WO2011036729A1 - Pile à combustible à oxyde solide - Google Patents

Pile à combustible à oxyde solide Download PDF

Info

Publication number
WO2011036729A1
WO2011036729A1 PCT/JP2009/004904 JP2009004904W WO2011036729A1 WO 2011036729 A1 WO2011036729 A1 WO 2011036729A1 JP 2009004904 W JP2009004904 W JP 2009004904W WO 2011036729 A1 WO2011036729 A1 WO 2011036729A1
Authority
WO
WIPO (PCT)
Prior art keywords
fuel electrode
catalyst
electrode
region
oxide
Prior art date
Application number
PCT/JP2009/004904
Other languages
English (en)
Japanese (ja)
Inventor
長田憲和
深澤孝幸
首藤直樹
Original Assignee
株式会社 東芝
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by 株式会社 東芝 filed Critical 株式会社 東芝
Priority to PCT/JP2009/004904 priority Critical patent/WO2011036729A1/fr
Publication of WO2011036729A1 publication Critical patent/WO2011036729A1/fr

Links

Images

Classifications

    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/86—Inert electrodes with catalytic activity, e.g. for fuel cells
    • H01M4/8636—Inert electrodes with catalytic activity, e.g. for fuel cells with a gradient in another property than porosity
    • H01M4/8642—Gradient in 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
    • H01M4/8605—Porous electrodes
    • H01M4/8621—Porous electrodes containing only metallic or ceramic material, e.g. made by sintering or sputtering
    • 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
    • H01M8/12—Fuel cells with solid electrolytes operating at high temperature, e.g. with stabilised ZrO2 electrolyte
    • H01M2008/1293—Fuel cells with solid oxide electrolytes
    • 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

Definitions

  • the present invention relates to a solid oxide fuel cell (SOFC), and particularly to an improved fuel electrode for SOFC.
  • SOFC solid oxide fuel cell
  • the solid oxide fuel cell can obtain a sufficient reaction rate without using an expensive noble metal catalyst due to its high operating temperature (700-1000 ° C), and compared with other types of fuel cells. As the power generation efficiency is the highest and the generation of CO 2 is small, it is expected as a next-generation clean power generation system.
  • a cermet material which is a mixed sintered body of metal particles having electronic conductivity and ceramic particles having ionic conductivity or mixed electron / ion conductivity is used for a general fuel electrode.
  • the metal used as the electrode catalyst also serves as an electron conduction path in the electrode, so the metal particles need to have a certain size.
  • the contributing three-phase interface is limited and it is difficult to improve the catalytic activity. For this reason, in order to improve the characteristics of the fuel electrode, it is necessary to increase the ion and electron conductivity in the electrode and to increase the surface area of the catalyst particles.
  • the metal particles near the electrolyte mainly function as an electrode catalyst, and the metal particles function as an electronic conduction path as they approach the surface of the fuel electrode.
  • the cermet material is used in this two-layer structure electrode, and the particle size of the metal particles used for the catalyst cannot be made very small, so that the catalytic activity is low and a significant improvement in characteristics cannot be expected.
  • the object of the present invention is to improve the catalytic activity in the solid oxide fuel cell.
  • the solid electrolyte fuel cell of the present invention is a solid oxide type comprising a sintered body of a metal catalyst or a catalyst particle comprising a metal catalyst-carrying metal oxide carrying a metal catalyst and an electron / ion mixed conductive particle.
  • a solid oxide fuel cell having a fuel cell anode The concentration of the catalyst in the fuel electrode is non-uniform in the direction perpendicular to the surface of the fuel electrode, and in the fuel electrode central region disposed between the electrolyte vicinity region and the fuel electrode surface vicinity region of the fuel electrode.
  • the catalyst concentration has a maximum value.
  • the anode activity of the solid oxide fuel cell can be improved, and the output of the solid oxide fuel cell can be increased.
  • FIG. 1 is a schematic sectional view of a solid oxide fuel cell (SOFC) fuel electrode according to a first embodiment of the present invention.
  • FIG. 2 is a schematic cross-sectional view of an SOFC fuel electrode having a catalyst concentration distribution in the fuel electrode using a reduction precipitation catalyst.
  • FIG. 3 is a diagram illustrating a manufacturing process of the fuel electrode according to the present embodiment.
  • SOFC solid oxide fuel cell
  • the fuel electrode material for a solid oxide fuel cell and the method for manufacturing the fuel electrode according to the present invention will be described, but the present invention is not limited to the following embodiments and examples.
  • the schematic diagram referred in the following description is a figure which shows the positional relationship of each structure, The ratio of the magnitude
  • Embodiments described herein relate generally to a fuel electrode and a solid oxide fuel cell using the same.
  • the SOFC is formed by laminating a fuel electrode material layer 12 on one surface and an oxygen electrode material layer 13 on the other surface with a solid oxide electrolyte plate 11 interposed therebetween.
  • Oxygen ions (O 2 ⁇ ) dissociated in the oxygen electrode material layer 13 move to the fuel electrode material layer 12 through the solid oxide electrolyte 11 and react with hydrogen to generate water.
  • the electrons generated at this time are taken out through an external circuit and used for power generation.
  • Ln rare earth element
  • A Sr, Ca, Ba
  • B At least one of Cr, Mn, Fe, Co, and Ni
  • x is 0 to 1
  • ⁇ in the above formula means that there is a defect in the oxygen atom
  • Consists of These complex oxides dissociate oxygen efficiently and have electronic conductivity. It is also possible to compensate for the ionic conductivity that is slightly insufficient with the composite oxide by adding an ionic conductive oxide together.
  • Sm 2 O 3 CeO 2 doped with, or Gd 2 O 3 CeO 2 doped with, Y 2 O 3 is used any one of the doped CeO 2 a.
  • These show mixed conductivity of electrons and ions in a reducing atmosphere, but only show high ionic conductivity in an oxygen-containing atmosphere, and are represented by the general formula Ln 1-x A x BO 3- ⁇ . It does not react with oxides showing mixed conductivity.
  • Ni—Al-based and Ni—Mg-based composite oxides The performance of composite electrodes with conductive particles has been demonstrated (see Japanese Patent Application Laid-Open Nos. 2009-64640 and 2009-64641).
  • Ni-Al-based and Ni-Mg-based composite oxides are reduced at high temperatures to form Ni particle-supported aluminum composite oxide / Ni particle-supported magnesium composite oxide on Al-based and Mg-based oxide substrates.
  • Ni fine particles can be formed, and the deposited Ni fine particles have a nanometer size, so that a large catalyst surface area can be obtained with a small amount of catalyst.
  • metal particles are produced as precipitates from the composite oxide during reduction, they are immobilized on the substrate, and the metal particles are hardly sintered even in a high-temperature reducing atmosphere.
  • the volume of the insulating substrate is larger than the volume of the deposited metal fine particles, the ohmic resistance in the fuel electrode layer is increased when forming an electrode.
  • the fuel electrode is formed by using the metal catalyst-supported oxide particles such as the Ni particle-supported aluminum oxide or the Ni particle-supported magnesium oxide and the electron / ion mixed conductive particles in combination.
  • the mixing ratio of the Ni particle-supported aluminum oxide or Ni particle-supported magnesium oxide and the electron / ion mixed conductive particles in the fuel electrode is changed.
  • the amount of the electron / ion mixed conductive particles 16 is increased in the fuel electrode surface vicinity region 18 and the electrolyte vicinity region 20, and Ni particle-supported aluminum composite oxide or Ni particle-supported magnesium composite oxidation is provided in the fuel electrode center region.
  • a fuel electrode central region 19 having a maximum catalyst concentration with an increased amount 17 is provided (FIG. 2).
  • the electron / ion mixed conductive particles 16 in the electrolyte vicinity region 20 mainly function as an ionic conductor
  • the electron / ion mixed conductive particles 16 in the surface vicinity portion 18 mainly function as an electron conductor. That is, the oxide ions (O 2 ⁇ ) generated at the oxygen electrode 13 can smoothly move through the solid oxide electrolyte 11 to the vicinity of the electrolyte 20, and the transferred oxygen ions (O 2 ⁇ ) Activated by many catalysts in the pole center region 19 and efficiently reacts with water vapor and electrons, and the generated electrons are transported to the current collector 21 through the fuel electrode surface vicinity region 18. Thereby, in addition to smooth conduction of electrons and ions in the fuel electrode, the catalyst can be used effectively, so that the fuel electrode characteristics are improved.
  • the metal catalyst-supported oxide particles used in the fuel electrode in the present embodiment are prepared by reducing a composite oxide that is a precursor containing a catalyst metal and an element constituting the metal oxide that supports the catalyst metal.
  • the metal catalyst-supported oxide particles can be used. Specifically, the Ni component in the Ni—Al composite oxide particles (NiAl 2 O 4 composite oxide) is precipitated on the surface by reduction, and the base material becomes aluminum oxide (mainly Al 2 O 3 ). That is, Ni particle carrying Al 2 O 3 is formed.
  • the size of the metal fine particles thus formed is generally several tens of nm. In order to perform an active catalytic function, the size of the metal fine particles is preferably about 5 nm to 500 nm.
  • a particle having a size of 5 nm or less is actually difficult to produce, and if the particle size is 500 nm or more, adjacent particles may be bonded to each other and may have the same problem as conventional NiO reduced.
  • a more preferable size for the catalyst is about 20 nm to 100 nm. Since this size is one to two orders of magnitude smaller than the conventional electrode catalyst size, an improvement in catalyst activity is expected. For this reason, the amount of NiAl 2 O 4 to be added is preferably in the range of 5 wt% to 80 wt% of the entire material constituting the electrode. More preferably, it is 10 to 50 weight%.
  • the particulate material having electron-ion mixed conductivity used in the fuel electrode CeO 2 doped with CeO 2 or Gd 2 O 3 doped with Sm 2 O 3, or a Y 2 O 3 doped and CeO 2 can be used with, without being limited thereto, as long as it has a high oxygen ion conductivity and electronic conductivity at 400 ° C. or higher 1000 ° C. or less.
  • CeO 2 doped with 10 to 50 mol% Sm 2 O 3 , Gd 2 O 3 , or Y 2 O 3 is preferable. (See J. Appl. Electrochem., 18, 527 (1988).).
  • the mixing ratio of the substances constituting the fuel electrode material layer is preferably set in the following range.
  • a range of ⁇ 9 is preferred. The reason is that it is necessary to produce a sufficient network of electron / ion conductive oxide particles.
  • the amount of the catalyst-supporting metal oxide is larger than the region near the fuel electrode surface and the region near the solid electrolyte, and it is necessary not to cut the network between the ion conductive oxide particles.
  • the reason is that it is necessary to produce a sufficient network of electron / ion conductive oxide particles.
  • the electrolyte vicinity region 20 indicates a region of the fuel electrode material layer having a thickness of 1/3 from the surface of the solid electrolyte plate 11 in the fuel electrode material layer 12, and the fuel electrode surface vicinity region 18. Similarly, the region of the fuel electrode material layer having a thickness of 1/3 from the surface thereof in the fuel electrode material layer.
  • the relationship between the catalyst concentration in the layer near the fuel electrode surface area 18, the catalyst concentration in the fuel electrode center area 19, and the catalyst concentration in the electrolyte vicinity area 20 is as follows. By configuring so as to be high, the effect of the present invention is achieved.
  • the fuel electrode material layer 12 may be a layer having a clearly discontinuous surface, or the fuel electrode material layer does not have a discontinuous surface whose composition changes continuously. It may be a uniform layer. In this case, the average concentration of the material composition constituting each region may satisfy the above-described conditions, or may be a configuration having a clearly maximum value in a thinner region.
  • a mesh-like current collecting wiring layer or a porous current collecting layer having high electronic conductivity may be provided between the fuel electrode current collector 21 and the fuel electrode material layer 12. This facilitates electronic conduction between the fuel electrode current collector and the fuel electrode.
  • FIG. 3 shows a method of manufacturing the fuel electrode for the fuel cell according to the present embodiment.
  • a catalyst metal particle-supported oxide precursor such as a nickel aluminum composite oxide
  • S1 the raw materials are mixed and made into a paste
  • S2 the raw materials are mixed and made into a paste
  • S3 the raw materials are mixed and made into a paste
  • S2 the raw materials are mixed and made into a paste
  • S3 the shape
  • S3 is performed
  • This process is repeated until the fuel electrode has a required thickness, and reduction is performed to reduce the catalyst metal particle-supported oxide precursor (S4).
  • S4 the catalyst metal particle-supported oxide precursor
  • NiO powder and Al 2 O 3 powder are mixed and fired to prepare a catalyst precursor made of a Ni—Al composite oxide represented by NiAl 2 O 4 , and then pulverized to obtain a Ni—Al composite oxide Precursor particles are created.
  • the composite oxide particle diameter after pulverization is preferably about 0.1 to several ⁇ m.
  • Ni—Al composite oxide precursor particles thus prepared and the electron / ion mixed conductive particles are mixed at a target ratio, and an aqueous solution of a metal salt such as nitrate is added to the target composition.
  • a paste S1 in FIG. 3
  • electron-ion mixed conductive particles Sm 2 O 3 CeO 2 was doped or CeO 2 doped with Gd 2 O 3, or uses a CeO 2 doped with Y 2 O 3, are limited to However, what is necessary is just to have high oxide ion electroconductivity and electronic conductivity in 400 degreeC or more and 1000 degrees C or less.
  • the pasted mixed powder is screen-printed on the surface of the solid electrolyte plate 11, and heated to a temperature at which the adhesive strength between the two is increased and baked (S2, S3 in FIG. 3).
  • the firing temperature is preferably in the range of 1000 ° C. to 1400 ° C.
  • the area near the fuel electrode surface 18 and the center of the fuel electrode where the ratio of the Ni—Al composite oxide particles and the electron / ion mixed conductive particles is different in each part, which is a feature of this embodiment Region 19 and electrolyte vicinity region 20 are formed.
  • the method of forming the electron / ion mixed conductive particles 16 and the Ni—Al composite oxide precursor particles is not limited to this.
  • the mixed powder may be made into a slurry by coating, dipping, or spray coating, or formed into a sheet and laminated.
  • the Ni—Al composite oxide particles and the electron / ion mixed conductive oxide particles are combined and integrated to form a network.
  • the fuel electrode material layer and the oxygen electrode material layer are preferably porous composed of open cells, and are mixed with a pore-forming material that is previously burned down to form pores.
  • pores can be effectively formed.
  • An example of the pore forming material is an organic material such as acrylic spherical particles.
  • the composite oxide represented by the formula (1) is pasted using water or an alcohol solvent, and the solid electrolyte plate 11 on the side opposite to the surface on which the fuel electrode is baked is formed. Screen printing is performed on the surface, and the temperature is raised to a temperature at which the adhesive strength between the two is increased, followed by firing. In general, it is preferable to fire in the range of 1000 ° C. to 1300 ° C.
  • particles exhibiting ionic conductivity may be mixed.
  • the particles having ion conductivity for example, SDC, GDC, YDC, or the like can be used.
  • the fuel electrode is reduced in a reducing atmosphere of 800 ° C. or higher and 1000 ° C. or lower (S4 in FIG. 3).
  • the reduction treatment of NiO is performed at about 900 ° C. so as not to raise the temperature more than necessary.
  • NiAl 2 O 4 as a main component, Ni is sufficiently precipitated, so that the reduction is performed at 900 ° C. or more. It is more preferable.
  • the reduction time is not particularly limited, but may be about 10 minutes.
  • NiAl 2 O 4 composite oxide The Ni component in the Ni—Al composite oxide precursor particles (NiAl 2 O 4 composite oxide) is deposited on the surface by the reduction, and the base material becomes aluminum oxide (mainly Al 2 O 3 ). That is, Ni particle-supported Al 2 O 3 is formed.
  • the size of the metal fine particles thus formed is generally several tens of nm. In order to perform an active catalytic function, the size of the metal fine particles is preferably about 5 nm to 500 nm. A particle having a size of 5 nm or less is actually difficult to produce, and if the particle size is 500 nm or more, adjacent particles may be bonded to each other and may have the same problem as conventional NiO reduced. A more preferable size for the catalyst is about 20 nm to 100 nm.
  • the amount of NiAl 2 O 4 to be added is preferably in the range of 5 wt% to 80 wt% of the entire material constituting the electrode. More preferably, it is 10 to 50 weight%.
  • the catalyst particle diameter to be formed is small, the amount of catalyst used in the conventional cermet type fuel electrode can be reduced even at the catalyst concentration maximum portion, and the mixed conductor portion can be made large. This makes it possible to suppress differences in thermal expansion from the solid electrolyte and differences due to matching mismatch.
  • the deposited metal particles are present only in one layer on the surface portion of the base material Al 2 O 3 , have good consistency with the base material, and have a strong bond. Therefore, it also has a feature that it does not move easily even when exposed to a high temperature reducing atmosphere.
  • the contact resistance of the fuel electrode using the composite oxide capable of fixing the fine Ni particles to the base material can be reduced, and the cell Loss can be reduced.
  • the precipitation catalyst can be used effectively, and the cell output can be improved.
  • an inexpensive manufacturing method such as screen printing and spray coating can be applied even in the electrode preparation process, and a cell can be manufactured at low cost.
  • NiO powder having an average particle diameter of about 1 ⁇ m and Al 2 O 3 powder having an average particle diameter of about 0.4 ⁇ m were mixed at a molar ratio of 1: 1, the mixed powder was press-molded, and the mixture was pressed in argon at 1300 ° C. for 5 minutes.
  • NiAl 2 O 4 composite oxide was produced by sintering for a period of time. Using a planetary ball mill, this composite oxide was pulverized until the specific surface area became 20 to 23 m 2 / g to obtain a NiAl 2 O 4 fuel electrode catalyst precursor.
  • NiAl 2 O 4 fuel electrode catalyst precursor prepared in “Preparation of Ni—Al composite oxide precursor” and SDC (Sm 0.2 Ce) having an average particle size of 0.3 ⁇ m as a sintered body having ionic conductivity. 0.8 O 2 ) particles were weighed so that the weight ratio of the pulverized particles was 10:90, 15:85, 20:80, and 30:70, respectively.
  • a fuel electrode paste was prepared by adding approximately 30% by weight of the Ce and Sm nitrate aqueous solution prepared in the above “adjustment of pasting solvent” to the mixed powder, and mixing the mixture with a high-speed rotary mixer.
  • a Pt electrode was similarly printed on the opposite surface of the YSZ electrolyte to form an oxygen electrode, and a Pt reference electrode was applied to the electrolyte side surface, followed by baking at 960 ° C. for 30 minutes.
  • the Ni paste mixed with YSZ powder Ni: YSZ is mixed so that the weight ratio is 82:18
  • a current collecting layer was laminated on the fuel electrode surface. Thereafter, heat treatment was performed at 960 ° C. for 30 minutes in an air atmosphere, and the current collecting layer was immobilized on the electrode surface.
  • a Pt electrode was similarly printed on the opposite surface of the YSZ electrolyte to form an oxygen electrode, and a Pt reference electrode was applied to the electrolyte side surface, followed by baking at 960 ° C. for 30 minutes.
  • the Ni paste mixed with YSZ powder Ni: YSZ is mixed so that the weight ratio is 82:18
  • a current collecting layer was laminated on the fuel electrode surface. Thereafter, heat treatment was performed at 960 ° C. for 30 minutes in an air atmosphere, and the current collecting layer was immobilized on the electrode surface.
  • Ni paste mixed with YSZ powder Ni: YSZ is mixed so that the weight ratio is 82:18 is printed in the same manner as the fuel electrode paste so that it overlaps exactly on the three-layer structure fuel electrode surface.
  • a current collecting layer was laminated on the fuel electrode surface. Thereafter, heat treatment was performed at 960 ° C. for 30 minutes in an air atmosphere, and the current collecting layer was immobilized on the electrode surface.
  • ⁇ Cell characteristic evaluation test> The flat plate type solid oxide electrochemical cell produced in Example 1 and the same cell produced in Comparative Examples 1 and 2 were set in an output characteristic evaluation apparatus, and the fuel electrode side was sealed with a Pyrex (registered trademark) glass material. A Pt wire having a diameter of 0.5 mm was attached to the side surface of the electrolyte to obtain a reference electrode. After raising the temperature in an N 2 atmosphere, hydrogen was introduced into the fuel electrode to perform a reduction treatment. The hydrogen reduction time was set at 1000 ° C. for 30 minutes.
  • Table 1 shows the electrochemical property evaluation results of the cells of Example 1 and Comparative Examples 1 and 2.
  • the power density of Example 1 is about 8% higher than the power density of Comparative Example 1, and the power density of about 32% higher than the power density of Comparative Example 2. It was observed.
  • the ohmic resistance in the fuel electrode is similarly compared. The ohmic resistance in the electrode is obtained by subtracting the theoretical electrolyte resistance of the YSZ electrolyte used from the cell resistance between the terminals, and the theoretical electrolyte resistance of 0.5 mm YSZ used in both cells is 0.50; cm 2 .
  • the contact resistance on the oxygen electrode side and the resistance in the electrode are regarded as sufficiently low, and the fuel electrode resistance is obtained by subtracting the theoretical electrolyte resistance from the cell resistance between the terminals. Comparing the calculation results of the ohmic resistance in the fuel electrode of both cells, the fuel electrode resistance of 0.01; cm 2 was compared in Comparative Example 1 while it was suppressed to almost zero in Example 1. In Example 2, an anode resistance of 0.05; cm 2 exists. As described above, from the comparison results of cell output density and ohmic resistance in the fuel electrode, the cell of Example 1 has higher characteristics than Comparative Examples 1 and 2, and has a structure having a catalyst concentration maximum at the center in the fuel electrode. The characteristic improvement effect by appears.
  • the effect of the catalyst concentration distribution in the fuel electrode is expected to be comparable even if the Ni-supported particles are not only aluminum oxide but also Ni-particle-supported magnesium oxide.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Electrochemistry (AREA)
  • General Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Ceramic Engineering (AREA)
  • Inert Electrodes (AREA)
  • Fuel Cell (AREA)

Abstract

La présente invention se rapporte à une pile à combustible à oxyde solide qui est apte à utiliser un catalyseur de façon beaucoup plus efficace. La pile à combustible à oxyde solide selon l'invention peut présenter des caractéristiques de rendement élevées grâce à une distribution de la concentration de catalyseur à l'intérieur d'une électrode à combustible. Une électrode à combustible est formée. La structure de l'électrode à combustible présente une concentration de catalyseur maximale dans une zone située entre une région proche d'un électrolyte solide de couche à combustible et une région proche de la surface de l'électrode à combustible. La construction susmentionnée permet de faciliter le transfert d'électrons et d'ions dans l'électrode à combustible autour de la partie qui présente la concentration de catalyseur maximale. Cette construction permet par ailleurs d'améliorer les propriétés d'une électrode à combustible et d'augmenter le rendement de la pile à combustible.
PCT/JP2009/004904 2009-09-28 2009-09-28 Pile à combustible à oxyde solide WO2011036729A1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
PCT/JP2009/004904 WO2011036729A1 (fr) 2009-09-28 2009-09-28 Pile à combustible à oxyde solide

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/JP2009/004904 WO2011036729A1 (fr) 2009-09-28 2009-09-28 Pile à combustible à oxyde solide

Publications (1)

Publication Number Publication Date
WO2011036729A1 true WO2011036729A1 (fr) 2011-03-31

Family

ID=43795502

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2009/004904 WO2011036729A1 (fr) 2009-09-28 2009-09-28 Pile à combustible à oxyde solide

Country Status (1)

Country Link
WO (1) WO2011036729A1 (fr)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2015114168A1 (fr) * 2014-02-03 2015-08-06 Centre National De La Recherche Scientifique (Cnrs) DEPOT METALLIQUE PROFOND DANS UNE MATRICE POREUSE PAR PULVERISATION MAGNETRON PULSEE HAUTE PUISSANCE HiPIMS, SUBSTRATS POREUX IMPREGNES DE CATALYSEUR METALLIQUE ET LEURS UTILISATIONS

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH1040933A (ja) * 1996-07-26 1998-02-13 Kansai Electric Power Co Inc:The 燃料電池におけるアノード成膜方法
JP2003151578A (ja) * 2001-08-30 2003-05-23 Toto Ltd 固体電解質型燃料電池燃料極膜の製造方法
JP2009064640A (ja) * 2007-09-05 2009-03-26 Toshiba Corp 固体酸化物電気化学セルの燃料極、その製造方法、及び固体酸化物電気化学セル

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH1040933A (ja) * 1996-07-26 1998-02-13 Kansai Electric Power Co Inc:The 燃料電池におけるアノード成膜方法
JP2003151578A (ja) * 2001-08-30 2003-05-23 Toto Ltd 固体電解質型燃料電池燃料極膜の製造方法
JP2009064640A (ja) * 2007-09-05 2009-03-26 Toshiba Corp 固体酸化物電気化学セルの燃料極、その製造方法、及び固体酸化物電気化学セル

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2015114168A1 (fr) * 2014-02-03 2015-08-06 Centre National De La Recherche Scientifique (Cnrs) DEPOT METALLIQUE PROFOND DANS UNE MATRICE POREUSE PAR PULVERISATION MAGNETRON PULSEE HAUTE PUISSANCE HiPIMS, SUBSTRATS POREUX IMPREGNES DE CATALYSEUR METALLIQUE ET LEURS UTILISATIONS
FR3017135A1 (fr) * 2014-02-03 2015-08-07 Centre Nat Rech Scient Depot metallique profond dans une matrice poreuse par pulverisation magnetron pulsee haute puissance hipims, substrats poreux impregnes de catalyseur metallique et leurs utilisations

Similar Documents

Publication Publication Date Title
JP5244423B2 (ja) 固体酸化物型電気化学セル、およびその製造方法
JP2009064641A (ja) 固体酸化物電気化学セルの燃料極、その製造方法、及び固体酸化物電気化学セル
JP5270885B2 (ja) 固体酸化物電気化学セルの燃料極、その製造方法、及び固体酸化物電気化学セル
JP2003132906A (ja) 燃料電池用単セル及び固体電解質型燃料電池
TW201900898A (zh) 電化學元件、電化學模組、電化學裝置、能源系統、固態氧化物型燃料電池、及電化學元件之製造方法
US9153831B2 (en) Electrode design for low temperature direct-hydrocarbon solid oxide fuel cells
JP2012033418A (ja) 固体酸化物型燃料電池、及びその製造方法
JP5613286B2 (ja) 固体酸化物電気化学セルの燃料極及び固体酸化物電気化学セル
Zhao et al. High-performance cathode-supported solid oxide fuel cells with copper cermet anodes
JP5329869B2 (ja) 固体酸化物型電気化学セル、およびその製造方法
Zhang et al. Stability of Ni-YSZ anode for SOFCs in methane fuel: the effects of infiltrating La0. 8Sr0. 2FeO3-δ and Gd-doped CeO2 materials
Han et al. Fabrication of a quasi-symmetrical solid oxide fuel cell using a modified tape casting/screen-printing/infiltrating combined technique
WO2020004333A1 (fr) Électrode pour piles à oxyde solide et pile à oxyde solide l'utilisant
WO2022180982A1 (fr) Électrode à combustible et cellule électrochimique
WO2011036729A1 (fr) Pile à combustible à oxyde solide
JP5498675B2 (ja) 固体酸化物型電気化学セル
JP6088949B2 (ja) 燃料電池単セルおよびその製造方法
JP2004355814A (ja) 固体酸化物形燃料電池用セル及びその製造方法
JP2010080304A (ja) 電気化学セル水素極材料の製造方法
JP5211533B2 (ja) 燃料極用集電材、及びそれを用いた固体酸化物形燃料電池
JP6075924B2 (ja) 燃料電池単セルおよびその製造方法
Wongsawatgul et al. SrO Doping Effect on Fabrication and Performance of Ni/Ce1− xSrxO2− x Anode-Supported Solid Oxide Fuel Cell for Direct Methane Utilization
JP5971672B2 (ja) 固体酸化物型燃料電池、及びその製造方法
JP2015005527A (ja) 固体酸化物電気化学セルの燃料極及び固体酸化物電気化学セル
JP2013089371A (ja) 固体酸化物型燃料電池及びその製造方法

Legal Events

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

Ref document number: 09849760

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 09849760

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: JP