EP0372069A1 - Preparations solides pour electrolytes de piles a combustible - Google Patents

Preparations solides pour electrolytes de piles a combustible

Info

Publication number
EP0372069A1
EP0372069A1 EP89907435A EP89907435A EP0372069A1 EP 0372069 A1 EP0372069 A1 EP 0372069A1 EP 89907435 A EP89907435 A EP 89907435A EP 89907435 A EP89907435 A EP 89907435A EP 0372069 A1 EP0372069 A1 EP 0372069A1
Authority
EP
European Patent Office
Prior art keywords
fuel cell
solid
solid electrolyte
lanthanum
electrolyte fuel
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Withdrawn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
EP89907435A
Other languages
German (de)
English (en)
Inventor
Marc J. Madou
Takaaki Otagawa
Arden Sher
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.)
SRI International Inc
Original Assignee
SRI International Inc
Stanford Research Institute
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 US07/196,498 external-priority patent/US4948680A/en
Application filed by SRI International Inc, Stanford Research Institute filed Critical SRI International Inc
Publication of EP0372069A1 publication Critical patent/EP0372069A1/fr
Withdrawn legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
    • C23C14/06—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the coating material
    • C23C14/0694—Halides
    • 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
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C14/00—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material
    • C23C14/06—Coating by vacuum evaporation, by sputtering or by ion implantation of the coating forming material characterised by the coating 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
    • H01M8/10—Fuel cells with solid electrolytes
    • H01M8/1007—Fuel cells with solid electrolytes with both reactants being gaseous or vaporised
    • 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
    • H01M8/1016—Fuel cells with solid electrolytes characterised by the electrolyte 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
    • H01M8/10—Fuel cells with solid electrolytes
    • H01M8/12—Fuel cells with solid electrolytes operating at high temperature, e.g. with stabilised ZrO2 electrolyte
    • H01M8/1231—Fuel cells with solid electrolytes operating at high temperature, e.g. with stabilised ZrO2 electrolyte with both reactants being gaseous or vaporised
    • 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
    • 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
    • H01M8/1004—Fuel cells with solid electrolytes characterised by membrane-electrode assemblies [MEA]
    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P70/00—Climate change mitigation technologies in the production process for final industrial or consumer products
    • Y02P70/50—Manufacturing or production processes characterised by the final manufactured product

Definitions

  • the present invention relates to materials and processes to prepare polycrystal and monocrystal forms for use as solid electrolytes in fuel cells.
  • a fuel cell having oxygen or air/solid O 2- (oxide ion) conducting lanthanum fluoride (as a single crystal) hydrogen configuration produces about 1 volt of open circuit potential at moderately low temperatures.
  • a fuel cell having oxygen or air/specific substituted alkaline earth lanthanide fluorides (either as a single crystal or poly crystal) that conduct O 2- /hydrogen configuration also produce electricity at moderately low temperatures compared to the present art.
  • Fuel cells convert chemical energy to electrical energy directly, without having a Carnot-cycle efficiency limitation, through electrochemical oxidation-reduction reactions of fuels.
  • Several types of fuel cells have been or are being investigated at the present time. These may generally be classified as shown in Figure 1A and 1B, as Table 1, depending upon the kinds of electrolyte used and the operation temperature.
  • the solid electrolyte fuel cell which can be considered as the third generation fuel cell technology, is essentially an oxygen-hydrogen (or H 2 -CO mixture) fuel cell operated at high temperature (ca. 1000o C) with a solid ceramic oxide material used as the electrolyte.
  • a solid ceramic oxide material used as the electrolyte.
  • yttrium- or calcium-stabilized zirconium oxides have been used as the electrolyte.
  • the mechanism of ionic conduction is oxygen ion transport via O 2- anion in the solid oxide crystal lattice.
  • the electrolyte composition is invariant and independent of the composition of the fuel and oxidant streams.
  • the solid electrolyte fuels cells demand less feed gas preparation than the phosphoric acid cell (see Figure 1), which requires a conversion of CO to H 2 via the water-gas shift reaction, or the molten carbonate cell (see Figure 1), which requires a carbon dioxide loop due to the use of carbonate ions for ionic transport.
  • the attraction of developing a solid electrolyte fuel cell is its simplicity.
  • a high operation temperature (ca. 1000oC) is by far the most critical aspect of this type of fuel cell.
  • high operation temperature produces high-quality exhaust heat that can generate additional electrical power, leading to a high overall system efficiency, maintaining the integrity of the cell components such as the interconnector is the most difficult challenge.
  • the present invention relates to the design of such low temperature solid electrolyte fuel cells based on non-oxide solid electrolytes, such as solid solutions of lanthanide fluorides (e.g. La 1-x Sr x F 3-x ).
  • references of interest regarding such lanthanide fluorides include:
  • G. W. Mellors in European Patent Application No. 055,135 discloses a composition which can be used as a solid state electrolyte comprising at least 70 mole percent of cerium trifluoride and/or lanthanum trifluoride an alkaline earth metal compound, e.g. fluoride, and an alkali metal compound, e.g. lithium fluoride.
  • the present invention relates to a solid O 2- (oxide ion) conducting material for use as an electrolyte for a fuel cell, comprising: (a) a monocrystal or polycrystal structure of the formula:
  • A is independently selected from lanthanum, cerium, neodymium, praseodymium, scandium or mixtures thereof;
  • B is independently selected from strontium, calcium, barium or magnesium, and x is between about 0 and 0.9999,
  • the present invention relates to a solid electrolyte fuel cell comprising a structure:
  • B is independently selected from strontium, calcium, barium, or magnesium, x is between about 0 and 0.9999,
  • the second electrode material is in contact with a porous metallic support (e.g. stainless steel, nickel) that also operates as a current collector.
  • a porous metallic support e.g. stainless steel, nickel
  • the present invention relates to a solid material for use as an electrolyte for a fuel cell comprising: a monocrystal or polycrystal structure of the formula:
  • Pb e Sn f F g wherein Pb is lead, Sn is tin, with the proviso that when f is 1, e is 1 and g is 4 and with the additional proviso that when e is 1, f is 0, and g is 2.
  • Figure 1 shows Table 1 as a comparison of various types of fuel cells.
  • Figure 2 shows a representative schematic diagram of the experimental set up to test the solid electrolyte fuel cell.
  • Figure 3 shows a representative schematic diagram of the solid electrolyte fuel cell assembly for testing.
  • Figure 4 shows a graph of a solid electrolyte fuel cell of dependence of V oc on temperature.
  • Figure 5 shows a typical chart recorder response of an open circuit voltage of a single crystal lanthanum fluoride disk upon an On/Off cycle of hydrogen/argon as a function of time.
  • Figure 6 shows a set of hydrogen/oxygen fuel cell current and power vs. cell voltage of single crystal lanthanum fluoride disks (0.64 mm thickness) as a function of temperature and pretreatment with oxygen.
  • Figure 7 is a phase diagram of the SrF 2 -LaF 3 system.
  • Figure 8 is an X-ray defraction (XRD) pattern from a sample with the nominal composition of
  • Figure 9 shows a set of data concerning the H 2 /O 2 fuel cell current and power-cell voltage relationship of La 0.92 Sr 0.08 F 2.92 Pellets.
  • Figure 10 shows a scanning electron micrograph of a cross-sectional view of the platinum catalyst view of the platinum catalyst/polished La 0.92 Sr 0.08 F 2.92 Pellet interface.
  • Figure 11 shows a set of data concerning H 2 /O 2 fuel-cell current and power versus cell voltage related to the roughened surface of a
  • Figure 12 shows a scanning electron micrographs of a cross-sectional view of the platinum catalyst/roughened
  • Figure 13 illustrates a typical response of a short-circuit current (I sc ) of a roughened surface
  • Figure 14 shows the Isc at 200°C as a function of time for 100 hours (6,000 minutes) for a pellet of
  • Figure 15 shows a schematic cross-sectional representation of a thin-film solid-electrolyte fuel cell.
  • Figures 16A and 16B show a graph of the projected performance of a thin film polycrystalline La 1-x Sr x F 3-x solid electrolyte fuel cell.
  • Figure 16A is conducted at 300oC
  • Figure 16B is conducted at 400oC.
  • Figures 17A, B and C show depth profiles of virgin and used polycrystalline LaF 3 pellets by Auger electron spectroscopy.
  • Figure 18A is a photograph of the original surface of PALL P05 porous stainless steel substrate (0.5 micrometer nominal pore size).
  • Figure 18B is the surface of the PALL
  • Figure 19 is an illustration of the vacuum deposition station used to deposit a thin film of La 1-x Sr x F 3-x on a porous substrate (e.g., stainless steel).
  • a porous substrate e.g., stainless steel
  • Figure 20 is a cut away exploded view of the sample placement within the vacuum deposition station of Figure 19.
  • Figure 21 is a photograph of lanthanum fluoride film (about 10 ⁇ m) deposited on an uncoated (i.e. no sample deposition) SSI (S-2930, 2 micrometer nomimal pore size) porous stainless steel substrate.
  • Figure 22 is a cross section of a solid material composite useful as a solid electrode having a catalyst support, a platinum contact, a solid coating of an electrolyte (e.g. La 0.7 Sr 0.3 F 2.7 ) with a solid discontinuous coating of a perovskite-type (e.g. La 0.7 Sr 0.3 CoCO 3 ) electrode.
  • an electrolyte e.g. La 0.7 Sr 0.3 F 2.7
  • a solid discontinuous coating of a perovskite-type e.g. La 0.7 Sr 0.3 CoCO 3
  • Figure 22A is an enlarged cross section showing the discontinuous nature of the electrolyte in contact with the electrode on the solid support.
  • Contact refers to the laminate structure of Figure 15. It refers not only to physical contact but also may refer to a new phase between layer 151 and 152 or between layer 152 and 153 (or i.e., C and E or E and A, respectively), which is produced during formation or afterward having different chemical properties and/or physical properties than the immediately adjacent phase (e.g., a mixed conduction - electron or ion - phase). See Figure 15 and Figures 22 and 22A.
  • Fluel gases refer to oxygen (as defined herein) and hydrogen (as defined herein) or liquids or gases which contain carbon, such as carbon dioxide, carbon monoxide, methane, ethane, natural gas, reformed natural gas or mixtures thereof. Liquids such as methanol, ethanol or mixtures thereof are also useful.
  • Hydrogen electrode or “hydrogen” refers to hydrogen and as used herein may refer to carbon containing fuel gases.
  • Oxygen electrode” or “oxygen” refers to the oxidizing electrode side of the fuel cell, and may be oxygen or oxygen mixed with air, or air itself.
  • O 2- (oxide ion) conducting lanthanum fluoride (either in its pure form or its substituted form) is the solid electrolyte of choice for a fuel cell.
  • the basic properties of LaF 3 are shown below in
  • hexagonal space group is P6 3 /mcm
  • the activation energy for fluorine ion diffusion is about 0.45 eV
  • -Activation energy for the formation of defects about 0.07eV
  • LaF 3 has unique physicochemical properties such as high electrical conductivity and high polorizability at room temperature.
  • the Debye temperature of LaF 3 is only 360oK, while its melting point is high at 1766oK.
  • the observed phenomena appear to be associated with the formation of Schottky defects and with the activation energy for the diffusion of defects having the unusually low value of about 0.42 eV, and the room temperature Schottky defect density is about 10 19 /cm 3 .
  • Fluorine in LaF 3 usually exists in three magnetically non-equivalent sites . Covalent bonding predominates in two of the sites. In the third site, the fluorines make up a layered array with approximately 60% ionic bonding and about 40% ⁇ -bonding.
  • the high polarizability and high conductivity of LaF 3 at room temperature is primarily due to the motion of F- ions through the latter sites.
  • the relatively small radius of F-(1.19A) is almost identical with that of the oxide O 2- ion (1.25A); therefore oxide ions (O 2- ions) can substitute for the F ions in LaF 3 .
  • the oxygen ion is transported through the bulk of a single crystal LaF 3 as measured by Auger electron spectroscopy.
  • the solid electrolyte LaF 3 serves as a supporting electrolyte analogous to liquid phase in which oxygen ions can move freely.
  • the mobile oxygen ions sitting in the vacant F ⁇ sites may be viewed as O c F d instead of pure F or Z (for both monocrystal and polycrystal forms).
  • LaF 3 has been extensively used as a F- ion selective electrode in electroanalytical chemistry. Recently LaF 3 has been applied to a room temperature potentiometric oxygen sensor and to a multifunctional sensor for humidity, temperature, oxygen gas, and dissolved oxygen.
  • a 1-x B x Z e.g. La 1-x B x F 3-x (where 0 ⁇ x ⁇ 0.5) as a single crystal or as a polycrystal for a solid electrolyte in a fuel cell.
  • Figure 2 depicts a block diagram of the experimental setup 20 used to evaluate various La 1-x B x F 3-x soli electrolytes (e.g., single crystal LaF 3 disk) for the fuel cell application.
  • the temperature of the cell 21 is maintained at a desired value (about 25-300°C) using a heating tape 22 (coiled around the cell), whose voltage is controlled by a transformer.
  • Cell voltages are measured by a high-input impedance electrometer 23 (e.g. Keithley Model 617).
  • a strip chart recorder 26 e.g., Soltec Model 1243; with three channels
  • FIG. 3 illustrates the design for the experimental fuel cell assembly 30 in detail.
  • a circle about 4 mm in diameter of Pt mesh 31 (or 31A) (mesh size: 50) is used as a current collector.
  • An ohmic contact is made by mechanically pressing a stainless steel mesh 32 (mesh size: about 60) against the Pt catalyst/Pt mesh using a stainless steel rod 33, which also serves as an electrical lead and is fixed in a rubber stopper 34 (or 34A).
  • a pair of stainless steel tubes 37A, 37B with appropriate gas inlet 38A, 38B and outlet 39A, 39B form the main body of the fuel cell 30.
  • the Teflon electrode holder system (35A and 35B) is inserted between the two stainless steel tubes, and the entire assembly is held together tightly by stainless steel screws 40A, 40B.
  • FIG 4 graphically presents the open-circuit cell voltages (V oc ) of a single crystal LaF 3 disk 0.64 mm thick as a function of temperature (0 to 300°C) when the cathode and anode were exposed to oxygen and hydrogen, respectively.
  • the LaF 3 disk is equilibrated with each new temperature for about 60 min before a steady-state reading of the V oc was taken.
  • the V oc appears to increase almost linearly with an increase of the cell temperature and saturates around 1.07 V at temperatures about 250oC.
  • the saturated value of 1.07 V obtained is in fair agreement with the theoretical value of V oc for a hydrogen/oxygen fuel cell, i.e. 1.13V at 227oC.
  • a slight hysteresis was observed in the V oc vs. temperature relation when the measurements are made in the direction of decreasing temperature, indicating that the reaction that determines V oc is not completely reversible.
  • the solid material electrolyte described as (AA) in the Summary is one where A is lanthanum, and/or where B is strontium.
  • the electrolyte of structure (AA) is one where Z is F 3-x .
  • the electrolyte (AA) is one where Z is O c F d and where the oxygen is an integral part of the crystal lattice, especially where A is lanthanum, Z is F 3-x , and x is 0, and the solid material is a monocrystal.
  • the solid material electrolyte (AA) is one where the solid material as a monocrystal has a thickness between about 1 and 300 micrometers, or as a polycrystal has a thickness between about 1 and 100 micrometers. Preferred temperatures of operation for the fuel cell of structure (AA) to generate an electrical current at a temperature of between about 20 and 600oC, especially between about 200 and 400oC.
  • Figure 6 presents a set of data concerning the H 2 /O 2 fuel cell current (I) and power (P) vs. cell voltage relations of a single crystal LaF 3 disks 0.64 mm thick with or without a pretreatment as a function of operating temperature.
  • Figures 6A, 6C and 6E have no pretreatment.
  • Figures 6B, 6D and 6F are pretreated in oxygen at 600 'C for 1 hour.
  • the electromotive forces show a good reproducibility, while the current densities do not, probably because of a variation in the morphology of the electrocatalyst/electrolyte interface (i.e., Pt black/LaF 3 disk) of each sample.
  • the current density increases with operating temperature, and the I sc of the LaF 3 disk becomes about 20 ⁇ A/cm 2 at 204oC (see Figure 6E), which is about 10 times that at room temperature.
  • the single-crystal LaF 3 disks are pretreated by annealing in an oxygen atmosphere for 1 hr at 600oC, current densities increased dramatically.
  • the fuel cell short-circuit current density becomes as high as 2 ⁇ 10 -4 A/cm 2 at 206°C.
  • the observed positive influence of the pretreatment of O 2 of the LaF 3 disk on the current density is most likely due to the formation and/or impregnation of O 2- ions into the lattice of LaF 3 .
  • the solid electrolyte fuel cell is one where the first electrode material is in contact with an oxidizing gas and the second electrode material is in contact with a reducing gas.
  • the solid electrolyte fuel cell is one where the anode material is in contact with a reducing gas and the second electrode material is in contact with an oxidizing gas.
  • the solid electrolyte fuel cell is one where the porous support is colloidal alumina. In a preferred embodiment, the solid electrolyte fuel cell is one where the thin film solid electrolyte is between about 1 and 300 micrometers in thickness.
  • the solid electrolyte fuel cell is one where in the thin film solid electrolyte B is strontium. In a preferred embodiment, the solid electrolyte fuel cell is one where in the thin film solid electrolyte A is lanthanum.
  • the solid electrolyte fuel cell is one where x is between about 0.001 and 0.2, especially about 0.1.
  • the solid electrolyte fuel cell is one where the thin film has a thickness of about 10 micrometers.
  • the use of the solid material of Claim 1 as an electrolyte (AA) for a fuel cell is conducted at a temperature of between about 200 and 500oC, especially at a temperature of between about 300 to
  • phase diagram of the system SrF 2 -LaF 3 is presented in Figure 7 (Yoshimoto, Kim and Somiya, 1985, 1986), together with our data points (shown as solid or open diamonds). According to this phase diagram, solubility limits in the system SrF 2 -LaF 3 to form a single phase solid solution are a function of temperature as follows:
  • Figure 9 presents a set of data concerning the H 2 /O 2 fuel cell current (I) and power (P) cell voltage relations of La 0.92 Sr 0.08 F 2.92 pellets (approximately 1 mm thick) with and without a physical pretreatment of polishing both sides of the pellets by an emery paper (#120) as a function of operating temperature.
  • Figures 9A and 9C are as prepared; Figures 9B, 9D and 9E are polished).
  • the polished pellet with the surface layer removed by polishing gives a much higher current density (by about a factor of 10) than the unpolished pellet with as-prepared surface.
  • the observed increase of reaction rate (i.e. current density) of the fuel cell is due to an increase the "real" electrochemical surface area, i.e. number of the triple contact points, where the gas reactions can take place.
  • a scanning electron micrograph (SEM) of a cross-sectional view of the platinum catalyst/polished La 0.92 Sr 0.08 F 2.92 pellet interface is shown in Figure 10.
  • An array of submicron-size "ridges" is visible at the platinum/solid electrolyte interface.
  • the observed enhancement of Isc on the polished surface could be also partly due to the removal of the surface layer that may contain some "undesirable” materials (e.g. LaOF). It therefore would be still possible to enhance the current density further, say by another factor of 10, by carefully optimizing the microstructure of the interface.
  • Figure 13 illustrates a typical response of a short-circuit current (I sc ) of a roughened surface La 0.904 Sr 0.096F2.904 pelled (used) as a function of time at approximately 200oC.
  • I sc short-circuit current
  • the Isc rapidly decays to around 0 within 20 s.
  • the Isc goes back to its original value within 20 s upon switching back to oxygen.
  • This observation strongly' supports the observation that an oxygen/hydrogen fuel-cell reaction is taking place on the pellet of La 0.904 Sr 0.096 F 2.904 .
  • the residual current observed in argon is most likely due to oxide ions (O 2- ) remaining in the lattice.
  • Figure 15 shows an idealized schematic cross section of a laminate of a thin-film La 1-x Sr x F 3-x solid-electrolyte fuel cell.
  • the cell is arranged in a multilayer structure on a porous support 154.
  • a similar basic structure but on a porous support "tube” has been used for Westinghouse thin-film zirconia solid-electrolyte fuel cell (Isenberg, 1981).
  • the porous support 154 such as porous sintered glass (e.g. Vycor glass) and porous alumina, provides mechanical integrity for the multilayer structure and also serves as conduit for one of the reactants, e.g. hydrogen.
  • an electronically conductive e.g., metallic substrate such as porous stainless steel or a nickel disk and porous sintered nickel plaque
  • the mechanical support 154 which also serves as a current collector
  • an electrocatalyst e.g. nickel
  • Figure 15 shows cathode (C) as 151, electrolyte (E) as 152, anode (A) as 153 and support (S) as 154.
  • the anode A and cathode (C) may be reversed when the gases O 2 and H 2 are also reversed.
  • Figures 22 and 22A present a more realistic view of the discontinuous surface of the solid electrolyte fuel cell of Figure 15.
  • Figure 22 shows the configuration of a supported composite for use in a fuel cell.
  • the perovskite substrate 71 is spray dried onto an inorganic or metal support 70 (or 154) such as silica, thoria, zirconia, magnesia, stainless steel or the like having mechanical stability.
  • the fluoride electrolyte (E) 72 is then vapor deposited on the surface of the perovskite 71.
  • the fluoride electrolyte 72 as a vapor enters the pores of the perovskite 71 and the substrate 70 in a discontinuous manner. In this way, millions of two-material catalytic surfaces 74 are created to facilitate the electrochemical reaction at the intersection of the perovskite 71 and fluoride 72.
  • V is the reversible thermodynamic electromotive force (emf)
  • R is gas constant
  • T absolute temperature
  • F Faraday's constant
  • L electrolyte thickness
  • J L,a and J L,c are limiting current densities at anode and at cathode
  • J o,a and J o,c are exchange current densities at anode and cathode, respectively.
  • the second and fourth terms in Eq. (8) represent the concentration polarization of the electrodes (which depends on the electrode morphological parameters, porosity and thichness); the third and fifth terms in Eq.
  • Eq. (8) represent activation polarization at the three-phase point of the electrode-electrolyte interface, and the last (sixth) term in Eq. (8) represents ohmic polarization (which solely depends on electrolyte resistivity and thickness).
  • Table 2 lists values of thermodynamic emf and resistively used in the calculations. In these calculations, values are used (as a first approximation) for exchange current density for electrodes J 0,a and J o,c data that were experimentally determined for the case of zirconia-and ceria-based fuel cells, viz. approximately 1 mA/cm2 for both electrodes (Canaday, et al., 1987).
  • Similar performance levels may be obtained by highly nonstoichiometric films of LaF 3-x (made by e.g., electron-beam evaporation) that exhibit comparable ionic conductivity.
  • a further increase in operating temperature to 500oC does not seem to improve the fuel-cell performance in terms of the I-V curves, so long as the strontium concentration is maintained between 2.6 and 10 mol-percent.
  • the fuel-cell maximum power density dramatically increases almost linearly with an increase of operating temperature; especially when the strontium content is 10 mol-percent, and reaches approximately 0.55 W/cm 2 at 500oC.
  • the set of I-V curves shown in Figure 16A and 16B may represent rather a modest case, because the calculations were made on the basis of highly resistive polycrystalline La 1-x Sr x F 3-x films [it was assumed that the resistivity of polycrystalline La 1-x Sr x F 3-x thin films is two orders of magnitude greater than the resistiveity of the single crystal, following the data given by Lilly et al. (1983) on thin films of LaF3]. Fuel-cell performance could be further significantly improved if we could reduce the resistivity of polycrystalline films by carefully optimizing a thin-film deposition process.
  • Table 3 compares three physical thin-film deposition techniques that might be used to fabricate thin films (e.g. 5 to 50 - ⁇ m (preferred 5 to 15 ⁇ m) thick of polycrystalline La 1-x Sr x F 3-x for the fuel-cell application.
  • the source compound is evaporated by heating with a thermal or electron-beam heater and deposited on the substrate. Areas are delineated either by a shadow mask or by photolithography. Electron beam evaporation is a particularly attractive method for depositing polycrystalline La 1-x Sr x F 3-x films for the fuel-cell application, because the film deposition rate can be as fast as 10 ⁇ m/h and highly nonstoichiometric, conductive films of LaF 3-x (for which strontium-doping might not be necessary) can be formed.
  • Magnetron sputtering is a process that is similar to (but faster than) diode sputtering and is primarily useful for films that are thicker than 5 ⁇ m. However, the film deposition rate of magnetron sputtering is still slower than vacuum evaporation methods.
  • chemical processes such as chemical vapor deposition and screen printing, may be used to prepare thin films of polycrystalline La 1-x Sr x F 3-x films.
  • Screen printing is widely used in electronic manufacturing (e.g. ceramic capacitors). Screen-printed deposits are thicker than sputtered and evaporated layers, usually in the range of 10 to 50 ⁇ m. The deposits are made from a paint-like suspension of particles and binders that, after application through a patterned screen, are dried and sintered to form a coherent (but often porous) mass. The resultant deposit can be similar to the pressed materials. Screen printing is particularly suited for volume production techniques, because manufacturing equipment is available and printing precision is relatively high. However, it is expected that this method is applicable to the deposition of polycrystalline LaF 3-x or La 1-x Sr x F 3-x films.
  • PECVD Plasma enhanced chemical vapor deposition
  • the present invention relates to a process [BB] for preparing a composite comprising:
  • a 1-x B x QO 3 having a perovskite or perovskite-type structure as an electrode catalyst in combination with:
  • a 1-x B x Z as a discontinuous polycrystalline surface coating solid electrolyte wherein A is independently selected from lanthanum, cerium, neodymium, praseodymium, or scandium, B is independently selected from strontium, calcium, barium or magnesium, Q is independently selected from nickel, cobalt, iron or manganese, and x is between about 0 and
  • Z is selected from the group consisting of F 3-x and
  • step (b) reacting the particulate of step (a) with a vapor comprising: A 1-x B x Z wherein A, B, Z and x are defined hereinabove, at about ambient pressure at between about 0 and 1000oC: for between about 10 and 30 hr. obtain the composite of between 25 to 1000 microns in thickness; and (c) recovering the composite of step (b) having multiple interfaces between:
  • a 1-x B x QO 3 and A 1-x B x Z said composite having a pore size of between about 25 and
  • a preferred embodiment in this process [BB] is wherein
  • A is lanthanum
  • B is strontium
  • Q is cobalt
  • x is about 0.3
  • Another preferred embodiment of process [BB] is wherein A is selected from cerium or scandium, B is selected from strontium or magnesium, Q is selected from nickel, cobalt or manganese and x is between about 0.2 and 0.4.
  • perovskites useful in this invention may be purchased or may be formed according to the procedures described in the literature, e.g., T. Kudo, et al., U.S.
  • Patent No. 3,804,674 which is incorporated herein by reference.
  • Electrolyte Fuel Cell LaF 3 single crystals (purity 99.99 percent; diameter; 10 mm) were purchased from Optovac, Incorporated, North Brookfield, Massachusetts 01535, and were sliced into disks 25 mil (0.64 mm) thick.
  • the nominal ionic conductivity of the LaF 3 single crystals is about 10 -7 S/cm at room temperature.
  • Platinum black that is made by a thermal decomposition of a Pt salt is used as an electrocatalyst for both oxygen cathode and hydrogen anode.
  • a typical catalyst loading is about 25-30 mg/cm 2 .
  • the procedure for depositing Pt black catalyst onto the LaF 3 single-crystal disk is as follows: (1) Place a tiny drop (about 0.002-0.005 mL) of a concentrated (about 2M) H 2 PtCl 6 aqueous solution on one side of a LaF 3 disk (previously cleaned with methanol), and using a metal rod, spread the solution into a circular spot with a diameter of about 4 or 5 mm.
  • the exhausted gas from the anodic compartment of the H 2 /O 2 fuel-cell of Part (a) based on a single crystal LaF 3 pellet under a short-circuit operating condition is introduced into a beaker containing 30 mL of a 5 percent CaCl 2 aqueous solution (about 1.4 ⁇ 10 -2 mol/30 mL or about 0.45 M). If HF, F 2 , or both are produced at the anode, white colloids of CaF 2 precipitates will be formed according to the following reaction: CaCl 2 + 2F-(or F 2 ) CaF 2 (s.) + 2Cl- (or Cl 2 ) (9)
  • the test was continued for 120 hours with an average I sc of 20 ⁇ A, which corresponds to 8.6 Coulombs, and 9 ⁇ 10 -5 mols of F- ions should be produced if HF (or F 2 ) is produced at 100 percent efficiency. The solution remained clear after this prolonged test, indicating no evidence for the formation of HF or F 2 .
  • a solution of 80 mL of buffered oxide etch (prepared by KTI Chemicals of Sunnyvale, California, by mixing 8.01 g of 42 percent NH 4 F with 1.31 g of 49 percent HF) in 400 mL deionized water is added as rapidly as possible with brisk stirring to encourage the maximum degree of coprecipitation. After about two minutes of vigorous stirring, the suspension is allowed to settle and a few drops of buffered oxide etch are added to check for complete precipitation. The material is washed three times by decantation and settling. Further washing results in peptization (i.e. formation of a colloidal suspension in the ion-free water), as indicated by a haze in the supernatant liquid.
  • buffered oxide etch prepared by KTI Chemicals of Sunnyvale, California, by mixing 8.01 g of 42 percent NH 4 F with 1.31 g of 49 percent HF
  • the mixture is filtered through Whatman No. 1 filter paper with limited washing with deionized water to aid in the transfer.
  • the solids and paper were dried overnight ot 120oC or until visibly dry.
  • the solid is removed from the filter paper and trasferred to a quartz boat and calcined in argon in a tube furnace at 950oC overnight so as to drive off the residual H 2 O, NH 4 Cl, and NH 4 F.
  • the calcined material is ground to pass a 100-mesh screen.
  • the particles are then all much less than 0.01 inch (250 ⁇ m) in diameter.
  • the pressed and sintered pellets are prepared by hot pressing in a heated graphite die at 1100°C and 15,000 pounds for 15 minutes.
  • the resultant 0.5 inch-diameter rod is sliced to 1-mm thick disks.
  • Auger electron spectroscopy (AES) analysis was employed to obtain the depth profile of the polycrystalline LaF 3 pellet that was used in a long-term fuel-cell test.
  • AES Auger electron spectroscopy
  • characteristic peaks are obtained for the elements of our concern, viz. oxygen, lanthanum, and fluorine at 503, 625, and 647 eV, respectively.
  • Figures 17 A, B and C show the Auger depth profile of the used sample as well as of a virgin LaF 3 pellet for comparison.
  • the y axis corresponds to the concentrations of these elements on arbitrary scale. No substantial difference was observed in the depth profile of lanthanum.
  • oxide ion (O 2- ) are, indeed, generated at the cathode by the H 2 /O 2 fuel-cell operation and transported to the anode, where they are consumed by a reaction with hydrogen with little production of such side products as HF and F 2 .
  • a porous stainless steel serves not only as a substrate but also as a current collector.
  • Porous stainless steel substrates are purchased from Pall Porous Metals Filter Corporation (PALL), East Hills, New York 11548, and from Sintered Specialities, Incorporated (SSI), Janesville, Wisconsin 53547. Table 4 summarizes their physical properties. These porous stainless steel materials are originally designed as filters for fluid clarification in high temperature, high pressure, and corrosive environments.
  • the Pall materials are rougher and have higher porosity; thus, they are attractive for our fuel-cell application because they potentially can provide a large number of triple-interface reaction sites.
  • the deposition of LaF 3 films on the PALL materials is not easy because of their wide open structures. Indeed, the PALL
  • 0.5 ⁇ m has been identified as the best substrate for experiments.
  • One difficulty associated with this material is, however, that although the manufacturer states (nominal) pore size to be 0.5 ⁇ m, the actual size of individual pores varies from 0.2 ⁇ m to as high as 40 ⁇ m, which makes the deposition of LaF 3 films difficult.
  • the SSI materials are substantially flatter and have pores much closer to the state 2 and 3 ⁇ m, with a concomitant lowering in the porosity.
  • the deposition of LaF 3 films should be easier with the SSI materials; however, their porosity is too low to provide enough triple interface reaction sites.
  • Method 1 produces a very rough surface with cracked PtO x layers, which is not favorable for the LaF 3 deposition. It is thought that the application of platinum black powder onto the substrate would result in the pores that are partly filled with" the platinum black, and the successive Pt deposition by the thermal decomposition method would completely fill the pores with Pt (Method 2). The resultant surface is much smoother than the one made by Method 1, however, there are still some unfilled, big cavities, and the deposited Pt is very flaky. Therefore, the surface made by Method 2 is not ideal either for the deposition of LaF 3 . Because the first two methods did not turn out to be effective for our purpose, an electroplating method (Method 3), i.e.
  • FIG. 18B shows the surface morphology of the platinum layers formed at about -670 mV versus SCE for 2.5 hours.
  • the surface morphology of the electroplated platinum depends strongly upon the applied potential; a platinum "black" film is obtained when the applied potential is in the range of about -600 mV to about -700 mV versus SCE, while the potential of about -500 mV to about -600 mV versus SCE produces a more metallic- looking Pt film.
  • the cut-off potential appears to be related to the competing hydrogen evolution reaction which initiates around -600 mV. In the case of metallic Pt, the pores appear to be totally clogged with Pt and few gas molecules can go through.
  • PALL PO5 porous stainless steel (0.5 ⁇ m nominal pore size) substrates that are electrochemically plated with Pt catalyst layer at about -670 mV for 2.5 hours are found to be the most desirable for the LaF 3 depositions.
  • the estimated Pt catalyst loading is in the range of 20-30 mg/cm 2 .
  • the surface consists of small clusters of platinum and exhibits more compact, "smooth" morphology, compared to the surfaces made by other Methods 1 and 2.
  • the perovskite powder is first mixed with a binder material-water glass (about 10 weight percent) made of sodium meta silicate.
  • the slurry is coated onto the lanthanum fluoride film followed by a sintering treatment in air of 450oC to 500oC for 1 hour.
  • the perovskite forms a physical combination with the electrolyte on the support.
  • Figures 19 and 20 illustrate the vacuum deposition station 19 used to deposit a thin film of La 1-x Sr x F 3-x on a porous stainless steel substrate ("sample").
  • the samples are placed into the sample holder 51, which holds up to four samples.
  • the vacuum system is prepared for the deposition by replacing the thickness monitor crystal 58 and by filling the evaporation boats 53 with source material 54.
  • the thickness monitor 58 calculates the thickness by measuring the amount of material evaporated onto the crystal and calculates the thickness from the density. If microcracks occur on the crystal, it ceases to function; and having a finite lifetime, it must be changed before each series of depositions.
  • the tantalum evaporation boats 53 are filled with source material 54.
  • the source material is either optical grade 99.999% crystalline LaF 3 , 99.999% crystalline SrF 2 , or a mixture of 99.999% LaF 3 powder and 99.994% SrF 2 .
  • Two evaporation source boats 53 are used to maximize the amount of material that can be deposited during one pump-down cycle of the vacuum chamber 55. The samples are placed in the chamber with the surface for the deposition perpendicular to the gas stream from the evaporation. In what follows, a typical deposition procedure is given:
  • FIG. 19 and 20 Additional features of Figures 19 and 20 include the apparatus support 59.
  • the thickness monitor crystal 58 which is connected to wire 60 which exits vaccum chamber 61 and is referred to as the thickness monitor outlet.
  • the tube support 62, shutter 63 and shield 64 are seen in both Figures 19 and 20.
  • Figure 21 shows a typical example of the deposited LaF 3 films with or without platinum catalyst layer.
  • a LaF 3 film was directly deposited on an SSI S-2930 porous stainless steel substrate. It can be seen that crystallites of LaF 3 grow almost perpendicular to the substrate plane, i.e. the direction to the evaporation source.
  • the deposited LaF 3 film unfortunately, exactly reflects the surface "roughness" of the substrate; viz. the film consists of many small islands surrounded with cracks, which may lower the energy density of the fuel cell through the possible cross-talk of gases.

Abstract

Matériau solide conducteur d'O2- destiné à être utilisé comme électrolyte (152) pour une pile à combustible, comprenant une structure monocristalline ou polycristalline de formule A1-xBxZ, dans laquelle A est sélectionné indépendamment parmi le lanthane, le cérium, le néodyme, le praséodyme, le scandium ou des mélanges de ces éléments; B est sélectionné indépendamment parmi le strontium, le calcium, le baryum ou le magnésium; la valeur de x est comprise entre environ 0 et 0,9999; Z est sélectionné dans le groupe composé de F3-x et d'OcFd, où F représente fluor, O représente oxygène, la valeur de x est comprise entre environ 0 et 0,9999 et 2c+d = 3-x, où la valeur de c est comprise entre 0,0001 et 1,5 et celle de d entre 0,0001 et 3, à condition que lorsque A représente lanthane, Z est F3-x et x vaut 0, le matériau solide est constitué uniquement d'un monocristal. On décrit également une pile à combustible composite à base de fluorure de strontium-lanthane mince présentant une structure du type stratifié (composite) (151, 152, 153, 154). Dans une variante, l'électrolyte solide présente une structure monocristalline ou polycristalline de PbeSnfFg, dans laquelle Pb représente plomb et Sn zinc. On décrit également l'utilisation des piles à combustible à électrolyte solide susmentionnées pour produire de l'électricité.
EP89907435A 1988-05-20 1989-05-18 Preparations solides pour electrolytes de piles a combustible Withdrawn EP0372069A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
US07/196,498 US4948680A (en) 1986-11-26 1988-05-20 Solid compositions for fuel cell electrolytes
US196498 1988-05-20

Publications (1)

Publication Number Publication Date
EP0372069A1 true EP0372069A1 (fr) 1990-06-13

Family

ID=22725649

Family Applications (1)

Application Number Title Priority Date Filing Date
EP89907435A Withdrawn EP0372069A1 (fr) 1988-05-20 1989-05-18 Preparations solides pour electrolytes de piles a combustible

Country Status (5)

Country Link
EP (1) EP0372069A1 (fr)
JP (1) JPH02504445A (fr)
KR (1) KR900702589A (fr)
GB (1) GB2232293A (fr)
WO (1) WO1989011739A2 (fr)

Families Citing this family (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE4025161A1 (de) * 1989-08-09 1991-02-14 Centr Nt Tvorcestva Molodezi G Fester elektrolyt und verfahren zu seiner herstellung
KR950001256B1 (ko) * 1989-08-24 1995-02-15 가부시끼가이샤 메이덴샤 고체 전해질을 이용하는 연료 전지 및 이의 형성 방법
EP1384280A2 (fr) * 2001-04-27 2004-01-28 Alberta Research Council, Inc. Cellule electrochimique a electrolyte solide sur support metallique et reacteur a cellules multiples comprenant de telles cellules
JP2019016425A (ja) 2017-07-03 2019-01-31 パナソニック株式会社 フッ化物イオン伝導材料およびフッ化物シャトル二次電池
JP7040903B2 (ja) 2017-07-03 2022-03-23 パナソニック株式会社 フッ化物イオン伝導材料およびフッ化物シャトル二次電池
JP7172574B2 (ja) * 2018-12-25 2022-11-16 トヨタ自動車株式会社 固体電解質およびフッ化物イオン電池

Family Cites Families (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
FR1377296A (fr) * 1963-05-08 1964-11-06 Comp Generale Electricite Pile électrique à combustible à électrolyte solide
FR2330127A1 (fr) * 1975-10-30 1977-05-27 Anvar Nouveaux conducteurs anioniques fluores
FR2403652A2 (fr) * 1977-09-16 1979-04-13 Anvar Conducteurs anioniques fluores en couches minces, leur fabrication et leurs applications electrochimiques
FR2486244A1 (fr) * 1980-07-01 1982-01-08 Centre Nat Rech Scient Dispositif potentiometrique utilisable comme capteur pour determiner la pression d'un gaz
JPS60250565A (ja) * 1984-05-28 1985-12-11 Asahi Glass Co Ltd 燃料電池
JPS6273155A (ja) * 1985-09-27 1987-04-03 Tokuyama Soda Co Ltd 酸素センサ−素子の特性改善方法
US4851303A (en) * 1986-11-26 1989-07-25 Sri-International Solid compositions for fuel cells, sensors and catalysts

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
See references of WO8911739A2 *

Also Published As

Publication number Publication date
WO1989011739A2 (fr) 1989-11-30
GB2232293A (en) 1990-12-05
JPH02504445A (ja) 1990-12-13
KR900702589A (ko) 1990-12-07
WO1989011739A3 (fr) 1990-04-05
GB9000121D0 (en) 1990-07-25

Similar Documents

Publication Publication Date Title
US4948680A (en) Solid compositions for fuel cell electrolytes
US11560636B2 (en) Low temperature electrolytes for solid oxide cells having high ionic conductivity
US9670586B1 (en) Solid oxide fuel cells, electrolyzers, and sensors, and methods of making and using the same
US8247113B2 (en) Titanates of perovskite or derived structure and applications thereof
US5134042A (en) Solid compositions for fuel cells, sensors and catalysts
Wang et al. The role of 8 mol% yttria stabilized zirconia in the improvement of electrochemical performance of lanthanum manganite composite electrodes
WO2015009618A1 (fr) Piles à oxyde solide à basse température
Zhang et al. Atomic layer deposited zirconia overcoats as on-board strontium getters for improved solid oxide fuel cell nanocomposite cathode durability
US20170162896A1 (en) Layered Electrolytes and Modules for Solid Oxide Cells
WO1996036085A1 (fr) Nouveaux corps monocomposants a base d'oxydes solides
Bloom et al. Oxide-ion conductivity of bismuth aluminates
Sındıraç et al. Electrochemical performance of La 0.6 Sr 0.4 Co 0.2 Fe 0.8 O 3–Ce 0.9 Gd 0.1 O 2-δ composite SOFC cathodes fabricated by electrocatalyst and/or electrocatalyst-ionic conductor infiltration
Gilev et al. Evaluation of La2-x (Ca/Sr) xNi1-yFeyO4+ δ (x= 0.5, 0.6; y= 0.4, 0.5) as cathodes for proton-conducting SOFC based on lanthanum tungstate
EP0372069A1 (fr) Preparations solides pour electrolytes de piles a combustible
Jue et al. Electrochemical Vapor Deposition of CeO2: Kinetics of Deposition of a Composite, Two‐Layer Electrolyte
Kalinina et al. Formation of Bilayer Thin-Film Electrolyte on Cathode Substrate by Electrophoretic deposition
JP2004265859A (ja) 電極及びその製造方法
Choudhary et al. Fabrication of fuel electrode supported proton conducting SOFC via EPD of La2Ce2O7 electrolyte and its performance evaluation
Tang et al. A new vapor deposition method to form composite anodes for solid oxide fuel cells
Sharma et al. Synthesis and Characterization of Ba0. 5 Sr0. 5 (CO0. 8Fe0. 2) 1-xZrx O3-δ (BSCF) Nanoceramic Cathode Powders by Sol-Gel Process for Solid Oxide Fuel Cell
CA1305751C (fr) Compositions solides pour piles a combustibles, capteurs et catalyseurs
Lyu et al. An in situ hydrothermally self-crystallized dense ceria-based barrier layer for solid oxide fuel cells
Kılıç Combinatorial development of LSF-based cathode materials for intermediate temperature solid oxide fuel cells
Zachariasen Aluminate spinels for use as catalyst enhancement of solid oxide fuel cells
JP2019163193A (ja) 酸化物イオン伝導体及び電気化学デバイス

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): FR IT

D17D Deferred search report published (deleted)
RIN1 Information on inventor provided before grant (corrected)

Inventor name: SHER, ARDEN

Inventor name: OTAGAWA, TAKAAKI

Inventor name: MADOU, MARC, J.

17P Request for examination filed

Effective date: 19900927

17Q First examination report despatched

Effective date: 19920507

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE APPLICATION IS DEEMED TO BE WITHDRAWN

18D Application deemed to be withdrawn

Effective date: 19930821