A high-oxygen calcined proton conductor solid oxide fuel cell electrode material and its preparation method

Abstract

The present invention relates to a composition of an electrode material for a high-oxygen calcined proton-conducting solid oxide fuel cell and a preparation method thereof. We developed a series of Ni-based perovskite oxides Ba(Zr 0.8 Y 0.2 ) x Ni 1‑x O 3‑δ (x = 0.1 - 0.5) for the cathode of a PCFC. Since the electrochemical activity of the Ni-based cathode is not as good as that of the traditional Co-based perovskite, and Ni and Fe perovskite oxides with high valence states and high activity can be synthesized under high-pressure or high-oxygen conditions, a high-oxygen calcination method is used to improve the ORR performance of the Ni-based cathode. The phase structure and electrochemical performance of Ba(Zr 0.8 Y 0.2 ) x Ni 1‑ x O 3‑δ (BZYN) calcined in an air atmosphere were analyzed in detail. BZYN calcined in a pure oxygen atmosphere exhibited a more stable phase structure and higher ORR activity.

Description

Technical Field

[0001] The present invention relates to a composition of an electrode material for a high-oxygen calcined proton-conducting solid oxide fuel cell and a preparation method thereof, belonging to the technical field of solid oxide fuel cells. Background Art

[0002] With the progress of science and technology, humanity's dependence on energy has been increasing. Moreover, due to the combustion of fossil fuels, a series of environmental problems such as the "greenhouse effect" and "haze" have been inevitably triggered. On the other hand, there are certain energy losses during the utilization of traditional fossil fuels, which directly lead to problems such as insufficient energy utilization efficiency and low working efficiency. As a non-renewable energy source, fossil energy will eventually be exhausted as the continuous growth of human energy demand. Therefore, seeking new renewable energy sources and efficient energy conversion technologies has become an important goal for humanity today.

[0003] As a fully solid-state fuel cell structure, the solid oxide fuel cell (SOFC) has good stability and is easy to assemble. Compared with traditional thermal power generation technologies, SOFC has high energy conversion efficiency, no pollution, and wide applicability to fuels, and is one of the most ideal energy conversion devices, having good application prospects at present.

[0004] Currently, the biggest factor affecting the industrialization process of SOFC is the excessively high operating temperature (800 - 1000 °C). If the operating temperature can be reduced to around 500 °C, problems such as electrode material sintering, catalyst poisoning, mismatch between electrode components, and short battery life will be mostly solved. Therefore, reducing the operating temperature of SOFC to the medium and low temperature range has been a research and development hotspot for fuel cells in recent years. However, reducing the temperature will lead to an increase in the polarization resistance of the electrode and electrolyte, thereby reducing the output power of the battery. Currently, we can develop electrode materials with high catalytic activity under medium and low temperature conditions to solve this problem.

[0005] Traditional cobalt-based perovskite oxide materials have been widely studied in medium and low temperature solid oxide fuel cells. However, limited by the limited stock of cobalt resources, non-cobalt-based perovskite oxide materials that can replace them need to be developed, such as nickel-based materials. However, due to the lower electrochemical activity of the Ni-based cathode compared to traditional Co-based perovskites, its application is restricted. Summary of the Invention

[0006] The problems to be solved by this patent are as follows: The polarization impedance of the electrodes of traditional proton-conducting solid oxide fuel cells increases at medium and low temperatures, and the catalytic activity is not high, resulting in a low output power of the cells. In addition, the electrochemical activity of the Ni-based cathode is not as good as that of the traditional Co-based perovskite. The present invention proposes a method for improving the electrochemical performance of solid oxide cells by using a cathode material of a proton-conducting solid oxide fuel cell calcined in a high-concentration oxygen atmosphere. The material has the general formula of Ba(Zr 0.8 Y 0.2 ) x Ni 1-x O 3-δ (BZYN). By calcining in a high-concentration oxygen atmosphere, the present invention reduces the oxygen vacancies in the cathode, stabilizes the phase structure, and improves the ORR ability of the cathode. This method has a simple process and provides an idea for the design of high-performance non-cobalt-based cathodes.

[0007] In the first aspect of the present invention, there is provided:

[0008] A high-oxygen-calcined proton-conducting solid oxide fuel cell electrode material with the chemical general formula of ABO 3-δ , and the specific molecular formula is: Ba(Zr 0.8 Y 0.2 ) x Ni 1-x O 3-δ (BZYN), where δ is the oxygen vacancy content and x = 0.1 - 0.5.

[0009] In one embodiment, the molecular formula is: Ba(Zr 0.8 Y 0.2 ) 0.3 Ni 0.7 O 3-δ (BZYN0.7).

[0010] In the second aspect of the present invention, there is provided:

[0011] The preparation method of the above high-oxygen-calcined proton-conducting solid oxide fuel cell electrode material includes the following steps:

[0012] Step 1, Weigh a certain mass of Ba(NO 0.8 Y 0.2 ) x Ni 1-x O 3-δ (BZYN) according to the stoichiometric ratio, Ba(NO 3 ) 2 , Zr(NO 3 ) 2 ·5H 2 O, Y(NO 3 ) 3 ·6H 2O and Ni(NO 3 ) 2 ·6H 2 O, appropriate amount of deionized water was added and stirred until dissolved to obtain a clear solution; after complete dissolution, ethylenediaminetetraacetic acid and citric acid monohydrate were added, and then ammonia water was added dropwise until the pH of the solution was between 7 and 8. Under the conditions of heating and stirring, the water was volatilized to obtain a gel-like substance; the gel-like substance was placed in an oven and dried to obtain a cathode material precursor.

[0013] Step 2, the precursor obtained in Step 1 was calcined in a muffle furnace under an air atmosphere or roasted in a tube furnace under a pure oxygen atmosphere to obtain the required cathode material.

[0014] In one embodiment, the molar ratio of total metal ions: ethylenediaminetetraacetic acid (EDTA): citric acid monohydrate (CA): ammonia water is 1:0.5 - 1.5:1 - 3:3 - 20.

[0015] In one embodiment, the drying conditions of the precursor are baking at 140 - 180 °C for 5 - 10 h.

[0016] In one embodiment, the calcination conditions are calcination at 1000 °C for 5 - 10 h under an air or pure oxygen / high oxygen atmosphere, and the heating rate is 2 - 5 °C / min.

[0017] In the third aspect of the present invention, there is provided:

[0018] The use of the above-mentioned solid oxide fuel cell cathode material for fuel cells.

[0019] In one embodiment, the use is as the cathode of a proton-conducting solid oxide fuel cell.

[0020] In one embodiment, the use mentioned above is to reduce cathode oxygen vacancies, stabilize the cathode phase stability, improve the oxygen reduction reaction ability of the cathode and the cell output performance.

[0021] Beneficial effects

[0022] The high-oxygen calcined solid oxide cell cathode material involved in the present invention has the following effects:

[0023] (1) This invention synthesizes the Ba(Zr 0.8 Y 0.2 ) x Ni 1-x O 3-δ (BZYN) cathode material by the sol-gel one-step method, and the elements in the material are evenly distributed, and the synthesis method is simple and efficient.

[0024] (2) By calcination in a pure oxygen / high oxygen atmosphere, the cathode oxygen vacancies are reduced and the phase structure is stabilized.

[0025] (3) Enhance the cathode ORR ability by calcining with pure oxygen / high oxygen. This method has a simple process and provides ideas for the design of high-performance non-cobalt-based cathodes. Description of the Drawings

[0026] Figure 1 is Ba(Zr0.8Y0.2) x Ni 1-x O 3-δ XRD patterns of (BZYN) series oxides after calcination in air atmosphere at 1000 °C for 5 h and then naturally cooled to room temperature;

[0027] Figure 2 are XRD patterns of BZYN series oxides after calcination in air atmosphere and pure oxygen atmosphere at 1000 °C for 5 h, respectively, and then naturally cooled to room temperature;

[0028] Figure 3 is the Arrhenius plot of the cathode ASR values of BZYN0.5, BZYN0.7 and BZYN0.9 varying with temperature during calcination in air with 5 vol.% water partial pressure;

[0029] Figure 4 is the Arrhenius plot of the cathode ASR values of BZYN0.7 varying with temperature during calcination in air with 5 vol.% water partial pressure and in pure oxygen atmosphere;

[0030] Figure 5 is the Nyquist plot of the BZYN0.7 cathode of a symmetrical cell based on BZCYYb electrolyte with BZYN0.7 - O 2 as the electrode tested at 650 °C and 550 °C;

[0031] Figure 6 is the impedance stability plot of a symmetrical cell based on BZCYYb electrolyte with BZYN0.7 - O 2 as the electrode stabilized for 6 h in humid air atmosphere at 600 °C;

[0032] Figure 7 is the SEM image of a symmetrical cell based on BZCYYb electrolyte with BZYN0.7 - O 2 as the electrode;

[0033] Figure 8 is the TG curve of the weight loss of BZYN0.7 after calcination in pure oxygen and air atmospheres respectively;

[0034] Figure 9 are the fitted XPS spectra of Ni 2p of BZYN0.7 - Air and BZYN0.7 - O 2 samples;

[0035] Figure 10 They are the XPS spectra of O1s after fitting of the BZYN0.7-Air and BZYN0.7-O 2 samples;

[0036] Figure 11 Taking Ni + BZCYYb as the anode, BZCYYb as the electrolyte, and BCYN0.7-O 2 as the cathode, a single anode-supported cell with the structure of Ni + BZCYYb|BZCYYb|BCYN0.7-O 2 was prepared, and the I-P and I-V performance curves obtained under the condition of using hydrogen as fuel. Detailed implementation mode

[0037] The present invention relates to a series of Ni-based perovskite oxides Ba(Zr 0.8 Y 0.2 ) x Ni 1-x O 3-δ (x = 0.1, 0.3, 0.5) developed by the self-assembly method and used for the cathode of proton-conducting solid oxide fuel cells. Since the electrochemical activity of the Ni-based cathode is not as good as that of the traditional Co-based perovskite, and the high-valence and highly active Ni and Fe perovskite oxides can be synthesized under high-pressure or high-oxygen conditions, the present invention adopts the method of high-oxygen calcination to improve the ORR performance of the Ni-based cathode. We respectively carried out a detailed analysis of the phase structure and electrochemical performance of Ba(Zr 0.8 Y 0.2 ) x Ni 1-x O 3-δ (BZYN) calcined in air / pure oxygen atmosphere. The BZYN calcined in pure oxygen atmosphere shows a more stable phase structure and higher ORR activity. In the present invention, a high-oxygen calcined cathode material for solid oxide fuel cells and a preparation method are developed, which improve the cathode ORR ability of proton-conducting solid oxide fuel cells.

[0038] Example 1

[0039] This example provides a preparation method for the cathode material Ba(Zr 0.8 Y 0.2 ) x Ni 1- x O 3-δ (BZYN) of medium and low temperature proton-conducting solid oxide cells, and the specific steps are as follows:

[0040] (1) Taking BZYN0.7 as an example, according to Ba(Zr 0.8 Y 0.2 ) 0.3 Ni0.7 O 3-δ Weigh 13.067 g of Ba(NO 3 ) 2 , 5.1518 g of Zr(NO 3 ) 2 ·5H 2 O, 1.1490 g of Y(NO 3 ) 3 ·6H 2 O and 10.1777 g of Ni(NO 3 ) 2 ·6H 2 O and place them in a clean beaker. Add an appropriate amount of deionized water and stir to dissolve on a hot plate with magnetic stirring to obtain a clear solution. Weigh 29.224 g of ethylenediaminetetraacetic acid and 42.028 g of citric acid monohydrate as complexing agents according to the molar ratio of ethylenediaminetetraacetic acid:citric acid monohydrate:total metal ions of 1:2:1 and dissolve them in deionized water.

[0041] (2) After adding the solution containing the complexing agent to the solution containing metal ions, add an appropriate amount of ammonia water until the pH of the solution reaches between 7 and 8, and then stir under magnetic stirring until the water is completely evaporated to obtain a gel-like substance.

[0042] (3) Place the gel-like substance in an oven and calcine it at 180 °C for 5 h to obtain the required precursor.

[0043] (4) Place the precursor in a high-temperature muffle furnace and calcine it at 1000 °C for 5 h to obtain the required BZYN cathode powder. (5) Place the precursor in a high-temperature tubular furnace and calcine it in a high-purity oxygen atmosphere. After calcining at 1000 °C for 5 h, obtain the required BZYN0.7 cathode powder.

[0044] Example 2

[0045] This example provides a preparation and testing method for a symmetrical cell with Ba(Zr 0.8 Y 0.2 ) 0.3 Ni 0.7 O 3-δ (BZYN0.7) as the electrode, and the specific steps are as follows:

[0046] (1) Weigh 1 g of the cathode powder Ba(Zr 0.8 Y 0.2 ) 0.3 Ni 0.7 O 3-δ(BZYN0.7), 10 ml of isopropanol, 2 ml of ethylene glycol, and 0.8 ml of glycerol are poured into a high-energy ball mill. After ball milling for 30 min at 400 r / min, it is transferred to a culture flask with a dropper to obtain the required cathode slurry.

[0047] (2) The prepared BZCYYb electrolyte is preheated on a heating table at 150 °C. The prepared cathode slurry is evenly sprayed on both sides of the electrolyte under the push of an inert gas using a spray gun. After the liquid has completely evaporated, the sprayed electrolyte is calcined in a high-temperature muffle furnace at 1000 °C for 2 h to obtain the required symmetrical cell, which is used for testing the polarization resistance of the cathode material in the temperature range of 500 - 650 °C. Taking BZYN0.7 as an example, the ASR value of the cathode calcined in pure oxygen is significantly lower than that of the cathode calcined in air. At 650, 600, 550, and 500 °C, the ASR values decrease from the original 0.35, 1.06, 3.61, and 17.52 Ω·cm 2 to 0.16, 0.39, 1.03, and 3.13 Ω·cm 2 .

[0048] Example 3

[0049] This example provides a preparation and testing method for a single cell with Ba(Zr 0.8 Y 0.2 ) 0.3 Ni 0.7 O 3-δ (BZYN0.7) as the cathode, and the specific steps are as follows:

[0050] (1) Weigh 1 g of the cathode powder Ba(Zr 0.8 Y 0.2 ) 0.3 Ni 0.7 O 3-δ (BZYN0.7) prepared in Example 1, 10 ml of isopropanol, 2 ml of ethylene glycol, and 0.8 ml of glycerol are poured into a high-energy ball mill. After ball milling for 30 min at 400 r / min, it is transferred to a culture flask with a dropper to obtain the required cathode slurry.

[0051] (2) The prepared NiO - BZCYYb dry-pressed battery sheet is preheated on a heating table at 150 °C. The prepared cathode slurry is evenly sprayed on the electrolyte surface of the dry-pressed sheet under the push of an inert gas using a spray gun. After the liquid has completely evaporated, the sprayed dry-pressed battery is calcined in a high-temperature muffle furnace at 1000 °C for 2 h to obtain the required single cell,

[0052] which is used for testing the battery performance of the cathode material in the temperature range of 500 - 650 °C. BCYN0.7 - O 2The power densities of a single cell at 650,

[0053] 600 and 550 °C are 333, 231 and 112 mW cm -2 .

[0054] Characterization results

[0055] 1. XRD Characterization

[0056] Figure 1 is the XRD pattern of the Ba(Zr 0.8 Y 0.2 ) x Ni 1-x O 3-δ (BZYN) series of oxides prepared in Example 1 after calcination in air at 1000 °C for 5 h and then naturally cooled to room temperature. We found that after self-assembly, BZYN all exhibited a multiphase structure; all consisted of a Zr-rich phase of BaZr 1-x (Y y Ni z ) x O 3-δ cubic perovskite, an Ni-rich phase of BaNi 1-x (Y y Zr z ) x O 3-δ hexagonal perovskite. Among them, the Ni-rich BaNi 1-x (Y y Zr z ) x O 3-δ contains two different oxygen vacancies in the perovskite, which we denoted as m-BZYN and n-BZYN respectively, and the Zr-rich phase of BaZr 1-x (Y y Ni z ) x O 3-δ was denoted as p-BZYN. This figure shows that as the Ni content in the BZYN series of oxides increases, the content of the self-assembled Ni-rich phase gradually increases, and the content of the Zr-rich phase gradually decreases.

[0057] Figure 2Shows the XRD patterns of the BZYN series oxides after calcination in air atmosphere and pure oxygen atmosphere at 1000 °C for 5 h, and then naturally cooled to room temperature. After calcination under high oxygen conditions, the Ni-rich phase m-BZYN at the 26° characteristic peak disappears, and the Ni-rich phase n-BZYN at the 27° characteristic peak increases significantly. This is because in a high oxygen environment, the valence states of metal ions in the perovskite oxide change, and in order to maintain charge balance, the oxygen vacancies in the oxide also change. Calcination in pure oxygen also makes the phase structure of BZYN more stable. Moreover, after calcination in pure oxygen, the relative content of the Ni-rich phase in the BZYN0.5-O 2 ,BZYN0.7-O 2 and BZYN0.9-O 2 samples increases significantly.

[0058] 2. Performance analysis of solid oxide symmetric cells

[0059] We first evaluated the electrochemical activity of BZYN by electrochemical impedance spectroscopy (EIS). The AC impedance spectra of the BCN|BZCYYb|BZYN symmetric cells were measured in the temperature range of 500 - 650 °C. The test atmosphere was first air, and then deionized water was introduced into the test device with air using a water pump and a vaporization device to obtain a "water-air" atmosphere with a water vapor partial pressure of 5 vol.% H 2 O. The ASR values at each temperature point of the cathode were obtained through fitting. The smaller the ASR value, the better the ORR performance of the cathode.

[0060] Figure 3 Shows the Arrhenius plots of the ASR values of the cathodes of BZYN0.5, BZYN0.7, and BZYN0.9 calcined in air as a function of temperature. The ASR values of BZYN0.5, BZYN0.7, and BZYN0.9 at 650, 600, 550, and 500 °C are 1.32, 3.27 and 0.35, 1.06, 3.61, 17.52 and 0.39, 1.14, 4.76, 30.28 Ω·cm 2 respectively. BZYN0.7 has relatively better ORR activity among the three.

[0061] The O 2 concentration in the pure oxygen atmosphere is higher than that in air, which is beneficial to enhancing the metal activity in the oxide. We evaluated the electrochemical activity of BZYN calcined in pure oxygen by electrochemical impedance spectroscopy (EIS). Taking BZYN0.7 shown in Figure 4 as an example, the ASR values of the cathode after calcination in pure oxygen decreased significantly. At 650, 600, 550, and 500 °C, the ASR values decreased from the original 0.35, 1.06, 3.61, and 17.52 Ω·cm 2Drop to 0.16, 0.39, 1.03 and 3.13 Ωcm 2 .

[0062] Figure 5 The Nyquist plots of the BZYN0.7 cathode of the symmetric cell based on the BZCYYb electrolyte with BZYN0.7-O 2 as the electrode tested at 650 °C and 550 °C are given, and the ORR activity advantage of the BZYN0.7 cathode after oxygen calcination can be more intuitively seen.

[0063] Figure 6 It reflects that the symmetric cell based on the BZCYYb electrolyte with BZYN0.7-O 2 as the electrode is stable for 6 h in a wet air atmosphere at 600 °C, and the impedance value does not decay, proving that BZYN0.7-O 2 has good impedance stability.

[0064] Figure 7 The SEM images of the symmetric cell with the BZCYYb electrolyte and BZYN0.7-O 2 as the electrode are given. The symmetric cell consists of a dense BZCYYb electrolyte layer and a porous BZYN0.7-O 2 electrode. After testing, the BZYN0.7-O 2 electrode still has good contact with the BZCYYb electrolyte, which can be attributed to the excellent thermal matching between the BZYN0.7-O 2 material and the BZCYYb electrolyte.

[0065] 3. Thermogravimetric analysis (TGA) characterization

[0066] Figure 8 The weight loss of BZYN0.7 after calcination in pure oxygen and air atmospheres is given. The sample is heated from room temperature to 1000 °C, the test atmosphere is air, and the sample is pre-treated at 300 °C in a muffle furnace for 2 h before testing, mainly to remove the absorbed moisture in the sample. It can be seen from the figure that the weight of the sample remains basically unchanged from room temperature to 400 °C, and obvious weight loss begins only after 400 °C. This is because as the temperature rises, the lattice oxygen in the BZYN0.7 sample begins to be released. We observe that in the battery test range (500 - 650 °C), the weight loss of the sample calcined in pure oxygen is significantly higher than that of the sample calcined in air, which indicates that the sample calcined in pure oxygen can release more oxygen vacancies in the test range, which is beneficial to the transport of oxygen ions in the cathode bulk phase and enhances the ORR activity. Therefore, in the test of the symmetric cell, the ASR value of the cathode sample calcined in pure oxygen is lower than that of the sample calcined in air.

[0067] 4. X-ray Photoelectron Spectroscopy (XPS) Characterization

[0068] Figure 9 The XPS spectra of Ni 2p after fitting for BZYN0.7 are shown. Ni generally shows +2 and +3 valence states in perovskite oxides. According to the fitting results, the binding energies of +2 and +3 valence states of the BZYN0.7 sample correspond to 854.03 eV and 859.6 eV respectively. According to the peak area integration, the ratios of Ni3+ to Ni2+ in the BZYN0.7-Air and BZYN0.7-O 2 samples are 0.38 / 0.62 and 0.55 / 0.45 respectively, and then the average valence states of Ni are +2.38 and +2.55 respectively. The valence state of Ni in BZYN0.7 calcined in pure oxygen atmosphere has increased significantly, indicating that pure oxygen calcination is beneficial to enhancing the activity of Ni ions.

[0069] Figure 10 The O 1s spectra of the BZYN0.7-Air and BZYN0.7-O 2 samples are shown. O 1s is fitted into three characteristic peaks. The binding energy at 526 eV corresponds to lattice oxygen species, the binding energy at 529 eV corresponds to chemically adsorbed oxygen species, and the binding energy at 531 eV corresponds to OH oxygen species. According to the peak area integration after fitting, the ratios of adsorbed oxygen to lattice oxygen in the BZYN0.7-Air and BZYN0.7-O 2 samples are 2.9 and 3.6 respectively. The adsorbed oxygen and lattice oxygen in perovskite oxides can reflect the ORR activity of different materials. The ratio of adsorbed oxygen to lattice oxygen in the BZYN0.7-O 2 sample is higher than that of the BZYN0.7-Air sample, indicating that BZYN0.7 calcined in pure oxygen has better oxygen adsorption capacity and enhanced ORR activity.

[0070] 5. Single Cell Performance Test

[0071] Figure 11 are the I-P and I-V curves of the single cell. We prepared an anode-supported single cell with the structure of Ni+BZCYYb|BZCYYb|BCYN0.7-O 2 using Ni+BZCYYb as the anode, BZCYYb as the electrolyte, and BCYN0.7-O 2 as the cathode, and obtained the I-P and I-V curves of the single cell under the condition of hydrogen as fuel. The power densities of the BCYN0.7-O 2 single cell at 650, 600 and 550 °C are 333, 231 and 112 mW cm -2 .

Claims

1. A high-oxygen calcined proton-conducting solid oxide battery electrode material with a chemical general formula of ABO 3-δ , It is characterized in that The molecular formula is Ba(Zr 0.8 Y 0.2 ) x Ni 1-x O 3-δ , where δ is the oxygen vacancy content and x = 0.1 - 0.5; The preparation method of the described electrode material comprises the following steps: Step 1, weigh a certain mass of Ba(NO 0.8 Y 0.2 ) x Ni 1-x O 3-δ according to the stoichiometric ratio, take Ba(NO 3 ) 2 , Zr(NO 3 ) 4 •5H 2 O, Y(NO 3 ) 3 •6H 2 O and Ni(NO 3 ) 2 •6H 2 O, add an appropriate amount of deionized water and stir to dissolve to obtain a clear solution; after all are dissolved, add ethylenediaminetetraacetic acid and citric acid monohydrate, then dropwise add ammonia water until the pH of the solution is between 7 and 8, and volatilize the water under the condition of heating and stirring to obtain a gel-like substance; place the gel-like substance in an oven to dry to obtain the electrode material precursor; Step 2, place the precursor in a tubular furnace and calcine it in a pure oxygen atmosphere to obtain the required electrode material; the calcination conditions are calcination at 1000 °C for 5 - 10 h in a pure oxygen atmosphere, and the heating rate is 2 - 5 °C / min.

2. The high-oxygen-calcined proton-conducting solid oxide fuel cell electrode material according to claim 1 It is characterized in that Molecular formula Ba(Zr 0.8 Y 0.2 ) 0.3 Ni 0.7 O 3-δ 。 3. The high-oxygen-calcined proton-conducting solid oxide fuel cell electrode material according to claim 1 It is characterized in that the molar ratio of total metal ions: EDTA: citric acid monohydrate: ammonia is 1:0.5 - 1.5:1 - 3:3 - 20.

4. The high-oxygen-calcined proton-conducting solid oxide fuel cell electrode material according to claim 1 It is characterized in that the drying conditions are baking at 140 - 180 °C for 5 - 10 h.

5. Use of the high-oxygen-calcined proton-conducting solid oxide fuel cell electrode material according to claim 1 in a solid oxide fuel cell.

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