CN116742085A - Composite ceramic electrolyte of solid oxide fuel cell and preparation method thereof - Google Patents

Composite ceramic electrolyte of solid oxide fuel cell and preparation method thereof Download PDF

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Publication number
CN116742085A
CN116742085A CN202310717602.8A CN202310717602A CN116742085A CN 116742085 A CN116742085 A CN 116742085A CN 202310717602 A CN202310717602 A CN 202310717602A CN 116742085 A CN116742085 A CN 116742085A
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China
Prior art keywords
electrolyte
fuel cell
composite ceramic
base
oxide fuel
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CN202310717602.8A
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Chinese (zh)
Inventor
白江云
张帅
韩修豪
程丽亚
贺建宇
钟秦
韩敏芳
朱腾龙
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Nanjing University of Science and Technology
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Nanjing University of Science and Technology
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Priority to CN202310717602.8A priority Critical patent/CN116742085A/en
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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
    • 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
    • H01M8/124—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
    • H01M2008/1293—Fuel cells with solid oxide electrolytes
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
    • Y02E60/30—Hydrogen technology
    • Y02E60/50—Fuel cells

Abstract

The invention discloses a solid oxide fuel cell composite ceramic electrolyte and a preparation method thereof. The composite electrolyte is prepared from continuously compact zirconia base/(Ce, zr) O 2 The three-layer electrolyte is composed of a base/cerium oxide base. The invention adopts a precursor salt solution of cerium oxide-based electrolyte, and prepares continuous compact cerium oxide-based electrolyte on sintered zirconium oxide-based electrolyte by a spin coating method or a hydrothermal in-situ growth method, and generates (Ce, zr) O in-situ between the zirconium oxide-based electrolyte and the cerium oxide-based electrolyte by one-time sintering 2 A base electrolyte. The three-layer electrolyte has the characteristics of continuous and compact structure, and the SOFC single cell prepared by the method has the advantages of low cost, small surface resistance, high performance, long service life and the like.

Description

Composite ceramic electrolyte of solid oxide fuel cell and preparation method thereof
Technical Field
The invention relates to a solid oxide fuel cell composite electrolyte and a preparation method thereof, belonging to the field of solid oxide fuel cells/electrolytic cells.
Background
During the last decades, a great deal of research and development effort has been devoted to the improvement of oxygen electrodes. The cathode material most commonly used in commercial application of SOFC is La 0.6 Sr 0.4 Co 0.2 Fe 0.8 O 3-δ (LSCF), which is a mixed ionic and electronic conductor with very high ionic and electronic conductivity and fast reaction kinetics. However, at high temperatures the Sr element in LSCF diffuses into the zirconia-based electrolyte (e.g., YSZ) and forms a secondary insulation with the Zr element SrO-ZrO 2 Phase (mainly SrZrO 3 ) The ionic conductivity of these phases is significantly reduced, impeding electron conduction, and degrading battery performance and stability. Cerium oxide-based materials have high electron conductivity even exceeding that of electrolytes, so it is currently common to add a cerium oxide-based thin film (GDC) layer to the electrolytes and cathode materials to reduce diffusion of Sr element along grain boundaries or defects, and improve battery performance and stability.
The current preparation method and process of the GDC isolation layer are deficient: the preparation of the micron-sized isolation layer can be realized by adopting advanced coating processes such as EVD (electro-dynamic deposition), PLD (pulse laser deposition), thermal spraying and the like, but the cost is high, the practicability is poor, and the isolation layer is in poor contact with an electrolyte and a cathode interface, so that the isolation layer cannot withstand long-term operation for tens of thousands of hours and the SOFC system start-stop thermal cycle. Therefore, a screen printing process and a high-temperature sintering method are commonly adopted at home and abroad to prepare the GDC on the surface of the compact YSZ. Due to the effect of high temperature, a GDC/YSZ inter-diffusion layer ((Ce, zr) O) is formed between GDC and YSZ 2 ). When the GDC co-sintering temperature is lower than 1100 ℃, no obvious inter-diffusion phenomenon occurs, and the formed diffusion phase is in an island chain shape. When the temperature is more than 1100 ℃, (Ce, zr) O 2 Layer followingThe increase in the co-sintering temperature became gradually continuous and the thickness increased, significant interdiffusion between GDC and YSZ occurred at 1400 ℃, and in the GDC interlayer, the Ce content was higher and the Zr content was lower, but the chemical properties of the YSZ electrolyte were not changed. Ideally, a broad, ce-rich and Zr-deficient (Ce, zr) O 2 The layer should be effective to prevent SrZrO 3 Is formed by the steps of (a).
Although the literature reports (Ce, zr) O 2 The conductivity of solid solutions is lower, but the results of the German Julich and KIT studies indicate that continuous (Ce, zr) O is formed by high temperature sintering (temperature above 1400 ℃ C.) 2 Can effectively block the diffusion of Sr element in LSCF cathode and avoid SrZrO 3 The positive effect of the increase in SOFC stability is over (Ce, zr) O 2 The lower ionic conductivity of the layer may cause losses.
Disclosure of Invention
The invention aims to provide a solid oxide fuel cell composite electrolyte and a preparation method thereof. The composite electrolyte is formed by continuously compacting zirconia-based/(Ce, zr) O 2 The invention adopts precursor salt solution of cerium oxide electrolyte to prepare continuous compact cerium oxide electrolyte on sintered zirconium oxide electrolyte by spin coating method or hydrothermal in-situ growth method, and generates (Ce, zr) O in-situ between the zirconium oxide electrolyte and cerium oxide electrolyte by high-temperature sintering 2 The base electrolyte can effectively prevent the reaction between the zirconia base electrolyte and the perovskite and other high-activity electrodes and the diffusion deposition of high-temperature elements, and then the anode support battery is manufactured.
The technical proposal for solving the problems in the prior art is as follows:
a solid oxide fuel cell composite electrolyte, the solid oxide fuel cell composite electrolyte being prepared by:
(1) Preparing a precursor solution by adopting soluble salt with the same component as the doped cerium oxide electrolyte, and preparing a compact doped cerium oxide electrolyte layer on the sintered compact solid oxide half-cell zirconia-based electrolyte by a spin coating or hydrothermal in-situ growth method.
Preferably, the precursor solution is a soluble Ce salt, including but not limited to trivalent nitrate, oxalate, acetate, chloride, etc.; or a mixture of a soluble salt of Ce and a soluble salt of lanthanide, wherein the soluble salt of lanthanide includes, but is not limited to, a trivalent nitrate such as La, gd, sm, pr, nd, an oxalate, an acetate, a chloride, etc., wherein the molar ratio of the soluble salt of Ce is not less than 50%, and the concentration of the precursor solution is 0.01-1mol/L.
(2) Then through one high temperature calcination, in situ formation of (Ce, zr) O between the zirconia-based electrolyte and the ceria-based electrolyte 2 A base electrolyte.
Preferably, the calcination temperature is 1200-1300 ℃, and the calcination time is not less than 1h.
Compared with the prior art, the invention has the advantages that:
(1) The three layers are all continuous compact ceramic films, and (Ce, zr) O 2 The thickness of the base and the cerium oxide base is smaller than 1 micron, only one sintering at a lower temperature is needed, and three layers of continuous compact composite electrolytes with different thicknesses can be obtained by adjusting the sintering time, and meanwhile, the three layers of continuous compact composite electrolytes have the characteristics of high density, low surface resistance, low preparation cost and the like.
(2) Continuously dense zirconia-based/(Ce, zr) O 2 The composite electrolyte based on the base/cerium oxide can realize high-performance output and effectively prevent SrZrO during high-temperature long-time operation 3 And simultaneously achieve high performance and long life operation.
Drawings
Fig. 1 (a) is a conventional single cell preparation flowchart, (b) is a composite electrolyte single cell preparation flowchart proposed by the present invention, and (c) is a composite electrolyte single cell structure diagram proposed by the present invention.
Fig. 2 is a graph of power density at 800 ℃ for screen printing of a prepared anode supported cell sample (comparative example 1) and a spin-on build composite electrolyte cell (example 1) sample.
Fig. 3 (a) is a long-term electrogram of a spin-on build composite electrolyte cell sample (example 1). (b) Is a graph comparing electrochemical performance of the battery at 720 ℃ before and after long-term discharge.
Fig. 4 is a cross-sectional view of the microstructure of a sample of a spin-on-fabricated composite electrolyte cell fabricated in example 1.
Fig. 5 is an XRD pattern of GDC surface of a hydrothermally constructed composite electrolyte single cell sample fabricated in example 2 at different sintering temperatures, (a) blank YSZ surface XRD pattern at different sintering temperatures, and (b) GDC surface XRD pattern after hydrothermal treatment at different sintering temperatures.
Fig. 6 is a graph comparing the electrical power density at 800 c of a hydrothermally constructed composite electrolyte cell sample fabricated at different sintering temperatures made in example 2 with a screen-printed anode-supported cell sample (comparative example 1).
FIG. 7 (a) is a long-term electrogram of a cell having a GDC sintering temperature of 1200℃in example 2; (b) Is the long-term electrography of the single cell with the GDC sintering temperature of 1300 ℃.
Detailed Description
The invention is further described in detail below with reference to examples and figures.
The electrolyte material of the thin film electrolyte of the solid oxide cell in each of the following examples is Y-doped ZrO 2 (YSZ) in practice, the methods of the invention are not limited to YSZ electrolyte films, as other types of electrolyte films exist.
The following examples use precursors of Ce, gd-hydrated nitrate electrolytes, and in practice, the methods described herein are not limited to Ce, gd-nitrate solutions, and soluble salts include, but are not limited to, la, gd, sm, pr, nd and other common trivalent nitrates, oxalates, acetates, chlorides, and the like. A compact GDC isolation layer is prepared on the sintered solid oxide battery YSZ electrolyte, and three layers of continuous compact composite ceramic electrolytes are obtained through one-time calcination treatment, so that the reaction between the zirconia-based electrolyte and a perovskite and other high-activity electrodes and the high-temperature element diffusion deposition are effectively prevented, and the battery performance is improved.
Comparative example 1 preparation of a silk-screened anode-supported cell
Gadolinium oxide doped ceria (GDC) was screen printed on NiO-YSZ (firing temperature 1250 ℃) half cell after firing, at 1250 ℃Calcining for 3h; LSCF-GDC LSCF was screen printed on GDC with an area of 0.5cm 2 Calcining at 1075 ℃ for 2 hours; screen-printed silver mesh current collectors on the anode and cathode sides were made into single cells, after which testing was performed and repeated to exclude contingencies.
EXAMPLE 1 spin coating construction of YSZ/(Ce, zr) O 2 GDC composite electrolyte
The volume fractions of water and ethanol in the solution are respectively 60% and 40%, polyvinylpyrrolidone (PVP) with mass fraction of 5% is added, the solution is sealed by tinfoil, and the solution is heated and dissolved at 60 ℃. Gd (NO) 3 ) 3 ·6H 2 O and Ce (NO) 3 ) 3 ·6H 2 O, molar ratio of 0.1:0.9 (Ce 0.9 Gd 0.1 O 2-m ) Dissolving at 60 ℃ to prepare CeO of 1.0mol/L 2 Spin coating liquid. Then the anode support half cell is fixed on the sucker of the spin coater in the middle, and the pipette gun sucks 40 mu LCeO 2 The spin-coated droplets were on the YSZ electrolyte side of the half cell, the turntable was first accelerated from 160rpm to 800rpm in 9s, then spun at 2000rpm for 30s, dried at 80℃for 15min, and sintered at 1250℃for 3h. Screen printing LSCF-GDC LSCF cathode with area of 0.5cm 2 Calcining at 1075 ℃ for 2 hours; and collecting electricity at the anode and the cathode by screen printing silver mesh to prepare single cells, and testing the electrochemical performance of the single cells. The microstructure of the section of the battery is photographed by a scanning electron microscope.
As shown in (a) a conventional single cell preparation flow and (b) a composite electrolyte single cell preparation flow proposed by the invention in fig. 1, the screen printing GDC is not dense in the conventional single cell preparation, the invention prepares a dense cerium oxide-based electrolyte on an anode YSZ half cell in the conventional single cell preparation process, and then prepares zirconium oxide-based/(Ce, zr) O through one-time calcination 2 The structure of the constructed cell is shown in figure (c) for the base/ceria-based three-layer electrolyte. The cell cross-section microstructure is shown in FIG. 4, where the combined thickness of the cerium oxide-based electrolyte and IDL is 0.98. Mu.m. The ohmic resistance of the SOFC is mainly determined by the electrolyte, and the thinner cerium oxide-based electrolyte and IDL can reduce the ohmic resistance of the SOFC to a certain extent, and when the cerium oxide-based electrolyte and IDL are smaller than 1 micron, the influence on the ohmic resistance of the cell is smaller.
Electrochemical performance test result at 800 ℃ shows that ohmic impedance of single cell sample prepared by spin coating is 0.185 ohm cm 2 Whereas the ohmic impedance of the single cell sample prepared by screen printing is 0.218 ohm cm 2 The polarization impedance was 1.082 Ω cm, respectively 2 、1.244Ω·cm 2 . The electric power density is shown in FIG. 2, and the maximum power densities of the anode-supported battery sample prepared by screen printing and the composite electrolyte battery sample constructed by spin coating at 800 ℃ are respectively 0.703W/cm 2 、0.611W/cm 2 。
The cell prepared in example 1 was subjected to constant current discharge at 720℃for 300 hours, and the resulting discharge voltage versus time was as shown in FIG. 3 (a), and during the discharge, the cell voltage was attenuated from 0.840V to 0.818V at an attenuation rate of 0.072V/kh. The electrochemical performance of the single cell sample before and after long-term discharge is tested at 720 ℃, after long-term operation, the ohmic resistance of the cell is increased by 0.038 ohm cm 2 While the polarization impedance is reduced by 0.182 Ω cm 2 . The maximum power density was reduced by 0.097W/cm as a result of the electric power density before and after the long-term discharge as shown in FIG. 3 (b) 2 . Thus, the battery exhibits good long-term stability.
EXAMPLE 2 construction of YSZ/(Ce, zr) O by hydrothermal method 2 GDC composite electrolyte
The hydrothermal conditions are selected from the technological conditions for growing GDC, the molar ratio Ce (NO 3 ) 3 ·6H 2 O:Gd(NO 3 ) 3 ·6H 2 O=0.9:0.1, the hydrothermal temperature is 180 ℃, the time is 36h, and the solution concentration is 0.02mol/L. And directly carrying out hydrothermal growth on the electrolyte surface of the YSZ layer to form a compact GDC layer, and sintering at 1150, 1200, 1250 and 1300 ℃. Screen printing LSCF-GDC LSCF cathode with area of 0.5cm 2 Calcining at 1075 ℃ for 2 hours; and collecting electricity at the anode and the cathode by screen printing silver mesh to prepare single cells, and testing the electrochemical performance of the single cells.
XRD characterization was performed on the blank YSZ electrolyte surface, after thermal reaction, and on the GDC surface at each sintering temperature. As shown in FIG. 5, XRD results indicate that the surface that has undergone hydrothermal reaction but has not yet been sintered appears as compared to the hydrothermal pre-blank YSZ electrolyteCharacteristic peaks of GDC are shown. The peaks of GDC and YSZ were unchanged at 1075, 1100, 1150 c, indicating that YSZ did not chemically react with GDC at sintering temperatures below 1200 c. When the sintering temperature is higher than 1200 ℃, the GDC peak gradually moves right and the YSZ peak gradually moves left along with the increase of the sintering temperature, and particularly the first main diffraction peak changes remarkably. The intensity of the first main diffraction peak of GDC (2 theta about 29 degrees) gradually decreases, small impurity peaks appear before the first main diffraction peak of YSZ, and the peak width gradually increases, and the small impurity peaks are (Ce, gd) obtained by comparing with a standard card and consulting the related literature 1-x Zr x O 2 As can be seen from the analysis results, when the sintering temperature is higher than 1200 ℃, YSZ and GDC start to react, zr 4+ And Y is equal to 3+ Gradually diffuses into GDC lattice to form (Ce, zr) O 2 Solid solution, forming GDC/(Ce, zr) O 2 A YSZ three-layer composite electrolyte structure.
As a result of electrochemical performance test at 800℃the GDC sintering temperature was 1200℃and 1250℃and 1300℃respectively, the ohmic resistance distribution was 0.081. Omega. Cm 2 、0.081Ω·cm 2 、0.095Ω·cm 2 Polarization impedance is 1.039 Ω & cm respectively 2 、0.732Ω·cm 2 、1.252Ω·cm 2 Compared with the anode support single cell sample prepared by screen printing, the ohmic resistance and the polarization resistance are reduced, wherein the ohmic resistance is reduced by 65.4%. The electric power density is shown in FIG. 6, the GDC sintering temperature is 1200 ℃,1250 ℃,1300 ℃ and the maximum power density is 0.806W/cm respectively 2 、0.707W/cm 2 、0.648W/cm 2 . The maximum power density of the anode support single cell sample prepared by the screen printing is improved compared with that of the anode support single cell sample prepared by the screen printing.
The cell samples of example 2, in which the GDC sintering temperature was 1200℃and 1300℃were subjected to constant current discharge at 750℃for 300 hours, and the discharge voltage versus time was as shown in FIG. 7. The cell voltage of the single cell with the GDC sintering temperature of 1200 ℃ decays from 0.915V to 0.822V during discharging, and the decay rate is 0.31V/kh. The cell voltage of the single cell with the GDC sintering temperature of 1300 ℃ decays from 0.883V to 0.796V to 0.29V/kh in the discharging process, and the cell shows good long-term stability.

Claims (8)

1. A solid oxide fuel cell composite ceramic electrolyte, characterized in that the solid oxide fuel cell composite ceramic electrolyte is obtained by: preparing dense cerium oxide-based electrolyte on dense zirconium oxide-based electrolyte by adopting soluble salt solution of cerium oxide-based electrolyte through spin coating method or hydrothermal in-situ growth method, and obtaining three layers of continuous dense zirconium oxide-based/(Ce, zr) O through one-time calcination treatment 2 A base/cerium oxide based composite ceramic electrolyte.
2. The solid oxide fuel cell composite ceramic electrolyte of claim 1, wherein the soluble salt is a soluble Ce salt comprising a trivalent nitrate, oxalate, acetate or chloride.
3. The solid oxide fuel cell composite ceramic electrolyte of claim 2, wherein the soluble salt is a mixture of a soluble salt of Ce and a soluble salt of lanthanide, wherein the soluble salt of lanthanide comprises La, gd, sm, pr, nd orthotrivalent nitrate, oxalate, acetate or chloride.
4. The solid oxide fuel cell composite ceramic electrolyte of claim 1, wherein the dense ceria-based electrolyte is prepared by spin coating, a pipette draws a soluble salt solution of the ceria-based electrolyte drop on the YSZ electrolyte side of the half cell, and the turntable is accelerated from 160rpm to 800rpm within 9s and then rotated at 2000rpm for 30s.
5. The solid oxide fuel cell composite ceramic electrolyte of claim 1, wherein the dense ceria-based electrolyte is prepared by a hydrothermal in-situ growth process, hydrothermal conditions are selected from process conditions for growing GDC, molar ratio of metal ions Ce: gd=0.9:0.1, hydrothermal temperature 180 ℃, time 36h.
6. The solid of claim 1A composite ceramic electrolyte for an oxide fuel cell, characterized in that it comprises a zirconia base, (Ce, zr) O 2 The three-layer electrolyte of the base and the cerium oxide base is a continuous, uniform and compact ceramic film, wherein (Ce, zr) O 2 The sum of the base and ceria base thicknesses is less than 1 micron.
7. The solid oxide fuel cell composite ceramic electrolyte of claim 1, wherein (Ce, zr) O is formed by one calcination 2 The calcination temperature of the base electrolyte layer is 1200-1300 ℃, and the calcination time is not less than 1h.
8. A method of preparing a solid oxide fuel cell composite ceramic electrolyte as claimed in any one of claims 1 to 7.
CN202310717602.8A 2023-06-16 2023-06-16 Composite ceramic electrolyte of solid oxide fuel cell and preparation method thereof Pending CN116742085A (en)

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