WO2013125182A1 - 固体高分子形燃料電池用膜電極接合体及びその製造方法と固体高分子形燃料電池 - Google Patents
固体高分子形燃料電池用膜電極接合体及びその製造方法と固体高分子形燃料電池 Download PDFInfo
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- H01M8/10—Fuel cells with solid electrolytes
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- H01M4/8647—Inert electrodes with catalytic activity, e.g. for fuel cells consisting of more than one material, e.g. consisting of composites
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- H01M4/8663—Selection of inactive substances as ingredients for catalytic active masses, e.g. binders, fillers
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- H01M4/88—Processes of manufacture
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- H01M4/88—Processes of manufacture
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- H01M4/88—Processes of manufacture
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- 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
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- H01M8/00—Fuel cells; Manufacture thereof
- H01M8/10—Fuel cells with solid electrolytes
- H01M8/1016—Fuel cells with solid electrolytes characterised by the electrolyte material
- H01M8/1018—Polymeric electrolyte materials
- H01M8/102—Polymeric electrolyte materials characterised by the chemical structure of the main chain of the ion-conducting polymer
- H01M8/1023—Polymeric electrolyte materials characterised by the chemical structure of the main chain of the ion-conducting polymer having only carbon, e.g. polyarylenes, polystyrenes or polybutadiene-styrenes
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- H01M8/00—Fuel cells; Manufacture thereof
- H01M8/10—Fuel cells with solid electrolytes
- H01M8/1016—Fuel cells with solid electrolytes characterised by the electrolyte material
- H01M8/1018—Polymeric electrolyte materials
- H01M8/1039—Polymeric electrolyte materials halogenated, e.g. sulfonated polyvinylidene fluorides
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- H01M8/10—Fuel cells with solid electrolytes
- H01M2008/1095—Fuel cells with polymeric electrolytes
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- H01M2250/00—Fuel cells for particular applications; Specific features of fuel cell system
- H01M2250/20—Fuel cells in motive systems, e.g. vehicle, ship, plane
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- H01M2300/00—Electrolytes
- H01M2300/0017—Non-aqueous electrolytes
- H01M2300/0065—Solid electrolytes
- H01M2300/0082—Organic polymers
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- H01M4/86—Inert electrodes with catalytic activity, e.g. for fuel cells
- H01M4/90—Selection of catalytic material
- H01M4/9075—Catalytic material supported on carriers, e.g. powder carriers
- H01M4/9083—Catalytic material supported on carriers, e.g. powder carriers on carbon or graphite
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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
- Y02E60/30—Hydrogen technology
- Y02E60/50—Fuel cells
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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
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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
- Y02T—CLIMATE CHANGE MITIGATION TECHNOLOGIES RELATED TO TRANSPORTATION
- Y02T90/00—Enabling technologies or technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02T90/40—Application of hydrogen technology to transportation, e.g. using fuel cells
Definitions
- the present invention relates to a membrane electrode assembly for a polymer electrolyte fuel cell, a method for producing the same, and a polymer electrolyte fuel cell.
- a fuel cell is a power generation system that generates electricity by using hydrogen and oxygen as fuel and causing a reverse reaction of water electrolysis. This has features such as high efficiency, low environmental load and low noise compared with the conventional power generation method, and is attracting attention as a clean energy source in the future.
- polymer electrolyte fuel cells that can be used near room temperature are considered promising for use in in-vehicle power supplies and household stationary power supplies.
- various research and development related to polymer electrolyte fuel cells have been conducted. ing. Challenges for commercialization include improving battery performance such as power generation characteristics and durability, and reducing infrastructure equipment and manufacturing costs.
- a polymer electrolyte fuel cell is configured by stacking a large number of single cells.
- the single cell has a structure in which a membrane / electrode assembly joined by sandwiching a polymer electrolyte membrane between two electrodes of an oxidation electrode and a reduction electrode is sandwiched by a separator having a gas flow path.
- a humidifier is required, which leads to high cost of the entire fuel cell system. Therefore, operation with low humidification is preferable, and further, non-humidification operation is desirable.
- Patent Document 1 As a method for obtaining high battery characteristics even under low humidification conditions, for example, there is a method for improving conductivity by changing the structure of the proton conductive polymer in the electrode catalyst layer as described in Patent Document 1. . According to Patent Document 1, the cell voltage can be improved by improving the conductivity of the proton conductive polymer in the electrode catalyst layer.
- x mass of polymer electrolyte / conductivity
- the structures of the proton conductive polymer in the electrode catalyst layer and the proton conductive polymer in the polymer electrolyte membrane are different, and the interface resistance between the electrode catalyst layer and the polymer electrolyte membrane is different.
- the membrane electrode assembly may be distorted or damaged due to an increase in the thickness or a difference in dimensional change rate between the electrode catalyst layer and the polymer electrolyte membrane when the humidity changes.
- the constituent components and the blending ratio thereof are optimized, the internal structure of the catalyst layer is not fully controlled, and battery characteristics may be deteriorated depending on the manufacturing method.
- the present invention has been made to solve the above-mentioned problems, and has a membrane electrode assembly for a polymer electrolyte fuel cell having high power generation characteristics even in a high-temperature and low-humidity environment, a method for producing the same, and a polymer electrolyte It is an object to provide a fuel cell.
- the invention according to claim 1 is directed to a polymer electrolyte fuel cell in which an electrode catalyst layer containing at least a proton conductive polymer and catalyst-supporting carbon is bonded to both surfaces of a polymer electrolyte membrane. It is a membrane electrode assembly, and the resistance value Ri of the proton conductive polymer of the electrode catalyst layer is within the range of 2 ⁇ cm 2 or more and 5 ⁇ cm 2 or less under the measurement conditions of relative humidity 20% and AC impedance 10 kHz to 100 Hz. It is characterized by.
- the invention according to claim 2 is characterized in that the thickness of the electrode catalyst layer is in the range of 1 ⁇ m to 15 ⁇ m.
- the invention according to claim 3 is characterized in that a ratio of the proton conductive polymer to the catalyst-supporting carbon is 0.8 or more and 1.1 or less.
- An invention according to claim 4 is a method for producing a membrane electrode assembly for a polymer electrolyte fuel cell according to any one of claims 1 to 3, wherein the catalyst-supporting carbon and a solvent are mixed.
- a solvent component from a coating step of applying the catalyst ink obtained in the main dispersion step to the surface of the substrate and a coating film of the catalyst ink applied to the surface of the substrate includes a pre-drying step of partially removing the coating film as a semi-dry catalyst layer, and a drying step of removing the solvent component from the semi-dry catalyst layer and drying.
- the invention according to claim 6 is characterized by having the membrane / electrode assembly for a polymer electrolyte fuel cell according to any one of claims 1 to 3.
- the first aspect of the present invention it is possible to obtain a membrane / electrode assembly for a polymer electrolyte fuel cell having high power generation characteristics even in a high temperature and low humidity environment.
- the second aspect of the present invention it is possible to provide a membrane electrode assembly for a polymer electrolyte fuel cell that does not have problems such as cracks on the surface of the catalyst layer while maintaining high power generation performance.
- the invention of claim 3 it is possible to obtain a membrane / electrode assembly for a polymer electrolyte fuel cell having high proton conductivity while maintaining gas and water diffusivity.
- FIG. 1 is a cross-sectional view of a membrane electrode assembly for a polymer electrolyte fuel cell according to a first embodiment of the present invention. It is explanatory drawing which shows the pre dispersion
- the present invention relates to a membrane electrode assembly for a polymer electrolyte fuel cell possessed by a polymer electrolyte fuel cell and a method for producing a membrane electrode assembly for a polymer electrolyte fuel cell possessed by a polymer electrolyte fuel cell (production) Method).
- the resistance value Ri of the proton conductive polymer in the electrode catalyst layer is high or low. I found that it had a big influence. Therefore, in the present invention, by setting the resistance value Ri of the proton conductive polymer in the electrode catalyst layer within a predetermined range, a solid polymer fuel cell having high power generation characteristics even in a high temperature and low humidity environment is obtained. Became possible.
- the production method of the electrode catalyst layer is greatly affected by the resistance value Ri of the proton conducting polymer. I found out that it was influencing. Therefore, in the present invention, at least the catalyst-carrying carbon and the solvent are mixed and subjected to a dispersion treatment, and then the obtained catalyst-carrying carbon dispersion is mixed with at least a proton conductive polymer and a solvent and subjected to the dispersion treatment.
- the resistance value Ri of the proton conductive polymer in the electrode catalyst layer can be set within a predetermined range.
- a semi-dry catalyst layer By removing the solvent component from the substrate and drying it, the resistance value Ri of the proton conductive polymer in the electrode catalyst layer can be kept within a predetermined range.
- FIG. 1 is a view showing a membrane electrode assembly for a polymer electrolyte fuel cell according to this embodiment.
- a membrane electrode assembly for a polymer electrolyte fuel cell (hereinafter referred to as a fuel cell membrane electrode assembly) 1 shown in FIG. 1 comprises a cathode catalyst layer 2 and an anode catalyst layer 3, and these electrode catalyst layers 2, 3 includes at least a proton conductive polymer and catalyst-supporting carbon.
- the fuel cell membrane electrode assembly 1 includes a polymer electrolyte membrane 4, and the cathode catalyst layer 2 is joined to one surface of the polymer electrolyte membrane 4 and the other side of the polymer electrolyte membrane 4.
- the anode catalyst layer 3 is bonded to the surface.
- the resistance value Ri is the relative humidity of 20%, the AC impedance 10kHz ⁇ 2 ⁇ cm 2 more 5Omucm 2 within the range of the measurement conditions of 100 Hz, more preferably 3Omucm 2 or more It is in the range of 5 ⁇ cm 2 or less.
- the resistance value is higher than this range, the output of the fuel cell decreases, and when the resistance value is lower than this range, there is a possibility that the short circuit occurs.
- the resistance value Ri of the proton conducting polymer of the electrode catalyst layers 2 and 3 was measured using a frequency response analyzer and a potentiogalvanostat, for example, an electrochemical evaluation apparatus such as 12608W type (1260/1287) or 1280C type manufactured by Solartron. It can be determined by measuring AC impedance.
- the thickness of the cathode catalyst layer 2 is preferably in the range of 0.1 ⁇ m to 20 ⁇ m, more preferably in the range of 3 ⁇ m to 15 ⁇ m, and still more preferably in the range of 10 ⁇ m to 15 ⁇ m. If it is thicker than this range, the surface of the catalyst layer may be cracked, or the diffusion of gas and generated water may be hindered, resulting in a decrease in fuel cell output, and the proton conductivity of the catalyst layer. It is difficult to set the resistance value Ri of the polymer within a desired range, specifically within a range of 5 ⁇ cm 2 or less. On the other hand, when the thickness is smaller than this range, the in-plane catalyst and the proton conductive polymer may be non-uniform.
- the thickness of the anode catalyst layer 3 is preferably in the range of 0.1 to 20 ⁇ m, more preferably in the range of 0.5 to 5 ⁇ m. If it is thicker than this range, the surface of the catalyst layer may be cracked, fuel supply may be hindered, and the output of the fuel cell may be reduced, and the resistance of the proton conductive polymer in the catalyst layer may decrease. It is difficult to set the value Ri within a desired range, specifically, a range of 5 ⁇ cm 2 or less. On the other hand, when the thickness is smaller than this range, the in-plane catalyst and the proton conductive polymer may be non-uniform.
- the thickness of the cathode catalyst layer 2 and the anode catalyst layer 3 can be confirmed as follows, for example. Observe at least five cross-sections at about 3000 to 10,000 times with a scanning electron microscope (SEM), measure three or more thicknesses at each observation point, and use the average value as a representative value at each observation point. . The average value of the representative values is defined as the catalyst layer thickness.
- the ratio of the proton conductive polymer to the carbon support of the electrode catalyst layers 2 and 3 is preferably in the range of 0.8 to 1.1. If it is higher than this range, the proton conductive polymer may interfere with the diffusion of gas and water generated, and the output of the fuel cell may be reduced. There is a possibility that the entanglement of the molecule with the catalyst becomes insufficient and the output of the fuel cell is lowered.
- Various proton conductive polymers for the electrode catalyst layers 2 and 3 and the polymer electrolyte membrane 4 are used.
- the proton conducting polymer used for the electrode catalyst layers 2 and 3 and the polymer electrolyte membrane 4 only needs to have proton conductivity, and a fluorine polymer electrolyte or a hydrocarbon polymer electrolyte may be used. Is possible.
- fluoropolymer electrolyte examples include Nafion (registered trademark) manufactured by DuPont, Flemion (registered trademark) manufactured by Asahi Glass Co., Ltd., Aciplex (registered trademark) manufactured by Asahi Kasei Co., Ltd., and Gore Select (registered trademark) manufactured by Gore. Etc. can be used.
- As the hydrocarbon polymer electrolyte sulfonated polyether ketone, sulfonated polyethersulfone, sulfonated polyetherethersulfone, sulfonated polysulfide, sulfonated polyphenylene and the like can be used.
- the catalyst for the electrode catalyst layers 2 and 3 includes platinum, palladium, ruthenium, iridium, rhodium, osmium, platinum group elements, iron, lead, copper, chromium, cobalt, nickel, manganese, vanadium, molybdenum, gallium, aluminum, etc. These metals or their alloys, or oxides, double oxides, carbides, and the like can be used.
- the carbon supporting these catalysts may be any powder as long as it is in the form of fine powder and has conductivity and is not affected by the catalyst, but carbon black, graphite, graphite, activated carbon, carbon nanotubes, Fullerene can be preferably used.
- a carrier other than carbon may be used as long as it has conductivity and is not affected by the catalyst.
- a method for manufacturing the fuel cell membrane electrode assembly 1 shown in FIG. 1 will be described with reference to FIGS.
- a proton-conducting polymer dispersion 14 in which at least a proton-conducting polymer is dispersed in a solvent is added, and the catalyst-carrying carbon 12 and the proton conduction are dispersed.
- the catalyst-supporting carbon dispersion 13 and the proton conductive polymer dispersion 14 are mixed so that the conductive polymer is dispersed in the solvent to obtain the catalyst ink 15 (main dispersion step 17).
- the solvent used for obtaining the catalyst ink 15 is one that can dissolve or disperse the proton conductive polymer in a highly fluid state without eroding the catalyst particles and the proton conductive polymer. There is no particular limitation.
- the solvent may contain water as long as it is compatible with the proton conductive polymer.
- the amount of water added is not particularly limited as long as the proton conductive polymer is not separated to cause white turbidity or gelation.
- a volatile liquid organic solvent may be used as the solvent, but when lower alcohol is used, there is a high risk of ignition, so when using such a solvent, a mixed solvent with water is preferable. .
- the catalyst ink 15 is obtained in the present dispersion step 17, as shown in FIG. 3, the catalyst ink 15 is applied to the surface of the substrate 21 formed in a sheet shape, and the solvent component is removed from the coating film of the catalyst ink 15.
- the catalyst ink 15 applied to the surface of the base material 21 is semi-dried until a part of the semi-dry catalyst layer 22 is removed (a coating process 23 and a pre-drying process 24). Then, the semi-dry catalyst layer 22 is dried until the semi-dry catalyst layer 22 becomes the electrode catalyst layer 2, and the solvent component is removed from the semi-dry catalyst layer 22 (drying step 25).
- Examples of the base material 21 to which the catalyst ink 15 is applied include an ethylene tetrafluoroethylene copolymer (ETFE), a tetrafluoroethylene-hexafluoropropylene copolymer (FEP), and a tetrafluoroperfluoroalkyl vinyl ether copolymer (PFA). ) And polytetrafluoroethylene (PTFE) and other fluororesins having excellent transferability can be used.
- ETFE ethylene tetrafluoroethylene copolymer
- FEP tetrafluoroethylene-hexafluoropropylene copolymer
- PFA tetrafluoroperfluoroalkyl vinyl ether copolymer
- PTFE polytetrafluoroethylene
- other fluororesins having excellent transferability can be used.
- Polymer films such as polyimide, polyethylene terephthalate, polyamide (nylon), polysulfone, polyethersulfone, polyphenylene sulfide, polyether ether ketone, polyetherimide, polyarylate, and polyethylene naphthalate can also be used. Furthermore, it is possible to directly apply the catalyst ink 15 using a polymer electrolyte membrane as the substrate 21.
- various coating methods such as die coating, roll coating, curtain coating, spray coating, and squeegee can be used.
- a die coat that can also be used.
- a warm air oven, IR drying, reduced-pressure drying, or the like can be used.
- a membrane electrode assembly 1 for a fuel cell as shown in FIG. 1 is obtained by forming the electrode catalyst layer 3 on the opposite surface in the same process.
- the cathode catalyst layer 2 and the anode catalyst layer 3 are formed by the above-described steps, and the polymer electrolyte membrane 4 is formed.
- the cathode catalyst layer 2 and the anode catalyst layer 3 are bonded to both surfaces of the polymer electrolyte membrane 4 by heating and pressurizing the laminated body in which the alignment is performed while the substrate surfaces are opposed to each other. Thereafter, the sheet-like substrate 21 is peeled off from the surfaces of the cathode catalyst layer 2 and the anode catalyst layer 3 to obtain a fuel cell membrane electrode assembly 1 as shown in FIG.
- the electrode catalyst layers 2 and 3 Is preferably 0.5 MPa or more and 20 MPa or less, and more preferably 2 MPa or more and 15 MPa or less.
- the pressure is higher than this, the electrode catalyst layers 2 and 3 are compressed too much, and when the pressure is lower than this, the bonding property between the electrode catalyst layers 2 and 3 and the polymer electrolyte membrane 4 is lowered and the battery performance is lowered.
- FIG. 4 shows the state of the electrode catalyst layer when the fuel cell membrane electrode assembly is manufactured by the above-described method, and the fuel cell membrane electrode assembly is obtained using the catalyst ink obtained without going through the pre-dispersion step.
- FIG. 5 shows the state of the electrode catalyst layer when the is manufactured.
- the oxidation-reduction reaction of the fuel cell is performed by the catalyst 32 (see FIG. 4) of the electrode catalyst layer in contact with both the carbon carrier 33 and the proton conductive polymer 31 which are electron conductors, and the introduced gas can adsorb. Only occurs at the surface (three-phase interface). Therefore, when the ratio of the carbon support 33 to the proton conductive polymer 31 is in the range of 0.8 to 1.1, as shown in FIG.
- the proton conducting polymer 31 has a structure in which the area of the three-phase interface is large, and the supply path for protons and fuel gas to the three-phase interface is good, so that the battery performance can be improved.
- the ratio of the carbon support 33 and the proton conductive polymer 31 when the ratio of the carbon support 33 and the proton conductive polymer 31 is higher than 1.1, as shown in FIG. 5A, the proton conductive polymer 31 prevents the diffusion of gas or generated water. There is a possibility of reducing the output of the fuel cell. Further, when the ratio of the carbon support 33 and the proton conductive polymer 31 is lower than 0.8, as shown in FIG. 5B, the entanglement of the proton conductive polymer 31 with the catalyst 32 becomes insufficient. This may reduce the output of the fuel cell.
- the electrode catalyst layers 2 and 3 are formed using the catalyst ink obtained without passing through the pre-dispersion step 16, as shown in FIG.
- the number of the catalyst 32 present in the non-existing area increases and does not contribute to the oxidation-reduction reaction of the electrode, so that the output of the fuel cell may be reduced.
- the aggregation of the proton conductive polymer 31 occurs, and the catalyst 32 present at a place other than the three-layer interface increases, which does not contribute to the oxidation-reduction reaction of the electrode. May decrease the output of.
- Example 1 A platinum-supported carbon catalyst (trade name: TEC10E50E, manufactured by Tanaka Kikinzoku Kogyo Co., Ltd.), a mixed solvent of water and ethanol was mixed and subjected to dispersion treatment with a planetary ball mill to prepare a catalyst-supported carbon dispersion. Next, a proton conductive polymer (Nafion: registered trademark of DuPont) dispersion is mixed with the catalyst-supported carbon dispersion so that the ratio x of the proton conductive polymer to the carbon carrier is 1. The catalyst ink was prepared by carrying out dispersion treatment with a planetary ball mill.
- TEC10E50E manufactured by Tanaka Kikinzoku Kogyo Co., Ltd.
- the adjusted catalyst ink is applied to the surface of the PTFE film in a rectangular shape by a slit die coater, and then the PTFE film coated with the catalyst ink is put in a 70 ° C. hot air oven to eliminate the catalyst ink tack. Until dried. Furthermore, the PTFE film on which the semi-dry catalyst layer was formed was placed in a 100 ° C. hot air oven to dry the catalyst layer, and a cathode catalyst layer was formed on the PTFE surface. Moreover, the anode catalyst layer was formed on the PTFE surface by the same method.
- the anode catalyst layer and the cathode catalyst layer formed on the PTFE film are arranged so as to face both surfaces of the polymer electrolyte membrane (Nafion 212: registered trademark, manufactured by Dupont), and this laminate is hot-pressed.
- the membrane / electrode assembly of Example 1 was obtained by peeling the PTFE film.
- Example 2 A membrane electrode assembly of Example 2 was obtained in the same manner as in Example 1 except that an ultrasonic homogenizer was used in place of the planetary ball mill in the pre-dispersing step.
- Example 3 A membrane / electrode assembly of Example 3 was obtained in the same manner as in Example 1 except that an IR drying furnace was used instead of the warm air oven in the pre-drying step.
- Example 4 A membrane electrode assembly of Example 4 was obtained in the same manner as in Example 1 except that the catalyst ink was prepared so that the ratio x of the proton conductive polymer to the carbon carrier was 0.8.
- Example 5 A membrane electrode assembly of Example 5 was obtained in the same manner as in Example 1 except that the catalyst ink was prepared so that the ratio x of the proton conductive polymer to the carbon support was 1.1.
- Comparative Example 1 A membrane / electrode assembly of Comparative Example 1 was obtained in the same manner as in Example 1 except that the catalyst ink was prepared so that the ratio x of the proton conductive polymer to the carbon carrier was 0.7.
- Comparative Example 2 A membrane electrode assembly of Comparative Example 2 was obtained in the same manner as in Example 1 except that the catalyst ink was prepared so that the ratio x of the proton conductive polymer to the carbon carrier was 1.2.
- Comparative Example 3 A platinum-supported carbon catalyst (trade name: TEC10E50E, manufactured by Tanaka Kikinzoku Kogyo Co., Ltd.), a mixed solvent of water and ethanol, and a proton conductive polymer (Nafion: registered trademark of DuPont) dispersion are mixed and dispersed with a planetary ball mill.
- a membrane / electrode assembly of Comparative Example 3 was obtained in the same manner as in Example 1 except that the treatment was performed to prepare a catalyst ink.
- Comparative Example 4 A membrane / electrode assembly of Comparative Example 4 was obtained in the same manner as in Example 1 except that the PTFE film coated with the catalyst ink was placed in a 100 ° C. hot air oven and the catalyst layer was dried.
- the coordinates (Z1, Z′1) of the intersection with the real axis when the high frequency region (45 ° region) is linearly approximated, the straight line approximation line in the high frequency region, and the straight line approximation line in the low frequency region Ri is calculated by multiplying the value of Ri / 3 obtained by the above-mentioned AC impedance measurement by 3 because Z2-Z1 corresponds to Ri / 3 when the coordinates of the intersection of (Z2, Z'2) are .
- This Ri is the resistance value of the proton conducting polymer contained in the cathode catalyst layer and the anode catalyst layer, and can be distinguished from the resistance value of the proton conducting polymer contained in the polymer electrolyte membrane.
- Example 1 a membrane electrode assembly for a polymer electrolyte fuel cell excellent in power generation performance was obtained in which the resistance value Ri of the proton conductive polymer in the electrode catalyst layer was within a predetermined range. .
- the resistance value Ri of the proton conducting polymer in the electrode catalyst layer was larger than the predetermined range, and the power generation performance was lowered.
- the present invention has a performance that can be suitably used for a fuel cell using a polymer electrolyte membrane, in particular, a stationary cogeneration system, a fuel cell vehicle, and the like, and can further reduce costs.
- the utility value is great.
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Abstract
Description
固体高分子形燃料電池では、高分子電解質膜や電極触媒層中のプロトン伝導性高分子のプロトン伝導性や導電性を確保するために、膜電極接合体を加湿する必要があるが、加湿する為には加湿器が必要となり、燃料電池システム全体のコスト高につながってしまう。その為、低加湿での運転が好ましく、さらには無加湿運転が望ましい。
また、特許文献2による方法では、構成成分及びその配合比が最適化されているものの、触媒層の内部構造が制御しきれておらず、製造方法によっては電池特性が低下する可能性がある。
請求項3に係る発明は、前記触媒担持カーボンに対する前記プロトン伝導性高分子の比率が0.8以上1.1以下であることを特徴とする。
請求項4に係る発明は、請求項1~3のいずれか一項に記載の固体高分子形燃料電池用膜電極接合体を製造する方法であって、触媒担持カーボンと溶媒とを混合して前記触媒担持カーボンを溶媒中に分散させるプレ分散工程と、前記プレ分散工程で得られた触媒担持カーボン分散液に少なくともプロトン伝導性高分子を加えて混合し、前記触媒担持カーボンと前記プロトン伝導性高分子とを溶媒中に分散させる本分散工程とを含むことを特徴とする。
請求項6に係る発明は、請求項1~3のいずれか一項に記載の固体高分子形燃料電池用膜電極接合体を有することを特徴とする。
請求項2に係る発明によれば、高い発電性能を維持しつつ、触媒層表面のひび割れ等の問題のない固体高分子形燃料電池用膜電極接合体を提供することが可能となる。
請求項3に係る発明によれば、ガスや水の拡散性を維持しつつ、高いプロトン伝導性を有する固体高分子形燃料電池用膜電極接合体を得ることが可能となる。
請求項5に係る発明によれば、触媒インクに含まれる溶媒成分による高分子電解質膜の膨潤を抑えつつ、高いプロトン伝導性を有する固体高分子形燃料電池用膜電極接合体を得ることが可能となる。
請求項6に係る発明によれば、高温低加湿環境下においても高い発電特性を有する固体高分子形燃料電池を得ることが可能となる。
以下、本発明の第1実施形態(以下、「本実施形態」と記載する)について、図面を参照しつつ説明する。なお、本実施形態は本発明の一例であり、本発明を限定するものではない。
本発明は、固体高分子形燃料電池が有する固体高分子形燃料電池用膜電極接合体と、固体高分子形燃料電池が有する固体高分子形燃料電池用膜電極接合体を製造する方法(製造方法)を提供するものである。
図1は、本実施形態に係る固体高分子形燃料電池用膜電極接合体を示す図である。図1に示される固体高分子形燃料電池用膜電極接合体(以下、燃料電池用膜電極接合体という)1はカソード触媒層2及びアノード触媒層3を具備し、これらの電極触媒層2,3は少なくともプロトン伝導性高分子と触媒担持カーボンを含んで構成されている。また、燃料電池用膜電極接合体1は高分子電解質膜4を具備し、この高分子電解質膜4の一方の表面にカソード触媒層2が接合されていると共に、高分子電解質膜4の他方の表面にアノード触媒層3が接合されている。
電極触媒層2,3のカーボン担体に対するプロトン伝導性高分子の比率は、0.8以上1.1以下の範囲内であることが好ましい。この範囲よりも高い場合には、プロトン伝導性高分子がガスや生成する水の拡散を妨げて燃料電池の出力が低下する可能性があり、この範囲よりも低い場合には、プロトン伝導性高分子の触媒への絡みが不十分となり、燃料電池の出力が低下する可能性がある。
また、電極触媒層2,3及び高分子電解質膜4に用いられるプロトン電導性高分子はプロトン伝導性を有するものであれば良く、フッ素系高分子電解質や炭化水素系高分子電解質を用いることが可能である。
また、炭化水素系高分子電解質としては、スルホン化ポリエーテルケトン、スルホン化ポリエーテルスルホン、スルホン化ポリエーテルエーテルスルホン、スルホン化ポリスルフィド、スルホン化ポリフェニレン等を用いることが可能である。
電極触媒層2,3の触媒としては白金、パラジウム、ルテニウム、イリジウム、ロジウム、オスミウムの白金族元素の他、鉄、鉛、銅、クロム、コバルト、ニッケル、マンガン、バナジウム、モリブデン、ガリウム、アルミニウムなどの金属またはこれらの合金、または酸化物、複酸化物、炭化物などを用いることが可能である。
図1に示した燃料電池用膜電極接合体1の製造方法について、図2及び図3を参照して説明する。
まず、図2に示すように、少なくとも触媒担持カーボン12と溶媒11とを混合し、触媒担持カーボン12が溶媒11中に分散した触媒担持カーボン分散液13を得る(プレ分散工程16)。
また、触媒インク15を得るときに用いる溶媒としては、触媒粒子やプロトン伝導性高分子を浸食することがなく、流動性の高い状態でプロトン伝導性高分子を溶解または微細ゲルとして分散できるものであれば良く、特に制限はない。
また、溶媒としては揮発性の液体有機溶媒を用いても良いが、低級アルコールを用いると発火の危険性が高いことから、このような溶媒を用いる際は水との混合溶媒とすることが好ましい。
プレ乾燥工程24及び乾燥工程25では、例えば、温風オーブン、IR乾燥、減圧乾燥等を用いることが可能である。
上述した方法で燃料電池用膜電極接合体を製造したときの電極触媒層の状態を図4に示すとともに、プレ分散工程を経ずに得られた触媒インクを用いて燃料電池用膜電極接合体を製造したときの電極触媒層の状態を図5に示す。
さらに、図5(d)に示すように、プロトン伝導性高分子31の凝集が発生し、三層界面でない所に存在する触媒32が多くなり、電極の酸化還元反応に寄与しないため、燃料電池の出力が低下する可能性がある。
(実施例1)
白金担持カーボン触媒(商品名:TEC10E50E、田中貴金属工業製)と水、エタノールの混合溶媒を混合し、遊星型ボールミルで分散処理を行い、触媒担持カーボン分散液を調製した。次に、この触媒担持カーボン分散液にプロトン伝導性高分子(ナフィオン:Nafion,デュポン社の登録商標)分散液を、カーボン担体に対するプロトン伝導性高分子の比率xが1となるように混合し、遊星型ボールミルで分散処理を行い、触媒インクを調製した。そして、調整した触媒インクを、PTFEフィルムの表面にスリットダイコーターにより矩形に塗布し、続けて、触媒インクが塗布されたPTFEフィルムを70℃の温風オーブンに入れて、触媒インクのタックがなくなるまで乾燥させた。さらに、半乾燥触媒層が形成されたPTFEフィルムを100℃の温風オーブンに入れて、触媒層を乾燥させ、カソード触媒層をPTFE表面に形成した。また、同様の方法により、アノード触媒層をPTFE表面に形成した。
そして、PTFEフィルム上に形成したアノード触媒層とカソード触媒層を、高分子電解質膜(ナフィオン212:登録商標、Dupont社製)の両面に対面するように配置し、この積層体をホットプレスした後にPTFEフィルムを剥離することで、実施例1の膜電極接合体を得た。
プレ分散工程において遊星型ボールミルのかわりに超音波ホモジナイザーを使用した以外は実施例1と同様にして、実施例2の膜電極接合体を得た。
(実施例3)
プレ乾燥工程において温風オーブンのかわりにIR乾燥炉を使用した以外は実施例1と同様にして、実施例3の膜電極接合体を得た。
(実施例4)
カーボン担体に対するプロトン伝導性高分子の比率xが0.8となるように触媒インクを調製した以外は実施例1と同様にして、実施例4の膜電極接合体を得た。
(実施例5)
カーボン担体に対するプロトン伝導性高分子の比率xが1.1となるように触媒インクを調製した以外は実施例1と同様にして、実施例5の膜電極接合体を得た。
カーボン担体に対するプロトン伝導性高分子の比率xが0.7となるように触媒インクを調製した以外は実施例1と同様にして、比較例1の膜電極接合体を得た。
(比較例2)
カーボン担体に対するプロトン伝導性高分子の比率xが1.2となるように触媒インクを調製した以外は実施例1と同様にして、比較例2の膜電極接合体を得た。
(比較例3)
白金担持カーボン触媒(商品名:TEC10E50E、田中貴金属工業製)と水、エタノールの混合溶媒とプロトン伝導性高分子(ナフィオン:Nafion,デュポン社の登録商標)分散液を混合し、遊星型ボールミルで分散処理を行い、触媒インクを調製した以外は実施例1と同様にして、比較例3の膜電極接合体を得た。
(比較例4)
触媒インクが塗布されたPTFEフィルムを100℃の温風オーブンに入れて触媒層を乾燥させた以外は実施例1と同様にして、比較例4の膜電極接合体を得た。
以下、実施例1~5と比較例1~4を用いて、高温低加湿環境下における電極触媒層中のプロトン伝導性高分子の抵抗値Ri及び発電性能を比較した結果を説明する。なお、膜電極接合体の両面にガス拡散層およびガスケット、セパレーターを配置し、所定の面圧となるように締め付けたセルを評価用単セルとして用いた。
電極触媒層中のプロトン伝導性高分子の抵抗値Riの測定は、R.Makhariaetal,Journal of The Electrochemical,152(5) A970-A977(2005)に記載の方法に準じて行った。
具体的には、まず、評価用単セルを80℃に設定し、アノード側に20%RHの水素ガス、カソード側に20%RHの窒素ガスを供給した。交流インピーダンス測定には、Solatino社製周波数応答アナライザ1260型とSolatino社製ポテンショガルバノスタット1287型を接続して使用し、印加電圧500mV、電位振幅10mVに設定して周波数10kHzから100Hzまで徐々に変化させた際の交流インピーダンスのナイキストプロットを得た。
評価用単セルを80℃に設定し、アノード側に25%RHの水素ガス、カソード側に25%SolatinoHの空気を供給した。水素利用率60%、空気利用率50%として、電流密度0.5A/cm2にて5分間発電保持した後のセル電圧を測定することで、発電性能の測定とした。
(比較結果)
実施例1~5と比較例1~4の固体高分子形燃料電池用膜電極接合体を用いた際の高温低加湿環境下の抵抗値Ri及びセル電圧を測定した結果を表1に示す。
2…カソード触媒層(電極触媒層)
3…アノード触媒層(電極触媒層)
4…高分子電解質膜
11…溶媒
12…触媒担持カーボン
13…触媒担持カーボン分散液
14…プロトン伝導性高分子分散液
15…触媒インク
16…プレ分散工程
17…本分散工程
21…基材
22…半乾燥触媒層
23…塗工工程
24…プレ乾燥工程
25…乾燥工程
31…プロトン伝導性高分子
32…触媒
33…カーボン担体
Claims (6)
- 高分子電解質膜の両面に、少なくともプロトン伝導性高分子と触媒担持カーボンを含む電極触媒層が接合された固体高分子形燃料電池用膜電極接合体であって、
前記電極触媒層のプロトン伝導性高分子の抵抗値Riが相対湿度20%、交流インピーダンス10kHz~100Hzの測定条件下で2Ωcm2以上5Ωcm2以下の範囲内であることを特徴とする固体高分子形燃料電池用膜電極接合体。 - 前記電極触媒層の厚さが0.1μm以上20μm以下の範囲内であることを特徴とする請求項1に記載の固体高分子形燃料電池用膜電極接合体。
- 前記触媒担持カーボンに対する前記プロトン伝導性高分子の比率が0.8以上1.1以下であることを特徴とする請求項1または2に記載の固体高分子形燃料電池用膜電極接合体。
- 請求項1~3のいずれか一項に記載の固体高分子形燃料電池用膜電極接合体を製造する方法であって、
触媒担持カーボンと溶媒とを混合して前記触媒担持カーボンを溶媒中に分散させるプレ分散工程と、
前記プレ分散工程で得られた触媒担持カーボン分散液に少なくともプロトン伝導性高分子を加えて混合し、前記触媒担持カーボンと前記プロトン伝導性高分子とを溶媒中に分散させる本分散工程とを含むことを特徴とする固体高分子形燃料電池用膜電極接合体の製造方法。 - 前記本分散工程で得られた触媒インクを基材表面に塗工する塗工工程と、前記基材表面に塗工された触媒インクの塗膜から溶媒成分を一部除去して前記塗膜を半乾燥触媒層とするプレ乾燥工程と、前記半乾燥触媒層から溶媒成分を除去して乾燥させる乾燥工程とを含むことを特徴とする請求項4に記載の固体高分子形燃料電池用膜電極接合体の製造方法。
- 請求項1~3のいずれか一項に記載の固体高分子形燃料電池用膜電極接合体を有することを特徴とする固体高分子形燃料電池。
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KR101877755B1 (ko) * | 2016-04-05 | 2018-07-13 | (주)상아프론테크 | 연료전지용 복합 전해질막, 이를 포함하는 막-전극 접합체, 이를 포함하는 연료전지, 및 이들의 제조방법 |
KR101877753B1 (ko) * | 2016-04-05 | 2018-07-13 | (주)상아프론테크 | 연료전지용 복합 전해질막, 이를 포함하는 막-전극 접합체, 이를 포함하는 연료전지, 및 이들의 제조방법 |
CN111837278A (zh) * | 2018-01-31 | 2020-10-27 | 凸版印刷株式会社 | 固体高分子型燃料电池用膜电极接合体及固体高分子型燃料电池 |
WO2020075777A1 (ja) * | 2018-10-09 | 2020-04-16 | 凸版印刷株式会社 | 燃料電池用膜電極接合体及び固体高分子形燃料電池 |
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Also Published As
Publication number | Publication date |
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US20140363756A1 (en) | 2014-12-11 |
KR20140138181A (ko) | 2014-12-03 |
EP2819227A1 (en) | 2014-12-31 |
JPWO2013125182A1 (ja) | 2015-07-30 |
EP2819227A4 (en) | 2015-11-25 |
JP6131944B2 (ja) | 2017-05-24 |
CN104115318A (zh) | 2014-10-22 |
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