WO2015008674A1 - 燃料電池用複合材料、燃料電池用複合材料の製造方法及び燃料電池 - Google Patents
燃料電池用複合材料、燃料電池用複合材料の製造方法及び燃料電池 Download PDFInfo
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- WO2015008674A1 WO2015008674A1 PCT/JP2014/068285 JP2014068285W WO2015008674A1 WO 2015008674 A1 WO2015008674 A1 WO 2015008674A1 JP 2014068285 W JP2014068285 W JP 2014068285W WO 2015008674 A1 WO2015008674 A1 WO 2015008674A1
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- solid electrolyte
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- 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
- H01M8/124—Fuel cells with solid electrolytes operating at high temperature, e.g. with stabilised ZrO2 electrolyte characterised by the process of manufacturing or by the material of the electrolyte
- H01M8/1246—Fuel cells with solid electrolytes operating at high temperature, e.g. with stabilised ZrO2 electrolyte characterised by the process of manufacturing or by the material of the electrolyte the electrolyte consisting of oxides
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M4/00—Electrodes
- H01M4/86—Inert electrodes with catalytic activity, e.g. for fuel cells
- H01M4/90—Selection of catalytic material
- H01M4/9041—Metals or alloys
- H01M4/905—Metals or alloys specially used in fuel cell operating at high temperature, e.g. SOFC
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- 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
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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- 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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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M2300/00—Electrolytes
- H01M2300/0017—Non-aqueous electrolytes
- H01M2300/0065—Solid electrolytes
- H01M2300/0068—Solid electrolytes inorganic
- H01M2300/0071—Oxides
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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
Definitions
- the present invention relates to a composite material for fuel cells, a method for producing a composite material for fuel cells, and a fuel cell. More specifically, the present invention relates to a composite material for a fuel cell that can enhance the power generation performance of an electrolyte layer in a solid oxide fuel cell.
- a solid oxide fuel cell (hereinafter referred to as “SOFC”) includes an electrolyte-electrode stack in which an anode layer and a cathode layer are provided on both sides of a solid electrolyte layer.
- SOFC solid oxide fuel cell
- the strength of the solid electrolyte layer is reduced, which causes troubles during the manufacturing process and use.
- a structure (anode support structure) in which the anode layer laminated on the solid electrolyte layer is set thick to ensure the strength as a laminated body is often employed.
- an anode powder in which BaZrO 3 —Y 2 O 3 (hereinafter referred to as BZY) powder is employed as an electrolyte material, and nickel (Ni) or nickel oxide (NiO) is added as a catalyst to the BZY powder as an anode material.
- BZY BaZrO 3 —Y 2 O 3
- NiO nickel oxide
- the electrolyte-anode laminate is formed by applying the BZY powder onto the surface of a compact formed by compacting the anode powder material to a predetermined thickness and firing it at 1400-1600 ° C. at the same time.
- the original ionic conductivity of the solid electrolyte layer made of BZY is impaired, and when this is applied to a fuel cell, the power generation performance is often lower than what is theoretically expected.
- the present invention has been devised in order to solve the above-mentioned problems, and prevents a decrease in ion conduction performance of the solid electrolyte layer when the electrolyte-anode laminate is fired at the same time. It is an object of the present invention to provide a composite material for a fuel cell that can enhance the fuel cell.
- One aspect of the present invention is a composite material for a fuel cell including a solid electrolyte layer and an anode layer laminated on the solid electrolyte layer, wherein the solid electrolyte layer has a perovskite structure A site,
- the anode layer comprises at least one of barium (Ba) and strontium (Sr) and an ion conductor in which a part of the tetravalent cation at the B site is substituted with a trivalent rare earth element.
- an electrolyte component having the same composition as the solid electrolyte layer and a nickel (Ni) catalyst, and an additive containing a rare earth element at least at the boundary between the solid electrolyte layer and the solid electrolyte layer.
- the additive containing the rare earth element in the anode layer By including the additive containing the rare earth element in the anode layer, even when a laminate made of the solid electrolyte material and the anode material is fired at the same time, the ion conduction performance of the solid electrolyte layer is not lowered. The power generation performance when this is adopted for a fuel cell can be enhanced.
- a solid electrolyte-anode laminate comprising a solid electrolyte layer made of BZY and an anode layer made of a material in which Ni is added to BZY as a catalyst, usually in the form of NiO
- the solid electrolyte after firing A detailed examination of the composition of the layer revealed that the Ni component was present at a high concentration throughout the solid electrolyte layer. It is clear that the Ni component is a catalyst component blended in the anode layer, but how the Ni component has moved to the electrolyte layer and this impedes ionic conductivity of the solid electrolyte layer. Whether it was unknown.
- the inventors have prototyped an electrolyte-anode laminate in which the Ni component migration to the solid electrolyte layer is suppressed and the concentration of the Ni component in the solid electrolyte layer is reduced.
- the power generation performance of a fuel cell having the electrolyte-anode laminate was compared. As a result, it was discovered that power generation performance is improved by reducing the Ni component of the solid electrolyte layer.
- One aspect of the present invention is a composite material for a fuel cell including a solid electrolyte layer and an anode layer laminated on the solid electrolyte layer, wherein the solid electrolyte layer has an A site having a perovskite structure.
- the anode layer comprising at least one of barium (Ba) and strontium (Sr), wherein a part of the tetravalent cation at the B site is substituted with a trivalent rare earth element.
- Is configured to include an electrolyte component having the same composition as that of the solid electrolyte layer and a nickel (Ni) catalyst, and includes an additive including a rare earth element at least at a boundary portion with the solid electrolyte layer.
- the amount of the additive containing the rare earth element is preferably 0.001 to 2 times the amount of the rare earth element in the solid electrolyte component contained in the anode layer in terms of the number ratio of the rare earth element. . If the amount of the additive containing the rare earth element is less than 0.001 times the atomic ratio of the amount of the rare earth element in the solid electrolyte component contained in the anode layer, a decrease in ion conductivity is prevented. Therefore, the power generation performance of the fuel cell cannot be improved.
- the amount of the additive containing the rare earth element exceeds twice the amount of the rare earth element in the solid electrolyte component contained in the anode layer in the atomic ratio of the rare earth element, the solid electrolyte layer There is a possibility that the adhesion between the layers and the adhesion between the layers may be reduced, or the composition of the solid electrolyte layer may be changed to lower the ionic conductivity.
- the amount of the additive containing the rare earth element is 0.01 to 1.5 times the amount of the rare earth element in the solid electrolyte component contained in the anode layer in terms of the number ratio of the rare earth element. More preferably, it is configured as follows.
- the amount of the additive containing the rare earth element is 0.01 times or more, the reaction suppressing effect becomes remarkable, and when the amount of the additive containing the rare earth element is 1.5 times or less, the above-mentioned interlayer adhesion The effect on the decrease in force and the composition of the solid electrolyte layer is extremely small.
- the anode layer is configured such that the ratio (B / A) of the number of atoms (B) of the Ni catalyst to the number of atoms (A) of a cationic element other than the Ni catalyst is 0.5 to 10. It is preferable to do this.
- the atomic ratio of the Ni catalyst to other cationic elements is less than 0.5, a sufficient catalytic effect cannot be expected, and the electron conductivity of the anode layer cannot be ensured.
- the atomic ratio of the Ni catalyst to other cationic elements exceeds 10, the volume change during reduction from NiO to Ni increases, or the coefficient of thermal expansion between the solid electrolyte layer and the anode layer. , The thermal stress increases, the electrolyte layer may be damaged, and the amount of Ni diffusion into the electrolyte layer may increase.
- the solid electrolyte constituting the solid electrolyte layer yttrium-added barium zirconate is adopted, and as the additive, for example, an additive containing yttrium can be adopted.
- the additive containing yttrium yttrium oxide (Y 2 O 3 ) or the like can be employed.
- the additive can be added to the entire anode layer, and an effect can be expected by adding at least the boundary portion with the solid electrolyte layer.
- an anode layer to which the additive is added may be provided between the solid electrolyte layer and the conventional anode layer.
- the composite material for a fuel cell according to the present invention comprises a laminate molding step of integrally laminating the powder material constituting the solid electrolyte layer and the powder material constituting the anode layer, and the laminate. It can be manufactured including a firing step for heat sintering.
- the laminate forming step the anode layer is formed on the solid electrolyte side and includes the additive and the other layer formed on the other side and does not include the additive. It can also be formed.
- FIG. 1 shows a cross-sectional view of a composite material for a fuel cell according to this embodiment.
- the fuel cell composite material 1 according to this embodiment is formed as an electrolyte-anode laminate including an anode layer 2 and a solid electrolyte layer 3.
- the solid electrolyte layer 3 is configured by firing a powder of yttrium-added barium zirconate (hereinafter, BZY), which is a solid solution of barium zirconate (BaZrO 3 ) and yttrium oxide (Y 2 O 3 ).
- BZY yttrium-added barium zirconate
- BaZrO 3 barium zirconate
- Y 2 O 3 yttrium oxide
- the ratio of Zr to Y in BZY is 8: 2, and the chemical formula of the solid solution powder is estimated to be Ba 10 (Zr 8 ⁇ Y 2 ) O 29 .
- a powder material for forming the anode layer 2 according to the present embodiment a BZY powder that is a constituent material of the solid electrolyte layer 3, a nickel oxide powder that is a catalyst (hereinafter referred to as NiO), and an additive containing a rare earth element
- the Y 2 O 3 powder was adjusted so as to have a blending ratio (cation ⁇ at%) shown in A of FIG.
- the material constituting the conventional anode layer was adjusted so as to have a blending ratio shown in FIG.
- the cations are Ba, Zr, Y, and Ni, and at% represents the atomic ratio for only cations.
- the inside of () is Y atom content in BZY.
- the sample A according to the present embodiment is formed of a material in which 2.8% Y 2 O 3 powder is additionally blended instead of the BZY component of the anode material composed of the conventional components shown in the sample B. .
- BZY powder slurry was prepared.
- the BZY powder slurry is applied to one side of the anode molded body A and the anode molded body B with a thickness of about 20 ⁇ m by screen printing to form a coating film constituting a solid electrolyte layer.
- a multilayer laminate according to Comparative Example B was formed.
- These multilayer laminates are heated in the air at a temperature of 700 ° C. for 24 hours to remove the resin component, and then fired in an oxygen atmosphere at a temperature of 1500 ° C. for 10 hours to be baked to obtain an electrolyte-anode laminate. Got the body.
- the shrinkage due to firing was about 20%.
- the electrolyte-anode laminate was heated in a H 2 atmosphere at a temperature of 700 ° C. for 1 hour, the anode layer was reduced, and metallic Ni was deposited to obtain the fuel cell composite material 1. Further, a slurry of LSCF (La—Sr—Co—Fe—O) powder constituting the cathode layer is applied to the surface of the solid electrolyte layer 3 opposite to the anode layer 2 to form a cathode layer of about 10 ⁇ m. Thus, an electrolyte-electrode laminate 11 was formed. A fuel cell 10 shown in FIG. 2 was constructed using the electrolyte-electrode laminate 11.
- LSCF La—Sr—Co—Fe—O
- the fuel cell 10 supports an electrolyte-electrode stack 11 at an intermediate portion of a cylindrical container 12, and includes flow paths 13 and 14 that allow fuel gas to act on one side and air to act on the other side.
- the flow path 15 and 16 which can be comprised are comprised.
- Platinum meshes 19 and 20 are provided as current collectors on the anode electrode surface and the cathode electrode surface of the electrolyte-electrode laminate 11, respectively, and lead wires 17 drawn out to the platinum meshes 19 and 20 are provided. , 18 are connected to each other.
- the power generation performance of 100 mW / cm 2 was obtained.
- the fuel cell configured to include the electrolyte-electrode laminate formed from the sample B that is a conventional composite material only a power generation performance of 30 mW / cm 2 is exhibited, and the sample that is the composite material according to the present embodiment It has been found that a fuel cell comprising an electrolyte-electrode laminate formed from A exhibits high power generation performance.
- a conventional anode layer is formed from a mixed powder of BZY powder and NiO powder, and it is considered that the following reaction occurs in the firing process.
- FIG. 4 shows a phase diagram of the BaO—NiO compound.
- the melting point of the BaO—NiO compound is about 1100 to 1200 ° C., and the temperature of the liquid phase is low in the vicinity where the mixing ratio of BaO and NiO is 1: 1.
- the composition BaNiO 2 estimated from the reaction formula 1 also has a molar ratio of BaO to NiO of 50%. Therefore, at a firing temperature of 1500 ° C., BaNiO 2 or a Ni-containing compound close to this is produced. It can be inferred that it is in a liquid phase.
- the BaNiO 2 in a liquid phase or a Ni-containing compound close thereto moved in the solid electrolyte layer in the firing process due to capillarity or the like and was present throughout the solid electrolyte layer. . Then, the BaNiO 2 or a Ni-containing compound close thereto is precipitated at the grain boundary of the solid electrolyte layer in the solidification process or the like, or Ni is solid-solved in the BZY grain, and between the grain boundaries in the solid electrolyte layer. It is thought that the ionic conductivity is inhibited.
- the inventors of the present invention presumed that the movement of the Ni component to the solid electrolyte layer can be suppressed by inhibiting the liquid phase of the Ni-containing compound, and as a result of repeated trials, The present invention has been devised.
- the powder material constituting the anode layer is fired by including an additive containing a rare earth element.
- NiO is added as a catalyst component to the BZY powder as the anode layer, and Y 2 O 3 is added as the additive and calcined.
- the amount of Y 2 O 3 added is the same as the amount of Y 2 O 3 contained in BZY in the anode layer.
- the reaction formula with NiO is considered to be as follows by addition of Y 2 O 3 .
- the region indicated by A2 corresponds to the region where Y 2 O 3 is not added and the liquidus temperature indicated by A1 shown in FIG. It is thought to occur.
- the material constituting the conventional anode layer has a composition that forms a grain boundary having a composition indicated by C2 when the total amount of Y in BZY flows out of the grains together with Ba and reacts with NiO. It can be presumed that the Ba—Ni—O compound is in a liquid phase state together with BaY 2 NiO 5 Ni during firing.
- the compound BaY 2 NiO 5 in the region D2 in the ternary phase diagram is generated.
- the BaY 2 NiO 5 has a high melting point, and it can be assumed that it is in a solid state even at a temperature of 1500 ° C.
- the amount of Y 2 O 3 added is preferably larger from the viewpoint of suppressing the formation of the liquid phase, but is smaller from the viewpoint of maintaining the affinity of the solid electrolyte layer with BZY and suppressing the influence on the anode layer. preferable.
- the amount of Y 2 O 3 added is less than 0.001 times the amount of rare earth element in the electrolyte component contained in the anode layer in terms of the number ratio of rare earth elements, the effect of suppressing liquid phase formation is obtained. Few.
- the affinity with the solid electrolyte layer may be reduced, the adhesion between the layers may be reduced, or the Zr: Y ratio of the electrolyte may be changed, resulting in a decrease in ionic conductivity.
- the amount of Y 2 O 3 added is configured to be 0.01 to 1.5 times the amount of rare earth element in the solid electrolyte component contained in the anode layer in terms of the number ratio of rare earth elements. Is more preferable.
- the addition amount of Y 2 O 3 is 0.01 times or more, the reaction suppressing effect becomes remarkable, and when the addition amount of the additive containing a rare earth element is 1.5 times or less, the above-mentioned interlayer adhesion is lowered. In addition, the influence on the composition of the solid electrolyte layer is extremely small.
- the A site of the perovskite structure is made of barium (Ba), and includes a solid electrolyte layer composed of an ionic conductor in which a part of tetravalent cations at the B site is substituted with yttrium.
- the present invention can also be applied to the case where the A site uses strontium (Sr) or an ion conductor made of barium (Ba) and strontium (Sr) as a solid electrolyte layer.
- Y 2 O 3 is added to the entire anode layer.
- an additive containing a rare earth element can be added at least at the boundary with the solid electrolyte layer.
- a layer to which Y 2 O 3 is added can be separately formed at the boundary portion.
- An electrolyte-anode laminate that can constitute a fuel cell with high power generation performance can be provided at low cost.
- Electrolyte-anode laminate composite material for fuel cells
- Anode layer Solid electrolyte layer 10
- Fuel cell 11 Electrolyte-electrode stack 12 Tubular container 13 Flow path (fuel gas) 14 Flow path (fuel gas) 15 Channel (Air) 16 Channel (Air) 17 Lead wire 18 Lead wire 19 Platinum mesh 20 Platinum mesh
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Abstract
Description
本発明の発明者らは、従来の電解質-アノード積層体について鋭意研究し、イオン伝導性能の低下原因について、以下の知見を得るに到った。
本発明の一形態は、固体電解質層と、前記固体電解質層に積層されたアノード層とを備えて構成される燃料電池用複合材料であって、前記固体電解質層は、ペロブスカイト構造のAサイトが、バリウム(Ba)とストロンチウム(Sr)の少なくとも一方からなるとともに、Bサイトの四価の陽イオンの一部を三価の稀土類元素で置換したイオン伝導体から構成されており、前記アノード層は、前記固体電解質層と同一組成の電解質成分と、ニッケル(Ni)触媒とを含んで構成されているとともに、少なくとも固体電解質層との境界部分に稀土類元素を含む添加物を含んで構成されるものである。
前記稀土類元素を含む添加物の添加量が、前記アノード層に含まれる前記固体電解質成分中の稀土類元素量の原子数比で0.001倍未満であると、イオン伝導性の低下を阻止する効果がほとんどみられず、燃料電池の発電性能を高めることができない。一方、前記稀土類元素を含む添加物の添加量が、稀土類元素の原子数比で、前記アノード層に含まれる前記固体電解質成分中の稀土類元素量の2倍を越えると、固体電解質層との親和性が低下して層間の密着力が低下したり、固体電解質層の組成が変化して、イオン伝導性が低下する恐れがある。さらに、前記稀土類元素を含む添加物の添加量が、稀土類元素の原子数比で、前記アノード層に含まれる前記固体電解質成分中の稀土類元素量の0.01~1.5倍となるように構成するのがより好ましい。稀土類元素を含む添加物の添加量が0.01倍以上では、反応抑制効果が顕著になり、稀土類元素を含む添加物の添加量が1.5倍以下であれば、上述の層間密着力の低下や、固体電解質層の組成への影響が極めて小さい。
以下、本発明の実施形態を図に基づいて説明する。
従来の電解質-アノード積層体において、固体電解質層におけるNi成分が相当量拡散する原因と、本発明の作用機構について、速度論的観点及び熱力学的観点から考察した。
Ba10(Zr8Y2)O29+2NiO→Ba8Zr8O24+Y2BaNiO5+BaNiO2
Ba10(Zr8Y2)O29+2NiO+Y2O3→Ba8Zr8O24+2Y2BaNiO5
Y2O3の添加量が0.01倍以上では、反応抑制効果が顕著になり、稀土類元素を含む添加物の添加量が1.5倍以下であれば、上述の層間密着力の低下や、固体電解質層の組成への影響が極めて小さい。
2 アノード層
3 固体電解質層
10 燃料電池
11 電解質-電極積層体
12 筒状容器
13 流路(燃料ガス)
14 流路(燃料ガス)
15 流路(空気)
16 流路(空気)
17 リード線
18 リード線
19 プラチナメッシュ
20 プラチナメッシュ
Claims (7)
- 固体電解質層と前記固体電解質層に積層されたアノード層とを備えて構成される燃料電池用複合材料であって、
前記固体電解質層は、ペロブスカイト構造のAサイトが、バリウム(Ba)とストロンチウム(Sr)の少なくとも一方からなるとともに、Bサイトの四価の陽イオンの一部を三価の稀土類元素で置換したイオン伝導体から構成されており、
前記アノード層は、前記固体電解質層と同一組成の電解質成分と、ニッケル(Ni)触媒とを含んで構成されているとともに、少なくとも固体電解質層との境界部分に稀土類元素を含む添加物を含んで構成されている、燃料電池用複合材料。 - 前記稀土類元素を含む添加物の添加量が、稀土類元素の原子数比で、前記アノード層に含まれる前記電解質成分中の稀土類元素量の0.001~2倍である、請求項1に記載の燃料電池用複合材料。
- 前記稀土類元素を含む添加物の添加量が、稀土類元素の原子数比で、前記アノード層に含まれる前記固体電解質成分中の稀土類元素量の0.01~1.5倍である請求項1に記載の燃料電池用複合材料。
- 前記アノード層は、前記Ni触媒以外の陽イオン元素の原子数(A)に対する前記Ni触媒の原子数(B)の比(B/A)が、0.5~10.0である請求項1から請求項3のいずれか1項に記載の燃料電池用複合材料。
- 前記固体電解質層を構成する固体電解質が、イットリウム添加ジルコン酸バリウム(BaZrO3-Y2O3)であり、
前記稀土類元素を含む添加物が、イットリウム(Y)を含む、請求項1から請求項4のいずれか1項に記載の燃料電池用複合材料。 - 請求項1から請求項5に記載された燃料電池用複合材料の製造方法であって、
前記固体電解質層を構成する粉体材料と、前記アノード層を構成する粉体材料とを一体的に積層成形する積層体成形工程と、
前記積層体を熱焼結させる焼成工程とを含む、燃料電池用複合材料の製造方法。 - 請求項1に記載の燃料電池用複合材料を備えて構成される、燃料電池。
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
US14/904,536 US20160156058A1 (en) | 2013-07-18 | 2014-07-09 | Composite material for fuel cell, method for producing composite material for fuel cell, and fuel cell |
EP14826230.6A EP3024073B1 (en) | 2013-07-18 | 2014-07-09 | Composite material for fuel cell, manufacturing method of composite material for fuel cell, and fuel cell |
KR1020167000991A KR101791442B1 (ko) | 2013-07-18 | 2014-07-09 | 연료 전지용 복합 재료, 연료 전지용 복합 재료의 제조 방법 및 연료 전지 |
CN201480040766.0A CN105393393B (zh) | 2013-07-18 | 2014-07-09 | 燃料电池用复合材料、燃料电池用复合材料的制造方法以及燃料电池 |
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JP2013149336A JP6132259B2 (ja) | 2013-07-18 | 2013-07-18 | 燃料電池用複合材料、燃料電池用複合材料の製造方法及び燃料電池 |
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EP (1) | EP3024073B1 (ja) |
JP (1) | JP6132259B2 (ja) |
KR (1) | KR101791442B1 (ja) |
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WO2016136111A1 (ja) * | 2015-02-27 | 2016-09-01 | 住友電気工業株式会社 | セラミックスの製造方法、コンデンサ、固体酸化物型燃料電池、水電解装置及び水素ポンプ |
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US10283794B2 (en) * | 2015-12-09 | 2019-05-07 | Syracuse University | Electricity and syngas co-generation system using porous solid oxide fuel cells |
CN108110286A (zh) * | 2016-11-25 | 2018-06-01 | 中国科学院大连化学物理研究所 | 一种质子传导氧化物电解质薄膜的制备方法 |
US20200212468A1 (en) * | 2017-06-15 | 2020-07-02 | Sumitomo Electric Industries, Ltd. | Solid electrolyte member, solid oxide fuel cell, water electrolysis device, hydrogen pump, and method for manufacturing solid electrolyte member |
CN111801827B (zh) * | 2018-03-06 | 2023-08-18 | 住友电气工业株式会社 | 电解质层-阳极复合部件以及电池结构体 |
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JP2016160111A (ja) * | 2015-02-27 | 2016-09-05 | 住友電気工業株式会社 | セラミックスの製造方法、コンデンサ、固体酸化物型燃料電池、水電解装置及び水素ポンプ |
CN107250085A (zh) * | 2015-02-27 | 2017-10-13 | 住友电气工业株式会社 | 陶瓷材料的制造方法、电容器、固体氧化物型燃料电池、水电解装置和氢泵 |
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US20160156058A1 (en) | 2016-06-02 |
EP3024073A1 (en) | 2016-05-25 |
EP3024073A4 (en) | 2016-07-13 |
CN105393393B (zh) | 2018-05-01 |
CN105393393A (zh) | 2016-03-09 |
KR20160020520A (ko) | 2016-02-23 |
KR101791442B1 (ko) | 2017-10-30 |
JP2015022869A (ja) | 2015-02-02 |
EP3024073B1 (en) | 2017-11-15 |
JP6132259B2 (ja) | 2017-05-24 |
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