the precursor sheet impregnated with the carbon powder and the fluorine resin may be dried at a temperature of 70 ° C. or more and less than 150 ° C. preferable.
- the time for the drying treatment can be, for example, 1 minute to 1 hour.
- the drying method is not particularly limited, and heat treatment using a high-temperature atmosphere furnace or far-infrared heating furnace, direct heat treatment using a hot plate, a hot roll, or the like can be applied.
- a drying treatment using a high-temperature atmosphere furnace is preferable in that adhesion of the carbon powder and the fluororesin to the heating source can be suppressed.
- the porous electrode substrate of the present invention can be suitably used for a membrane-electrode assembly.
- the membrane-electrode assembly using the porous electrode substrate of the present invention can be suitably used for a polymer electrolyte fuel cell.
- the thickness of the porous electrode substrate was measured using a thickness measuring device dial thickness gauge (trade name: 7321 manufactured by Mitutoyo Corporation). The size of the probe was 10 mm in diameter, and the measurement pressure was 1.5 kPa.
- Through-direction resistance The electrical resistance in the thickness direction of the porous electrode base material (through-direction resistance) is 10 mA / cm by pressing the porous electrode base material between the upper and lower sides of the copper plate with the porous electrode base material sandwiched between gold-plated copper plates.
- the resistance value when a current was passed at a current density of cm 2 was measured and obtained from the following formula.
- Through-direction resistance (m ⁇ ⁇ cm 2 ) Measured resistance value (m ⁇ ) ⁇ Sample area (cm 2 )
- Average diameter of oxidized fiber (B) The average diameter of oxidized fiber (B) is determined by measuring the diameter of oxidized fiber (B) at any 50 locations from a scanning electron micrograph of the surface of the porous electrode substrate. The average value was calculated.
- Content of oxidized fiber (B) The content of oxidized fiber (B) is based on the basis weight of the porous electrode substrate prepared without impregnating carbon powder and fluorine resin, and the short carbon fibers used ( From the basis weight of A), it was calculated from the following formula.
- Content (%) of oxidized fiber (B) (W2 ⁇ W1) ⁇ W2 ⁇ 100
- W2 is the basis weight (g / m 2 ) of the porous electrode substrate prepared without impregnating the carbon powder and the fluororesin
- W1 is the basis weight of the carbon short fiber (A). (G / m 2 ).
- the waviness of the porous electrode substrate is the maximum value of the height of the porous electrode substrate when a 250 mm long and 250 mm wide porous electrode substrate is allowed to stand on a flat plate. And the difference between the minimum values.
- Example 1 As the carbon short fiber (A), a PAN-based carbon fiber having an average fiber diameter of 7 ⁇ m and an average fiber length of 3 mm was prepared. Moreover, as the oxidized fiber precursor short fiber (b), an acrylic short fiber (Mitsubishi Rayon Co., Ltd., trade name: D122) having an average fiber diameter of 4 ⁇ m and an average fiber length of 3 mm was facilitated.
- an acrylic short fiber Mitsubishi Rayon Co., Ltd., trade name: D122
- a product manufactured by Rayon Co., Ltd., trade name: Bonnell MVP-C651, average fiber length: 3 mm) was prepared.
- the production of the precursor sheet and the three-dimensional entangled structure precursor sheet by the entanglement treatment were performed by the following wet continuous papermaking method and the entanglement treatment method by the continuous pressurized water jet treatment.
- oxidized fiber precursor short fibers As oxidized fiber precursor short fibers (b), acrylic short fibers having an average fiber diameter of 4 ⁇ m and an average fiber length of 3 mm (made by Mitsubishi Rayon Co., Ltd., trade name) : D122) was dispersed in water such that the fiber concentration was 1% (10 g / L) to obtain disaggregated slurry fibers (Sb).
- the carbon short fiber (A), the oxidized fiber precursor short fiber (b), and the fibrillated oxidized fiber precursor fiber (b ′) have a mass ratio of 50:30:20.
- the disaggregation slurry fiber (SA), the disaggregation slurry fiber (Sb), the disaggregation slurry fiber (Sb ′), and the dilution water are adjusted so that the concentration of the fiber (hereinafter abbreviated as “floc”) in the slurry is 1.44 g / L.
- loc concentration of the fiber
- the apparatus connects a net driving unit and a plain woven mesh made of plastic net having a width of 60 cm and a length of 585 cm in a belt shape, a sheet-like material conveying unit comprising a continuously rotatable net, a papermaking slurry supply unit (slurry supply)
- the opening width of the part is 48 cm, the amount of slurry supplied is 30 L / min), a vacuum dewatering part arranged at the lower part of the net, and a pressurized water jet treatment part.
- the pressurized water jet processing section is composed of two types of water jet nozzles, and the following two types of nozzles were used as the water jet nozzles.
- ⁇ Nozzle 1 Hole diameter ⁇ 0.10mm ⁇ 501Hole, Pitch between width direction holes 1mm (1001hole / width 1m), 1 row arrangement, nozzle effective width 500mm
- Nozzle 2 Hole diameter ⁇ 0.10mm ⁇ 501Hole, Pitch between width direction holes 1mm (1001hole / width 1m), 1 row arrangement, nozzle effective width 500mm
- Nozzle 3 Hole diameter ⁇ 0.15mm ⁇ 1002 Hole, width direction hole pitch 1.5mm, 3 rows arrangement, row pitch 5mm, nozzle effective width 500mm [Interlacing method] The papermaking slurry was supplied onto the net of the testing machine by a metering pump.
- the papermaking slurry was supplied after being widened to a predetermined size through a flow box for rectification into a uniform flow. Thereafter, it was allowed to stand, passed through a portion to be naturally dehydrated, completely dehydrated by a vacuum dehydration apparatus, and a wet paper web having a target weight of 50 g / m 2 was loaded on the net. As soon as this process is completed, the water jet nozzle at the back of the test machine is passed through the pressurized water jet pressure in the order of 1 MPa (nozzle 1), pressure 2 MPa (nozzle 2), and pressure 1 MPa (nozzle 3) to add the confounding process. It was.
- the entangled sheet-like material is dried at 150 ° C. for 3 minutes by a pin tenter tester (manufactured by Sakurai Dyeing Machine, trade name: PT-2A-400) to obtain a three-dimensional entangled structure precursor having a basis weight of 48 g / m 2.
- a sheet was obtained.
- the dispersion state of the oxidized fiber precursor short fiber (b) and the fibrillated oxidized fiber precursor fiber (b ′) in the obtained three-dimensional entangled structure precursor sheet was good.
- the excess dispersed aqueous solution was removed with a nip device. Thereafter, the three-dimensional entangled structure precursor sheet impregnated with the mixture of carbon powder and fluororesin was dried with a batch dryer at 100 ° C. for 20 minutes.
- Example 4 A porous electrode substrate was obtained in the same manner as in Example 1 except that the number of impregnations of the dispersion of the mixture of carbon powder and fluororesin was set to 2.
- the obtained porous electrode substrate had no in-plane shrinkage during heat treatment, and gas permeability, thickness and penetration direction resistance were good.
- the short carbon fibers (A) dispersed in the three-dimensional structure are joined together by the oxidized fibers (B), and further the short carbon fibers (A) and the oxidized fibers (B).
- Table 1 The composition and evaluation results of the porous electrode substrate are shown in Table 1.
- Example 5 A porous electrode substrate was obtained in the same manner as in Comparative Example 1 except that the number of impregnations of the dispersion of the mixture of carbon powder and fluororesin was set to 3.
- the obtained porous electrode substrate had no in-plane shrinkage at the time of heat treatment, and the gas permeability decreased as compared with Example 1, but the thickness and penetration direction resistance were good.
- the carbon short fibers (A) are dispersed in a two-dimensional plane, the carbon short fibers (A) are joined together by the oxidized fibers (B), and the carbon short fibers
- the fiber (A) and the oxidized fiber (B) were joined by the carbon powder and the fluororesin. Even when a compressive load having a surface pressure of 1.5 MPa was applied to the porous electrode substrate, the sheet form could be maintained.
- Table 1 The composition and evaluation results of the porous electrode substrate are shown in Table 1.
- Example 6 Without using the oxidized fiber precursor short fiber (b), the carbon short fiber (A) and the fibrillated oxidized fiber precursor fiber (b ′) in the papermaking slurry had a mass ratio of 70:30. Except for the above, a porous electrode substrate was obtained in the same manner as in Example 1. The obtained porous electrode substrate had no in-plane shrinkage during heat treatment, and gas permeability, thickness and penetration direction resistance were good. In the obtained porous electrode substrate, the short carbon fibers (A) dispersed in the three-dimensional structure are joined together by the oxidized fibers (B), and further the short carbon fibers (A) and the oxidized fibers (B). Was bonded by carbon powder and fluororesin. Even when a compressive load having a surface pressure of 1.5 MPa was applied to the porous electrode substrate, the sheet form could be maintained. The composition and evaluation results of the porous electrode substrate are shown in Table 1.
- Example 7 As the fibrillated oxidized fiber precursor fiber (b ′), except that a polyacrylonitrile pulp (b 1 ′) produced by spray coagulation, in which a large number of fibrils having a diameter of 3 ⁇ m or less were branched from the fibrous trunk, in the same manner as in Example 6, a porous electrode substrate was obtained.
- the obtained porous electrode substrate had no in-plane shrinkage during heat treatment, and gas permeability, thickness and penetration direction resistance were good.
- the short carbon fibers (A) dispersed in the three-dimensional structure are joined together by the oxidized fibers (B), and further the short carbon fibers (A) and the oxidized fibers (B).
- Table 1 The composition and evaluation results of the porous electrode substrate are shown in Table 1.
- Example 9 A porous electrode substrate was obtained in the same manner as in Example 1 except that the target basis weight of the precursor sheet was 60 g / m 2 .
- the obtained porous electrode substrate had no in-plane shrinkage during heat treatment, and gas permeability, thickness and penetration direction resistance were good.
- the short carbon fibers (A) dispersed in the three-dimensional structure are joined together by the oxidized fibers (B), and further the short carbon fibers (A) and the oxidized fibers (B).
- the composition and evaluation results of the porous electrode substrate are shown in Table 1.
- Example 10 Production of membrane-electrode assembly (MEA) Two sets of porous electrode substrates obtained in Example 1 were prepared as cathode electrode and anode electrode porous electrodes. Further, a catalyst layer (catalyst layer area: 25 cm 2 , Pt) composed of catalyst-supported carbon (catalyst: Pt, catalyst support amount: 50 mass%) on both surfaces of a perfluorosulfonic acid polymer electrolyte membrane (film thickness: 30 ⁇ m). The laminated body which formed the adhesion amount: 0.3 mg / cm ⁇ 2 >) was made easy. The laminate was sandwiched between cathode and anode porous carbon electrode substrates, and joined to obtain an MEA.
- a catalyst layer catalyst layer area: 25 cm 2 , Pt
- catalyst support amount catalyst-supported carbon
- the fuel cell characteristics were evaluated by measuring the current density-voltage characteristics of this single cell. Hydrogen gas was used as the fuel gas, and air was used as the oxidizing gas.
- the single cell temperature was 80 ° C.
- the fuel gas utilization rate was 60%
- the oxidizing gas utilization rate was 40%.
- the humidification of the fuel gas and the oxidizing gas was performed by passing the fuel gas and the oxidizing gas through an 80 ° C. bubbler, respectively.
- the current density was 0.8 A / cm 2
- the cell voltage of the fuel battery cell was 0.584 V
- the internal resistance of the cell was 4.8 m ⁇ , which showed good characteristics.
- a short carbon fiber (A), an oxidized fiber precursor short fiber (b), and a fibrillated oxidized fiber precursor fiber (b ′) in the papermaking slurry were prepared so as to have a mass ratio of 80:10:10,
- the target basis weight of the precursor sheet was 55 g / m 2 .
- Ketjen Black manufactured by Lion Corporation
- pyrolytic graphite trade name: PC-H, manufactured by Ito Graphite Industries Co., Ltd.
- polytetrafluoroethylene particles trade name: FluonPTFE
- polyoxyethylene octylphenyl ether as a dispersant
- ketjen black pyrolytic graphite
- fluororesin and dispersant are 6.3% by mass and 0.7% by mass, respectively.
- Dispersion liquid of a mixture of carbon powder and fluororesin was prepared so that it might become%, 4.5 mass%, and 5.0 mass%.
- the obtained porous electrode substrate had no in-plane shrinkage during heat treatment, and gas permeability, thickness and penetration direction resistance were good.
- the short carbon fibers (A) dispersed in the three-dimensional structure are joined together by the oxidized fibers (B), and further the short carbon fibers (A) and the oxidized fibers (B).
- the sheet form could be maintained.
- the composition and evaluation results of the porous electrode substrate are shown in Table 1.
- Example 12 As the fibrillated oxidized fiber precursor fiber (b ′), except that a polyacrylonitrile-based pulp (b 1 ′) produced by spray coagulation, in which many fibrils having a diameter of 3 ⁇ m or less were branched from the fibrous trunk,
- a porous electrode substrate was obtained.
- the obtained porous electrode substrate had no in-plane shrinkage during heat treatment, and gas permeability, thickness and penetration direction resistance were good.
- the short carbon fibers (A) dispersed in the three-dimensional structure are joined together by the oxidized fibers (B), and further the short carbon fibers (A) and the oxidized fibers (B).
- Table 1 The composition and evaluation results of the porous electrode substrate are shown in Table 1.
- Example 13 The short carbon fiber (A), oxidized fiber precursor short fiber (b), and fibrillated oxidized fiber precursor fiber (b ′) in the papermaking slurry were prepared so as to have a mass ratio of 70:10:20.
- a porous electrode substrate was obtained in the same manner as in Example 11 except that the target weight of the precursor sheet was 50 g / m 2 .
- the obtained porous electrode substrate had no in-plane shrinkage during heat treatment, and gas permeability, thickness and penetration direction resistance were good.
- the short carbon fibers (A) dispersed in the three-dimensional structure are joined together by the oxidized fibers (B), and further the short carbon fibers (A) and the oxidized fibers (B).
- the composition and evaluation results of the porous electrode substrate are shown in Table 1.
- Example 14 Without using the oxidized fiber precursor short fiber (b), the carbon short fiber (A) and the fibrillated oxidized fiber precursor fiber (b ′) in the papermaking slurry were prepared so as to have a mass ratio of 80:20. , Ketjen black, pyrolytic graphite, fluororesin and dispersant so that the carbon powder and fluorine are 4.2 mass%, 1.8 mass%, 6.0 mass% and 3.0 mass%, respectively.
- a porous electrode substrate was obtained in the same manner as in Example 1 except that a dispersion of a mixture with a resin was prepared and the heat treatment temperature was 300 ° C.
- the obtained porous electrode substrate had no in-plane shrinkage during heat treatment, and gas permeability, thickness and penetration direction resistance were good.
- the short carbon fibers (A) dispersed in the three-dimensional structure are joined together by the oxidized fibers (B), and further the short carbon fibers (A) and the oxidized fibers (B).
- the sheet form could be maintained.
- the composition and evaluation results of the porous electrode substrate are shown in Table 1.
- Ketjen black (made by Lion Corporation) and spherical graphite (trade name: SG-BH8, manufactured by Ito Graphite Industries Co., Ltd.) as carbon powder, polytetrafluoroethylene particles (trade name: Fluon PTFE lubrication L172J, Asahi Glass Co., Ltd.) and polyoxyethylene octylphenyl ether as a dispersant were prepared.
- Ketjen black, spherical graphite, fluororesin and dispersant were 5.6% by mass, 1.4% by mass and 6.% by mass, respectively.
- a porous electrode was prepared in the same manner as in Example 14 except that a dispersion of a mixture of carbon powder and fluororesin was prepared so as to be 0% by mass and 5.5% by mass, and the heat treatment temperature was 330 ° C.
- a substrate was obtained.
- the obtained porous electrode substrate had no in-plane shrinkage during heat treatment, and gas permeability, thickness and penetration direction resistance were good.
- the short carbon fibers (A) dispersed in the three-dimensional structure are joined together by the oxidized fibers (B), and further the short carbon fibers (A) and the oxidized fibers (B).
- the composition and evaluation results of the porous electrode substrate are shown in Table 1.
- Example 16 When the target weight of the precursor sheet is 50 g / m 2 , Ketjen black, spherical graphite, fluororesin and dispersant are 5.6% by mass, 2.4% by mass, 6.0% by mass and 6.0%, respectively.
- a porous electrode base material was obtained in the same manner as in Example 14 except that a dispersion of a mixture of carbon powder and fluororesin was prepared so as to have a mass%, and that the heat treatment temperature was 360 ° C.
- the obtained porous electrode substrate had no in-plane shrinkage during heat treatment, and gas permeability, thickness and penetration direction resistance were good.
- the short carbon fibers (A) dispersed in the three-dimensional structure are joined together by the oxidized fibers (B), and further the short carbon fibers (A) and the oxidized fibers (B).
- the sheet form could be maintained.
- the composition and evaluation results of the porous electrode substrate are shown in Table 1.
- Ketjen black (made by Lion Corporation) and pyrolytic graphite (trade name: PC-H, made by Ito Graphite Industries Co., Ltd.) as carbon powder, tetrafluoroethylene-hexafluoropropylene as fluorine resin as fluorine resin
- Polymer particle dispersion (trade name: FEP Dispersion 120-JR, manufactured by Mitsui-Dupont Fluorochemical Co., Ltd.), polyoxyethylene octylphenyl ether as a dispersant, ketjen black, pyrolytic graphite, fluorine-based
- a dispersion of a mixture of carbon powder and fluororesin is prepared so that the resin and the dispersant are 6.3% by mass, 0.7% by mass, 6.0% by mass, and 3.5% by mass, respectively.
- a porous electrode substrate was obtained in the same manner as in Example 14 except that the heat treatment temperature was 330 ° C.
- the obtained porous electrode substrate had no in-plane shrinkage during heat treatment, and gas permeability, thickness and penetration direction resistance were good.
- the short carbon fibers (A) dispersed in the three-dimensional structure are joined together by the oxidized fibers (B), and further the short carbon fibers (A) and the oxidized fibers (B).
- Table 1 The composition and evaluation results of the porous electrode substrate are shown in Table 1.
- a polyvinyl alcohol (PVA) short fiber (manufactured by Kuraray Co., Ltd., trade name: VBP105-1) having an average fiber length of 3 mm is used as a fiber that disappears during heat treatment.
- a porous electrode substrate was obtained in the same manner as in Example 5 except that. The obtained porous electrode substrate had no in-plane shrinkage during heat treatment, and gas permeability, thickness and penetration direction resistance were good.
- the short carbon fibers (A) dispersed in the tertiary structure were joined only by the carbon powder and the fluororesin. When a compressive load having a surface pressure of 1.5 MPa was applied to the porous electrode substrate, the sheet form could not be maintained.
- Table 1 The composition and evaluation results of the porous electrode substrate are shown in Table 1.
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Chemical Kinetics & Catalysis (AREA)
- General Chemical & Material Sciences (AREA)
- Electrochemistry (AREA)
- Manufacturing & Machinery (AREA)
- Sustainable Energy (AREA)
- Textile Engineering (AREA)
- Life Sciences & Earth Sciences (AREA)
- Sustainable Development (AREA)
- Composite Materials (AREA)
- Inorganic Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Organic Chemistry (AREA)
- Inert Electrodes (AREA)
- Paper (AREA)
- Treatments For Attaching Organic Compounds To Fibrous Goods (AREA)
- Treatment Of Fiber Materials (AREA)
- Chemical Or Physical Treatment Of Fibers (AREA)
Abstract
Description
1)炭素短繊維(A)と、1種類以上の酸化繊維前駆体短繊維(b)および/または1種類以上のフィブリル状酸化繊維前駆体繊維(b’)とを2次元平面内において分散させた前駆体シートを製造する工程(1)と、前記前駆体シートを交絡処理して、3次元交絡構造を形成する工程(2)と、前記3次元交絡構造が形成された前駆体シートに、炭素粉とフッ素系樹脂とを含浸させる工程(3)と、前記前駆体シートを150℃以上400℃未満の温度で熱処理する工程(4)とを有する多孔質電極基材の製造方法。
2)前記工程(2)の後で前記工程(3)の前に、前記前駆体シートを200℃未満の温度で加熱加圧成型する工程(5)をさらに有する前記1)に記載の多孔質電極基材の製造方法。
3)前記工程(3)の後で前記工程(4)の前に、前記前駆体シートを、70℃以上150℃未満の温度で乾燥処理する工程(6)をさらに有する前記1)または2)に記載の多孔質電極基材の製造方法。
4)前記炭素粉が、カーボンブラックを含有する前記1)~3)のいずれかに記載の多孔質電極基材の製造方法。
5)前記カーボンブラックが、ケッチェンブラックである前記4)に記載の多孔質電極基材の製造方法。
6)前記炭素粉が、黒鉛粉を含有する前記1)~5)のいずれかに記載の多孔質電極基材の製造方法。
7)前記1)~6)のいずれかに記載の多孔質電極基材の製造方法で製造される多孔質電極基材。
8)3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに前記炭素短繊維(A)と前記酸化繊維(B)とが炭素粉とフッ素系樹脂とにより接合された3次元交絡構造体からなる多孔質電極基材。
9)前記7)または8)に記載の多孔質電極基材を用いた膜-電極接合体。
10)前記9)に記載の膜-電極接合体を用いた固体高分子型燃料電池。
本発明の多孔質電極基材は、3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに前記炭素短繊維(A)と前記酸化繊維(B)とが炭素粉とフッ素系樹脂とにより接合された3次元交絡構造体からなる。
本発明でいう3次元交絡構造体とは、後述するように、構造体を構成する炭素短繊維(A)が、酸化繊維(B)によって互いに絡まり合って接合され、されに炭素粉とフッ素系樹脂とによって接合された構造体である。
多孔質電極基材を構成する炭素短繊維(A)は、3次元交絡構造体中で厚み方向に交絡しており、ポリアクリロニトリル系炭素繊維(以下「PAN系炭素繊維」という。)、ピッチ系炭素繊維、レーヨン系炭素繊維等の炭素繊維を適当な長さに切断したものが挙げられる。多孔質電極基材の機械的強度の観点から、PAN系炭素繊維が好ましい。
酸化繊維(B)は、炭素短繊維(A)同士を接合する繊維であり、接合部において屈曲状または湾曲状になっている状態で存在し、それぞれが繊維構造を形成していても、3次元的な網目構造を形成していても良い。
炭素粉としては、カーボンブラック、またはカーボンブラックと黒鉛粉の混合物を用いることが、導電性の発現およびシート形状維持の点で好ましい。
フッ素系樹脂としては、特に限定されないが、テトラフルオロエチレン(TFE)、ヘキサフルオロプロピレン(HFP)、フッ化ビニリデン(VDF)、クロロトリフルオロエチレン(CTFE)、フッ化ビニル、パーフルオロアルキルビニルエーテル、パーフルオロ(アリルビニルエーテル)、パーフルオロ(ブテニルビニルエーテル)(PBVE)、パーフルオロ(2,2-ジメチル-1,3-ジオキソール)(PDD)等のフッ素系モノマーの単独重合物または共重合物を用いることができる。また、これらとエチレンに代表されるオレフィン類との共重合物であるエチレン-テトラフルオロエチレン共重合体(ETFE)、エチレン-クロロトリフルオロエチレン共重合体(ECTFE)等も用いることができる。これらのフッ素系樹脂の形態としては、溶媒に溶解した状態のものや、粒状の形態で水やアルコールなどの分散媒に分散している状態のものが、導電性の発現と炭素短繊維(A)と酸化繊維(B)とを接合した際のバインダー性能を発現できるという点で好ましい。溶液、分散液、あるいは粒状の形態で市販品の調達が容易なものとしては、ポリテトラフルオロエチレン(PTFE)、テトラフルオロエチレン-ヘキサフルオロプロピレン共重合体(FEP)、テトラフルオロエチレン-パーフルオロアルキルビニルエーテル(PFA)、ポリフッ化ビニリデン(PVDF)等があり、これらを用いることが取り扱い性、製造コストの観点から好ましい。なお、これらのフッ素系樹脂は、撥水性を有している。
炭素粉とフッ素系樹脂の質量比は、導電性の発現とバインダー性能の発現の点から、2:8~8:2であることが好ましく、4:6~7:3であることがより好ましい。
本発明の多孔質電極基材は、例えば、以下の製法により製造することができる。
酸化繊維前駆体短繊維(b)は、長繊維状の酸化繊維前駆体繊維を適当な長さにカットしたものである。酸化繊維前駆体短繊維(b)の繊維長は、分散性の点から、2~20mm程度が好ましい。酸化繊維前駆体短繊維(b)の断面形状は特に限定されないが、炭素化した後の機械的強度、製造コストの面から、真円度の高いものが好ましい。また、酸化繊維前駆体短繊維(b)の直径は、150℃以上400℃未満の温度で熱処理する時の収縮による破断を抑制するため、5μm以下であることがさらに好ましい。
フィブリル状酸化繊維前駆体繊維としては、繊維状の幹より直径が数μm以下(例えば0.1~3μm)のフィブリルが多数分岐した構造を有する酸化繊維前駆体繊維や、叩解によってフィブリル化する酸化繊維前駆体短繊維を用いることができる。このフィブリル状酸化繊維前駆体繊維を用いることにより、前駆体シート中で炭素短繊維(A)とフィブリル状酸化繊維前駆体繊維(b’)が良く絡み合い、機械的強度の優れた前駆体シートを得ることが容易となる。フィブリル状酸化繊維前駆体繊維(b’)の濾水度は特に限定されないが、一般的に濾水度が高いフィブリル状繊維を用いると前駆体シートの機械的強度が向上するが、多孔質電極基材のガス透気度が低下する。
フィブリルが多数分岐した構造を有する酸化繊維前駆体繊維として用いられるポリマーは、熱処理する工程(4)における残存質量が20質量%以上であることが好ましい。熱処理する工程(4)における残存質量が20質量%以上であるポリマーとしては、アクリル系ポリマー、セルロース系ポリマー、フェノール系ポリマーを挙げることができる。
叩解によってフィブリル化する酸化繊維前駆体短繊維は、適当な長さにカットした長繊維状の易割繊性海島複合繊維であり、リファイナーやパルパーなどによって叩解しフィブリル化するものである。叩解によってフィブリル化する酸化繊維前駆体短繊維は、共通の溶剤に溶解し、かつ非相溶性である2種類以上の異種ポリマーを用いて製造される。その少なくとも1種類のポリマーは、熱処理する工程(4)における残存質量が20質量%以上であることが好ましい。
前駆体シートを製造するにあたっては、液体の媒体中に、炭素短繊維(A)と、1種類以上の酸化繊維前駆体短繊維(b)および/または1種類以上のフィブリル状酸化繊維前駆体繊維(b’)とを分散させて抄造する湿式法;空気中に、炭素短繊維(A)と、1種類以上の酸化繊維前駆体短繊維(b)および/または1種類以上のフィブリル状酸化繊維前駆体繊維(b’)を分散させて降り積もらせる乾式法;などの抄紙方法を適用できるが、湿式法が好ましい。炭素短繊維(A)が単繊維に開繊するのを助け、開繊した単繊維が再収束することを防止し、さらに炭素短繊維(A)と1種類以上の酸化繊維前駆体短繊維(b)とを絡み合うことでシート強度が向上し、実質的にバインダーフリーとするためにも、1種類以上のフィブリル状酸化繊維前駆体繊維(b’)を使用し、湿式抄紙することが好ましい。
前駆体シート中の炭素短繊維(A)と、前駆体シート中の1種類以上の酸化繊維前駆体短繊維(b)および/または1種類以上のフィブリル状酸化繊維前駆体繊維(b’)とを交絡させる交絡処理は、3次元交絡交構造が形成される方法であれば特に限定はなく、ニードルパンチング法などの機械交絡法、ウォータージェットパンチング法などの高圧液体噴射法、スチームジェットパンチング法などの高圧気体噴射法、あるいはこれらの組み合わせによる方法で行うことができる。交絡処理工程での炭素短繊維(A)の破断を抑制でき、かつ十分な交絡性が得られるという点において、高圧液体噴射法が好ましい。
炭素粉とフッ素系樹脂とを含浸する方法としては、3次元交絡構造前駆体シートに、炭素粉とフッ素系樹脂とを付与することができる方法であれば特に限定されないが、コーターを用いて3次元交絡構造前駆体シート表面に炭素粉とフッ素系樹脂とを均一にコートする方法、絞り装置を用いるdip-nip方法などを用いることができる。
1種類以上の酸化繊維前駆体短繊維(b)および/または1種類以上のフィブリル状酸化繊維前駆体繊維(b’)による炭素短繊維(A)の融着を良好に行い、かつ、バインダー成分のフッ素系樹脂を焼結し、炭素短繊維(A)と酸化繊維(B)との接合を良好に行うという観点から、炭素粉とフッ素系樹脂とを含浸した前駆体シートを、150℃以上400℃未満の温度で熱処理する。熱処理の温度は、フッ素系樹脂を軟化・溶融させるために200℃以上が好ましく、フッ素系樹脂の熱分解を抑制するために400℃未満が好ましく、300~370℃がより好ましい。
炭素短繊維(A)を1種類以上の酸化繊維前駆体短繊維(b)および/または1種類以上のフィブリル状酸化繊維前駆体繊維(b’)で融着させ、かつ多孔質電極基材の厚みムラを低減させ、さらに、交絡処理によりシート表面に毛羽立った状態となった炭素短繊維(A)と1種類以上の酸化繊維前駆体短繊維(b)および/または1種類以上のフィブリル状酸化繊維前駆体繊維(b’)とのシート表面近傍における毛羽立ちを抑制し、燃料電池として組み込んだ際の短絡電流やガスリークを抑制するという観点から、炭素粉とフッ素系樹脂と含浸処理の前に、前駆体シートを200℃未満の温度で加熱加圧成型することが好ましい。
炭素粉とフッ素系樹脂とを含浸した前駆体シートから分散溶媒を除去するために、炭素粉とフッ素系樹脂とを含浸した前駆体シートを70℃以上150℃未満の温度で乾燥処理することが好ましい。乾燥処理の時間は、例えば1分間~1時間とすることができる。
本発明の多孔質電極基材は、膜-電極接合体に好適に用いることができる。また本発明の多孔質電極基材を用いた膜-電極接合体は、固体高分子型燃料電池に好適に用いることができる。
JIS規格P-8117に準拠し、ガーレーデンソメーターを使用して200mLの空気が透過するのにかかった時間を測定し、ガス透気度(mL/hr/cm2/mmAq)を算出した。
多孔質電極基材の厚みは、厚み測定装置ダイヤルシックネスゲージ((株)ミツトヨ製、商品名:7321)を使用して測定した。測定子の大きさは直径10mmで、測定圧力は1.5kPaとした。
多孔質電極基材の厚さ方向の電気抵抗(貫通方向抵抗)は、金メッキした銅板に多孔質電極基材を挟み、銅板の上下から0.6MPaで加圧し、10mA/cm2の電流密度で電流を流したときの抵抗値を測定し、次式より求めた。
貫通方向抵抗(mΩ・cm2)=測定抵抗値(mΩ)×試料面積(cm2)
酸化繊維(B)の平均径は、多孔質電極基材の表面の走査型電子顕微鏡写真から任意の50箇所における酸化繊維(B)の直径を測定し、その平均値を算出した。
酸化繊維(B)の含有率は、炭素粉とフッ素系樹脂とを含浸させずに作製した多孔質電極基材の目付と、使用した炭素短繊維(A)の目付から、次式より算出した。
酸化繊維(B)の含有率(%)=(W2-W1)÷W2×100
なお、上記式において、W2は、炭素粉とフッ素系樹脂とを含浸させずに作製した多孔質電極基材の目付(g/m2)であり、W1は、炭素短繊維(A)の目付(g/m2)である。
多孔質電極基材のうねりは、平板上に縦250mm横250mmの多孔質電極基材を静置した際の、多孔質電極基材の高さの最大値と最小値の差より算出した。
炭素短繊維(A)として、平均繊維径が7μm、平均繊維長が3mmのPAN系炭素繊維を用意した。また、酸化繊維前駆体短繊維(b)として、平均繊維径が4μm、平均繊維長が3mmのアクリル短繊維(三菱レイヨン(株)製、商品名:D122)を容易した。また、フィブリル状酸化繊維前駆体繊維(b’)として、叩解によってフィブリル化するアクリル系ポリマーとジアセテート(酢酸セルロース)とからなる易割繊性アクリル系海島複合短繊維(b2’)(三菱レイヨン(株)製、商品名:ボンネルM.V.P.-C651、平均繊維長:3mm)を用意した。
(1)炭素短繊維(A)の離解
平均繊維径が7μm、平均繊維長が3mmのPAN系炭素繊維を、繊維濃度が1%(10g/L)になるように水中へ分散して、ディスクリファイナー(熊谷理機製)を通して離解処理し、離解スラリー繊維(SA)とした。
酸化繊維前駆体短繊維(b)として、平均繊維径が4μm、平均繊維長が3mmのアクリル短繊維(三菱レイヨン(株)製、商品名:D122)、を、繊維濃度が1%(10g/L)になるように水中へ分散し、離解スラリー繊維(Sb)とした。
フィブリル状酸化繊維前駆体繊維(b’)として、叩解によってフィブリル化するアクリル系ポリマーとジアセテート(酢酸セルロース)とからなる易割繊性アクリル系海島複合短繊維(三菱レイヨン(株)製、商品名:ボンネルM.V.P.-C651、平均繊維長:3mm)を、繊維濃度が1%(10g/L)になるように水中へ分散し、離解スラリー繊維(Sb’)とした。
炭素短繊維(A)と酸化繊維前駆体短繊維(b)とフィブリル状酸化繊維前駆体繊維(b’)とが、質量比50:30:20とるように、かつスラリー中の繊維(以下、フロックと略す)の濃度が1.44g/Lとなるように、離解スラリー繊維(SA)、離解スラリー繊維(Sb)、離解スラリー繊維(Sb’)および希釈水を計量し、スラリー供給タンクに投入した。さらに、ポリアクリルアマイドを添加して粘度22センチポイズの抄紙用スラリーを調製した。
〔交絡処理装置〕
以下の構成からなる交絡処理装置を使用した。前記装置は、ネット駆動部および幅60cm×長さ585cmのプラスチックネット製平織メッシュをベルト状につなぎあわせ、連続的に回転可能なネットよりなるシート状物搬送部、抄紙用スラリー供給部(スラリー供給部の開口幅が48cm、供給スラリー量が30L/min)、ネット下部に配置した減圧脱水部、および加圧水流噴射処理部からなる。加圧水流噴射処理部は、2種類のウォータージェットノズルから構成されており、ウォータージェットノズルとしては、以下の2種類のノズルを3本用いた。
・ノズル1:
孔径φ0.10mm×501Hole、幅方向孔間ピッチ1mm(1001hole/幅1m)、1列配置、ノズル有効幅500mm
・ノズル2:
孔径φ0.10mm×501Hole、幅方向孔間ピッチ1mm(1001hole/幅1m)、1列配置、ノズル有効幅500mm
・ノズル3:
孔径φ0.15mm×1002Hole、幅方向孔間ピッチ1.5mm、3列配置、列間ピッチ5mm、ノズル有効幅500mm
〔交絡処理方法〕
試験機のネット上に上記抄紙用スラリーを定量ポンプによりネット上に供給した。抄紙用スラリーは均一な流れに整流するためのフローボックスを通して所定サイズに拡幅して供給した。その後静置、自然脱水する部分を通過して、減圧脱水装置により完全脱水し、目標目付50g/m2の湿紙ウエッブをネット上に積載した。この処理が完了すると同時に、試験機後方のウォータージェットノズルより、加圧水流噴射圧力を1MPa(ノズル1)、圧力2MPa(ノズル2)、圧力1MPa(ノズル3)の順で通過させて交絡処理を加えた。
この3次元交絡構造前駆体シートの両面を、シリコーン系離型剤をコートした紙で挟んだ後、バッチプレス装置にて180℃、3MPaの条件下で3分間加圧加熱成型した。
次に、炭素粉としてケッチェンブラック(ライオン(株)製)とフッ素系樹脂としてポリテトラフルオロエチレン粒子分散液(商品名:PTFEディスパージョン31-JR、三井-デュポンフロロケミカル(株)製)、また分散剤としてポリオキシエチレンオクチルフェニルエーテルを用意した。
その後、バッチ雰囲気炉にて、大気中、360℃の条件下で1時間熱処理して多孔質電極基材を得た。
炭素粉、フッ素系樹脂および分散剤が、それぞれ4.0質量%、4.0質量%および4.5質量%となるように、炭素粉とフッ素系樹脂との混合物の分散液を調製したこと以外は、実施例1と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度、厚みおよび貫通方向抵抗はそれぞれ良好であった。得られた多孔質電極基材では、3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに炭素短繊維(A)と酸化繊維(B)が炭素粉とフッ素系樹脂とによって接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加しても、シート形態を保つことができた。多孔質電極基材の組成および評価結果を表1に示した。
炭素粉、フッ素系樹脂および分散剤が、それぞれ4.0質量%、2.0質量%および4.5質量%となるように、炭素粉とフッ素系樹脂との混合物の分散液を調製したこと以外は、実施例1と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度、厚みおよび貫通方向抵抗はそれぞれ良好であった。得られた多孔質電極基材では、3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに炭素短繊維(A)と酸化繊維(B)が炭素粉とフッ素系樹脂とによって接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加しても、シート形態を保つことができた。多孔質電極基材の組成および評価結果を表1に示した。
炭素粉とフッ素系樹脂との混合物の分散液の含浸回数を2回としたこと以外は、実施例1と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度、厚みおよび貫通方向抵抗はそれぞれ良好であった。得られた多孔質電極基材では、3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに炭素短繊維(A)と酸化繊維(B)が炭素粉とフッ素系樹脂とによって接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加しても、シート形態を保つことができた。多孔質電極基材の組成および評価結果を表1に示した。
炭素粉とフッ素系樹脂との混合物の分散液の含浸回数を3回としたこと以外は、比較例1と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度が実施例1と比較して低下したものの、厚みおよび貫通方向抵抗はそれぞれ良好であった。得られた多孔質電極基材では、炭素短繊維(A)は2次元平面内に分散した状態であり、その炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに炭素短繊維(A)と酸化繊維(B)が炭素粉とフッ素系樹脂とによって接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加しても、シート形態を保つことができた。多孔質電極基材の組成および評価結果を表1に示した。
酸化繊維前駆体短繊維(b)を用いず、抄紙用スラリー中の炭素短繊維(A)とフィブリル状酸化繊維前駆体繊維(b’)とが、質量比70:30となるようにしたこと以外は、実施例1と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度、厚みおよび貫通方向抵抗はそれぞれ良好であった。得られた多孔質電極基材では、3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに炭素短繊維(A)と酸化繊維(B)が炭素粉とフッ素系樹脂とによって接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加しても、シート形態を保つことができた。多孔質電極基材の組成および評価結果を表1に示した。
フィブリル状酸化繊維前駆体繊維(b’)として、繊維状の幹より直径が3μm以下のフィブリルが多数分岐した、噴射凝固によって作製したポリアクリロニトリル系パルプ(b1’)を用いたこと以外は、実施例6と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度、厚みおよび貫通方向抵抗はそれぞれ良好であった。得られた多孔質電極基材では、3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに炭素短繊維(A)と酸化繊維(B)が炭素粉とフッ素系樹脂とによって接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加しても、シート形態を保つことができた。多孔質電極基材の組成および評価結果を表1に示した。
加圧水流噴射圧力を3MPa(ノズル1)、圧力4MPa(ノズル2)、圧力3MPa(ノズル3)となるようにしたこと以外は、実施例1と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度、厚みおよび貫通方向抵抗はそれぞれ良好であった。得られた多孔質電極基材では、3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに炭素短繊維(A)と酸化繊維(B)が炭素粉とフッ素系樹脂とによって接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加しても、シート形態を保つことができた。多孔質電極基材の組成および評価結果を表1に示した。
前駆体シートの目標目付を60g/m2にしたこと以外は、実施例1と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度、厚みおよび貫通方向抵抗はそれぞれ良好であった。得られた多孔質電極基材では、3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに炭素短繊維(A)と酸化繊維(B)が炭素粉とフッ素系樹脂とによって接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加しても、シート形態を保つことができた。多孔質電極基材の組成および評価結果を表1に示した。
(1)膜-電極接合体(MEA)の製造
実施例1で得られた多孔質電極基材2組を、カソード用およびアノード用の多孔質電極基材として用意した。また、パーフルオロスルホン酸系の高分子電解質膜(膜厚:30μm)の両面に触媒担持カーボン(触媒:Pt、触媒担持量:50質量%)からなる触媒層(触媒層面積:25cm2、Pt付着量:0.3mg/cm2)を形成した積層体を容易した。この積層体を、カソード用およびアノード用の多孔質炭素電極基材で挟持し、これらを接合して、MEAを得た。
得られたMEAを、蛇腹状のガス流路を有する2枚のカーボンセパレーターによって挟み、固体高分子型燃料電池(単セル)を形成した。
抄紙用スラリー中の炭素短繊維(A)と酸化繊維前駆体短繊維(b)とフィブリル状酸化繊維前駆体繊維(b’)とが、質量比80:10:10となるように調製し、前駆体シートの目標目付を55g/m2とした。また、炭素粉としてケッチェンブラック(ライオン(株)製)と熱分解黒鉛(商品名:PC-H、伊藤黒鉛工業(株)製)、フッ素系樹脂としてポリテトラフルオロエチレン粒子(商品名:FluonPTFEルブリカントL172J、旭硝子(株)製)、分散剤としてポリオキシエチレンオクチルフェニルエーテルを用意し、ケッチェンブラック、熱分解黒鉛、フッ素系樹脂および分散剤が、それぞれ6.3質量%、0.7質量%、4.5質量%および5.0質量%となるように、炭素粉とフッ素系樹脂との混合物の分散液を調製した。それ以外は実施例1と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度、厚みおよび貫通方向抵抗はそれぞれ良好であった。得られた多孔質電極基材では、3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに炭素短繊維(A)と酸化繊維(B)が炭素粉とフッ素系樹脂とによって接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加しても、シート形態を保つことができた。多孔質電極基材の組成および評価結果を表1に示した。
フィブリル状酸化繊維前駆体繊維(b’)として、繊維状の幹より直径が3μm以下のフィブリルが多数分岐した、噴射凝固によって作製したポリアクリロニトリル系パルプ(b1’)を用いたこと以外は、実施例11と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度、厚みおよび貫通方向抵抗はそれぞれ良好であった。得られた多孔質電極基材では、3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに炭素短繊維(A)と酸化繊維(B)が炭素粉とフッ素系樹脂とによって接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加しても、シート形態を保つことができた。多孔質電極基材の組成および評価結果を表1に示した。
抄紙用スラリー中の炭素短繊維(A)と酸化繊維前駆体短繊維(b)とフィブリル状酸化繊維前駆体繊維(b’)とが、質量比70:10:20となるように調製し、前駆体シートの目標目付を50g/m2としたこと以外は実施例11と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度、厚みおよび貫通方向抵抗はそれぞれ良好であった。得られた多孔質電極基材では、3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに炭素短繊維(A)と酸化繊維(B)が炭素粉とフッ素系樹脂とによって接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加しても、シート形態を保つことができた。多孔質電極基材の組成および評価結果を表1に示した。
酸化繊維前駆体短繊維(b)を用いず、抄紙用スラリー中の炭素短繊維(A)とフィブリル状酸化繊維前駆体繊維(b’)とが、質量比80:20となるように調製し、ケッチェンブラック、熱分解黒鉛、フッ素系樹脂および分散剤が、それぞれ4.2質量%、1.8質量%、6.0質量%および3.0質量%となるように、炭素粉とフッ素系樹脂との混合物の分散液を調製し、熱処理温度を300℃としたこと以外は実施例1と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度、厚みおよび貫通方向抵抗はそれぞれ良好であった。得られた多孔質電極基材では、3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに炭素短繊維(A)と酸化繊維(B)が炭素粉とフッ素系樹脂とによって接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加しても、シート形態を保つことができた。多孔質電極基材の組成および評価結果を表1に示した。
炭素粉としてケッチェンブラック(ライオン(株)製)と球状黒鉛(商品名:SG-BH8、伊藤黒鉛工業(株)製)、フッ素系樹脂としてポリテトラフルオロエチレン粒子(商品名:FluonPTFEルブリカントL172J、旭硝子(株)製)、分散剤としてポリオキシエチレンオクチルフェニルエーテルを用意し、ケッチェンブラック、球状黒鉛、フッ素系樹脂および分散剤が、それぞれ5.6質量%、1.4質量%、6.0質量%および5.5質量%となるように、炭素粉とフッ素系樹脂との混合物の分散液を調製し、熱処理温度を330℃としたこと以外は実施例14と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度、厚みおよび貫通方向抵抗はそれぞれ良好であった。得られた多孔質電極基材では、3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに炭素短繊維(A)と酸化繊維(B)が炭素粉とフッ素系樹脂とによって接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加しても、シート形態を保つことができた。多孔質電極基材の組成および評価結果を表1に示した。
前駆体シートの目標目付を50g/m2として、ケッチェンブラック、球状黒鉛、フッ素系樹脂および分散剤が、それぞれ5.6質量%、2.4質量%、6.0質量%および6.0質量%となるように炭素粉とフッ素系樹脂との混合物の分散液を調製し、熱処理温度を360℃としたこと以外は実施例14と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度、厚みおよび貫通方向抵抗はそれぞれ良好であった。得られた多孔質電極基材では、3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに炭素短繊維(A)と酸化繊維(B)が炭素粉とフッ素系樹脂とによって接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加しても、シート形態を保つことができた。多孔質電極基材の組成および評価結果を表1に示した。
炭素粉としてケッチェンブラック(ライオン(株)製)と熱分解黒鉛(商品名:PC-H、伊藤黒鉛工業(株)製)、フッ素系樹脂としてフッ素系樹脂としてテトラフルオロエチレン-ヘキサフルオロプロピレン共重合体粒子分散液(商品名:FEPディスパージョン120-JR、三井-デュポンフロロケミカル(株)製)、分散剤としてポリオキシエチレンオクチルフェニルエーテルを用意し、ケッチェンブラック、熱分解黒鉛、フッ素系樹脂および分散剤が、それぞれ6.3質量%、0.7質量%、6.0質量%および3.5質量%となるように、炭素粉とフッ素系樹脂との混合物の分散液を調製し、熱処理温度を330℃としたこと以外は実施例14と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度、厚みおよび貫通方向抵抗はそれぞれ良好であった。得られた多孔質電極基材では、3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに炭素短繊維(A)と酸化繊維(B)が炭素粉とフッ素系樹脂とによって接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加しても、シート形態を保つことができた。多孔質電極基材の組成および評価結果を表1に示した。
実施例17で得られた多孔質電極基材を用いたこと以外は、実施例10と同様にして燃料電池特性評価を行った。その結果、電流密度が0.8A/cm2のときの燃料電池セルのセル電圧が0.536V、セルの内部抵抗が7.0mΩであり、良好な特性を示した。
加圧水流噴射による交絡処理を実施しなかったこと以外は、実施例1と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度および厚みはそれぞれ良好であったが、貫通方向抵抗が実施例1と比較して高かった。得られた多孔質電極基材では、炭素短繊維(A)は2次元平面内に分散した状態であり、その炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに炭素短繊維(A)と酸化繊維(B)が炭素粉とフッ素系樹脂とによって接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加しても、シート形態を保つことができた。多孔質電極基材の組成および評価結果を表1に示した。
炭素粉とフッ素系樹脂との混合物の分散液を含浸させずに、熱処理したこと以外は、実施例1と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度および厚みはそれぞれ良好であったが、貫通方向抵抗が実施例1と比較して高かった。得られた多孔質電極基材では、3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によってのみ接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加しても、シート形態を保つことができた。多孔質電極基材の組成および評価結果を表1に示した。
フィブリル状酸化繊維前駆体繊維(b’)の代わりに、熱処理時に消失する繊維として平均繊維長が3mmのポリビニルアルコール(PVA)短繊維(クラレ(株)製、商品名:VBP105-1)を用いたこと以外は、実施例5と同様にして多孔質電極基材を得た。得られた多孔質電極基材は、熱処理時における面内の収縮がなく、ガス透気度、厚みおよび貫通方向抵抗はそれぞれ良好であった。得られた多孔質電極基材では、3次構造体中に分散された炭素短繊維(A)同士が、炭素粉とフッ素系樹脂とによってのみ接合されていた。この多孔質電極基材に面圧1.5MPaの圧縮荷重を印加した際、シート形態を保つことができなかった。多孔質電極基材の組成および評価結果を表1に示した。
Claims (10)
- 炭素短繊維(A)と、1種類以上の酸化繊維前駆体短繊維(b)および/または1種類以上のフィブリル状酸化繊維前駆体繊維(b’)とを2次元平面内において分散させた前駆体シートを製造する工程(1)と、
前記前駆体シートを交絡処理して、3次元交絡構造を形成する工程(2)と、
前記3次元交絡構造が形成された前駆体シートに、炭素粉とフッ素系樹脂とを含浸させる工程(3)と、
前記前駆体シートを150℃以上400℃未満の温度で熱処理する工程(4)と
を有する多孔質電極基材の製造方法。 - 前記工程(2)の後で前記工程(3)の前に、前記前駆体シートを200℃未満の温度で加熱加圧成型する工程(5)をさらに有する請求項1に記載の多孔質電極基材の製造方法。
- 前記工程(3)の後で前記工程(4)の前に、前記前駆体シートを、70℃以上150℃未満の温度で乾燥処理する工程(6)をさらに有する請求項1または2に記載の多孔質電極基材の製造方法。
- 前記炭素粉が、カーボンブラックを含有する請求項1~3のいずれかに記載の多孔質電極基材の製造方法。
- 前記カーボンブラックが、ケッチェンブラックである請求項4に記載の多孔質電極基材の製造方法。
- 前記炭素粉が、黒鉛粉を含有する請求項1~5のいずれかに記載の多孔質電極基材の製造方法。
- 請求項1~6のいずれかに記載の多孔質電極基材の製造方法で製造される多孔質電極基材。
- 3次元構造体中に分散された炭素短繊維(A)同士が、酸化繊維(B)によって接合され、さらに前記炭素短繊維(A)と前記酸化繊維(B)とが炭素粉とフッ素系樹脂とにより接合された3次元交絡構造体からなる多孔質電極基材。
- 請求項7または8に記載の多孔質電極基材を用いた膜-電極接合体。
- 請求項9に記載の膜-電極接合体を用いた固体高分子型燃料電池。
Priority Applications (6)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP10833195.0A EP2506352B1 (en) | 2009-11-24 | 2010-11-24 | Porous electrode base material and process for production thereof |
JP2010548311A JP5433588B2 (ja) | 2009-11-24 | 2010-11-24 | 多孔質電極基材およびその製造方法 |
CA2767211A CA2767211C (en) | 2009-11-24 | 2010-11-24 | Porous electrode substrate and method for producing the same |
KR1020127016384A KR101671558B1 (ko) | 2009-11-24 | 2010-11-24 | 다공질 전극 기재 및 그의 제조방법 |
US13/384,729 US20120115063A1 (en) | 2009-11-24 | 2010-11-24 | Porous electrode substrate and method for producing the same |
CN201080018395.8A CN102422471B (zh) | 2009-11-24 | 2010-11-24 | 多孔质电极基材及其制造方法 |
Applications Claiming Priority (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2009266278 | 2009-11-24 | ||
JP2009-266278 | 2009-11-24 | ||
JP2010-157824 | 2010-07-12 | ||
JP2010157824 | 2010-07-12 |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2011065349A1 true WO2011065349A1 (ja) | 2011-06-03 |
Family
ID=44066454
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2010/070862 WO2011065349A1 (ja) | 2009-11-24 | 2010-11-24 | 多孔質電極基材およびその製造方法 |
Country Status (7)
Country | Link |
---|---|
US (1) | US20120115063A1 (ja) |
EP (1) | EP2506352B1 (ja) |
JP (1) | JP5433588B2 (ja) |
KR (1) | KR101671558B1 (ja) |
CN (2) | CN102422471B (ja) |
CA (1) | CA2767211C (ja) |
WO (1) | WO2011065349A1 (ja) |
Cited By (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2013118051A (ja) * | 2011-12-01 | 2013-06-13 | Mitsubishi Rayon Co Ltd | 多孔質電極基材の製造方法及び多孔質電極基材 |
JP2013119690A (ja) * | 2011-12-08 | 2013-06-17 | Mitsubishi Rayon Co Ltd | 多孔質電極基材前駆体シートの製造方法、多孔質電極基材の製造方法、多孔質電極基材、膜−電極接合体、および固体高分子型燃料電池 |
JP2013119691A (ja) * | 2011-12-08 | 2013-06-17 | Mitsubishi Rayon Co Ltd | 多孔質電極基材前駆体シート、その製造方法、多孔質電極基材、膜−電極接合体、および固体高分子型燃料電池 |
JP2013175384A (ja) * | 2012-02-27 | 2013-09-05 | Mitsubishi Rayon Co Ltd | 多孔質電極基材の製造方法 |
WO2014014055A1 (ja) * | 2012-07-20 | 2014-01-23 | 三菱レイヨン株式会社 | 多孔質電極基材、その製造方法、膜-電極接合体、及び固体高分子型燃料電池 |
JP2014103030A (ja) * | 2012-11-21 | 2014-06-05 | Toho Tenax Co Ltd | 多孔質導電シート及びその製造方法、電極材、燃料電池 |
JPWO2012099036A1 (ja) * | 2011-01-21 | 2014-06-30 | 三菱レイヨン株式会社 | 多孔質電極基材、その製造方法、膜−電極接合体、固体高分子型燃料電池、前駆体シート、およびフィブリル状繊維 |
WO2014181771A1 (ja) * | 2013-05-10 | 2014-11-13 | 三菱レイヨン株式会社 | 多孔質電極基材、その製造方法および固体高分子型燃料電池 |
JP2015022838A (ja) * | 2013-07-17 | 2015-02-02 | 東邦テナックス株式会社 | 多孔質導電シート及びその製造方法 |
Families Citing this family (16)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US8986907B2 (en) | 2009-02-04 | 2015-03-24 | Mitsubishi Rayon Co., Ltd. | Porous electrode substrate, method for producing the same, membrane electrode assembly, and polymer electrolyte fuel cell |
KR101536835B1 (ko) | 2010-11-01 | 2015-07-14 | 미쯔비시 레이온 가부시끼가이샤 | 다공질 전극 기재, 그의 제조 방법, 다공질 전극 기재 전구체 시트, 막-전극 접합체 및 고체 고분자형 연료 전지 |
US9412986B2 (en) * | 2013-07-31 | 2016-08-09 | GM Global Technology Operations LLC | Porous composite structures for lithium-ion battery separators |
GB201401952D0 (en) | 2014-02-05 | 2014-03-19 | Johnson Matthey Fuel Cells Ltd | Gas diffusion substrate |
CN106029756B (zh) * | 2014-02-26 | 2019-12-24 | 东丽株式会社 | 多孔质碳材料、多孔质碳材料前体、及其制造方法、以及碳材料增强复合材料 |
CN104485457B (zh) * | 2015-01-08 | 2016-10-05 | 深圳市玖创科技有限公司 | 一种新型锂离子电池负极材料的制备方法 |
JP6729373B2 (ja) * | 2015-03-25 | 2020-07-22 | 東レ株式会社 | 多孔質炭素電極基材、その製造方法、ガス拡散層、および燃料電池用膜−電極接合体 |
KR101886190B1 (ko) * | 2015-09-24 | 2018-08-08 | 주식회사 아모그린텍 | 연료전지용 분리막, 그의 제조방법 및 연료전지 전극 어셈블리 |
EP3486984A4 (en) * | 2016-07-14 | 2020-03-11 | Toray Industries, Inc. | GAS DIFFUSION ELECTRODE BASE, METHOD FOR PRODUCING SAID ELECTRODE BASE, GAS DIFFUSION ELECTRODE, MEMBRANE ELECTRODE ASSEMBLY, AND SOLID POLYMER FUEL CELL |
KR102339301B1 (ko) * | 2016-07-22 | 2021-12-14 | 미쯔비시 케미컬 주식회사 | 다공질 기재, 다공질 전극, 탄소 섬유지, 탄소 섬유지의 제조 방법, 다공질 기재의 제조 방법 |
KR101885781B1 (ko) * | 2017-07-05 | 2018-08-06 | (주)다오코리아 | 온열 매트 |
CN111712955A (zh) * | 2018-02-15 | 2020-09-25 | 三菱化学株式会社 | 亲水性多孔质碳电极及其制造方法 |
TWI705953B (zh) * | 2018-08-31 | 2020-10-01 | 日商旭化成股份有限公司 | 碳發泡材、複合體及製造方法 |
CN111082069B (zh) * | 2019-12-20 | 2022-07-29 | 大连博融新材料有限公司 | 一种植入式梯度复合电极、生产方法及其用途 |
CN111900417B (zh) * | 2020-07-31 | 2022-03-29 | 齐鲁工业大学 | 一种高碳含量燃料电池气体扩散层用碳纸的制备方法 |
CN115385707B (zh) * | 2021-05-20 | 2023-08-08 | 中国科学院上海硅酸盐研究所 | 一种高体积分数碳粘结短切碳纤维复合材料的制备方法 |
Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2001056103A1 (fr) | 2000-01-27 | 2001-08-02 | Mitsubishi Rayon Co., Ltd. | Materiau d'electrode a base de carbone poreux, son procede de fabrication, et papier a fibres de carbone |
JP2001240477A (ja) * | 2000-02-28 | 2001-09-04 | Mitsubishi Rayon Co Ltd | 炭素質多孔質体とその製造方法 |
WO2002042534A1 (fr) | 2000-11-24 | 2002-05-30 | Toho Tenax Co., Ltd. | Feuille de fibres de carbone et son procede de production |
JP2003183962A (ja) * | 2001-12-14 | 2003-07-03 | Toho Tenax Co Ltd | ポリアクリロニトリル系炭素繊維シート、及びその製造法 |
JP2005273051A (ja) * | 2004-03-24 | 2005-10-06 | Toray Ind Inc | 耐炎化繊維不織布、炭素繊維不織布およびそれらの製造方法 |
JP2006040575A (ja) * | 2004-07-22 | 2006-02-09 | Nitto Denko Corp | 燃料電池用アノード電極 |
JP2007273466A (ja) | 2006-03-20 | 2007-10-18 | Gm Global Technology Operations Inc | 燃料電池用ガス拡散媒体としてのアクリル繊維結合炭素繊維紙 |
JP2008503043A (ja) | 2004-06-15 | 2008-01-31 | ジョンソン、マッセイ、パブリック、リミテッド、カンパニー | ガス拡散基材 |
JP2009087616A (ja) * | 2007-09-28 | 2009-04-23 | Aisin Seiki Co Ltd | 燃料電池用拡散層、燃料電池用拡散層の製造方法、燃料電池 |
Family Cites Families (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
TW540177B (en) * | 2000-07-14 | 2003-07-01 | Mitsubishi Rayon Co | Device and method for manufacturing resin-impregnated hard sheet |
WO2003087470A1 (fr) * | 2002-04-17 | 2003-10-23 | Mitsubishi Rayon Co., Ltd. | Papier en fibre de carbone et substrat d'electrode en fibre de carbone poreux, destine aux piles |
JP4190768B2 (ja) * | 2002-02-01 | 2008-12-03 | 東邦テナックス株式会社 | ポリアクリロニトリル系炭素繊維紡績糸織物、及びその製造方法 |
WO2004085728A1 (ja) * | 2003-03-26 | 2004-10-07 | Toray Industries, Inc. | 多孔質炭素基材、その製造方法、ガス拡散体、膜-電極接合体、および、燃料電池 |
US20040241537A1 (en) * | 2003-03-28 | 2004-12-02 | Tetsuo Okuyama | Air battery |
JP4409211B2 (ja) * | 2003-06-06 | 2010-02-03 | 三菱レイヨン株式会社 | 固体高分子型燃料電池用多孔質電極基材の製造方法 |
JP4824298B2 (ja) * | 2003-12-04 | 2011-11-30 | パナソニック株式会社 | 燃料電池用ガス拡散層、電極及び膜電極接合体及びその製造方法 |
EP1788651B1 (en) * | 2004-06-21 | 2019-04-03 | Mitsubishi Chemical Corporation | Porous electrode base material and process for producing the same |
JP2006040886A (ja) * | 2004-06-21 | 2006-02-09 | Mitsubishi Rayon Co Ltd | 多孔質電極基材およびその製造方法 |
TWI296449B (en) * | 2006-01-04 | 2008-05-01 | Univ Feng Chia | Porous carbon electrode substrates and methods for preparing the same |
KR101180172B1 (ko) * | 2007-02-28 | 2012-09-05 | 가부시키가이샤 도모에가와 세이시쇼 | 고체 고분자형 연료 전지용 가스 확산 전극, 고체 고분자형 연료 전지용 막-전극 접합체와 그 제조 방법, 및 고체 고분자형 연료 전지 |
JP5433147B2 (ja) * | 2007-11-21 | 2014-03-05 | 三菱レイヨン株式会社 | 多孔質電極基材、その製造方法、膜−電極接合体、および固体高分子型燃料電池 |
CN101463521B (zh) * | 2007-12-19 | 2011-09-28 | 逢甲大学 | 高性能多孔性碳化织物及其制备方法与用途 |
US8986907B2 (en) * | 2009-02-04 | 2015-03-24 | Mitsubishi Rayon Co., Ltd. | Porous electrode substrate, method for producing the same, membrane electrode assembly, and polymer electrolyte fuel cell |
-
2010
- 2010-11-24 US US13/384,729 patent/US20120115063A1/en not_active Abandoned
- 2010-11-24 CN CN201080018395.8A patent/CN102422471B/zh not_active Expired - Fee Related
- 2010-11-24 CA CA2767211A patent/CA2767211C/en not_active Expired - Fee Related
- 2010-11-24 EP EP10833195.0A patent/EP2506352B1/en not_active Not-in-force
- 2010-11-24 JP JP2010548311A patent/JP5433588B2/ja not_active Expired - Fee Related
- 2010-11-24 WO PCT/JP2010/070862 patent/WO2011065349A1/ja active Application Filing
- 2010-11-24 CN CN201410569390.4A patent/CN104409758B/zh not_active Expired - Fee Related
- 2010-11-24 KR KR1020127016384A patent/KR101671558B1/ko active IP Right Grant
Patent Citations (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
WO2001056103A1 (fr) | 2000-01-27 | 2001-08-02 | Mitsubishi Rayon Co., Ltd. | Materiau d'electrode a base de carbone poreux, son procede de fabrication, et papier a fibres de carbone |
JP2001240477A (ja) * | 2000-02-28 | 2001-09-04 | Mitsubishi Rayon Co Ltd | 炭素質多孔質体とその製造方法 |
WO2002042534A1 (fr) | 2000-11-24 | 2002-05-30 | Toho Tenax Co., Ltd. | Feuille de fibres de carbone et son procede de production |
JP2003183962A (ja) * | 2001-12-14 | 2003-07-03 | Toho Tenax Co Ltd | ポリアクリロニトリル系炭素繊維シート、及びその製造法 |
JP2005273051A (ja) * | 2004-03-24 | 2005-10-06 | Toray Ind Inc | 耐炎化繊維不織布、炭素繊維不織布およびそれらの製造方法 |
JP2008503043A (ja) | 2004-06-15 | 2008-01-31 | ジョンソン、マッセイ、パブリック、リミテッド、カンパニー | ガス拡散基材 |
JP2006040575A (ja) * | 2004-07-22 | 2006-02-09 | Nitto Denko Corp | 燃料電池用アノード電極 |
JP2007273466A (ja) | 2006-03-20 | 2007-10-18 | Gm Global Technology Operations Inc | 燃料電池用ガス拡散媒体としてのアクリル繊維結合炭素繊維紙 |
JP2009087616A (ja) * | 2007-09-28 | 2009-04-23 | Aisin Seiki Co Ltd | 燃料電池用拡散層、燃料電池用拡散層の製造方法、燃料電池 |
Non-Patent Citations (1)
Title |
---|
See also references of EP2506352A4 |
Cited By (14)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPWO2012099036A1 (ja) * | 2011-01-21 | 2014-06-30 | 三菱レイヨン株式会社 | 多孔質電極基材、その製造方法、膜−電極接合体、固体高分子型燃料電池、前駆体シート、およびフィブリル状繊維 |
JP5713003B2 (ja) * | 2011-01-21 | 2015-05-07 | 三菱レイヨン株式会社 | 多孔質電極基材、その製造方法、膜−電極接合体、固体高分子型燃料電池、前駆体シート、およびフィブリル状繊維 |
JP2013118051A (ja) * | 2011-12-01 | 2013-06-13 | Mitsubishi Rayon Co Ltd | 多孔質電極基材の製造方法及び多孔質電極基材 |
JP2013119690A (ja) * | 2011-12-08 | 2013-06-17 | Mitsubishi Rayon Co Ltd | 多孔質電極基材前駆体シートの製造方法、多孔質電極基材の製造方法、多孔質電極基材、膜−電極接合体、および固体高分子型燃料電池 |
JP2013119691A (ja) * | 2011-12-08 | 2013-06-17 | Mitsubishi Rayon Co Ltd | 多孔質電極基材前駆体シート、その製造方法、多孔質電極基材、膜−電極接合体、および固体高分子型燃料電池 |
JP2013175384A (ja) * | 2012-02-27 | 2013-09-05 | Mitsubishi Rayon Co Ltd | 多孔質電極基材の製造方法 |
JP5664791B2 (ja) * | 2012-07-20 | 2015-02-04 | 三菱レイヨン株式会社 | 多孔質電極基材、その製造方法、膜−電極接合体、及び固体高分子型燃料電池 |
KR20150033659A (ko) * | 2012-07-20 | 2015-04-01 | 미쯔비시 레이온 가부시끼가이샤 | 다공질 전극 기재, 그의 제조 방법, 막-전극 접합체 및 고체 고분자형 연료 전지 |
WO2014014055A1 (ja) * | 2012-07-20 | 2014-01-23 | 三菱レイヨン株式会社 | 多孔質電極基材、その製造方法、膜-電極接合体、及び固体高分子型燃料電池 |
KR101654488B1 (ko) * | 2012-07-20 | 2016-09-05 | 미쯔비시 레이온 가부시끼가이샤 | 다공질 전극 기재, 그의 제조 방법, 막-전극 접합체 및 고체 고분자형 연료 전지 |
JP2014103030A (ja) * | 2012-11-21 | 2014-06-05 | Toho Tenax Co Ltd | 多孔質導電シート及びその製造方法、電極材、燃料電池 |
WO2014181771A1 (ja) * | 2013-05-10 | 2014-11-13 | 三菱レイヨン株式会社 | 多孔質電極基材、その製造方法および固体高分子型燃料電池 |
JP6044639B2 (ja) * | 2013-05-10 | 2016-12-14 | 三菱レイヨン株式会社 | 多孔質電極基材、その製造方法および固体高分子型燃料電池 |
JP2015022838A (ja) * | 2013-07-17 | 2015-02-02 | 東邦テナックス株式会社 | 多孔質導電シート及びその製造方法 |
Also Published As
Publication number | Publication date |
---|---|
EP2506352A1 (en) | 2012-10-03 |
CA2767211C (en) | 2018-07-31 |
CA2767211A1 (en) | 2011-06-03 |
CN102422471A (zh) | 2012-04-18 |
EP2506352A4 (en) | 2014-05-07 |
KR101671558B1 (ko) | 2016-11-01 |
CN102422471B (zh) | 2014-10-22 |
JPWO2011065349A1 (ja) | 2013-04-11 |
US20120115063A1 (en) | 2012-05-10 |
JP5433588B2 (ja) | 2014-03-05 |
KR20120102721A (ko) | 2012-09-18 |
CN104409758B (zh) | 2017-08-01 |
EP2506352B1 (en) | 2017-01-04 |
CN104409758A (zh) | 2015-03-11 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
JP5433588B2 (ja) | 多孔質電極基材およびその製造方法 | |
US9716278B2 (en) | Porous electrode base material, method for manufacturing same, and precursor sheet | |
JP5664791B2 (ja) | 多孔質電極基材、その製造方法、膜−電極接合体、及び固体高分子型燃料電池 | |
JP6481766B2 (ja) | 多孔質基材、多孔質電極、炭素繊維紙、炭素繊維紙の製造方法、多孔質基材の製造方法 | |
JP6044639B2 (ja) | 多孔質電極基材、その製造方法および固体高分子型燃料電池 | |
JP2018133267A (ja) | 多孔質炭素電極 | |
JP5430537B2 (ja) | 多孔質電極基材及びその製造方法 | |
JP5430509B2 (ja) | 多孔質電極基材及びその製造方法 | |
JP5430513B2 (ja) | 多孔質電極基材及びその製造方法 | |
JP5501332B2 (ja) | 多孔質電極基材前駆体シート、その製造方法、多孔質電極基材、膜−電極接合体、および固体高分子型燃料電池 | |
JP2018142449A (ja) | 多孔質電極基材およびその製造方法 | |
JP2018055969A (ja) | 多孔質電極基材およびその製造方法 |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
WWE | Wipo information: entry into national phase |
Ref document number: 201080018395.8 Country of ref document: CN |
|
ENP | Entry into the national phase |
Ref document number: 2010548311 Country of ref document: JP Kind code of ref document: A |
|
121 | Ep: the epo has been informed by wipo that ep was designated in this application |
Ref document number: 10833195 Country of ref document: EP Kind code of ref document: A1 |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2767211 Country of ref document: CA |
|
WWE | Wipo information: entry into national phase |
Ref document number: 13384729 Country of ref document: US |
|
REEP | Request for entry into the european phase |
Ref document number: 2010833195 Country of ref document: EP |
|
WWE | Wipo information: entry into national phase |
Ref document number: 2010833195 Country of ref document: EP |
|
NENP | Non-entry into the national phase |
Ref country code: DE |
|
WWE | Wipo information: entry into national phase |
Ref document number: 5415/CHENP/2012 Country of ref document: IN |
|
ENP | Entry into the national phase |
Ref document number: 20127016384 Country of ref document: KR Kind code of ref document: A |