WO2020191829A1 - 一种SOFC抗积碳Ni-YSZ阳极材料的制备方法 - Google Patents

一种SOFC抗积碳Ni-YSZ阳极材料的制备方法 Download PDF

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WO2020191829A1
WO2020191829A1 PCT/CN2019/083023 CN2019083023W WO2020191829A1 WO 2020191829 A1 WO2020191829 A1 WO 2020191829A1 CN 2019083023 W CN2019083023 W CN 2019083023W WO 2020191829 A1 WO2020191829 A1 WO 2020191829A1
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anode
ysz
sofc
nio
powder
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PCT/CN2019/083023
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French (fr)
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罗凌虹
程亮
徐序
王乐莹
吴也凡
余永志
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景德镇陶瓷大学
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Priority to US16/937,588 priority Critical patent/US11594739B2/en
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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
    • H01M4/9066—Metals or alloys specially used in fuel cell operating at high temperature, e.g. SOFC of metal-ceramic composites or mixtures, e.g. cermets
    • 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
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    • H—ELECTRICITY
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    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/86—Inert electrodes with catalytic activity, e.g. for fuel cells
    • H01M4/90—Selection of catalytic material
    • H01M4/9016—Oxides, hydroxides or oxygenated metallic salts
    • H01M4/9025—Oxides specially used in fuel cell operating at high temperature, e.g. SOFC
    • H01M4/9033—Complex oxides, optionally doped, of the type M1MeO3, M1 being an alkaline earth metal or a rare earth, Me being a metal, e.g. perovskites
    • C—CHEMISTRY; METALLURGY
    • C04—CEMENTS; CONCRETE; ARTIFICIAL STONE; CERAMICS; REFRACTORIES
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    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/622—Forming processes; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • H—ELECTRICITY
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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
    • H01M4/8652—Inert electrodes with catalytic activity, e.g. for fuel cells consisting of more than one material, e.g. consisting of composites as mixture
    • H—ELECTRICITY
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    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
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    • H01M4/88—Processes of manufacture
    • H01M4/8878—Treatment steps after deposition of the catalytic active composition or after shaping of the electrode being free-standing body
    • H01M4/8882—Heat treatment, e.g. drying, baking
    • H01M4/8885—Sintering or firing
    • H—ELECTRICITY
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    • H01M4/86—Inert electrodes with catalytic activity, e.g. for fuel cells
    • H01M4/90—Selection of catalytic material
    • H01M4/9016—Oxides, hydroxides or oxygenated metallic salts
    • H—ELECTRICITY
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    • 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
    • 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
    • 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
    • H01M8/1213—Fuel cells with solid electrolytes operating at high temperature, e.g. with stabilised ZrO2 electrolyte characterised by the electrode/electrolyte combination or the supporting material
    • H—ELECTRICITY
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    • 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
    • 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
    • H01M8/1253—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 the electrolyte containing zirconium oxide
    • 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
    • H01M2004/8678—Inert electrodes with catalytic activity, e.g. for fuel cells characterised by the polarity
    • H01M2004/8684—Negative electrodes
    • H—ELECTRICITY
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    • 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
    • H01M2008/128—Fuel cells with solid halide electrolytes
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M8/00—Fuel cells; Manufacture thereof
    • H01M8/10—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 invention relates to the field of solid oxide fuel cells, in particular to a preparation method of SOFC anti-carbon deposition Ni-YSZ anode material.
  • Solid oxide fuel cell (SOFC, Solid oxide of fulle cell) is a power generation method that converts the chemical energy in fuel and oxygen into electrical energy without burning. There is no need to comply with the Carnot cycle, the conversion efficiency is high, and the co-efficiency of the heat and power can reach more than 80%. At the same time, the products of the electrochemical reaction are hot water and carbon dioxide. Due to the high concentration of carbon dioxide, it is easy to recover, so the products of power generation are also clean and clean. of. Therefore, the solid oxide fuel cell is an efficient and green power generation method.
  • the operating temperature of the intermediate temperature solid oxide fuel cell (IT-SOFC) is about 750°C. Commercially, the battery is a second-generation battery.
  • the first-generation battery is an electrolyte-supported type and belongs to a high-temperature solid oxide fuel cell. At least 850°C.
  • the structure of IT-SOFC generally adopts an anode-supported (electrolyte thin film) battery structure.
  • the bottleneck problem of the commercialization of IT-SOFC is the resistance to carbon deposition of the battery anode.
  • the traditional Ni/YSZ anode (mixed porous cermet of metallic nickel and yttria-stabilized zirconia) battery uses carbon at the working temperature (ie around 750°C) In the case of hydrogen fuel, it is easy to accumulate carbon and the battery performance is quickly degraded.
  • the purpose of the present invention is to provide a preparation method of SOFC anode material, and further provide the SOFC anode material prepared by the preparation method and its use, to solve the problem in the prior art The problem.
  • one aspect of the present invention provides a preparation method of SOFC anode material, including:
  • step (2) The mixed powder provided in step (1) is subjected to two-phase mutual solid solution treatment,
  • the specific method for providing the mixed powder of NiO and YSZ is: pulverizing and mixing NiO and YSZ.
  • the weight ratio of NiO and YSZ is 1 to 1.8:1.
  • the SOFC anode material is an anode support material
  • the SOFC anode material is an anode functional layer material
  • the YSZ particles in the step (1), have a particle size of 50-1000 nm, and the NiO powder has a crystallite size of 10-20 nm.
  • NiO and YSZ are pulverized and mixed by ball milling.
  • the ball milling is preferably wet ball milling.
  • the powder obtained by ball milling is also dried, and the drying temperature can be 60-80 °C.
  • pulverization and mixing are carried out in the presence of a dispersant.
  • the dispersant is preferably selected from the group consisting of triethanolamine, citric acid, polyethylene glycol, acetylacetone, and polyacetone.
  • a combination of one or more of vinylpyrrolidone and polyacrylic acid, the weight ratio of the powder to the dispersant is 1:0.005 to 0.1, preferably 1:0.02 to 0.05.
  • pulverization and mixing are carried out in the presence of a solvent
  • the solvent is preferably selected from absolute ethanol, acetone, methyl ethyl ketone, isopropanol, dimethyl methyl
  • the weight ratio of powder to solvent is 1:0.2 to 1.5, preferably 1:0.4 to 0.8.
  • the specific method for subjecting the mixed powder provided in step (1) to two-phase mutual solid solution treatment is: drying the mixed powder provided in step (1) , Calcination.
  • the calcination temperature is 600-1200°C, preferably 800-950°C.
  • the calcination time is 1-10, preferably 2-8 hours.
  • the specific method for adjusting the particle size of the product obtained in step (2) solution treatment is: pulverizing and drying the calcined product provided in step (2), preferably , The calcined product is crushed by ball milling.
  • Another aspect of the present invention provides a SOFC anode material, which is prepared by the preparation method.
  • Another aspect of the present invention provides an SOFC single cell, which includes an anode material layer, an electrolyte green sheet and a cathode material layer, and the anode material layer is prepared from the SOFC anode material.
  • the anode material layer includes an anode support layer and/or anode functional layer, and the anode support layer and/or anode functional layer are prepared from the SOFC anode material.
  • the thickness of the anode support layer is 300-700 ⁇ m, preferably 400-500 ⁇ m, the pore size is 3-10 ⁇ m, and the porosity of the anode support layer after reduction is 25-40 vol.%, preferably 30- 35vol.%; the thickness of the anode functional layer is 5-30 ⁇ m, preferably 5-10 ⁇ m, the pore size is 1-5 ⁇ m, and the porosity of the anode functional layer after reduction is 25-40 vol.%, preferably 30-35 vol.%.
  • the electrolyte green sheet is selected from YSZ electrolyte green sheets, and the thickness of the electrolyte green sheet is 2-10 ⁇ m.
  • the cathode material layer is selected from the combination of LSM and YSZ or the combination of LSM and SSZ, the weight ratio of the two is 5-7:5-3, the combination of LSCF and GDC, the weight of both The ratio is 5-7:5-3.
  • the thickness of the cathode material layer is 20-40 ⁇ m, preferably 20-25 ⁇ m, and the cathode material layer has a porous structure with a porosity of 25-40 vol.%, preferably 30- 35vol.%.
  • Another aspect of the present invention provides an anode-reduced SOFC single cell, which is obtained by reducing and/or discharging the SOFC single cell.
  • FIG. 1 Schematic diagram of the preparation process of SOFC anti-carbon Ni-YSZ anode material.
  • Figure 2 SEM image of the microstructure of a full SOFC cell (after reduction).
  • Figure 3 SEM image of the microstructure of the anode support layer of the battery before reduction (a is a low-magnification image of the anode, the full view of the reaction anode; b and c are partial enlarged images).
  • Figure 4 Cell reduction (reduction conditions are at 750°C, H 2 +3% H 2 O is fuel, and reduced in open circuit for 1 h). After the single cell is reduced at 750°C, H 2 + 3% H 2 O is fuel and air is oxidant. SEM of the anode support layer cross-section after 4h under discharge (current 0.4A/cm 2 ) (a is a low-magnification image of the anode, the full view of the reaction anode; b and c are partial enlarged images).
  • FIG. 5 Comparison of SEM images before and after reduction (discharge) of the anode functional layer of a single cell.
  • b c battery reduction (reduction conditions are at 750°C, H 2 +3% H 2 O is fuel, and reduction is 1h in open circuit), and then the single cell is at 750°C, H 2 +3% H SEM of the anode functional layer section after 4h discharge (current 0.4A/cm 2 ) under 2 O as fuel and air as oxidant.
  • Figure 7 Single cell uses CH 4 (+3% H 2 O) as fuel, air as oxidant, and discharge curve at a current density of 0.40 A/cm 2 .
  • Figure 8 Ethanol is the IV and EIS curves of a single fuel cell at 750°C.
  • Figure 9 uses ethanol as the fuel cell operating curve at different discharge currents.
  • Figure 10 The particle size distribution curve of the powder (anode support layer powder) after 5YSZ/NiO ball milling calcination and ball milling.
  • FIG. 11 Schematic diagram of SOFC anode anti-carbon deposition mechanism.
  • Ni nanoparticles HAADF, high-angle annular dark field image
  • EDS element mapping
  • the inventors of the present invention have discovered through a large number of studies that by pulverizing, mixing, and further calcining NiO and YSZ by a suitable method, a new SOFC anode material can be provided, and the SOFC anode material can be used to prepare SOFC single cells.
  • the anode of the SOFC single cell has good carbon deposition resistance, and the present invention has been completed on this basis.
  • the first aspect of the present invention provides a preparation method of SOFC anode material, including:
  • the preparation method of the SOFC anode material provided by the present invention may include: providing a mixed powder of NiO and YSZ, so that the two-phase mixing of NiO and YSZ powder particles is more uniform and the powder particle size is reduced.
  • the raw materials of the anode material may include NiO and YSZ, and the two oxides are fully crushed and mixed, so as to obtain a mixture of submicron YSZ particles and nanocrystalline NiO powder.
  • FIG 1 after two powders with different particle sizes are mixed together and dispersed by ball milling, there will be two basic situations including the following: First, NiO with a nano-crystalline size is adsorbed on the surface of sub-micron YSZ particles.
  • the particle size of the YSZ particles is usually 50 to 1000 nm, 50 to 100 nm, 100 to 200 nm, 200 to 300 nm, 300 to 500 nm, or 500 to 1000 nm, and the crystallite size of the NiO powder (The crystallite size is obtained by XRD test and calculated by using the Scherrer formula, the same below) can be 10-20nm, 10-15nm, or 15-20nm.
  • a suitable method to provide a mixed powder of NiO and YSZ for example, NiO and YSZ can be crushed and mixed.
  • NiO and YSZ should be known to those skilled in the art.
  • methods such as ball milling for example, wet ball milling, etc.
  • pulverization and mixing can be carried out in the presence of a dispersant and/or solvent, so that NiO powder and YSZ powder can be uniformly mixed.
  • the dispersant can be selected from triethanolamine, citric acid , Polyethylene glycol, acetylacetone, polyvinylpyrrolidone, polyacrylic acid, etc.
  • the weight ratio of powder to dispersant can be 1:0.005 ⁇ 0.1, 1:0.005 ⁇ 0.01, 1: 0.01 ⁇ 0.02, 1:0.02 ⁇ 0.03, 1:0.03 ⁇ 0.04, 1:0.04 ⁇ 0.05, or 1:0.05 ⁇ 0.1, preferably 1:0.02 ⁇ 0.05.
  • the solvent can be selected from absolute ethanol , Acetone, methyl ethyl ketone, isopropanol, dimethyl formamide (DMF), etc.
  • the weight ratio of powder to solvent can be 1:0.2 ⁇ 1.5, 1: 0.2 ⁇ 0.4, 1:0.4 ⁇ 0.6, 1:0.6 ⁇ 0.8, 1:0.8 ⁇ 1.0, 1:1.0 ⁇ 1.2, or 1:1.2 ⁇ 1.5, preferably 1:0.4 ⁇ 0.8, for example, oxidation can be used in the preparation process of ball milling
  • the weight ratio of powder to balls can be 1:1.5 ⁇ 2.0, 1:1.5 ⁇ 1.6, 1:1.6 ⁇ 1.8, or 1:1.8 ⁇ 2.0
  • the diameter of zirconia balls can be 0.3 ⁇ 0.8mm, 0.3 ⁇ 0.4mm, 0.4 ⁇ 0.5mm, 0.5 ⁇ 0.6mm, 0.6 ⁇ 0.7mm, or 0.7 ⁇ 0.8mm.
  • the powder obtained by ball milling can also be dried, and the drying temperature can be 60 ⁇ 80°C, 60 ⁇ 65°C , 65 ⁇ 70°C, 70 ⁇ 75°C, or 75 ⁇ 80°C.
  • the SOFC anode material can be used to prepare an anode material layer, and more specifically, it can be used to prepare an anode support layer and/or an anode functional layer.
  • the anode functional layer is the place where the electrochemical reaction of the anode is completed; the anode support layer plays a whole
  • the supporting role of the battery and the role of electron conduction, generally speaking, the anode supporting layer is relatively thick and has high mechanical strength.
  • the properties of the SOFC anode material and the anode material layer obtained by the preparation thereof mainly depend on the mixing ratio between NiO and YSZ during the preparation process, the content and/or stability of Y 2 O 3 in YSZ, the particle size of the raw material powder, etc.
  • the weight ratio of NiO and YSZ can be 1-1.8:1, 1-1.2:1, 1.2-1.4:1, 1.4-1.6:1, or 1.6-1.8:1, in a specific embodiment of the present invention
  • the weight ratio of NiO and YSZ is 1-1.8:1, 1-1.2:1, 1.2-1.4:1, 1.4-1.6:1, or 1.6-1.8:1
  • the YSZ powder can be 3 ⁇ 8mol% Y 2 O 3 doped zirconia, 3 ⁇ 4 mol% Y 2 O 3 doped zirconia, 4 ⁇ 5 mol% Y 2 O 3 doped zirconia, 5 ⁇ 6 mol % Y 2 O 3 doped zirconia, 6-7 mol% Y 2 O 3 doped zirconia, 7-8 mol% Y 2 O 3 doped zirconia (the expression of YSZ material is for those skilled in the art It should be well-known, for example, 5 mol% Y 2 O 3 doped zirconia
  • the crystallite size of NiO raw material can be 5-20nm, 5-10nm , 10-15nm, or 15-20nm
  • the weight ratio of NiO and YSZ is 1 to 1.8:1, 1 to 1.2:1, 1.2 to 1.4:1, 1.4 to 1.6:1, or 1.6 ⁇ 1.8:1, YSZ powder is 7-9 mol% Y 2 O 3 doped zirconia, 7 to 7.5 mol% Y 2 O 3 doped zirconia, 7.5 to 8 mol% Y 2 O 3 doped oxide Zirconium, 8-8.5 mol% Y 2 O 3 doped zirconia, or 8.5-9 mol% Y 2 O 3 doped zirconia (the content of Y 2 O 3 in the crystal lattice is usually up to 8 mol% At this ratio, the phase transition of zirconia is basically stabilized, and there is no phase transition of zirconia with temperature changes), the crystallite size of NiO raw material can be 5-20nm, 5-10nm, 10-15nm, or 15 ⁇ 20nm,
  • the preparation method of the SOFC anode material provided by the present invention may include: subjecting the mixed powder provided in step (1) to two-phase mutual solid solution treatment.
  • the two-phase mutual solid solution treatment usually refers to the solid solution of NiO nanoparticles adsorbed around the YSZ particles into the YSZ lattice to form a solid solution, and the YSZ nanoparticles adsorbed around the NiO particles are dissolved into the NiO lattice to form a solid solution.
  • Treatment methods The specific method for subjecting the mixed powder provided in step (1) to two-phase mutual solid solution treatment may be: drying and calcining the mixed powder provided in step (1).
  • the inventors of the present invention found that the powders will be solid-solved with each other during the calcination process, and the NiO particles have small crystal grains (high activity) and low temperature. During the calcination process, they are easily dissolved into the surface of the YSZ particles, that is, nano-NiO enters the YSZ particle crystals. The inside of the lattice forms a solid solution; at the same time, it is also found that the YSZ of small-size crystal grains also dissolves into the larger NiO particles during the calcination process, that is, the nanometer YSZ enters the inside of the NiO particle lattice to form a solid solution.
  • the surface of the calcined powder is smooth, and the particle surface usually has no obvious nano-protrusions.
  • the calcination temperature can be 600-1200°C, 600-800°C, 800-850°C, 850-900°C, 900-950°C, 950-1000°C, or 1000-1200°C, preferably 800-950°C, calcination
  • the time can be 1 to 10 hours, 1 to 2 hours, 2 to 4 hours, 4 to 6 hours, 6 to 8 hours, or 8 to 10 hours, preferably 2 to 8 hours, and the calcination time is specifically the product to be processed The holding time at the calcination temperature.
  • the preparation method of the SOFC anode material provided by the present invention may include: adjusting the particle size of the product obtained in step (2) solution treatment, so as to reduce the particle size of the NiO and YSZ mixed powder grown by calcination.
  • the particle size adjustment generally refers to a processing method of adjusting the particle size of the powder to a target size using an appropriate physical method.
  • the specific method for adjusting the particle size of the product obtained in step (2) solution treatment may be: pulverizing and drying the calcined product provided in step (2). After calcination, the powder particles will increase to a certain extent. After pulverization, powder particles of suitable particle size can be obtained.
  • the method of pulverizing the calcined product should be known to those skilled in the art.
  • the calcined product can be pulverized by a method such as ball milling.
  • the second aspect of the present invention provides an SOFC anode material, which is prepared by the preparation method of the SOFC anode material provided in the first aspect of the present invention.
  • the third aspect of the present invention provides the use of the SOFC anode material provided by the second aspect of the present invention as an SOFC anode material.
  • the SOFC anode material may be used to prepare a SOFC anode material layer.
  • the SOFC anode material layer may include an anode support layer and/or an anode functional layer, etc.
  • the SOFC anode material layer prepared by the SOFC anode material has good properties Carbon deposition resistance.
  • the fourth aspect of the present invention provides a SOFC anode material layer prepared from the SOFC anode material provided in the second aspect of the present invention.
  • the SOFC anode material layer may include an anode support layer and/or an anode functional layer.
  • Those skilled in the art can choose a suitable method to prepare the SOFC anode material layer from the SOFC anode material. For example, it can be formed by casting methods.
  • the thickness of the anode support layer in the formed anode material layer can be 300 ⁇ 700 ⁇ m, preferably 400-500 ⁇ m
  • the pores of the anode support layer are relatively large
  • the size of the pores can be 3-10 ⁇ m, 3-5 ⁇ m, 5-7 ⁇ m, or 7-10 ⁇ m
  • the porosity of the electrode support layer can be 25 after reduction %, 25 to 30 vol. %, 30 to 35 vol. %, or 35 to 40 vol. %, preferably 30 to 35 vol. %.
  • the thickness of the anode functional layer may be 5 to 30 ⁇ m, 5 to 10 ⁇ m, 10-20 ⁇ m, or 20-30 ⁇ m, preferably 5-10 ⁇ m
  • the pores of the anode functional layer are relatively small, and the pore size can be 1-5 ⁇ m, 1-2 ⁇ m, 2-3 ⁇ m, 3-4 ⁇ m, or 4-5 ⁇ m
  • the porosity of the anode functional layer after reduction is 25-40 vol.%, 25-30 vol.%, 30-35 vol.%, or 35-40 vol.%, preferably 30-35 vol.%.
  • the fifth aspect of the present invention provides a SOFC single cell, including the anode material layer, the electrolyte green sheet and the cathode material layer provided in the third aspect of the present invention.
  • the basic structure of the SOFC single cell should be known to those skilled in the art.
  • the anode material layer, the electrolyte green sheet, and the cathode material layer can usually be superimposed in sequence, and the anode material layer and the cathode material The layers can be located on both sides of the electrolyte green sheet.
  • the electrolyte green sheet and the cathode material layer can be selected from various related materials in the field suitable for constructing SOFC single cells.
  • the electrolyte green sheet is selected from YSZ electrolyte green sheets, more specifically 8YSZ
  • the electrolyte sheet, the thickness of the electrolyte green sheet may be 2-10 ⁇ m, 2-4 ⁇ m, 4-6 ⁇ m, 6-8 ⁇ m, or 8-10 ⁇ m, and the electrolyte green sheet is usually a dense sintered thin layer.
  • the weight ratio of LSM to YSZ or SSZ is 5 ⁇ 7:5 ⁇ 3
  • GDC for example, Ce 0.9 Gd 0.1 O 1.95 , Ce 0.8 Gd 0.2 O 1.9
  • the weight ratio of LSCF and GDC can be 5-7:5-3, when using a combination of LSCF and GDC as the cathode
  • the SOFC single cell usually further includes a resistance layer
  • the resistance layer may be located on the YSZ electrolyte green sheet, and the thickness of the resistance layer may be 1 to 3 ⁇ m, 1 to 1.5
  • the thickness of the cathode material layer can be 20 ⁇ 40 ⁇ m, 20 ⁇ 25 ⁇ m , 25-30 ⁇ m, 30-35 ⁇ m, or 35-40 ⁇ m, the cathode material layer has a porous structure, and its porosity may be 25-40vol.%, 25-30vol.%, 30-35vol.%, or 35-40vol. .%.
  • the anode material layer (including the anode support layer and/or the anode functional layer) and the electrolyte green sheet can be sequentially laminated, hot pressed, and sintered (sintered).
  • the temperature can be 1350°C ⁇ 1450°C, and the holding time can be 3 ⁇ 6h) to obtain a half-cell, and further form (for example, painting, screen printing, etc.) cathode material (usually in the form of a paste) on the obtained half-cell ,
  • the whole battery can be obtained by baking.
  • the hot pressing temperature may be 50-150°C
  • the hot pressing time may be 5-40 min
  • the pressure may be 5-30Mpa
  • the firing temperature may be 1050-1250°C, 1050-1100°C , 1100 ⁇ 1150°C, 1150 ⁇ 1200°C, or 1200 ⁇ 1250°C.
  • the sixth aspect of the present invention provides an anode-reduced SOFC single cell, which is obtained from the SOFC single cell provided by the fourth aspect of the present invention after reduction treatment and/or discharge treatment.
  • the SOFC single cell provided by the fourth aspect of the present invention usually requires reduction of the anode before operation.
  • Those skilled in the art can choose a suitable method to perform anode reduction on the SOFC single cell. For example, it can be reduced in a hydrogen atmosphere, the reduction temperature can be 650-950°C, and the reduction time can be 1-6h, 1-2h, 2-4h, Or 4 ⁇ 6h.
  • the purpose of anode reduction is to reduce NiO into metallic Ni, and the anode into porous cermet Ni/YSZ.
  • further discharge can be performed.
  • the temperature can be 650 ⁇ 750°C
  • H 2 + 3% H 2 O is used as fuel and air is used as oxidant to discharge for 4 to 8 hours
  • the discharge current is 0.6 to 0.8V.
  • the solid solution of NiO in the YSZ particles no longer matches the lattice parameters, and nano-Ni precipitates on the surface of the YSZ particles.
  • the solid solution of YSZ in the NiO particles is no longer matched because of the lattice parameters, and nano-YSZ is precipitated on the surface of the Ni particles. Because the anode has the above structure, the anode has good carbon deposition resistance.
  • the cathode of the battery When the SOFC single cell provided by the present invention is in operation, the cathode of the battery is in contact with air, and the anode is in contact with fuel gas.
  • the oxygen in the cathode is adsorbed and dissociated into oxygen atoms.
  • the oxygen atoms obtain electrons from the external circuit of the cathode to become oxygen ions.
  • the oxygen ions diffuse through the sintered dense electrolyte layer through the lattice to the anode functional layer.
  • the C adsorbed on Ni can migrate in the Ni crystal lattice, mainly using Ni's (1 1 1) crystal plane as a template to deposit carbon, and eventually form various carbon substances such as graphite carbon, carbon fiber, hollow carbon nanotubes, and Shaped carbon, etc.
  • Ni has a face-centered cubic structure (closest packing), and the atomic arrangement of the (1 1 1) crystal plane is a uniform and symmetrical arrangement, which is exactly the template for forming carbon.
  • the method for preparing the SOFC anode material and the SOFC cell obtained by further preparation of the SOFC anode material provided by the present invention due to mutual solid solution, when the anode is in use, after the anode is reduced at a certain temperature, the original NiO solid solution on the surface of the YSZ crystal grains Site reduction precipitates into nano-metal Ni particles; YSZ, which is also solid-dissolved on the surface of NiO grains, will be reduced to metallic Ni, and YSZ that does not match the crystal lattice will be precipitated and become nano-YSZ grains on the surface of NiO.
  • the nano-Ni not only has a strong catalytic cracking ability for hydrocarbon fuels, but also has carbon deposition resistance.
  • fuel molecules enter the SOFC anode they are preferentially cracked at this location.
  • the fuel gas such as CH 4 and ethanol entering the anode does not need to be cracked on the large Ni particles in the anode.
  • the large particles of Ni in the anode are the main phase in the anode and communicate with each other, which can play the role of electron conduction.
  • a small amount of YSZ nanoparticles will precipitate on the surface of some large particles of Ni in the anode.
  • the large particles of Ni Due to the strong interaction between these precipitated nano YSZ particles and Ni particles, the large particles of Ni have the ability to resist carbon deposition, which can make the anode resistant Carbon deposition, that is, the phenomenon of carbon deposition will not occur when hydrocarbon fuel is cracked on Ni.
  • YSZ is a weakly basic oxide. This type of oxide easily adsorbs H 2 O in the fuel gas, and then further dissociates water molecules into adsorbed hydroxyl radicals and adsorbed hydrogen atoms. The OH adsorbed on YSZ and adsorbed The C on Ni combines to become COH adsorbed on Ni, and the catalytic reaction equation for eliminating carbon deposits is as follows:
  • Anode support layer :
  • the anti-carbon deposition catalytic reaction of the anode functional layer involves the participation of oxygen ions that continuously migrate from the electrolyte to the anode functional layer, so the carbon oxidation reaction has some different reaction mechanisms from the upper support layer.
  • the main difference is that the CO and H adsorbed on Ni will migrate on Ni to the three-phase line (tpb) of the anode functional layer to react with oxygen ions diffused from the electrolyte.
  • the equation for the catalytic reaction to eliminate carbon deposits is as follows:
  • the related embodiments of the present invention also further verify the carbon deposition resistance of the SOFC single cell.
  • no carbon deposition was observed on the large particles of Ni on the anode (including the anode support layer and the anode functional layer).
  • the experiment proved The cracking reaction of the hydrocarbon fuel in the entire anode is basically on the nano-Ni crystal grains reduced and precipitated on the YSZ crystal grains, but there is no carbon deposit.
  • the advantages of good performance, long-term stability of battery performance, and battery preparation methods are also easy to realize industrialization.
  • the one or more method steps mentioned in the present invention does not exclude that there may be other method steps before and after the combined steps or other method steps may be inserted between these explicitly mentioned steps, unless otherwise.
  • the number of each method step is only a convenient tool for identifying each method step, and is not intended to limit the sequence of each method step or limit the scope of implementation of the present invention. The change or adjustment of the relative relationship is If there is no substantial change in the technical content, it shall be regarded as the scope of the present invention.
  • FIG. 12 is a schematic diagram of Ni nanoparticles (HAADF, high-angle annular dark field image) and EDS (element mapping) precipitated on the surface of 5YSZ particles.
  • This powder is the anode support layer powder prepared by the above-mentioned mixing, ball milling, calcining and ball milling. , Reduce 4h at 900°C, hydrogen atmosphere.
  • the element mapping diagrams are six mapping diagrams of Ni, Zr, O, Y, Ni+Zr and Ni+Zr+O+Y. It can be further proved from this figure that there are more nano-metal Ni particles precipitated on the sub-micron 5YSZ powder particles.
  • the powder treatment process is the same as supporting anode powder. The processed powder is ready for use.
  • the processed anode support layer powder and anode functional layer powder are molded by casting method, and the YSZ electrolyte blank is cast well (the electrolyte/functional anode blank is prepared by double-layer casting method).
  • Hot press lamination at 100°C and 15MPa for 15min. Three layers are hot pressed together to obtain an anode-supported electrolyte film blank (from top to bottom: electrolyte layer + anode functional layer + anode support layer), cut to a certain size and then sintered (Incubate at 1400°C for 3h) to obtain a half-cell.
  • the specific structure and performance of the battery are as follows:
  • Figure 2 shows the SEM image of the microstructure of the SOFC full battery (after reduction), including the cathode, electrolyte and anode, where the anode includes an anode functional layer and an anode support layer.
  • the electrolyte is a dense burnt thin layer with a thickness of 10 ⁇ m.
  • the cathode has a porous structure and the cathode has a thickness of 20 ⁇ m.
  • the anode is composed of an anode functional layer with small cavities and an anode supporting layer with larger cavities.
  • the thickness of the functional layer is 23 ⁇ m, and the supporting layer The thickness is 450 ⁇ m.
  • Figure 3 shows the microstructure of the anode support layer of the battery before reduction.
  • Figure a is a low-magnification view of the anode support layer. It can be seen from the figure: the anode is a porous structure, with the main pore size of about 5 ⁇ m, and no small nanocrystals are precipitated on the surface of the crystal grains;
  • Figures b and c are A partial enlarged view of the anode hole, it can be seen that there is no nanocrystal precipitation on the surface of the crystal grain inside the hole.
  • Figure a is a low-magnification view of the anode support layer. It can be seen from the figure: the anode is a porous structure, the size of the main pores is about 5 ⁇ m, and it can be seen that there are small nanocrystals precipitated on the surface of the crystal grains;
  • Figures b and c are partial enlarged views It can be seen that there are many nanocrystals precipitated on the surface of nickel oxide and zirconium oxide grains.
  • the crystal grains with a sharp shape are 5YSZ crystal grains, and the crystal grains with a nearly circular shape are metallic Ni crystal grains.
  • the nanocrystalline grains precipitated on the 5YSZ grains are more obvious; the nanocrystalline grains precipitated on the metallic Ni grains are not very obvious, and the precipitated nanocrystalline grains are smaller. There is no precipitation on some surfaces in the picture, and this surface is a newly fractured surface.
  • Figure 5 shows the microstructure of the battery anode functional layer before and after reduction (discharge).
  • Figure a is a full view of the low multiple of the anode functional layer before the battery is reduced (discharged). It can be seen from the figure that the anode functional layer is a porous structure with a main hole size of about 1.8 ⁇ m, and the functional layer is closely combined with the electrolyte. The functional layer did not see small nanocrystals precipitated on the surface of the crystal grains;
  • Figure b and Figure c are partial enlarged views of the anode functional layer after the battery is reduced and discharged. It can be seen that there are more nanocrystals precipitated on the surface of the nickel oxide and zirconium oxide grains. .
  • the crystal grains with a sharp shape are 8YSZ crystal grains, and the crystal grains with a nearly circular shape are metal Ni crystal grains.
  • the nanocrystalline grains precipitated on the 8YSZ grains are more obvious; the nanocrystalline grains precipitated on the metallic Ni grains are not very obvious, and the precipitated nanocrystalline grains are smaller. There is no precipitation on some surfaces in the picture, and this surface is a newly fractured surface.
  • FIG. 6 shows the electrochemical performance of the battery. It can be seen from the figure that H 2 is used as fuel (flow rate 30ml/min) at 750°C, and air is oxidizing gas (static).
  • the highest power density is 0.52W/cm 2
  • the open circuit voltage is 1.05V
  • the ohmic impedance and the bipolar impedance are 0.14 ⁇ cm 2 and 0.87 ⁇ cm 2 respectively
  • CH 4 +3% H 2 O is used as fuel at 750°C (Methane flow rate is 30ml/min)
  • air is oxidizing gas (static)
  • the highest power density of the battery is 0.42W/cm 2
  • the open circuit voltage is 1.10V
  • the ohmic impedance and the two-pole impedance are 0.14 ⁇ cm 2 and 2.84 ⁇ respectively ⁇ Cm 2 .
  • Figure 8 shows the use of wet ethanol as fuel (using N 2 gas to pass through the ethanol liquid, the flow rate of N 2 is 30 ml/min, bringing ethanol molecules into the anode, where the N 2 content is 92 vol% and the ethanol content is 8 vol%), air It is the oxidizer (static), the electrochemical performance of the battery.
  • the anode of the single cell was discharged in H 2 + H 2 O atmosphere and the cathode was discharged at 750° C. for 4 hours (the electro-discharge voltage was 0.7V), and then operated at 750° C. with N 2 + ethanol as fuel and air as oxidant.
  • the open circuit voltage of the single cell is 1.0V, the maximum power density is 0.36W/cm 2 , and the total impedance is 1.48 ⁇ cm 2 , where the ohmic impedance is 0.37 ⁇ cm 2 and the polarization impedance is 1.11 ⁇ cm 2 .
  • Figure 9 shows the operating curve of a single cell with ethanol as fuel at different discharge currents.
  • the single cell runs at 750°C with N 2 + ethanol as fuel and air as oxidant.
  • the maximum power density of a single cell is 0.36W/cm 2 , and it is discharged at different current densities, and there is basically no attenuation of the single cell after 40 hours of operation.
  • the present invention effectively overcomes various shortcomings in the prior art and has high industrial value.

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Abstract

一种SOFC抗积碳Ni-YSZ阳极材料的制备方法，属于材料领域，该制备方法包括：(1)提供NiO和YSZ的混合粉料；(2)将步骤(1)所提供的混合粉体进行两相相互固溶处理；(3)将步骤(2)固溶处理所得产物进行粒径调整。本发明所提供的SOFC阳极材料及其制备获得的SOFC单电池，其阳极具有良好的抗积碳性，且阳极材料整体上具有廉价、催化性能好、电子导电性好、与YSZ的化学相容性好等优点，电池性能的长期稳定性好，电池的制备方法也易于实现产业化。

Description

一种SOFC抗积碳Ni-YSZ阳极材料的制备方法 技术领域
本发明涉及固体氧化物燃料电池领域，特别是涉及一种SOFC抗积碳Ni-YSZ阳极材料的制备方法。
背景技术
固体氧化物燃料电池(SOFC，Solid oxide of fule cell)是一种将燃料和氧气中的化学能不通过燃烧直接换成为电能的一种发电方式。不需要遵守卡诺循环，转化效率高，热电联共效率可达80％以上，同时电化学反应的产物是热水和二氧化碳，由于该二氧化碳的浓度高，易于回收，故发电的产物也是清洁干净的。因此固体氧化物燃料电池是一种高效绿色的发电方式。中温固体氧化物燃料电池(IT-SOFC)的使用温度约750℃左右，在商业上该电池属于第二代电池，第一代电池为电解质支撑型，属于高温固体氧化物燃料电池，其工作温度至少850℃。IT-SOFC的结构一般采用阳极支撑型(电解质薄膜)电池结构。IT-SOFC商业化的瓶颈问题是电池阳极的抗积碳性，传统Ni/YSZ阳极(金属镍和氧化钇稳定的氧化锆的混合多孔金属陶瓷)电池在工作温度(即750℃左右)使用碳氢燃料的情况下很容易积碳使得电池性能很快衰减。这样使得传统Ni/YSZ需要经过各种改性或掺杂来提高其抗积碳性，或者使用重整后的碳氢燃料为燃料，前者会大大增大电池的制造成本或同时带来电池性能的长期稳定性差；后者会使得电池的使用不方便而带来其他的问题。然而，由于缺乏有效的替代品，在工业上商业化的SOFC电池仍然是采用传统Ni/YSZ阳极，至今未寻找到更好的阳极催化剂代替Ni，所以如何提高传统Ni/YSZ阳极的抗积碳性是SOFC商业化亟待解决的关键难题。
发明内容
鉴于以上所述现有技术的缺点，本发明的目的在于提供一种SOFC阳极材料的制备方法，并进一步提供了由该制备方法制备获得的SOFC阳极材料及其用途，用于解决现有技术中的问题。
为实现上述目的及其他相关目的，本发明一方面提供一种SOFC阳极材料的制备方法，包括：
(1)提供NiO和YSZ的混合粉料；
(2)将步骤(1)所提供的混合粉体进行两相相互固溶处理，
(3)将步骤(2)固溶处理所得产物进行粒径调整。
在本发明一些实施方式中，所述步骤(1)中，提供NiO和YSZ的混合粉料的具体方法为：将NiO和YSZ粉碎、混合。
在本发明一些实施方式中，所述步骤(1)中，NiO和YSZ的重量比为1～1.8:1。
在本发明一些实施方式中，所述步骤(1)中，当SOFC阳极材料为阳极支撑材料时，YSZ粉体为3～8mol％Y 2O 3掺杂的氧化锆，NiO原料的微晶尺寸为5～20nm，YSZ原料的粒径为D 50＝0.2～1.0μm。
在本发明一些实施方式中，所述步骤(1)中，当SOFC阳极材料为阳极功能层材料时，YSZ粉体为7～9mol％Y 2O 3掺杂的氧化锆，NiO原料的微晶尺寸为5～20nm，YSZ原料的粒径为D 50＝50～100nm。
在本发明一些实施方式中，所述步骤(1)中，混合粉体中，YSZ颗粒的粒径为50～1000nm，NiO粉体的微晶尺寸为10～20nm。
在本发明一些实施方式中，所述步骤(1)中，通过球磨将NiO和YSZ粉碎、混合，所述球磨优选为湿法球磨，球磨所得粉体还进行干燥，干燥温度可以为60～80℃。
在本发明一些实施方式中，所述步骤(1)中，在分散剂存在的条件下进行粉碎、混合，所述分散剂优选选自三乙醇胺、柠檬酸、聚乙二醇、乙酰丙酮、聚乙烯吡咯烷酮、聚丙烯酸中的一种或多种的组合，粉体与分散剂的重量比为1:0.005～0.1，优选的为1:0.02～0.05。
在本发明一些实施方式中，所述步骤(1)中，在溶剂存在的条件下进行粉碎、混合，所述溶剂优选选自无水乙醇、丙酮、丁酮、异丙醇、二甲基甲酰胺中的一种或多种的组合，粉体与溶剂的重量比为1:0.2～1.5，优选的为1:0.4～0.8。
在本发明一些实施方式中，所述步骤2)中，将步骤(1)所提供的混合粉体进行两相相互固溶处理的具体方法为：将步骤(1)所提供的混合粉体干燥、煅烧。
在本发明一些实施方式中，所述步骤(2)中，所述煅烧温度为600～1200℃，优选的为800～950℃。
在本发明一些实施方式中，所述步骤(2)中，煅烧时间为1～10，优选的2～8小时。
在本发明一些实施方式中，所述步骤(3)中，将步骤(2)固溶处理所得产物进行粒径调整的具体方法为：将步骤(2)所提供的煅烧产物粉碎、干燥，优选的，通过球磨将煅烧产物粉碎。
本发明另一方面提供一种SOFC阳极材料，由所述的制备方法制备获得。
本发明另一方面提供一种SOFC单电池，包括阳极材料层、电解质坯片和阴极材料层， 所述阳极材料层由所述的SOFC阳极材料制备获得。
在本发明一些实施方式中，所述阳极材料层包括阳极支撑层和/或阳极功能层，所述阳极支撑层和/或阳极功能层由所述的SOFC阳极材料制备获得。
在本发明一些实施方式中，阳极支撑层的厚度为300～700μm，优选为400～500μm，孔洞大小为3～10μm，阳极支撑层还原后其孔隙率为25～40vol.％，优选为30～35vol.％；阳极功能层的厚度为5～30μm，优选为5～10μm，孔洞大小为1～5μm，阳极功能层还原后其孔隙率为25～40vol.％，优选为30～35vol.％。
在本发明一些实施方式中，所述电解质坯片选自YSZ电解质坯片，所述电解质坯片的厚度为2～10μm。
在本发明一些实施方式中，所述阴极材料层选自LSM和YSZ的组合或者LSM和SSZ的组合，两者的重量比例为5～7:5～3、LSCF和GDC的组合，两者重量比为5～7:5～3。
在本发明一些实施方式中，所述阴极材料层的厚度为20～40μm，优选的为20～25μm，所述阴极材料层为多孔结构，孔隙率为25～40vol.％，优选的为30～35vol.％。
本发明另一方面提供一种阳极还原的SOFC单电池，由所述的SOFC单电池经还原处理和/或放电处理后获得。
附图说明
图1 SOFC抗积碳Ni-YSZ阳极材料的制备过程示意图。
图2 SOFC全电池(还原后)微观结构SEM图。
图3电池阳极支撑层还原前的微观结构SEM图(a为阳极低倍数的图，反应阳极的全貌；b和c为局部放大图)。
图4电池还原(还原条件是在750℃，H 2+3％H 2O为燃料，开路下还原1h)后单电池再在750℃，H 2+3％H 2O为燃料，空气为氧化剂下放电放电(电流为0.4A/cm 2)4h后的阳极支撑层断面SEM(a为阳极低倍数的图，反应阳极的全貌；b和c为局部放大图)。
图5单电池阳极功能层还原(放电)前后的对比SEM图。a还原前阳极功能层；b、c电池还原(还原条件是在750℃，H 2+3％H 2O为燃料，开路下还原1h)后单电池再在750℃，H 2+3％H 2O为燃料，空气为氧化剂下放电(电流为0.4A/cm 2)4h后的阳极功能层断面SEM。
图6单电池在750℃下H 2(+3％H 2O)和CH 4(+3％H 2O)不同燃料的IV和EIS曲线。
图7单电池以CH 4(+3％H 2O)为燃料，空气为氧化剂，0.40A/cm 2的电流密度下放电曲线。
图8乙醇为燃料单电池在750℃下IV和EIS曲线。
图9以乙醇为燃料单电池在不同放电电流下的运行曲线。
图10 5YSZ/NiO球磨煅烧再球磨后的粉体(阳极支撑层粉体)的粒度分布曲线图。
图11 SOFC阳极抗积碳的机制示意图。
图12 5YSZ颗粒表面析出Ni纳米颗粒(HAADF，高角环形暗场像)以及相应的EDS(元素mapping)。
具体实施方式
本发明发明人通过大量研究发现，采用合适的方法将NiO和YSZ粉碎、混合，并进一步煅烧，可以提供一种新的SOFC阳极材料，所述SOFC阳极材料可以用于制备SOFC单电池，制备获得SOFC单电池的阳极具备良好的抗积碳性能，在此基础上完成了本发明。
本发明第一方面提供一种SOFC阳极材料的制备方法，包括：
(1)提供NiO和YSZ的混合粉料；
(2)将步骤(1)所提供的混合粉体进行固溶处理；
(3)将步骤(2)固溶处理所得产物进行粒径调整。
本发明所提供的SOFC阳极材料的制备方法，可以包括：提供NiO和YSZ的混合粉，从而将NiO和YSZ粉体颗粒两相混合更均匀且粉体颗粒尺寸减少。所述阳极材料的原料可以包括NiO和YSZ，将两种氧化物充分粉碎、混合，从而可以获得亚微米级的YSZ颗粒和纳米晶NiO粉体的混合物。如图1所示，两种不同粒径的粉体混合在一起球磨分散后会出现包括以下两种的基本情况：第一，微晶尺寸为纳米级的NiO吸附在亚微米级的YSZ颗粒表面；第二较，少量的纳米级YSZ颗粒被吸附在NiO粉体的团聚体周围。所获得的混合粉体中，所述YSZ颗粒的粒径通常50～1000nm、50～100nm、100～200nm、200～300nm、300～500nm、或500～1000nm，所述NiO粉体的微晶尺寸(微晶尺寸由XRD测试并采用scherrer公式计算获得，下同)可以为10～20nm、10～15nm、或15～20nm。本领域技术人员可选择合适的方法，以提供NiO和YSZ的混合粉料，例如，可以将NiO和YSZ粉碎、混合。更具体的，将NiO和YSZ粉碎、混合的方法对于本领域技术人员来说应该是已知的，例如，可以采用球磨(例如，湿法球磨等)等方法将NiO和YSZ粉碎、混合。所述制备过程中，可以在分散剂和/或溶剂存在的条件下进行粉碎、混合，从而可以使NiO粉体和YSZ粉体均匀混合，例如，所述分散剂可以选自三乙醇胺、柠檬酸、聚乙二醇、乙酰丙酮、聚乙烯吡咯烷酮、聚丙烯酸等中的一种或多种的组合，粉体与分散剂的重量比可以为1:0.005～0.1、1:0.005～0.01、1:0.01～0.02、 1:0.02～0.03、1:0.03～0.04、1:0.04～0.05、或1:0.05～0.1，优选可以为1:0.02～0.05，再例如，所述溶剂可以选自无水乙醇、丙酮、丁酮、异丙醇、二甲基甲酰胺(DMF)等中的一种或多种的组合，粉体与溶剂的重量比可以为1:0.2～1.5、1:0.2～0.4、1:0.4～0.6、1:0.6～0.8、1:0.8～1.0、1:1.0～1.2、或1:1.2～1.5，优选可以为1:0.4～0.8，再例如，球磨制备过程中可以使用氧化锆球，粉体和球的重量比可以为1:1.5～2.0、1:1.5～1.6、1:1.6～1.8、或1:1.8～2.0，氧化锆球的直径可以为0.3～0.8mm、0.3～0.4mm、0.4～0.5mm、0.5～0.6mm、0.6～0.7mm、或0.7～0.8mm，再例如，球磨所得粉体还可以进行干燥，干燥温度可以为60～80℃、60～65℃、65～70℃、70～75℃、或75～80℃。所述SOFC阳极材料可以用于制备阳极材料层，更具体可以用于制备阳极支撑层和/或阳极功能层，阳极功能层是完成阳极的电化学反应的场所；阳极支撑层起的作用是整个电池的支撑作用和电子传导的作用，通常来说，阳极支撑层相对较厚，且具有较高的机械强度。所述SOFC阳极材料及其制备获得的阳极材料层的性质主要取决于制备过程中NiO和YSZ之间的混合比例、YSZ中Y 2O 3的含量和/或稳定性、原料粉体粒径等参数，例如，NiO和YSZ的重量比可以为1～1.8:1、1～1.2:1、1.2～1.4:1、1.4～1.6:1、或1.6～1.8:1，在本发明一具体实施例中，当SOFC阳极材料为阳极支撑材料时，NiO和YSZ的重量比为1～1.8:1、1～1.2:1、1.2～1.4:1、1.4～1.6:1、或1.6～1.8:1，YSZ粉体可以为3～8mol％Y 2O 3掺杂的氧化锆、3～4mol％Y 2O 3掺杂的氧化锆、4～5mol％Y 2O 3掺杂的氧化锆、5～6mol％Y 2O 3掺杂的氧化锆、6～7mol％Y 2O 3掺杂的氧化锆、7～8mol％Y 2O 3掺杂的氧化锆(YSZ材料的表达方式对于本领域技术人员来说应该是公知的，例如，5mol％Y 2O 3掺杂的氧化锆即5mol％Y 2O 3+95mol％ZrO2固溶形成的YSZ材料，也可以表示为5YSZ，由于晶格中固溶了适当含量的Y 2O 3，使得氧化锆的相变被部分稳定住了，氧化锆随着温度的变化仅仅是部分进行相变)，NiO原料的微晶尺寸可以为5～20nm、5～10nm、10～15nm、或15～20nm，YSZ原料的粒径可以为D 50＝0.2～1.0μm、0.2～0.4μm、0.4～0.6μm、0.6～0.8μm、或0.8～1.0μm，在本发明另一具体实施例中，当SOFC阳极材料为阳极功能层材料时，NiO和YSZ的重量比为1～1.8:1、1～1.2:1、1.2～1.4:1、1.4～1.6:1、或1.6～1.8:1，YSZ粉体为7～9mol％Y 2O 3掺杂的氧化锆、7～7.5mol％Y 2O 3掺杂的氧化锆、7.5～8mol％Y 2O 3掺杂的氧化锆、8～8.5mol％Y 2O 3掺杂的氧化锆、或8.5～9mol％Y 2O 3掺杂的氧化锆(晶格中固溶的Y 2O 3含量通常最高可以达到8mol％左右，该比例下氧化锆的相变被基本稳定住了，氧化锆随着温度的变化没有相变)，NiO原料的微晶尺寸可以为5～20nm、5～10nm、10～15nm、或15～20nm，YSZ原料的粒径可以为D 50＝50～100nm、50～60nm、60～70nm、70～80nm、80～90nm、或90～100nm。
本发明所提供的SOFC阳极材料的制备方法，可以包括：将步骤(1)所提供的混合粉体 进行两相相互固溶处理。本发明中，所述两相相互固溶处理通常指将YSZ颗粒周边吸附的NiO纳米颗粒固溶进入YSZ晶格形成固溶体，并在NiO颗粒周围吸附的YSZ纳米颗粒固溶进入NiO晶格形成固溶体的处理方法。将步骤(1)所提供的混合粉体进行两相相互固溶处理的具体方法可以是：将步骤(1)所提供的混合粉体干燥、煅烧。本发明发明人发现，煅烧过程中粉体会相互固溶，NiO颗粒晶粒小(活性高)、温度低，在煅烧过程中很容易固溶进入YSZ颗粒的表面，即纳米NiO进入YSZ颗粒晶格的内部，形成固溶体；同时也发现小尺寸晶粒的YSZ在煅烧过程中也同样固溶进入较大NiO颗粒中，即纳米的YSZ进入NiO颗粒晶格的内部，形成固溶体。煅烧所得的粉体的表面是光滑的，颗粒表面通常没有明显的纳米凸起。所述煅烧温度可以为600～1200℃、600～800℃、800～850℃、850～900℃、900～950℃、950～1000℃、或1000～1200℃，优选为800～950℃，煅烧时间可以为1～10小时、1～2小时、2～4小时、4～6小时、6～8小时、或8～10小时，优选为2～8小时，所述煅烧时间具体为待处理产品在煅烧温度下的保温时间。
本发明所提供的SOFC阳极材料的制备方法，可以包括：将步骤(2)固溶处理所得产物进行粒径调整，从而可以减小因煅烧长大的NiO和YSZ混合粉体的颗粒尺寸，所述粒径调整通常指使用适当的物理方法，将粉体粒径调整至目标尺寸的处理方法。将步骤(2)固溶处理所得产物进行粒径调整的具体方法可以为：将步骤(2)所提供的煅烧产物粉碎、干燥。煅烧后，粉体颗粒会有一定程度的增大，粉碎后可以获得合适粒径的粉体颗粒，例如，粉碎后的煅烧产物的粒径可以为0.1～1.1μm、0.1～0.3μm、0.3～0.5μm、0.5～0.8μm、或0.8～1.1μm，D 50＝0.190μm，进一步干燥以后，体系中基本不含有溶剂，即可获得可以作为SOFC阳极材料的粉体，再例如，再例如，球磨制备过程中可以使用氧化锆球，粉体和球的重量比可以为1:1.5～2.0、1:1.5～1.6、1:1.6～1.8、或1:1.8～2.0。将煅烧产物粉碎的方法对于本领域技术人员来说应该是已知的，例如，可以采用球磨等方法将煅烧产物进行粉碎。
本发明第二方面提供一种SOFC阳极材料，由本发明第一方面所提供的SOFC阳极材料的制备方法制备获得。
本发明第三方面提供本发明第二方面所提供的SOFC阳极材料作为SOFC阳极材料的用途。所述SOFC阳极材料可以用于制备SOFC阳极材料层，例如，所述SOFC阳极材料层可以包括阳极支撑层和/或阳极功能层等，通过所述SOFC阳极材料制备的SOFC阳极材料层具有良好的抗积碳性能。
本发明第四方面提供一种SOFC阳极材料层，由本发明第二方面提供的SOFC阳极材料制备获得，所述SOFC阳极材料层可以包括阳极支撑层和/或阳极功能层等。本领域技术人员 可选择合适的方法通过所述SOFC阳极材料制备SOFC阳极材料层，例如，可以采用流延等方法成型，再例如，所形成的阳极材料层中，阳极支撑层的厚度可以为300～700μm，优选为400～500μm，阳极支撑层的孔隙相对较大，孔洞大小可以为3～10μm、3～5μm、5～7μm、或7～10μm，极支撑层还原后其孔隙率可以为25～40vol.％、25～30vol.％、30～35vol.％、或35～40vol.％，优选的为30～35vol％，再例如，阳极功能层的厚度可以为5～30μm、5～10μm、10～20μm、或20～30μm，优选的为5～10μm，阳极功能层的孔隙相对较小，孔洞大小可以为1～5μm、1～2μm、2～3μm、3～4μm、或4～5μm，阳极功能层还原后其孔隙率为25～40vol.％、25～30vol.％、30～35vol.％、或35～40vol.％，优选的为30～35vol％。
本发明第五方面提供一种SOFC单电池，包括本发明第三方面所提供的阳极材料层、电解质坯片和阴极材料层。SOFC单电池的基本结构对于本领域技术人员来说应该是已知的，例如，所述SOFC单电池中，阳极材料层、电解质坯片和阴极材料层通常可以依次叠加，阳极材料层和阴极材料层可以分别位于电解质坯片两侧。所述电解质坯片和阴极材料层可以选用本领域各种适用于构建SOFC单电池的相关材料，在本发明一具体实施例中，所述电解质坯片选自YSZ电解质坯片，更具体为8YSZ电解质片，所述电解质坯片的厚度可以为2～10μm、2～4μm、4～6μm、6～8μm、或8～10μm，电解质坯片通常是致密的烧薄层。在本发明另一具体实施例中，所述阴极材料层选自LSM(其通式可以是La 1-xSr xMnO 3，x＝0.1～0.9)和YSZ的组合或LSM和SSZ的组合，LSM与YSZ或SSZ的重量比例为5～7:5～3，LSCF(其通式可以是La 1-xSr xCo 1-yFe yO 3-δ，x＝0.1～0.9；y＝0.1～0.9)和GDC(例如，Ce 0.9Gd 0.1O 1.95、Ce 0.8Gd 0.2O 1.9)的组合，LSCF和GDC的重量比例可以为5～7:5～3，当使用LSCF与GDC的组合作为阴极时，所述SOFC单电池通常还包括阻抗层，所述阻抗层可以位于YSZ电解质坯片上，所述阻抗层的厚度可以为1～3μm、1～1.5μm、1.5～2μm、2～2.5μm、或2.5～3μm，避免YSZ与LSCF在高温下反应生成第二相，同时可以使GDC的膨胀系数与阴极LSCF和GDC更为匹配，所述阴极材料层的厚度可以为20～40μm、20～25μm、25～30μm、30～35μm、或35～40μm，所述阴极材料层为多孔结构，其孔隙率可以为25～40vol.％、25～30vol.％、30～35vol.％、或35～40vol.％。本领域技术人员可选择合适的方法制备所述SOFC单电池，例如，可以将阳极材料层(包括阳极支撑层和/或阳极功能层)、电解质坯片依次叠层、热压、烧结(烧结的温度可以为1350℃～1450℃，保温时间可以为3～6h)以获得半电池，并在所得半电池上进一步形成(例如，涂刷、丝网印刷等)阴极材料(通常为浆料形式)，焙烧即可获得全电池。在本发明一具体实施例中，所述热压温度可以是50～150℃，热压时间可以是5～40min，压力可以是5～30Mpa，焙烧温度可以是1050～1250℃、1050～1100℃、1100～1150℃、1150～1200℃、或 1200～1250℃。
本发明第六方面提供一种阳极还原的SOFC单电池，由本发明第四方面提供的SOFC单电池经还原处理和/或放电处理后获得。本发明第四方面所提供的SOFC单电池在运行前通常需要进行阳极的还原。本领域技术人员可选择合适的方法对SOFC单电池进行阳极还原，例如，可以在氢气气氛下还原，还原温度可以为650～950℃，还原时间为1～6h、1～2h、2～4h、或4～6h。阳极还原的目的是将NiO还原成金属Ni，阳极变成多孔金属陶瓷Ni/YSZ。为进一步在亚微米级颗粒上析出更多的纳米晶粒，还可以进一步进行放电，本领域技术人员可选择合适的方法对SOFC单电池进行放电，例如，可以在650～750℃，H 2+3％H 2O为燃料，空气为氧化剂下放电4～8h，放电电流为0.6～0.8V。如图1所示，由于NiO还原为Ni，使得YSZ颗粒中固溶的NiO由于晶格参数不再匹配，而在YSZ颗粒的表面析出纳米Ni。另外NiO颗粒中固溶的YSZ也由于晶格参数不再匹配，而在Ni颗粒的表面析出纳米YSZ，由于阳极具有上述结构，所以使得阳极具有良好的抗积碳性能。
本发明所提供的SOFC单电池在工作时，电池的阴极与空气接触，阳极与燃料气体接触。阴极的氧气被吸附后解离成氧原子，氧原子获得阴极外电路传入的电子变成氧离子，氧离子通过晶格扩散穿过烧结致密的电解质层来到阳极功能层，由于阳极层中有燃料气体，例如甲烷、乙醇等碳氢燃料，该碳氢燃料可以在阳极的Ni上进行裂解反应成H、CO和CO 2等产物，进而由此在该层进行电化学反应：O 2-+2H＝H 2O+2e；O 2-+CO＝CO 2+2e；2O 2-+C＝CO 2+4e。电化学反应的产物是水和二氧化碳，所获得的电子由阳极传导出去。传统的Ni阳极在Ni对碳氢化合物裂解的这一过程很容易积碳，进而电池性能迅速降低。积碳的基本过程如下：以Ni对CH 4进行裂解为例，CH 4＝C+CH 3；CH 3＝C+CH 2；CH 2＝C+CH；CH＝C+H。吸附在Ni上的C可以在Ni晶格中迁移，主要以Ni的(1 1 1)晶面为模板积碳，最终可以形成各种碳物质如石墨碳、碳纤维、中空的碳纳米管、无定形碳等。Ni是面心立方结构(最紧密堆积)，(1 1 1)晶面的原子排布是均匀对称的排列，正好是形成碳的模板。而本发明提出的SOFC阳极材料的制备方法及其进一步制备获得的SOFC单电池，由于相互的固溶使得阳极在使用时，阳极在一定温度下还原后，固溶在YSZ晶粒表面的NiO原位还原析出成为纳米金属Ni颗粒；同样固溶在NiO晶粒表面的YSZ由于NiO晶粒要还原成金属Ni，就会将与晶格不匹配的YSZ析出，成为NiO表面的纳米YSZ晶粒。这些在YSZ晶粒表面析出的大量的纳米Ni，该纳米Ni不仅具有对碳氢燃料很强的催化裂解能力而且具有抗积碳性。当燃料分子进入SOFC阳极后优先在该位置进行裂解，由于这种纳米Ni颗粒比较多，故进入阳极的CH 4、乙醇等燃料气体不需要在阳极中大颗粒的Ni上进行裂解。此时阳极中大 颗粒Ni是阳极中的主要相且相互连通，可起电子传导的作用。另外阳极中某些大颗粒的Ni表面也会析出少量YSZ纳米颗粒，由于这些析出的纳米YSZ颗粒与Ni颗粒间存在强相互作用，使得大颗粒Ni具有抗积碳的能力，可以使得阳极具有抗积碳性，即碳氢燃料在Ni上进行裂解时不会产生积碳的现象。
YSZ是属于弱碱性氧化物，这类氧化物容易吸附燃料气体中的H 2O，然后进一步将水分子解离成吸附的羟基自由基和吸附的氢原子，吸附在YSZ上的OH与吸附在Ni上的C结合成为吸附在Ni上的COH，消除积碳的催化反应方程如下：
阳极支撑层：
H 2O(YSZ)＝OH(YSZ)+H(YSZ)
C(Ni)+OH(YSZ)＝COH(Ni)
COH(Ni)＝CO(Ni)+H(Ni)
CO(Ni)+OH(YSZ)＝COOH(Ni)+YSZ
COOH(Ni)+OH(YSZ)＝CO 2+H 2O
总反应式：C(Ni)+3H 2O(YSZ)＝CO 2+H 2O+2H 2
阳极功能层的抗积碳催化反应含有从电解质不断迁移到阳极功能层的氧离子参与，所以其氧化碳的反应有一些不同于上面支撑层的反应机理。主要的不同是在于吸附在Ni上的CO和H会在Ni上进行迁移到阳极功能层的三相线(tpb)上与从电解质扩散过来的氧离子反应。消除积碳的催化反应的方程如下：
H 2O(YSZ)＝OH(YSZ)+H(YSZ)
C(Ni)+OH(YSZ)＝COH(Ni)
COH(Ni)＝CO(Ni)+H(Ni)
CO(Ni)→CO(tpb)；H(Ni)→H(tpb)
CO(tpb)+O 2-＝CO 2+2e；2H(tpb)+O 2-＝H 2O+4e
总反应式：C(Ni)+H 2O(YSZ)+2O 2-＝CO 2+H 2O+4e
本发明相关实施例也进一步验证了SOFC单电池的抗积碳性能，在实验中，阳极(包括阳极支撑层和阳极功能层)大颗粒的Ni上没有观测到有任何积碳的现象，实验证明了整个阳极的碳氢燃料的裂解反应基本上都在YSZ晶粒上还原析出的纳米Ni晶粒上，然而并没有积碳。
本发明所提供的SOFC阳极材料及其制备获得的SOFC单电池，其阳极具有良好的抗积碳性，且阳极材料整体上具有廉价、催化性能好、电子导电性好、与YSZ的化学相容性好等优点，电池性能的长期稳定性好，电池的制备方法也易于实现产业化。
以下通过特定的具体实例说明本发明的实施方式，本领域技术人员可由本说明书所揭露的内容轻易地了解本发明的其他优点与功效。本发明还可以通过另外不同的具体实施方式加以实施或应用，本说明书中的各项细节也可以基于不同观点与应用，在没有背离本发明的精神下进行各种修饰或改变。
须知，下列实施例中未具体注明的工艺设备或装置均采用本领域内的常规设备或装置。
此外应理解，本发明中提到的一个或多个方法步骤并不排斥在所述组合步骤前后还可以存在其他方法步骤或在这些明确提到的步骤之间还可以插入其他方法步骤，除非另有说明；还应理解，本发明中提到的一个或多个设备/装置之间的组合连接关系并不排斥在所述组合设备/装置前后还可以存在其他设备/装置或在这些明确提到的两个设备/装置之间还可以插入其他设备/装置，除非另有说明。而且，除非另有说明，各方法步骤的编号仅为鉴别各方法步骤的便利工具，而非为限制各方法步骤的排列次序或限定本发明可实施的范围，其相对关系的改变或调整，在无实质变更技术内容的情况下，当亦视为本发明可实施的范畴。
实施例1
阳极支撑层选用微晶尺寸约为10nm的NiO(INCO公司，A级)粉体和D 50为0.53μm的5YSZ(九江泛美亚，YSZ-F-DM-5.0)粉体，按照NiO:5YSZ＝60:40(质量比)混合。采用直径为0.6～0.8mm的氧化锆球，以无水乙醇为介质进行球磨(粉:球:乙醇:分散剂＝1:1.8:0.6:0.04，质量比)，分散剂为三乙醇胺。在行星球磨机400rpm下球磨4h。球磨后的粉体在80℃下干燥后再在800℃下煅烧2h。经煅烧后的粉体在行星球磨机400rpm下球磨2h，球磨后的粉体在80℃下干燥。该加工好的粉体备用，图10为5YSZ/NiO粉体球磨后煅烧再球磨(球磨煅烧再球磨)的粒度分布曲线，由图10可知，经过加工处理后的阳极支撑层粉体粒度分布范围变窄，粒度分布为0.1～1.1μm，分布为双峰分布，D 50＝0.190μm，与原始尺寸相比明显减少和粒度分布变窄，该粉体的粒度大小和分布范围更适合制备SOFC的阳极以及流延制备工艺。图12为5YSZ颗粒表面析出Ni纳米颗粒(HAADF，高角环形暗场像)以及EDS(元素mapping)示意图，该粉体为上述经过经过混合、球磨然后煅烧再球磨处理制备获得的阳极支撑层粉体，在900℃，氢气氛下还原4h。元素mapping图为Ni、Zr、O、Y、Ni+Zr和Ni+Zr+O+Y六个mapping图。由该图可进一步证明，在亚微米级的5YSZ粉体颗粒上较多地析出了纳米金属Ni颗粒。
功能层阳极选用微晶尺寸约为10nm的NiO(INCO公司，A级)粉体和D 50为90nm的8YSZ(Tosoh公司，TZ-8YS)粉体，按照NiO:8YSZ＝65:35(质量比)混合。粉体处理工艺与 支撑阳极粉体相同。该加工好的粉体备用。
将上述加工好的阳极支撑层粉体和阳极功能层粉体采用流延成型的方法成型，同时将YSZ电解质坯片流延好(电解质/功能阳极坯片采用双层流延法制备)，在100℃，15MPa下热压叠层15min三层热压在一起获得阳极支撑的电解质薄膜的坯片(从上到下：电解质层+阳极功能层+阳极支撑层)，切割一定的尺寸后进行烧结(1400℃保温3h)获得半电池。该半电池进一步印刷阴极浆料(LSM/8YSZ，锰酸镧锶和8YSZ的混合物，质量比LSM:8YSZ＝6:4)，然后在1100～1200℃下焙烧阴极获得全电池，阴极厚度为20μm，为多孔结构，孔隙率为33vol.％。电池制备结束后，进行电池的电化学性能测试和稳定性测试。该电池的具体结构与性能如下：
电池结构：
如图2所示为SOFC全电池(还原后)微观结构SEM图，包括阴极、电解质和阳极，其中阳极包括阳极功能层和阳极支撑层。电解质是致密的烧薄层，厚度为10μm，阴极为多孔结构，阴极厚度为20μm；阳极为空洞细小的阳极功能层和空洞较大的阳极支撑层构成，其中功能层的厚度为23μm，支撑层的厚度为450μm。
如图3所示为电池阳极支撑层还原前的微观结构图。其中，图a是阳极支撑层低倍数的全貌图，由图可见：阳极为多孔结构，主要孔洞的大小为5μm左右，未见有小的纳米晶在晶粒表面析出；图b和图c是阳极孔洞的局部放大图，可见孔洞内部也未见晶粒表面有纳米晶析出。
如图4所示为电池阳极支撑层还原并放电后(放电条件：单电池在750℃，H 2+H 2O为燃料，空气为氧化剂，电压＝0.7V，下放电4h)的微观结构图。图a是阳极支撑层低倍数的全貌图，由图可见：阳极为多孔结构，主要孔洞的大小为5μm左右，可见有小的纳米晶在晶粒表面析出；图b和图c是局部放大图，可见氧化镍和氧化锆晶粒表面都有较多纳米晶析出。图中外形菱角分明的晶粒为5YSZ晶粒的，外形近圆形的晶粒为金属Ni晶粒。在5YSZ晶粒上析出的纳米晶粒比较明显；在金属Ni晶粒上析出的纳米晶粒不十分明显，析出的纳米晶粒要更小。图中有些表面没有任何析出，该表面是新断裂的表面。
如图5所示为电池阳极功能层还原(放电)前后的微观结构图。图a是电池还原(放电)前阳极功能层低倍数的全貌图，由图可见：阳极功能层为多孔结构，主要孔洞的大小为1.8μm左右，功能层与电解质紧密结合。功能层未见有小的纳米晶在晶粒表面析出；图b和图c是电池还原和放电后阳极功能层的局部放大图，可见氧化镍和氧化锆晶粒表面都有较多 纳米晶析出。图中外形菱角分明的晶粒为8YSZ晶粒的，外形近圆形的晶粒为金属Ni晶粒。在8YSZ晶粒上析出的纳米晶粒比较明显；在金属Ni晶粒上析出的纳米晶粒不十分明显，析出的纳米晶粒要更小。图中有些表面没有任何析出，该表面是新断裂的表面。
电池性能：
将实施例1制备获得的电池进一步进行性能测试，图6为电池的电化学性能，从图中可知750℃下以H 2为燃料(流量30ml/min)，空气为氧化气体(静态)，电池的最高功率密度为0.52W/cm 2，开路电压为1.05V，欧姆阻抗和两极阻抗分别为0.14Ω·cm 2、0.87Ω·cm 2；750℃下以CH 4+3％H 2O为燃料(甲烷流量为30ml/min)，空气为氧化气体(静态)，电池的最高功率密度为0.42W/cm 2，开路电压为1.10V，欧姆阻抗和两极阻抗分别为0.14Ω·cm 2、2.84Ω·cm 2。
图7为单电池以湿甲烷为燃料(甲烷流量为30ml/min)，空气为氧化剂(静态)，0.40A/cm 2的电流密度下放电曲线。单电池在H 2+H 2O为燃料时以0.4A/cm 2放电5h后，以CH 4+H 2O为燃料工作运行(甲烷从水中通过，甲烷从水中通过后一般带水3wt.％)。图7中单电池运行约8h后，关闭通风设备，电压有一上扬(可能是因为空气中氧浓度微增)，运行60h后，CH 4不再从水中通过，运行80h，燃料为干CH 4，甲烷浓度增加造成电压有一上扬。由图可知：该电池开始时使用湿甲烷(后期可使用干甲烷)，电池不积碳，可长期稳定输出。
图8为以湿乙醇为燃料(以N 2气通过乙醇液体，N 2的流量为30ml/min，将乙醇分子带入阳极中，其中N 2含量为92vol％，乙醇含量为8vol％)，空气为氧化剂(静态)，电池的电化学性能。单电池阳极在H 2+H 2O气氛、阴极在空气气氛、750℃下放电4h后(电放电压为0.7V)，在750℃下以N 2+乙醇为燃料，空气为氧化剂运行。单电池的开路电压为1.0V，最大功率密度为0.36W/cm 2，总阻抗为1.48Ω·cm 2，其中欧姆阻抗为0.37Ω·cm 2，极化阻抗为1.11Ω·cm 2。
图9为以乙醇为燃料单电池在不同放电电流下的运行曲线单电池在750℃下以N 2+乙醇为燃料，空气为氧化剂运行。单电池的最大功率密度为0.36W/cm 2，在不同电流密度下放电，单电池经过40h运行后基本没有衰减。
综上所述，本发明有效克服了现有技术中的种种缺点而具高度产业利用价值。
上述实施例仅例示性说明本发明的原理及其功效，而非用于限制本发明。任何熟悉此技术的人士皆可在不违背本发明的精神及范畴下，对上述实施例进行修饰或改变。因此，举凡所属技术领域中具有通常知识者在未脱离本发明所揭示的精神与技术思想下所完成的一切等 效修饰或改变，仍应由本发明的权利要求所涵盖。

Claims (10)

  1. 一种SOFC阳极材料的制备方法，包括：
    (1)提供NiO和YSZ的混合粉料；
    (2)将步骤(1)所提供的混合粉体进行两相相互固溶处理，
    (3)将步骤(2)固溶处理所得产物进行粒径调整。
  2. 如权利要求1所述的制备方法，其特征在于，所述步骤(1)中，提供NiO和YSZ的混合粉料的具体方法为：将NiO和YSZ粉碎、混合；
    和/或，所述步骤(1)中，NiO和YSZ的重量比为1～1.8:1；
    和/或，所述步骤(1)中，当SOFC阳极材料为阳极支撑材料时，YSZ粉体为3～8mol％Y 2O 3掺杂的氧化锆，NiO原料的微晶尺寸为5～20nm，YSZ原料的粒径为D50＝0.2～1.0μm；
    和/或，所述步骤(1)中，当SOFC阳极材料为阳极功能层材料时，YSZ粉体为7～9mol％Y 2O 3掺杂的氧化锆，NiO原料的微晶尺寸为5～20nm，YSZ原料的粒径为D50＝50～100nm；
    和/或，所述步骤(1)中，混合粉体中，YSZ颗粒的粒径为50～1000nm，NiO粉体的微晶尺寸为10～20nm。
  3. 如权利要求2所述的制备方法，其特征在于，所述步骤(1)中，通过球磨将NiO和YSZ粉碎、混合，所述球磨优选为湿法球磨，球磨所得粉体还进行干燥，干燥温度可以为60～80℃；
    和/或，所述步骤(1)中，在分散剂存在的条件下进行粉碎、混合，所述分散剂优选选自三乙醇胺、柠檬酸、聚乙二醇、乙酰丙酮、聚乙烯吡咯烷酮、聚丙烯酸中的一种或多种的组合，粉体与分散剂的重量比为1:0.005～0.1，优选的为1:0.02～0.05；
    和/或，所述步骤(1)中，在溶剂存在的条件下进行粉碎、混合，所述溶剂优选选自无水乙醇、丙酮、丁酮、异丙醇、二甲基甲酰胺中的一种或多种的组合，粉体与溶剂的重量比为1:0.2～1.5，优选的为1:0.4～0.8。
  4. 如权利要求1所述的制备方法，其特征在于，所述步骤2)中，将步骤(1)所提供的混合粉体进行两相相互固溶处理的具体方法为：将步骤(1)所提供的混合粉体干燥、煅烧；
    和/或，所述步骤(2)中，所述煅烧温度为600～1200℃，优选的为800～950℃；
    和/或，所述步骤(2)中，煅烧时间为为1～10，优选的2～8小时。
  5. 如权利要求1所述的制备方法，其特征在于，所述步骤(3)中，将步骤(2)固溶处理所得产物进行粒径调整的具体方法为：将步骤(2)所提供的煅烧产物粉碎、干燥，优选的，通过球磨将煅烧产物粉碎。
  6. 一种SOFC阳极材料，由权利要求1～5任一权利要求所述的制备方法制备获得。
  7. 一种SOFC单电池，包括阳极材料层、电解质坯片和阴极材料层，所述阳极材料层由权利要求6所述的SOFC阳极材料制备获得。
  8. 如权利要求7所述的单电池，其特征在于，所述阳极材料层包括阳极支撑层和/或阳极功能层，所述阳极支撑层和/或阳极功能层由权利要求6所述的SOFC阳极材料制备获得。
  9. 如权利要求8所述的单电池，其特征在于，阳极支撑层的厚度为300～700μm，优选为400～500μm，孔洞大小为3～10μm，阳极支撑层还原后其孔隙率为25～40vol.％，优选为30～35vol.％；阳极功能层的厚度为5～30μm，优选为5～10μm，孔洞大小为1～5μm，阳极功能层还原后其孔隙率为25～40vol.％，优选为30～35vol.％；
    和/或，所述电解质坯片选自YSZ电解质坯片，所述电解质坯片的厚度为2～10μm；
    和/或，所述阴极材料层选自LSM和YSZ的组合或者LSM和SSZ的组合，两者的重量比例为5～7:5～3、LSCF和GDC的组合，两者重量比为5～7:5～3；
    和/或，所述阴极材料层的厚度为20～40μm，优选的为20～25μm，所述阴极材料层为多孔结构，孔隙率为25～40vol.％，优选的为30～35vol.％。
  10. 一种阳极还原的SOFC单电池，由权利要求7～9任一权利要求所述的SOFC单电池经还原处理和/或放电处理后获得。
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