EP1782490A2 - Cathode side hardware for carbonate fuel cells - Google Patents

Cathode side hardware for carbonate fuel cells

Info

Publication number
EP1782490A2
EP1782490A2 EP05757500A EP05757500A EP1782490A2 EP 1782490 A2 EP1782490 A2 EP 1782490A2 EP 05757500 A EP05757500 A EP 05757500A EP 05757500 A EP05757500 A EP 05757500A EP 1782490 A2 EP1782490 A2 EP 1782490A2
Authority
EP
European Patent Office
Prior art keywords
fuel cell
accordance
carbonate fuel
coating
cathode
Prior art date
Legal status (The legal status 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 status listed.)
Withdrawn
Application number
EP05757500A
Other languages
German (de)
French (fr)
Other versions
EP1782490A4 (en
Inventor
Gengfu Xu
Chao-Yi Yuh
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Fuelcell Energy Inc
Original Assignee
Fuelcell Energy Inc
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
Priority claimed from US10/867,975 external-priority patent/US7914946B2/en
Application filed by Fuelcell Energy Inc filed Critical Fuelcell Energy Inc
Publication of EP1782490A2 publication Critical patent/EP1782490A2/en
Publication of EP1782490A4 publication Critical patent/EP1782490A4/en
Withdrawn legal-status Critical Current

Links

Classifications

    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M8/00—Fuel cells; Manufacture thereof
    • H01M8/02—Details
    • H01M8/0202—Collectors; Separators, e.g. bipolar separators; Interconnectors
    • H01M8/0204—Non-porous and characterised by the material
    • H01M8/0215—Glass; Ceramic materials
    • H01M8/0217—Complex oxides, optionally doped, of the type AMO3, A being an alkaline earth metal or rare earth metal and M being a metal, e.g. perovskites
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/86—Inert electrodes with catalytic activity, e.g. for fuel cells
    • H01M4/88—Processes of manufacture
    • 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
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M8/00—Fuel cells; Manufacture thereof
    • H01M8/02—Details
    • H01M8/0202—Collectors; Separators, e.g. bipolar separators; Interconnectors
    • H01M8/0204—Non-porous and characterised by the material
    • H01M8/0206—Metals or alloys
    • H01M8/0208—Alloys
    • H01M8/021—Alloys based on iron
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M8/00—Fuel cells; Manufacture thereof
    • H01M8/02—Details
    • H01M8/0202—Collectors; Separators, e.g. bipolar separators; Interconnectors
    • H01M8/0204—Non-porous and characterised by the material
    • H01M8/0223—Composites
    • H01M8/0228—Composites in the form of layered or coated products
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M8/00—Fuel cells; Manufacture thereof
    • H01M8/02—Details
    • H01M8/0202—Collectors; Separators, e.g. bipolar separators; Interconnectors
    • H01M8/0247—Collectors; Separators, e.g. bipolar separators; Interconnectors characterised by the form
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M8/00—Fuel cells; Manufacture thereof
    • H01M8/02—Details
    • H01M8/0202—Collectors; Separators, e.g. bipolar separators; Interconnectors
    • H01M8/0247—Collectors; Separators, e.g. bipolar separators; Interconnectors characterised by the form
    • H01M8/0254—Collectors; Separators, e.g. bipolar separators; Interconnectors characterised by the form corrugated or undulated
    • 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
    • H01M8/14—Fuel cells with fused 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
    • H01M8/14—Fuel cells with fused electrolytes
    • H01M8/141—Fuel cells with fused electrolytes the anode and the cathode being gas-permeable electrodes or electrode layers
    • H01M8/142—Fuel cells with fused electrolytes the anode and the cathode being gas-permeable electrodes or electrode layers with matrix-supported or semi-solid matrix-reinforced electrolyte
    • 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

  • cathode side hardware is defined as the current collector and/or the bipolar plate on the cathode side of a fuel cell and, in particular, a molten carbonate fuel cell. Corrosion is a life-limiting factor for molten carbonate fuel cells. The prevailing corrosion is at the oxide-gas (or liquid) interface, i.e., at the cathode side hardware.
  • This hardware is typically formed from chromium containing stainless steel and corrosion of the hardware is governed by the outward cation diffusion via metal vacancies. It is estimated that twenty five percent (25%) of the internal resistance of a molten carbonate fuel cell could be attributed to the oxide corrosion layer that forms on the cathode side hardware. More particularly, the cathode current collector, generally made of 316L stainless steel, becomes corroded during fuel cell operation and multi-corrosion oxide layers having a relatively high electrical resistance are formed on the surface of the collector. Moreover, the formed corrosion layers usually thicken with time. Additionally, the corrosion layers on the cathode side hardware cause electrolyte loss through surface and corrosion creepage.
  • Electrolyte surface creepage is controlled by capillary forces dominated by the surface roughness, porosity and pore size in corrosion layers. Electrolyte corrosion creepage is controlled by scale thickness and phase composition of the formed scale. In cathode side hardware formed with stainless steel, a high roughness of the scale surface and the porous structure of the scale cause high electrolyte surface creepage. It has been estimated that electrolyte loss in a molten carbonate fuel cell is a significant life-limiting factor for achieving a lifetime of 40,000 hours. Analysis of cathode side hardware has indicated that sixty five percent (65%) of electrolyte loss is attributed to this hardware.
  • US Patent 5,643,690 discloses a coating of this type in the form of a non- stoichiometric composite oxide layer (Ni ferrite based oxide) formed by in cell oxidation of a layer of Fe, Ni and Cr clad on cathode current collector.
  • a non- stoichiometric composite oxide layer Ni ferrite based oxide
  • Japanese patent 5-324460 discloses a stainless steel collector plate covered with a NiO layer (formed by oxidation of a Ni layer plated or clad on a cathode current collector).
  • the coatings formed in these cases are porous and consume a significant amount of electrolyte. Also, the electrical conductivity of the layers may not be as high as desired.
  • US 2002/0164522 assigned to the same assignee hereof, discloses another coating layer which is formed as a conductive layer of ceramic material using a sol-gel process.
  • the materials used for the conductive layer in this case are, preferably, LiCoO 2 or Co doped LiFeO 2 , and the thickness of the layer is between 1 to 5 ⁇ m.
  • the aforesaid conductive ceramic layers of the 2002/0164522 publication have proven satisfactory in providing corrosion resistance of the cathode side hardware. However, the materials are costly and add to the overall expense of the fuel cell. Moreover, higher conductivities are still desired. Fuel cell designers have thus continued to search for other coating materials which offer the desired corrosion resistance, but are more cost effective and are higher in conductivity. It is therefore an object of the present invention to provide cathode side hardware which does not suffer from the above disadvantages; and It is a further object of the present invention to provide cathode side hardware having a high corrosion resistance and electrical conductivity and a lower cost.
  • the above and other objects are realized in cathode side hardware by forming the hardware to have a thin film of a dense conductive ceramic coating comprised of Perovskite AMeO 3 , wherein A is at least one of lanthanum and a combination of lanthanum and strontium and Me is one or more of transition metals, lithiated NiO (Li x NiO, where x is 0.1 to 1) and X-doped LiNiO 2 , wherein X is one of Mg, Ca and Co.
  • the coating is realized using a sol-gel process.
  • FIG. 1 schematically illustrates a fuel cell including cathode side hardware in accordance with the principles of the present invention
  • FIGS. 2A and 2B show SEM micrographs of different magnifications of a conductive lithiated NiO coating of cathode side hardware in accordance with the principles of the present invention
  • FIG. 3 shows an SEM micrograph of a conductive LSC coating of cathode side hardware in accordance with the principles of the present invention
  • FIG. 4 shows the phase evolution with heat treatment temperature of a lithiated NiO coating of the type shown in FIGS.
  • FIGS. 5A-5D illustrate the effect of immersion corrosion testing both on cathode side hardware coated with a lithiated NiO conductive coating in accordance with the invention and on uncoated cathode side hardware
  • FIGS. 6 A and 6B show the out-of-cell electrical resistivity and the out-of-cell metal-to-metal electrical resistivity, respectively, of uncoated cathode side hardware and cathode side hardware coated with a lithiated NiO coating and an LSC coating in accordance with the invention
  • FIG. 7 and 8 show the resistance lifegraphs of molten carbonate fuel cells having cathode side hardware with the lithiated NiO and LSC conductive ceramic coatings of the invention and fuel cells with uncoated cathode side hardware;
  • FIG. 9 shows the corrosion thickness after fuel cell testing of cathode side hardware using the conductive ceramic coating of the invention as compared to the corrosion thickness after fuel cell use of uncoated cathode side hardware;
  • FIG. 10 illustrates the electrolyte loss in a molten carbonate fuel cell using cathode side hardware having the conductive ceramic coating of the invention as compared to the electrolyte loss in a molten carbonate fuel cell using uncoated cathode side hardware;
  • FIG. 9 shows the corrosion thickness after fuel cell testing of cathode side hardware using the conductive ceramic coating of the invention as compared to the corrosion thickness after fuel cell use of uncoated cathode side hardware;
  • FIG. 10 illustrates the electrolyte loss in a molten carbonate fuel cell
  • FIG. 11 shows an SEM micrograph of a conductive LSCF coating of cathode side hardware in accordance with the principles of the present invention
  • FIG. 12 shows an SEM micrograph of a conductive Mg-doped LiNiO 2 coating of cathode side hardware in accordance with the principles of the present invention
  • FIG. 13 shows an SEM micrograph of a conductive Co-doped LiNiO 2 coating ' of cathode side hardware in accordance with the principles of the present invention.
  • FIG. 1 schematically shows a fuel having a cathode 2 and an anode 3. Between the cathode 2 and the anode 3 is a matrix 4 containing an alkali carbonate electrolyte. Adjacent the anode 3 is a corrugated current collector 3a and a bipolar plate 3b. Adjacent the cathode 2 is the cathode side hardware 5 comprising a corrugated current collector 5 a and a bipolar plate 5b. As shown, the bipolar plates 3b and 5b are the same. In accordance with the principles of the present, cathode side hardware 5 of the fuel cell 1 of FIG. 1 is coated with a conductive ceramic to obtain lower electrical resistivity for lower contact voltage loss.
  • Perovskite materials having a general formula AMeO 3 where A is at least one of lanthanum and a combination of lanthanum and strontium and Me is a transition metal
  • lithiated NiO Li x NiO, where x is 0.1 to 1
  • X-doped LiNiO 2 materials, where X is one of Mg, Co and Ca can be utilized as coating materials for the cathode side hardware.
  • Transition metals indicated as "Me" in AMeO 3 include, but are not limited to, Co, Fe, Cr, Mn, and mixtures thereof.
  • Perovskite materials include, but are not limited to, LSC (La x Sr 1-x CoO 3 and, specifically La C sSr 0 ⁇ CoO 3 ), LaMnO 3 , LaCoO 3 , LaCrO 3 and LSCF (Lao.gCr 0 .2Coo.8Feo. 2 0 3 ).
  • X-doped LiNiO 2 materials include Mg-doped LiNiO 2 , Ca-doped LiNiO 2 and Co-doped LiNiO 2 . These materials have a low solubility in alkali molten carbonate (e.
  • the sol is then coated on the hardware surface by a spray or dipping process, subsequently gelled, and dried, followed by densification and crystallization. Drying is generally performed between room temperature and 200°C.
  • the densification and recrystallization processes are usually carried out at temperatures above 35O 0 C.
  • the surface of the metal substrate may require degreasing and pickling to remove surface debris and oxide for better coating adhesion. Although 100% of coating coverage is not necessary for carbonate fuel cell application in terms of ohmic contact resistance, it is desirable to have >95% coverage of the surface by the ceramic coating to achieve the desired benefits of increased corrosion protection and reduced electrolyte loss.
  • the resultant cathode side hardware can thus be provided with the required structure and phase assemblage to provide the desired properties.
  • the precursors for the Perovskite materials, lithiated NiO (Li x NiO, where x is 0.1 to 1) and X-doped LiNiO 2 materials can be acetates or inorganic salts like nitrate or hydroxide.
  • the solutions can be aqueous based or solvent based.
  • the body or substrate member of the cathode side hardware can be stainless steel.
  • the dense oxide coating significantly delays mobile carbonate ion attack of the underlying body (e.g., stainless steel body) of the hardware.
  • the main effect of the formed oxide layer is to barrier gas, vapor and liquid contact with the hardware body.
  • the corrosion resistant oxide layer being highly conductive, the contact resistance between the hardware body and the cathode electrode is also reduced as compared with corrosion scale formed on hardware which is uncoated. In comparison to an uncoated hardware body formed of chromium steel, the electrical resistance is lowered 50% as exhibited in out of cell testing.
  • lithiated NiO and X-doped LiNiO 2 coatings of the cathode side hardware of the invention surface roughness and corrosion are both minimized. Accordingly, electrolyte surface and corrosion creepage are also minimized.
  • the coatings of the cathode side hardware have also been found to exhibit favorable adhesion, well matched thermal expansion coefficients, effective electronic conductivity, and protection against hot oxidation/corrosion. Accelerated thermal cyclic testing of the coatings have indicated that the coatings are thin and are very adhesive. Good adhesion is attributed to reaction-bonded structure between the coating and the body of the hardware and also its thin film character (tensile stress is proportional to coating thickness).
  • the coatings of the invention (Lio . iNiO, Perovskite materials and X-doped LiNiO 2 ) also exhibit a much higher conductivity (e.g. 33 S/cm for LiojNiO, 650 S/cm for LSC, and 26 S/cm for Mg-doped LiNiO 2 and 15 S/cm of Co- doped LiNiO 2 at 65O 0 C) and more importantly, are dense and smooth with a controlled coating thickness, as compared with the LiCoO 2 coating (conductivity of lS/cm) of the 2002/0164522 publication.
  • the following are examples of the invention. EXAMPLE I - Lithiated NiO Cathode Side Hardware
  • Lithiated NiO Sol-Gel A starting solution with a nominal Li:Ni composition of 0.1 : 1 (molar ratio) was prepared using reagent grade Li acetate and Ni acetate as cation source compounds. Appropriate quantities of these materials to be included in the starting solution were then calculated on the basis of obtaining 1 M NiO sol-gel. Measured amounts of the cation source compounds were then mixed with 200 ml distilled water, 300 ml ethylene glycol and 1.5 mol citric acid in a 600 ml beaker to form a precipitate-free starting solution. The starting solution was heated on a hot plate at about 80 0 C to concentrate until it turned to a viscous liquid. A green, transparent solution resulted.
  • the solution was allowed to stand at 25 0 C in a sealed glass beaker for at least half a year without precipitation.
  • the change in the viscosity of the solution due to polymerization was measured at room temperature by means of a Brookfield viscometer.
  • the viscosity of the precursor increases significantly with increased heating time due to the increase in average molecular weight as a result of polymerization.
  • precursors with viscosity below 125 cp at room temperature could not homogeneously wet a smooth substrate, such as stainless steel.
  • highly viscous precursors having a viscosity above about 1000 cP at room temperature resulted in inhomogeneous films and crack formation unless the substrate was heated at higher temperatures. Therefore, it is important to control the viscosity of the solution to obtain high quality films.
  • the viscosity of the precursor solutions used in this Example ranged between 200 and 275 cP at room temperature.
  • FIGS. 2A and 2B show SEM photographs of a fractured cross section of the film coated hardware at different magnifications. From these figures, it can be seen that a thin lithiated Ni oxide film of substantially uniform thickness ⁇ 1 micron, was realized.
  • I l comprising a polymer containing the metal cations. It is important that the cations remain in solution throughout the polymerization process. The change in the viscosity of the solution as it was converted into the polymeric precursor was measured at room temperature by means of a Brookfield viscometer.
  • (2) Deposition and Formation of Cathode Side Hardware With Smooth, Dense LSC Films To increase sol wetting and increase bond strength between the LSC film and the stainless steel (316L) cathode side hardware, the stainless steel was acid treated first, followed by acetone washed ultrasonically to remove any possible dust and carbon film formed during heat treatment in graphite furnace.
  • FIG. 3 shows a SEM photograph of the surface morphology of the LSC coated cathode side hardware. The effect of thermal cycling on the integrity of the lithiated NiO and LSC coated cathode side hardware sheets was also evaluated.
  • FIGS. 5A-5D The cross sectional SEM observations for a representative example of cathode side hardware coated with lithiated NiO in accord with the invention as compared with uncoated cathode side hardware is shown in FIGS. 5A-5D.
  • the lithiated NiO coating of the invention (FIGS. 5 A and 5B), had significantly reduced the thickness of the corrosion scale, as compared to the uncoated hardware (FIGS. 5C and 5D). More particularly, the corrosion scales show a similar dual-layered structure whether or not sol-gel coated.
  • FIG. 6 A shows the out-of-cell electrical resistivity of cathode side hardware in the form of a cathode current collector ("CCC") having the lithiated NiO and LSC coatings of the invention. It also shows the out-of-cell electrical resistivity of a non- coated stainless steel current collector. As can be seen, the coated CCCs of the invention have comparable resistivities to the non-coated CCC.
  • CCC cathode current collector
  • FIGS. 7 and 8 show the resistance lifegraphs of a fuel cells utilizing CCCs coated with the lithiated NiO and LSC coatings of the invention, respectively, as compared to fuel cells utilizing uncoated stainless steel CCCs. As can be appreciated from these graphs, an improved resistance life is realized for the fuel cells using the CCCs with the coatings of the invention.
  • FIG. 9 shows the corrosion thickness after fuel cell testing of CCCs coated with coatings of the invention as compared to the corrosion thickness after fuel cell testing of uncoated CCCs.
  • the coated CCCs of the invention are seen to exhibit measurably less corrosion than the uncoated CCCs.
  • FIG. 10 illustrates the electrolyte loss in a molten carbonate fuel cell using CCCs coated with the coatings of the invention as compared to the electrolyte loss in a molten carbonate fuel cell with uncoated CCCs. As can be seen, the electrolyte loss is considerably less in the fuel cell using the coatings of the invention.
  • Measured quantities of the cation source compounds were then mixed with distilled water (150 ml) and ethylene glycol (350 ml) in a 1,000 ml beaker to form a starting solution.
  • the starting solution was then heated on a hot plate to about 65 0 C and stirred at 65 0 C for about 48 hours to expel water and other volatile matter and to form a viscous polymer containing the metal cations. It is important that the solution is not overheated during the formation of the viscous polymer since this formation is an exothermic process. After the heating of the solution was turned off, the change in the viscosity of the solution as it was converted into the polymeric precursor was measured using a Brookfield viscometer.
  • FIG. 11 shows an SEM photograph of the surface morphology of the LSCF coated cathode side hardware. Similar to LSC coated cathode side hardware shown in FIG. 3, the SEM shown in FIG. 11 reveals that the LSCF coating is thermally compatible with the hardware body or substrate, and that no thermal stress induced cracks were detected.
  • Mg acetate, Li acetate and hydrated Ni acetate were then mixed with distilled water (400 ml) and citric acid (2 mol) in a 1,000 ml beaker while heating the solution to about 80°C and stirring it using a magnetic agitator to form a clear precipitate-free starting solution.
  • the starting solution was then heated on a hot plate at 80°C until a green transparent viscous solution was formed. After the solution reached a desired concentration, the heating was turned off and the viscosity of the solution was measured. The change in viscosity of the solution as it was converted into the viscous solution was measured at room temperature by means of a Brookfield viscometer.
  • Measured quantities of the cation source compounds were then mixed with distilled water (400 ml) and citric acid (2 mol) in a 1,000 ml beaker, while heating the solution to about 80°C and stirring it using a magnetic agitator to form a clear precipitate-free starting solution.
  • the starting solution was heated at about 80°C to expel the water and other volatile matter and to form a green, transparent viscous solution.
  • the change in viscosity of the solution as it was converted into the viscous solution was measured at room temperature by means of a Brookfield viscometer. As in the previous example, the viscosity of the solution increased significantly with increased heating time due to the increase in the average molecular weight as a result of polymerization.

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Abstract

Carbonate fuel cathode side hardware having a thin coating of a conductive ceramic formed from one of Perovskite AMeO3, wherein A is at least one of lanthanum and a combination of lanthanum and strontium and Me is one or more of transition metals, lithiated NiO (LixNiO, where x is 0.1 to 1) and X-doped LiMeO2, wherein X is one of Mg, Ca, and Co.

Description

CATHODE SIDE HARDWARE FOR CARBONATE FUEL CELLS Background of the Invention This invention relates to molten carbonate fuel cells and, in particular, to cathode side hardware employed in such cells. As used herein the term "cathode side hardware" is defined as the current collector and/or the bipolar plate on the cathode side of a fuel cell and, in particular, a molten carbonate fuel cell. Corrosion is a life-limiting factor for molten carbonate fuel cells. The prevailing corrosion is at the oxide-gas (or liquid) interface, i.e., at the cathode side hardware. This hardware is typically formed from chromium containing stainless steel and corrosion of the hardware is governed by the outward cation diffusion via metal vacancies. It is estimated that twenty five percent (25%) of the internal resistance of a molten carbonate fuel cell could be attributed to the oxide corrosion layer that forms on the cathode side hardware. More particularly, the cathode current collector, generally made of 316L stainless steel, becomes corroded during fuel cell operation and multi-corrosion oxide layers having a relatively high electrical resistance are formed on the surface of the collector. Moreover, the formed corrosion layers usually thicken with time. Additionally, the corrosion layers on the cathode side hardware cause electrolyte loss through surface and corrosion creepage. Electrolyte surface creepage is controlled by capillary forces dominated by the surface roughness, porosity and pore size in corrosion layers. Electrolyte corrosion creepage is controlled by scale thickness and phase composition of the formed scale. In cathode side hardware formed with stainless steel, a high roughness of the scale surface and the porous structure of the scale cause high electrolyte surface creepage. It has been estimated that electrolyte loss in a molten carbonate fuel cell is a significant life-limiting factor for achieving a lifetime of 40,000 hours. Analysis of cathode side hardware has indicated that sixty five percent (65%) of electrolyte loss is attributed to this hardware. It is estimated that a forty five percent (45%) reduction in electrolyte loss could result in ~1.7yr life extension of the molten carbonate fuel cell. In order to counter the corrosion of the cathode side hardware, it has been proposed to provide a protective oxide coating on the cathode side hardware to realize a low contact resistance and low electrolyte loss. These coatings, however, must satisfy stringent requirements in that they must, on the one hand, have a high corrosion resistance, and, on the other hand, a high electrical conductivity. The coatings must also be able to provide a stable surface oxide capable of providing a barrier between the coating alloys and the environment of the molten carbonate fuel cell. US Patent 5,643,690 discloses a coating of this type in the form of a non- stoichiometric composite oxide layer (Ni ferrite based oxide) formed by in cell oxidation of a layer of Fe, Ni and Cr clad on cathode current collector. Similarly Japanese patent 5-324460 discloses a stainless steel collector plate covered with a NiO layer (formed by oxidation of a Ni layer plated or clad on a cathode current collector). The coatings formed in these cases are porous and consume a significant amount of electrolyte. Also, the electrical conductivity of the layers may not be as high as desired. US Patent Application Publication No. US 2002/0164522, assigned to the same assignee hereof, discloses another coating layer which is formed as a conductive layer of ceramic material using a sol-gel process. The materials used for the conductive layer in this case are, preferably, LiCoO2 or Co doped LiFeO2, and the thickness of the layer is between 1 to 5 μm. The aforesaid conductive ceramic layers of the 2002/0164522 publication have proven satisfactory in providing corrosion resistance of the cathode side hardware. However, the materials are costly and add to the overall expense of the fuel cell. Moreover, higher conductivities are still desired. Fuel cell designers have thus continued to search for other coating materials which offer the desired corrosion resistance, but are more cost effective and are higher in conductivity. It is therefore an object of the present invention to provide cathode side hardware which does not suffer from the above disadvantages; and It is a further object of the present invention to provide cathode side hardware having a high corrosion resistance and electrical conductivity and a lower cost.
SUMMARY OF THE INVENTION The above and other objects are realized in cathode side hardware by forming the hardware to have a thin film of a dense conductive ceramic coating comprised of Perovskite AMeO3, wherein A is at least one of lanthanum and a combination of lanthanum and strontium and Me is one or more of transition metals, lithiated NiO (LixNiO, where x is 0.1 to 1) and X-doped LiNiO2, wherein X is one of Mg, Ca and Co. Preferably, the coating is realized using a sol-gel process. BRIEF DESCRIPTION OF THE DRAWINGS The above and other features and aspects of the present invention will become more apparent upon reading the following detailed description in conjunction with the accompanying drawings, in which: FIG. 1 schematically illustrates a fuel cell including cathode side hardware in accordance with the principles of the present invention; FIGS. 2A and 2B show SEM micrographs of different magnifications of a conductive lithiated NiO coating of cathode side hardware in accordance with the principles of the present invention; FIG. 3 shows an SEM micrograph of a conductive LSC coating of cathode side hardware in accordance with the principles of the present invention; FIG. 4 shows the phase evolution with heat treatment temperature of a lithiated NiO coating of the type shown in FIGS. 2 A and 2B synthesized by a sol-gel process; FIGS. 5A-5D illustrate the effect of immersion corrosion testing both on cathode side hardware coated with a lithiated NiO conductive coating in accordance with the invention and on uncoated cathode side hardware; FIGS. 6 A and 6B show the out-of-cell electrical resistivity and the out-of-cell metal-to-metal electrical resistivity, respectively, of uncoated cathode side hardware and cathode side hardware coated with a lithiated NiO coating and an LSC coating in accordance with the invention; FIGS. 7 and 8 show the resistance lifegraphs of molten carbonate fuel cells having cathode side hardware with the lithiated NiO and LSC conductive ceramic coatings of the invention and fuel cells with uncoated cathode side hardware; FIG. 9 shows the corrosion thickness after fuel cell testing of cathode side hardware using the conductive ceramic coating of the invention as compared to the corrosion thickness after fuel cell use of uncoated cathode side hardware; FIG. 10 illustrates the electrolyte loss in a molten carbonate fuel cell using cathode side hardware having the conductive ceramic coating of the invention as compared to the electrolyte loss in a molten carbonate fuel cell using uncoated cathode side hardware; FIG. 11 shows an SEM micrograph of a conductive LSCF coating of cathode side hardware in accordance with the principles of the present invention; FIG. 12 shows an SEM micrograph of a conductive Mg-doped LiNiO2 coating of cathode side hardware in accordance with the principles of the present invention; and FIG. 13 shows an SEM micrograph of a conductive Co-doped LiNiO2 coating ' of cathode side hardware in accordance with the principles of the present invention.
DETAILED DESCRIPTION FIG. 1 schematically shows a fuel having a cathode 2 and an anode 3. Between the cathode 2 and the anode 3 is a matrix 4 containing an alkali carbonate electrolyte. Adjacent the anode 3 is a corrugated current collector 3a and a bipolar plate 3b. Adjacent the cathode 2 is the cathode side hardware 5 comprising a corrugated current collector 5 a and a bipolar plate 5b. As shown, the bipolar plates 3b and 5b are the same. In accordance with the principles of the present, cathode side hardware 5 of the fuel cell 1 of FIG. 1 is coated with a conductive ceramic to obtain lower electrical resistivity for lower contact voltage loss. In further accord with the invention, Perovskite materials having a general formula AMeO3, where A is at least one of lanthanum and a combination of lanthanum and strontium and Me is a transition metal, and lithiated NiO (LixNiO, where x is 0.1 to 1), which have previously been proposed for use as cathode materials, are now utilized as coating materials for the cathode side hardware. Also in accord with the invention, X-doped LiNiO2 materials, where X is one of Mg, Co and Ca can be utilized as coating materials for the cathode side hardware. Transition metals indicated as "Me" in AMeO3 include, but are not limited to, Co, Fe, Cr, Mn, and mixtures thereof. Perovskite materials include, but are not limited to, LSC (LaxSr1-xCoO3 and, specifically LaCsSr0^CoO3), LaMnO3, LaCoO3, LaCrO3 and LSCF (Lao.gCr0.2Coo.8Feo.203). Examples of X-doped LiNiO2 materials include Mg-doped LiNiO2, Ca-doped LiNiO2 and Co-doped LiNiO2. These materials have a low solubility in alkali molten carbonate (e. g., 2μg/cm2/h for lithiated NiO) and very high electrical conductivity (600 S/m at 600° C for LSC, 33 S/cm at 6500C for lithiated NiO, 26 S/cm for Mg-doped LiNiO2, and 15 S/cm for Co- doped LiNiO2 at 650°C). These materials can be coated on the cathode side hardware using a variety of coating techniques. In the present illustrative case, a thin film sol-gel coating process has been employed. This process involves the dissolution of precursors containing the required metal ions in a suitable solvent to form the sol. The sol is then coated on the hardware surface by a spray or dipping process, subsequently gelled, and dried, followed by densification and crystallization. Drying is generally performed between room temperature and 200°C. The densification and recrystallization processes are usually carried out at temperatures above 35O0C. The surface of the metal substrate may require degreasing and pickling to remove surface debris and oxide for better coating adhesion. Although 100% of coating coverage is not necessary for carbonate fuel cell application in terms of ohmic contact resistance, it is desirable to have >95% coverage of the surface by the ceramic coating to achieve the desired benefits of increased corrosion protection and reduced electrolyte loss. The resultant cathode side hardware can thus be provided with the required structure and phase assemblage to provide the desired properties. The precursors for the Perovskite materials, lithiated NiO (LixNiO, where x is 0.1 to 1) and X-doped LiNiO2 materials can be acetates or inorganic salts like nitrate or hydroxide. The solutions can be aqueous based or solvent based. The body or substrate member of the cathode side hardware can be stainless steel. By properly controlling processing parameters, the coating technique and heat treatment (sol-gel in this case), a dense, uniform and smooth thin coating can be obtained. The major corrosion resistance of the dense oxide coated cathode side hardware of the invention is governed by transport through the purposefully coated dense oxide layer. The dense oxide coating significantly delays mobile carbonate ion attack of the underlying body (e.g., stainless steel body) of the hardware. In particular, the main effect of the formed oxide layer is to barrier gas, vapor and liquid contact with the hardware body. On the other hand, due to the corrosion resistant oxide layer being highly conductive, the contact resistance between the hardware body and the cathode electrode is also reduced as compared with corrosion scale formed on hardware which is uncoated. In comparison to an uncoated hardware body formed of chromium steel, the electrical resistance is lowered 50% as exhibited in out of cell testing. Moreover, due to the dense and smooth surface of the Perovskite materials, lithiated NiO and X-doped LiNiO2 coatings of the cathode side hardware of the invention, surface roughness and corrosion are both minimized. Accordingly, electrolyte surface and corrosion creepage are also minimized. The coatings of the cathode side hardware have also been found to exhibit favorable adhesion, well matched thermal expansion coefficients, effective electronic conductivity, and protection against hot oxidation/corrosion. Accelerated thermal cyclic testing of the coatings have indicated that the coatings are thin and are very adhesive. Good adhesion is attributed to reaction-bonded structure between the coating and the body of the hardware and also its thin film character (tensile stress is proportional to coating thickness). Matching of bulk properties over the harsh temperature and chemical potential ranges of the fuel cell have also been achieved. As above-noted, the coatings of the invention (Lio.iNiO, Perovskite materials and X-doped LiNiO2) also exhibit a much higher conductivity (e.g. 33 S/cm for LiojNiO, 650 S/cm for LSC, and 26 S/cm for Mg-doped LiNiO2 and 15 S/cm of Co- doped LiNiO2 at 65O0C) and more importantly, are dense and smooth with a controlled coating thickness, as compared with the LiCoO2 coating (conductivity of lS/cm) of the 2002/0164522 publication. The following are examples of the invention. EXAMPLE I - Lithiated NiO Cathode Side Hardware
(1) Preparation of Lithiated NiO Sol-Gel A starting solution with a nominal Li:Ni composition of 0.1 : 1 (molar ratio) was prepared using reagent grade Li acetate and Ni acetate as cation source compounds. Appropriate quantities of these materials to be included in the starting solution were then calculated on the basis of obtaining 1 M NiO sol-gel. Measured amounts of the cation source compounds were then mixed with 200 ml distilled water, 300 ml ethylene glycol and 1.5 mol citric acid in a 600 ml beaker to form a precipitate-free starting solution. The starting solution was heated on a hot plate at about 800C to concentrate until it turned to a viscous liquid. A green, transparent solution resulted. The solution was allowed to stand at 250C in a sealed glass beaker for at least half a year without precipitation. The change in the viscosity of the solution due to polymerization was measured at room temperature by means of a Brookfield viscometer. The viscosity of the precursor increases significantly with increased heating time due to the increase in average molecular weight as a result of polymerization. (2) Deposition and Formation of Cathode Side Hardware With the Dense, Smooth Lithiated NiO Films A dip-coating technique was used to form wet films of the precursor on corrugated stainless steel (316L) sheets or substrates used as the cathode side bodies. The film thickness was established by controlling withdrawal speed and the viscosity of the precursor. In general, precursors with viscosity below 125 cp at room temperature could not homogeneously wet a smooth substrate, such as stainless steel. On the other hand, highly viscous precursors having a viscosity above about 1000 cP at room temperature resulted in inhomogeneous films and crack formation unless the substrate was heated at higher temperatures. Therefore, it is important to control the viscosity of the solution to obtain high quality films. The viscosity of the precursor solutions used in this Example ranged between 200 and 275 cP at room temperature. With a withdrawal speed of 1 inch /min, dense lithiated NiO oxide films were obtained having a thickness in the range of about 0.5 to about 1 micron for each coating after firing at about 6000C To increase sol wetting and increase bond strength between the lithiated nickel oxide film and stainless steel sheets, the sheets were acid treated first, followed by acetone washed ultrasonically to remove any possible dusts and carbon film formed during heat treatment in graphite furnace. Gel film were deposited in a either 1.5 inch by 1.5 inch or 7 inch by 7 inch of a cathode corrugation by dip coating at a substrate withdrawal rate of 1 inch/min. Substrates with gel films were transferred to a furnace preheated to 70° C just after gel film deposition, held for 3 hours and heated up to a temperature no more than 600°C for another 3 hours for complete crystallization and sintering. After heating to 6000C, the film remained continuous, smooth and dense on the cathode side hardware body. FIGS. 2A and 2B show SEM photographs of a fractured cross section of the film coated hardware at different magnifications. From these figures, it can be seen that a thin lithiated Ni oxide film of substantially uniform thickness ~ 1 micron, was realized. (3) Characterization of the Lithiated NiO films The phase evolution of the Li0-1NiO oxide films deposited on the stainless steel (316L) substrates were studied by x-ray diffraction analysis performed on a Philips diffractometer, using Cu Ka radiation. The result is shown in FIG 4. The substrate heat treated at 200° C shows no peaks, indicating amorphous structure. The formation of the rock salt NiO structure is observed at temperatures as low as 350°C. However, there is a secondary phase formed at 350°C and is indexed as NiC. At higher temperature, NiC oxidizes to form NiO. At 450 0C, crystallization is complete, there is no broadened peaks and the intensities of peaks did not change above 450° C. Except for 2000C and 350°C, all the coatings are single phase, neither other secondary product nor reactant was detected. As we can see, lithiated NiO adopt a NiO (rock salt structure) structure and the patterns can be indexed in the Braggs peaks of NiO. There is no preferential position for lithium and nickel ions; thus, there is only one cation crystallographic site. The partial substitution of Nickel (II) (r = 0.83 A) by lithium (I) (r = 0.90 A) implies the creation of nickel (III) (r = 0.70 A) whose ionic radius r is smaller, which shrink the lattice. With higher heat treatment temperature, phases shift to larger angles implying more Li dissolving in the NiO structure (more Ni (III) is created). Also peaks become narrower with increasing temperature indicating crystallite size growth. EXAMPLE II - Lan sSrn 7CoQ1 Cathode Side Hardware (1) Preparation of LansSrn^CoO^ Sol-Gel A starting solution with a nominal La:Sr:Co composition of 0.8:0.2:1 (molar ratio) was prepared using reagent grade La nitrate hydrate and Sr nitrate hydrate and Co nitrate hydrate. Appropriate quantities of these materials to be included in the starting solution were then calculated on the basis of obtaining 1 M LSC sol-gel. Measured quantities of the cation source compounds were then mixed with distilled water (150 ml), ethylene glycol (350 ml) in a 600 ml beaker to form a precipitate-free starting solution. The starting solution was then heated on a hot plate at about 8O0C to expel the water and other volatile matter and form a viscous polymer precursor
I l comprising a polymer containing the metal cations. It is important that the cations remain in solution throughout the polymerization process. The change in the viscosity of the solution as it was converted into the polymeric precursor was measured at room temperature by means of a Brookfield viscometer. (2) Deposition and Formation of Cathode Side Hardware With Smooth, Dense LSC Films To increase sol wetting and increase bond strength between the LSC film and the stainless steel (316L) cathode side hardware, the stainless steel was acid treated first, followed by acetone washed ultrasonically to remove any possible dust and carbon film formed during heat treatment in graphite furnace. Gel film were deposited in a either 1.5 inch by 1.5 inch or 7 inch by 7 inch of a cathode corrugation by dip coating at a substrate withdrawal rate of 1 inch/min. Gel film were transferred to a furnace preheated to 70°C just after gel film deposition, held for 3 hours and heated up to a temperature no more than 600°C for another 3 hours for complete crystallization and sintering. After heating to 600°C, the film remained continuous, smooth and dense on the cathode side hardware body. FIG. 3 shows a SEM photograph of the surface morphology of the LSC coated cathode side hardware. The effect of thermal cycling on the integrity of the lithiated NiO and LSC coated cathode side hardware sheets was also evaluated. Examination of the post cycling specimens by optical microscopy and SEM revealed that the coatings were thermally compatible with the hardware body or substrate, without detectable thermal stress induced cracks or microcracks. The cross sectional SEM observations for a representative example of cathode side hardware coated with lithiated NiO in accord with the invention as compared with uncoated cathode side hardware is shown in FIGS. 5A-5D. As can be seen, the lithiated NiO coating of the invention (FIGS. 5 A and 5B), had significantly reduced the thickness of the corrosion scale, as compared to the uncoated hardware (FIGS. 5C and 5D). More particularly, the corrosion scales show a similar dual-layered structure whether or not sol-gel coated. However, for the coated hardware, the outer oxide scale may have been denser to better protect the inner Cr-rich scale. Consequently, the Cr-rich inner scale of the coated sheets was denser and more protective to reduce the overall corrosion rate. FIG. 6 A shows the out-of-cell electrical resistivity of cathode side hardware in the form of a cathode current collector ("CCC") having the lithiated NiO and LSC coatings of the invention. It also shows the out-of-cell electrical resistivity of a non- coated stainless steel current collector. As can be seen, the coated CCCs of the invention have comparable resistivities to the non-coated CCC. Additionally, as can be seen from FIG 6B, the out-of-cell current collector-to-electrode resistivities (metal- to-metal) of the CCCs of the invention are also comparable to the current collector-to electrode resistivity of the non-coated stainless steel CCC. FIGS. 7 and 8 show the resistance lifegraphs of a fuel cells utilizing CCCs coated with the lithiated NiO and LSC coatings of the invention, respectively, as compared to fuel cells utilizing uncoated stainless steel CCCs. As can be appreciated from these graphs, an improved resistance life is realized for the fuel cells using the CCCs with the coatings of the invention. FIG. 9 shows the corrosion thickness after fuel cell testing of CCCs coated with coatings of the invention as compared to the corrosion thickness after fuel cell testing of uncoated CCCs. The coated CCCs of the invention are seen to exhibit measurably less corrosion than the uncoated CCCs. Finally, FIG. 10 illustrates the electrolyte loss in a molten carbonate fuel cell using CCCs coated with the coatings of the invention as compared to the electrolyte loss in a molten carbonate fuel cell with uncoated CCCs. As can be seen, the electrolyte loss is considerably less in the fuel cell using the coatings of the invention. EXAMPLE III - LSCF (Lan sSrft ?Con sFen 7O^ Cathode Side Hardware fP Preparation of LSCF (Lan sSm .?Con sFen 7OV) Sol-Gel A starting solution with a nominal La:Sr:Co:Fe composition of 0.8:0.2:0.8:0.2 (molar ratio) was prepared using analytical grade La nitrate, Sr nitrate, Co nitrate and Fe nitrate. Appropriate quantities of these materials to be included in the starting solution were then calculated on the basis of obtaining IM LSCF sol-gel. Measured quantities of the cation source compounds were then mixed with distilled water (150 ml) and ethylene glycol (350 ml) in a 1,000 ml beaker to form a starting solution. The starting solution was then heated on a hot plate to about 650C and stirred at 650C for about 48 hours to expel water and other volatile matter and to form a viscous polymer containing the metal cations. It is important that the solution is not overheated during the formation of the viscous polymer since this formation is an exothermic process. After the heating of the solution was turned off, the change in the viscosity of the solution as it was converted into the polymeric precursor was measured using a Brookfield viscometer. (2) Deposition and Formation of Cathode Side Hardware With Smooth, Dense LSCF (Lan sSrn ?Con »Fen,CM Films LSCF films were deposited on the cathode side hardware using dip coating as described above in Example II. The LSCF film formed on the cathode side hardware body was continuous, smooth and dense. FIG. 11 shows an SEM photograph of the surface morphology of the LSCF coated cathode side hardware. Similar to LSC coated cathode side hardware shown in FIG. 3, the SEM shown in FIG. 11 reveals that the LSCF coating is thermally compatible with the hardware body or substrate, and that no thermal stress induced cracks were detected.
EXAMPLE IV- Mg-Doped LiNiQ7 Cathode Side Hardware (1) Preparation of Mg-Doped LiNiO7 Sol-Gel A starting solution with a Mg: Li :Ni: Citric Acid composition having a molar ratio of 0.1 :0.9: 1:2 was prepared using reagent grade Mg acetate, Li acetate (Li- (CH3COO)), hydrated Ni acetate (Ni-(CH3COO)2) and citric acid. Appropriate quantities of these materials to be included in the starting solution were then calculated on the basis of obtaining IM Mg-doped LiNiO2 sol-gel. Measured amounts of cation source compounds, i.e. Mg acetate, Li acetate and hydrated Ni acetate, were then mixed with distilled water (400 ml) and citric acid (2 mol) in a 1,000 ml beaker while heating the solution to about 80°C and stirring it using a magnetic agitator to form a clear precipitate-free starting solution. The starting solution was then heated on a hot plate at 80°C until a green transparent viscous solution was formed. After the solution reached a desired concentration, the heating was turned off and the viscosity of the solution was measured. The change in viscosity of the solution as it was converted into the viscous solution was measured at room temperature by means of a Brookfield viscometer. These measurements showed that the viscosity of the solution increased significantly with increased heating time due to the increase in the average molecular weight as a result of polymerization. The viscous solution was then allowed to stand at about 25°C in a sealed glass beaker for at least a half a year without precipitation. (2) Deposition and Formation of Cathode Side Hardware With Smooth, Dense Mg-Doped LiNiOi Films Mg-doped LiNiO2 films were deposited on the cathode side hardware using dip coating as described above in Example II. FIG. 12 shows an SEM micrograph of surface morphology of the Mg-doped LiNiO2 coating on the 316L cathode side hardware. As in FIGS. 3 and 11, the Mg-doped LiNiO2 coating on the cathode side hardware body remained continuous, smooth and dense, and no thermal stress induced cracks were detected since the coating was thermally compatible with the hardware body or substrate.
EXAMPLE V- Co-Doped LiNiO7 Cathode Side Hardware (1) Preparation of Co-Doped LiNiO7 Sol-Gel A starting solution with a Co/Li/Ni/Citric Acid composition of 0.1/0.9/1/2 (molar ratio) was prepared using reagent grade Co acetate, Li acetate (Li-(CH3COO)), hydrated Ni acetate (Ni-(CH3COO)2) and citric acid. Appropriate quantities of these materials to be included in the starting solution were then calculated on the basis of obtaining 1 M Co-doped LiNiO2 sol-gel. Measured quantities of the cation source compounds were then mixed with distilled water (400 ml) and citric acid (2 mol) in a 1,000 ml beaker, while heating the solution to about 80°C and stirring it using a magnetic agitator to form a clear precipitate-free starting solution. The starting solution was heated at about 80°C to expel the water and other volatile matter and to form a green, transparent viscous solution. The change in viscosity of the solution as it was converted into the viscous solution was measured at room temperature by means of a Brookfield viscometer. As in the previous example, the viscosity of the solution increased significantly with increased heating time due to the increase in the average molecular weight as a result of polymerization. The viscous solution was then allowed to stand at about 25°C in a sealed glass beaker for at least a half a year without precipitation. (2) Deposition and Formation of Cathode Side Hardware With Smooth, Dense Co-Doped LiNiO7 Films Co-doped LiNiO2 films were deposited on the cathode side hardware using dip coating as described above in Example II. FIG. 13 shows an SEM micrograph of surface morphology of the Co-doped LiNiO2 coating on the 316L cathode side hardware. As in FIGS. 3, 11 and 12, the Co-doped LiNiO2 coating on the cathode side hardware body remained continuous, smooth and dense. No thermal stress induced cracks were detected in the coating. In all cases it is understood that the above-described arrangements are merely illustrative of the many possible specific embodiments which represent applications of the present invention. Numerous and varied other arrangements can be readily devised in accordance with the principles of the present invention without departing from the spirit and scope of the invention.

Claims

What is claimed is: 1. A carbonate fuel cell cathode current collector having a thin film coating of a conductive ceramic comprising one of Perovskite AMeO3, wherein A is at least one of lanthanum and a combination of lanthanum and strontium and Me is one or more transition metals, lithiated NiO (LixNiO, where x is 0.1 to 1) and X- doped LiNiO2, X is one of Mg, Ca and Co. 2. A carbonate fuel cell current collector in accordance with claim 1 wherein said coating is obtained by a sol-gel process. 3. A carbonate fuel cell current collector in accordance with claim 2 wherein the thickness of said coating is between 0.5 μm and 5μm. 4. A carbonate fuel cell current collector in accordance with claim 3, wherein said Perovskite AMeO3 is one of LSC (LaxSrx-1CoO3), LaMnO3, LaCoO3, LaCrO3 and LSCF (Lao.8Sro.2Co0.8Fe0.2O3). 5. A carbonate fuel cell cathode bipolar plate having a thin film coating of a conductive ceramic comprising one of Perovskite AMeO3, wherein A is at least one of lanthanum and a combination of lanthanum and strontium and Me is one or more of transition metals, lithiated NiO (LixNiO, where x is 0.1 to 1) and X-doped LiNiO2, wherein X is one of Mg, Ca and Co. 6. A carbonate fuel cell cathode bipolar plate in accordance with claim 5 wherein said coating is obtained by a sol-gel process. 7. A carbonate fuel cell cathode bipolar plate in accordance with claim 6 wherein the thickness of said coating is between 0.5 μm and 5μm. 8. A carbonate fuel cell cathode bipolar plate in accordance with claim 7, wherein said Perovskite AMeO3 is one of LSC (LaxSrx-1CoO3), LaMnO3, LaCoO3, LaCrO3 and LSCF (Lao.8Sro.2Co0.8Fe0.2O3). 9. A carbonate fuel cell comprising: a cathode; an anode; a matrix for storing carbonate electrolyte disposed between said anode and cathode; a cathode current collector situated adjacent said cathode; a bipolar plate situated adjacent said cathode current; and wherein at least one of said cathode current collector and said bipolar plate includes an electrically conductive ceramic comprising one of Perovskite AMeO3, wherein A is at least one of lanthanum and a combination of lanthanum and strontium and Me is one or more of transition metals, litbiated NiO (LixNiO, where x is 0.1 to 1) and X-doped LiNiO2, wherein X is one of Mg, Ca and Co. 10. A carbonate fuel cell in accordance with claim 9 wherein said coating is obtained by a sol-gel process. 11. A carbonate fuel cell in accordance with claim 10 wherein the thickness of said coating is between 0.5μm and 5μm. 12. A carbonate fuel cell in accordance with claim 11, wherein said Perovskite AMeO3 is one of LSC (LaxSrx-1CoO3), LaMnO3, LaCoO3, LaCrO3 and LSCF (La018SrO12COo18FeC2O3). 13. A carbonate fuel cell in accordance with claim 9 wherein both said cathode current collector and said bipolar plate include an electrically conductive ceramic coating comprising one of Perovskite AMeO3, wherein A is at least one of lanthanum and a combination of lanthanum and strontium and Me is one or more of transition metals, lithiated NiO (LixNiO, where x is 0.1 to 1) and X-doped LiNiO2, wherein X is one of Mg, Ca and Co. 14. A carbonate fuel cell in accordance with claim 13 wherein said coatings are obtained by a sol-gel process. 15. A carbonate fuel cell in accordance with claim 14 wherein the thickness of each of said coatings is between 0.5μm and 5μm. 16. A carbonate fuel cell in accordance with claim 15, wherein said Perovskite AMeO3 is one of LSC (LaxSrx-1CoO3), LaMnO3, LaCoO3, LaCrO3 and LSCF (Lao.8Sro.2Co0.8Feo.2θ3). 17. A method of making a carbonate fuel cell cathode current collector or a bipolar plate comprising the steps of: preparing a viscous solution having a viscosity in the range of 125cp to lOOOcp at room temperature and containing one of : lithium and Ni cations; and at least La and Me cations, wherein Me is a transitional metal; dipping a substrate into said viscous solution and withdrawing said substrate from said solution to form a coating of said viscous solution on said substrate; and heating said coated substrate after withdrawal from said viscous solution. 18. A method according to claim 17, wherein: said viscosity of said viscous solution is in a range of 200cp to 275cp at room temperature. 19. A method according to claim 18, wherein: said withdrawing of said substrate from said solution is at a rate of one inch/min.; and said step of heating is carried out at a temperature of 600°C for a period of three hours. 20. A method in accordance with claim 21, wherein: said substrate comprises stainless steel. 21. A method in accordance with claim 20, wherein: said substrate is corrugated. 22. A method in accordance with claim 17, wherein said viscous solution contains lithium and Ni cations and further contains one of Mg, Co and Ca cations. 23. A method in accordance with claim 17, wherein said viscous solution contains La and Me cations and further contains Sr cations. 24. A method in accordance with claim 23, wherein Me is at least one of Co, Fe, Cr and Mn.
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KR101250692B1 (en) 2013-04-03
JP2008503058A (en) 2008-01-31

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