WO2012145531A2 - Structure multicouche à conductivité ionique - Google Patents

Structure multicouche à conductivité ionique Download PDF

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Publication number
WO2012145531A2
WO2012145531A2 PCT/US2012/034285 US2012034285W WO2012145531A2 WO 2012145531 A2 WO2012145531 A2 WO 2012145531A2 US 2012034285 W US2012034285 W US 2012034285W WO 2012145531 A2 WO2012145531 A2 WO 2012145531A2
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WO
WIPO (PCT)
Prior art keywords
layer
ion conductive
thin
film ion
conductive structure
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PCT/US2012/034285
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English (en)
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WO2012145531A8 (fr
WO2012145531A3 (fr
Inventor
Chonglin Chen
Jian Liu
Gregory Roy COLLINS
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Broard Of Regents Of The University Of Texas System
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Publication of WO2012145531A2 publication Critical patent/WO2012145531A2/fr
Publication of WO2012145531A8 publication Critical patent/WO2012145531A8/fr
Publication of WO2012145531A3 publication Critical patent/WO2012145531A3/fr

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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M8/00—Fuel cells; Manufacture thereof
    • H01M8/10—Fuel cells with solid electrolytes
    • H01M8/12—Fuel cells with solid electrolytes operating at high temperature, e.g. with stabilised ZrO2 electrolyte
    • H01M8/1213—Fuel cells with solid electrolytes operating at high temperature, e.g. with stabilised ZrO2 electrolyte characterised by the electrode/electrolyte combination or the supporting material
    • H—ELECTRICITY
    • 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
    • H01M4/8825—Methods for deposition of the catalytic active composition
    • H01M4/8867—Vapour deposition
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/86—Inert electrodes with catalytic activity, e.g. for fuel cells
    • H01M4/90—Selection of catalytic material
    • H01M4/9016—Oxides, hydroxides or oxygenated metallic salts
    • H01M4/9025—Oxides specially used in fuel cell operating at high temperature, e.g. SOFC
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/86—Inert electrodes with catalytic activity, e.g. for fuel cells
    • H01M4/90—Selection of catalytic material
    • H01M4/9016—Oxides, hydroxides or oxygenated metallic salts
    • H01M4/9025—Oxides specially used in fuel cell operating at high temperature, e.g. SOFC
    • H01M4/9033—Complex oxides, optionally doped, of the type M1MeO3, M1 being an alkaline earth metal or a rare earth, Me being a metal, e.g. perovskites
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M4/00—Electrodes
    • H01M4/86—Inert electrodes with catalytic activity, e.g. for fuel cells
    • H01M4/90—Selection of catalytic material
    • H01M4/9041—Metals or alloys
    • H01M4/905—Metals or alloys specially used in fuel cell operating at high temperature, e.g. SOFC
    • H01M4/9066—Metals or alloys specially used in fuel cell operating at high temperature, e.g. SOFC of metal-ceramic composites or mixtures, e.g. cermets
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M8/00—Fuel cells; Manufacture thereof
    • H01M8/10—Fuel cells with solid electrolytes
    • H01M8/12—Fuel cells with solid electrolytes operating at high temperature, e.g. with stabilised ZrO2 electrolyte
    • H01M8/124—Fuel cells with solid electrolytes operating at high temperature, e.g. with stabilised ZrO2 electrolyte characterised by the process of manufacturing or by the material of the electrolyte
    • H01M8/1246—Fuel cells with solid electrolytes operating at high temperature, e.g. with stabilised ZrO2 electrolyte characterised by the process of manufacturing or by the material of the electrolyte the electrolyte consisting of oxides
    • H01M8/1253—Fuel cells with solid electrolytes operating at high temperature, e.g. with stabilised ZrO2 electrolyte characterised by the process of manufacturing or by the material of the electrolyte the electrolyte consisting of oxides the electrolyte containing zirconium oxide
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • H01M8/00—Fuel cells; Manufacture thereof
    • H01M8/10—Fuel cells with solid electrolytes
    • H01M8/12—Fuel cells with solid electrolytes operating at high temperature, e.g. with stabilised ZrO2 electrolyte
    • H01M8/124—Fuel cells with solid electrolytes operating at high temperature, e.g. with stabilised ZrO2 electrolyte characterised by the process of manufacturing or by the material of the electrolyte
    • H01M8/1246—Fuel cells with solid electrolytes operating at high temperature, e.g. with stabilised ZrO2 electrolyte characterised by the process of manufacturing or by the material of the electrolyte the electrolyte consisting of oxides
    • H01M8/126—Fuel cells with solid electrolytes operating at high temperature, e.g. with stabilised ZrO2 electrolyte characterised by the process of manufacturing or by the material of the electrolyte the electrolyte consisting of oxides the electrolyte containing cerium oxide
    • 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
    • H01M8/1286—Fuel cells applied on a support, e.g. miniature fuel cells deposited on silica supports
    • 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
    • H01M4/8825—Methods for deposition of the catalytic active composition
    • H01M4/8867—Vapour deposition
    • H01M4/8871—Sputtering
    • 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

  • This specification relates to the field of ion conductive electrolyte materials, and more particularly to a multilayer structure for ion conductivity.
  • Ion conductive materials are used in applications where conductivity of ionic species through a solid state phase is desired.
  • the ionic conductivity may be specific to a particular ionic species for a given ion conductive material.
  • the ionic conductivity may also be selective for ionic species in contrast to electronic conduction.
  • Ion conductive materials may be used as membranes to facilitate ion exchange processes and/or reactions, such as an electrolyte in an electrochemical cell.
  • a solid-oxide fuel cell uses an ion conductive electrolyte, or SOFC electrolyte, to selectively conduct oxygen ions in order to generate electrical current.
  • SOFC electrolyte may be selected based on a high ionic conductivity and a low electronic conductivity for efficient operation of the SOFC.
  • SOFCs are often operated at high temperatures up to about 1100°C in order to attain desired ion conductive properties of the SOFC electrolyte.
  • a high operating temperature of an SOFC is energetically disadvantageous and may be associated with a range of deleterious material properties that can shorten the lifetime of SOFC components.
  • FIG. 1 is a block diagram of a prior art SOFC
  • FIG. 2 is a block diagram of selected elements of an embodiment of a novel and patentably distinct ion conductive material
  • FIG. 3 is an image of a multilayer thin film
  • FIG. 4 is a block diagram of selected elements of an embodiment of a novel SOFC stack.
  • FIG. 5 is a flowchart disclosing an exemplary method of forming a novel ion conductive material.
  • the present disclosure pertains to a novel ion conductive material that is suitable for various applications where improved ionic conductivity is desired through a solid state structure, such as a membrane.
  • an improvement in the ionic conductivity may be manifest as a lower temperature for a given ionic conductivity.
  • Exemplary embodiments disclosed herein are described in the context of an electrolyte suitable for conducting oxygen ions in an SOFC.
  • SOFC embodiments are intended as descriptive, yet non-limiting, examples and that the novel ion conductive material disclosed herein may be used to advantageously conduct various types of ions in a number of different applications, as desired, including electrochemical electrolytes, ion exchange membranes, purification membranes, decontamination membranes, and ion exchange chromatography, among others.
  • the novel ion conductive material described herein may be configured to transport any of a number of ion species, including: O “ , O 2" (oxygen anion); H + (proton); OH “ (hydroxide ion); single-charged monoatomic ions, such as Na + ,K + , CI " ; double-charged monoatomic ions, such as Ca 2+ , Mg 2+ ; polyatomic inorganic ions; and organic ions.
  • widget 12-1 refers to an instance of a widget class, which may be referred to collectively as widgets 12 and any one of which may be referred to generically as a widget 12.
  • a prior art SOFC employs an electrochemical reduction- oxidation (redox) reaction of a gaseous fuel with oxygen to generate electrical current and water exothermically.
  • the gaseous fuel may be a vaporized hydrocarbon, hydrogen, or other fuel that is oxidized at an anode separated by the SOFC electrolyte from a cathode, where reduction of oxygen from a supplied source, such as air, occurs.
  • oxygen ions are drawn from the cathode by diffusion to react with the fuel at the anode, which provides a source of the voltage potential across the anode and the cathode.
  • Electronic current flowing through an external circuit across the anode and the cathode provides electrical energy output and a pathway for the redox reaction to be sustained in the SOFC.
  • desired properties of the anode material and the cathode material include high porosity, high electrical conductivity and high ionic conductivity, which favor the redox reaction.
  • desired properties of the SOFC electrolyte include high ionic conductivity but low electrical conductivity, in order to prevent current leakage that would inhibit transport phenomena associated with the redox reaction, as described above.
  • the SOFC electrolyte should also be non-porous to prevent mixing of the fuel (i.e., organic compounds) and oxidant gas feeds.
  • Many conventional SOFC electrolyte materials exhibit desirable ion conduction only at relatively high temperatures, that is, well above 600°C and up to about 1100°C.
  • a conventional SOFC may be formed with a solid-state sandwich comprising three individual layers: the anode, the cathode and the SOFC electrolyte.
  • the anode of an SOFC may be composed of Ni (nickel), Cu (copper), Co (cobalt), Ru (ruthinium), which may be dispersed with a ceramic particulate, such as YSZ (yttria-stabilized zirconia), or Ce0 2 (ceria), to form a porous cermet.
  • the anode may further be doped with a noble metal, such as Mo (molybdenum), Au (gold), Ru, and Li (lithium), among others.
  • An alloy composition, such as Ni-Cu, Ni-Co, Cu-Co may also be used for a metallic fraction of the anode.
  • perovskites specifically titanates and chromates, which may be doped with Sr (strontium), La (lanthanum), Mn (manganese), Ga (gallium), Gd (gadolinium), Y (yttrium), Ni (niobium), Fe (iron), Co, Ni, and Cu.
  • Materials that have been used for the cathode in an SOFC include perovskite oxides, of the form ABO 3 , where A may be Ba (barium), La, Sr and/or Ga; while B may be Co, Fe, Mn and/or Mg.
  • the SOFC electrolyte has been formed as a single layer of ceramic material.
  • Conventional SOFC electrolytes have been formed using specialized ceramic powders which are sintered to achieve a desired uniform microstructure of perovskite and/or fluorite structure types.
  • fluorite structures for SOFC electrolytes are Gd-doped ceria (Gd:Ce0 2 or GCO), Sm (samarium)-stabilized ceria (Sm:Ce0 2 or SCO), and yttria- stabilized zirconia (Y:Zr0 2 or YSZ).
  • YSZ in bulk form is a good ionic conductor with very good electronic insulating properties and has been used for SOFC electrolyte applications.
  • a commonly used formulation in bulk form is YSZ having 8 mol % Y 2 0 3 content.
  • ion conduction of bulk YSZ to a degree feasible for SOFC operation i.e., high oxide ion conductivity sufficient to efficiently sustain the redox reaction
  • Ion conductive material 200 is comprised of a multilayer of alternating phases: insulating phase 202 and conducting phase 204.
  • Insulating phase 202 is a material that is a good electronic insulator
  • conducting phase 204 is a material that is a good electronic conductor. Since insulating phase 202 is thoroughly interspersed between layers of conducting phase 204, the overall electrical conduction of ion conductive material 200 may be sufficiently low such that, in aggregate, ion conductive material 200 may be considered to be an insulating film or membrane.
  • both insulating phase 202 and conducting phase 204 may exhibit very good ionic conductivity.
  • the ion conduction property of insulating phase 202 and/or conducting phase 204 may result from their respective material composition and may be a function of temperature, environment, or dependent on a particular ion species that is diffused or conducted through ion conductive material 200.
  • the ion conduction property of insulating phase 202 and/or conducting phase 204 may also be a function of layer thickness 212 and/or 214, respectively, as will now be described in further detail.
  • ion conductive material 200 may be formed using a deposition process to deposit, or grow, insulating phase 202 and conducting phase 204, in an alternating manner.
  • the deposition process used to manufacture ion conductive material 200 may be any of a number of known thin-film deposition processes, such as pulsed laser deposition (PLD), RF/plasma deposition (sputtering), molecular beam epitaxy (MBE), cathodic arc deposition (arc-PVD), or electron beam evaporation, among other types of physical vapor deposition (PVD).
  • PLD pulsed laser deposition
  • MBE molecular beam epitaxy
  • arc-PVD cathodic arc deposition
  • electron beam evaporation among other types of physical vapor deposition (PVD).
  • insulating phase 202 and/or conducting phase 204 may be used to form ion conductive material 200.
  • CVD chemical vapor deposition
  • a deposition process used to grow insulating phase 202 and/or conducting phase 204 may result in a highly non-porous composite form of ion conductive material 200.
  • a deposition process used to grow insulating phase 202 and/or conducting phase 204 may result in substantially pure individual layers of a desired chemical composition that have not been adulterated or contaminated in an undesired manner.
  • layer thickness 212 and/or 214 may be controllably dimensioned to be extremely small, down to a range of about 5-10 nanometers (nm). Due to the observation that material properties in the nanometer scale may be governed by quantum mechanics (also known as the quantum size effect), substantially different electronic and/or ionic transport properties may be observed and exploited, even when the underlying mechanisms are not yet well understood.
  • quantum mechanics also known as the quantum size effect
  • One factor that may govern quantum size effects in nanoscale films is the vastly increased ratio of surface area to volume, similar to that of nanoparticles.
  • ion conductive behavior of insulating phase 202 may be drastically and unexpectedly different when deposited as a nanofilm than was previously observed for the same material in bulk form, which may impart significantly favorable properties to ion conductive material 200.
  • a temperature dependence of ion conductive behavior may be observed to be different in a deposited nanofilm as compared to the bulk material form. It is therefore noted that different values fnr a nhvsical dimension of a nanoscale thin-film (e.g., thickness) may drastically change and/or govern material properties, in particular, electronic and/or ion transport properties.
  • layer thickness 212 of insulating phase 202 may be about 10 nm, while layer thickness 214 of conducting phase 204 may be about 100 nm.
  • insulating phase 202 is formed as a first fluorite-type ceramic material, ion conduction of insulating phase 202 having about 10 nm layer thickness 212 may be significantly improved in comparison to bulk properties of that same material (e.g., for dimensions greater than about 1 ⁇ ). The improvement in ion conduction may be manifested as a much higher ion conductivity at a lower temperature, or more generally, as higher ion conductivity versus temperature.
  • conducting phase 204 is formed as a second fluorite-type ceramic material exhibiting substantially higher ion conduction than insulating phase 202, the overall ion conduction of ion conductive material 200 may be significantly improved in comparison to a bulk material comprised of the first fluorite-type material.
  • insulating phase 202 retains low electronic conductivity, even at layer thickness 212 of about 10 nm, then ion conductive material 200 may behave in aggregate as an insulator, even though conducting phase 204 is a good electronic conductor. It is noted that similar properties, or analogous changes in properties, may be observed with perovskite-type ceramic materials formed in the nanometer scale for insulating phase 202 and/or conducting phase 204.
  • ion conductive material 200 is depicted having two (2) alternating layers of insulating phase 202 and conductive phase 204.
  • sublayer 210 of ion conductive material 200 may refer to a single instance of insulating phase 202 and conductive phase 204.
  • ion conductive material 200 may be configured with two sublayers 210, as shown in FIG. 2.
  • configurations of ion conductive material 200 having different numbers of sublayers 210, as well as configurations terminating on two sides with an instance of insulating phase 202 may be implemented in different embodiments, as desired.
  • the number of alternating layers as well as a relative thicknesses of each layer may be varied or 'tuned' or 'modulated' to achieve desired aggregate properties of ion conductive material 200, in particular, with respect to desired ion conductivity and/or electronic conductivity.
  • FIG. 3 a transmission-electron microscopy image of an embodiment of an ion conductive multilayer film having alternating layers of barium titanate and strontium titanate is shown.
  • the non-porous multilayer film is shown having 12 sublayers that are less than about 100 nm in thickness and is illustrative of various types of ceramic thin-films that may represent ion conductive materials, as described herein.
  • SOFC electrolyte 410 may be formed with ion conductive material 200 (see FIG. 2) and may represent a configuration suitable for use as an SOFC electrolyte at a relatively low temperature.
  • SOFC 400 includes anode 406 and cathode 408.
  • anode 406 and cathode 408 are formed using a new double -perovskite oxide including Pr (praseodymium), namely PrBaCo 2 0 5+0 or PBCO.
  • cathode 408 is formed using PBCO while anode 406 is formed using Ni/YSZ cermet.
  • SOFC electrolyte 410 is shown comprising four (4) sublayers 420 of insulating phase 402 and conducting phase 404, along with terminating insulating phase 402-1 at anode 406.
  • insulating phase 402 may be formed from YSZ having about 10 nm thickness
  • conducting phase 404 may be formed from GCO having about 100 nm thickness (not drawn to scale in FIG. 4) in which a ratio of Gd:Ce is about 0.25.
  • SOFC stack 400 may be configured to sustain the redox reaction at temperatures as low as 400°C. It is noted that, in particular embodiments, SOFC stack 400 may be configured with six (6), eight (8), twelve (12), sixteen (16) or more sublayers 420, among other desired configurations.
  • respective composite material layers of ion conductive material 200 and SOFC electrolyte 410 are shown having uniform thickness for descriptive clarity.
  • a uniformity of respective material layers of ion conductive material 200 and SOFC electrolyte 410 may vary with an acceptable variance, for example, such as within about 1 nm.
  • a desired thickness of a particular type of material layer may vary across ion conductive material 200 and SOFC electrolyte 410.
  • different instances of insulating phase 402 may be grown to different thickness, such as 10 nm, 8, nm, 5 nm, 20 nm, etc., within a single instance of SOFC electrolyte 410.
  • Method 500 may begin by growing (operation 502) a first material layer.
  • the first material layer may be a nanoscale film, such as insulating phase 202 (see FIG. 2).
  • a second material layer may be grown (operation 504).
  • a deposition process as described previously herein, may be employed to grow material layers in operations 502 and 504.
  • An individual layer thickness, which may be in the nanoscale range, of material layers formed in operations 502 and 504 may be tuned for desired properties, in particular, for desired ion conductivity and/or for desired electronic conductivity.
  • a decision may be made whether a desired number of sublayers has been formed (operation 506).
  • method 500 may loop back to operation 502 and operation 504 for growing additional material layers.
  • a terminal layer may be grown (operation 508).
  • the terminal layer may be another instance of the first or second material layers, or may be a different material than the first and/or second material layers. It is noted that, in certain embodiments, operation 508 may be omitted from method 500.
  • additional operations for growing material layers of desired composition and thickness may be employed in conjunction with method 500 to form a desired structure, such as an SOFC electrolyte.

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  • Chemical Kinetics & Catalysis (AREA)
  • General Chemical & Material Sciences (AREA)
  • Electrochemistry (AREA)
  • Manufacturing & Machinery (AREA)
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Abstract

L'invention concerne un nouveau matériau à conductivité ionique pouvant être réalisé sous la forme d'une structure multicouche à couches minces. La structure multicouche à couches minces peut être formée à partir de plusieurs sous-couches à conductivité ionique d'un isolant électronique et d'un conducteur ionique. Une épaisseur de l'ordre du nanomètre de l'isolant électronique peut être sélectionnée pour obtenir des propriétés ioniques souhaitables pouvant être différentes des propriétés du matériau massif en raison d'effets de taille quantique. La structure multicouche à couches minces peut se comporter dans un agrégat en tant qu'isolant électronique tout en se comportant en tant que conducteur ionique à des températures relativement basses. La structure multicouche à couches minces peut être utilisée en tant qu'électrolyte dans une pile à combustible à oxyde solide (SOFC, Solid Oxide Fuel Cell) pour la conduction d'ions oxygène à des températures relativement basses, par exemple inférieures à environ 600°C.
PCT/US2012/034285 2011-04-21 2012-04-19 Structure multicouche à conductivité ionique WO2012145531A2 (fr)

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US201161477959P 2011-04-21 2011-04-21
US61/477,959 2011-04-21

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WO2012145531A3 WO2012145531A3 (fr) 2013-02-21

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Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2015004237A1 (fr) * 2013-07-10 2015-01-15 Danmarks Tekniske Universitet Hétérostructure à film mince stabilisée destinée à des applications électrochimiques

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6849354B2 (en) * 2000-07-04 2005-02-01 Nissan Motor Co., Ltd. Solid oxide fuel cell having perovskite solid electrolytes
US7452622B2 (en) * 2002-01-16 2008-11-18 Alberta Research Council Inc. Metal-supported tubular fuel cell
US20090011314A1 (en) * 2007-07-05 2009-01-08 Cheng-Chieh Chao Electrode/electrolyte interfaces in solid oxide fuel cells
WO2010029242A1 (fr) * 2008-09-11 2010-03-18 Commissariat A L'energie Atomique Electrolyte pour pile sofc et son procédé de fabrication
US20110076594A1 (en) * 2009-09-30 2011-03-31 Zeng Fan Ceria-based electrolytes in solid oxide fuel cells

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US6849354B2 (en) * 2000-07-04 2005-02-01 Nissan Motor Co., Ltd. Solid oxide fuel cell having perovskite solid electrolytes
US7452622B2 (en) * 2002-01-16 2008-11-18 Alberta Research Council Inc. Metal-supported tubular fuel cell
US20090011314A1 (en) * 2007-07-05 2009-01-08 Cheng-Chieh Chao Electrode/electrolyte interfaces in solid oxide fuel cells
WO2010029242A1 (fr) * 2008-09-11 2010-03-18 Commissariat A L'energie Atomique Electrolyte pour pile sofc et son procédé de fabrication
US20110076594A1 (en) * 2009-09-30 2011-03-31 Zeng Fan Ceria-based electrolytes in solid oxide fuel cells

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2015004237A1 (fr) * 2013-07-10 2015-01-15 Danmarks Tekniske Universitet Hétérostructure à film mince stabilisée destinée à des applications électrochimiques

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WO2012145531A3 (fr) 2013-02-21

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