KR101100349B1 - Fabrication methods of solid electrolyte of solid oxide fuel cell and solid oxide fuel cell using the same - Google Patents

Abstract

The present invention provides a method of lowering the existing high sintering temperature (≥1500 ° C) through a sintering aid while maintaining the properties of La _0.8 Sr _0.2 Ga _0.8 Mg _0.2 O _2.8 which is widely used as a solid electrolyte of a medium temperature solid oxide fuel cell. According to the present invention, at least one of V, Ba and Li as a sintering aid may be added to a raw powder having La, Sr, Ga, and Mg components and sintered at 1200 to 1300 ° C. The sintering temperature can be lowered without degrading the density and the conductivity characteristics. Therefore, the solid electrolyte for the solid oxide fuel cell can be produced at a low sintering temperature while maintaining the characteristics of the LSGM, thereby enabling simultaneous sintering with the cathode.

Description

Solid electrolyte fuel cell manufacturing method and solid oxide fuel cell manufacturing method using the same {Fabrication methods of solid electrolyte of solid oxide fuel cell and solid oxide fuel cell using the same}

The present invention relates to a method for preparing a solid electrolyte for a solid oxide fuel cell (SOFC) and a method for manufacturing a solid oxide fuel cell using the same, and more particularly, to a multi-component solid oxide having a perovskite structure in a solid electrolyte. The present invention relates to a method for producing a lanthanum gallate oxide sintered body as an electrolyte and a method for manufacturing a solid oxide fuel cell using the same.

BACKGROUND ART A fuel cell is a device that generates electricity by reacting fuel such as hydrogen or natural gas with oxygen, and is recognized as one of the main energy technologies of the future because of its high efficiency, pollution-free, and noise-free characteristics. There are many kinds of fuel cells. Among them, solid oxide fuel cell (SOFC) is composed of a solid electrolyte, an anode where hydrogen is oxidized, and a cathode where ionizes oxygen. The first sintered body is first manufactured, and then the negative electrode material is coated on one side and the positive electrode material is coated on the other side to be heat-treated.

Representative solid electrolytes are Yttria Stabilized Zirconia (YSZ) with fluorite structure, and have characteristics suitable for use as solid oxides such as high ion conductivity, extremely low electron conductivity, and long-term stability in a reducing atmosphere. However, in order to operate the solid oxide fuel cell using the same, there is a disadvantage in that a temperature of about 1000 ° C. is required to increase the ion conductivity of the solid oxide.

When the operating temperature of the solid oxide fuel cell is lowered to 800 ° C. or lower, the manufacturing cost of the fuel cell can be significantly lowered. As a method of lowering the operating temperature, there is a method of reducing the thickness of the solid electrolyte to lower the resistance, configuring the electrode as a support, and replacing it with a new solid electrolyte having high ion conductivity even at low and low temperatures.

Materials having high ionic conductivity at low and low temperatures include fluorite structure oxides such as Scandia substituted zirconia, gadolinian substituted ceria (GDC) and samarium substituted ceria (SDC), and LSGM (Sr- and Mg-doped LaGaO _3). Cation substituted lanthanum gallate having a perovskite structure such as

LSGM is promising as a medium temperature SOFC electrolyte material because of its high ion conductivity, and its oxygen ion conductivity is 0.15 S / cm at 800 ° C, which is about three times higher than YSZ. However, the core technology in the manufacture of fuel cell based on LSGM is to secure the interfacial stability of LSGM / fuel electrode. To solve this problem, low temperature sintering (sintering temperature: 1400 ℃ or less) of LSGM is the most important. LSGM contains four components of oxide, and high temperature heat treatment (calcination) and sintering temperature are required for them to represent a single phase of perovskite structure. For example, in order to form LSGM by the solid-phase reaction method, a calcination temperature of 1200 ° C. is required, and when sintered using fine powder prepared by high temperature calcination, a high temperature of 1400 ° C. or higher is required.

Efforts have been made to reduce the sintering temperature by introducing various manufacturing processes, but it is very difficult to obtain a compact sintered body at a temperature below 1400 ° C. It is known that there are problems of poor electrical conductivity due to existence. When sintered at a temperature of 1400 ~ 1500 ℃ or more, the La component in the LSGM diffuses toward the anode, and Ni diffuses toward the LSGM from anodes such as Ni-GDC, Ni-SDC, Ni-LDC (lanthanum-substituted ceria), and Ni-LSGM. It is known to form a LaNiO ₃ phase at the interface. In the LSGM near the interface, since La is insufficient, there is a problem that a secondary phase such as LaSrGa ₃ O ₇ is not generated and the LaSrGa ₃ O ₇ is not present. Therefore, it is common to form a buffer layer of LDC at the interface between the electrolyte and the cathode.

For the synthesis of LSGM low-temperature sintering powder, organic precursors, carbonate co-precipitation, citric acid, microwave polymerization, glycine, etc. are applied. In addition, spark plasma sintering, hot isostatic pressing (HIP) sintering, and microwave sintering have been applied for low temperature sintering, but the proposed method can ensure the stability of LSGM / fuel electrode. The low-temperature sintering fine powder is not synthesized, and low-temperature sintering is not performed by a commercial method.

The problem to be solved by the present invention is to provide a method for producing a solid electrolyte for a solid oxide fuel cell by low temperature sintering, and a method for producing a solid oxide fuel cell using this method.

In the solid electrolyte production method according to the present invention for solving the above problems is mixed with a sintering aid of a composition containing at least any one of V, Ba and Li to the raw material powder having La, Sr, Ga and Mg components and sintering after molding It includes a step.

The composition of the raw material powder is preferably La _0.8 Sr _0.2 Ga _0.8 Mg _0.2 O _2.8 , even if the temperature of the sintering step is 1200 ~ 1300 ℃ there is no problem in densification. The sintering aid is preferably mixed with 0.1 to 2 mol% based on the raw material powder. If it is added below 0.1 mol%, the effect of sintering promotion is not great, and if it is added more than 2 mol%, the phase purity and electrical conductivity decrease.

In the method of manufacturing a solid oxide fuel cell according to the present invention, after stacking a solid electrolyte compact on a cathode compact, the cathode compact and the solid electrolyte compact are simultaneously sintered at 1200 to 1300 ° C., wherein the solid electrolyte compact is formed. Is characterized in that the raw powder having La, Sr, Ga and Mg components are mixed by molding a sintering aid of a composition containing at least one of V, Ba and Li.

According to the present invention, the existing high sintering temperature (≧ 1500 ° C.) can be lowered to 1200 to 1300 ° C. through a sintering aid while maintaining the properties of LSGM, which is a solid electrolyte material for a medium temperature solid oxide fuel cell. The sintering aid proposed by the present invention improves the phase purity and ion conductivity while reducing the sintering temperature of the solid electrolyte. Therefore, generation of high resistance secondary phase generated at the interface between the solid electrolyte and the fuel electrode can be suppressed, and the interfacial stability of the solid electrolyte / fuel electrode can be improved.

As in the present invention, when the sintering temperature of the LSGM is lowered to 1300 ° C. or lower through the addition of a sintering aid, the buffer layer is unnecessary because the stability of the interface between the anode and the electrolyte is ensured when the cathode support unit cell is constructed. There are advantages such as being possible. Co-sintering not only shortens the process time and saves energy costs, but also eliminates the risk of thermal shocks on the molded part during sintering.

Hereinafter, preferred embodiments of the present invention will be described in detail with reference to the accompanying drawings. However, embodiments of the present invention may be modified in many different forms, and the scope of the present invention should not be construed as being limited to the embodiments described below. The embodiments of the present invention are provided to more completely explain the present invention to those skilled in the art. Accordingly, the shape of the elements in the drawings and the like are exaggerated to emphasize a clearer description.

1 is a flow chart of the LSGM solid electrolyte production method according to the present invention.

First, a raw powder having La, Sr, Ga and Mg components, preferably La _0.8 Sr _0.2 Ga _0.8 Mg _0.2 O _2.8 (LSGM) powder, is prepared (step S1). This powder may be used a commercially available powder or may be newly synthesized. Hereinafter, the synthesis | combination by GNP method is given.

First, LSGMs such as La (NO ₃ ) ₃ · 6H ₂ O, Sr (NO ₃ ) ₂ , Ga (NO ₃ ) ₃ · xH ₂ O and Mg (NO ₃ ) ₂ · 6H ₂ O are used as starting salts of the raw materials. Nitrate of each constituent metal La, Sr, Ga, and Mg was dissolved in distilled water through stoichiometric weighing, and then glycine (NH ₂ CH ₂ COOH, Sigma) was weighed and dissolved so that the glycine / nitrate molar ratio was 1.0. do. At this time, the aqueous solution is kept at 80 ℃ temperature for 10 hours while stirring properly to make a gel state, it is heated to 200 ~ 300 ℃ by explosion to obtain LSGM precursor. The LSGM precursor was calcined at 1000 ° C. for 2 hours, and then ball milled with alcohol as a solvent for 24 hours, dried and pulverized to obtain LSGM fine powder . This process describes a typical process for obtaining LSGM fine powder, and the same inventive effect can be obtained by using LSGM powder prepared by other methods such as solid phase reaction method, ultrasonic spray pyrolysis method, and carbonate coprecipitation method.

Next, V, Ba as the sintering aid unique to the present invention to the LSGM powder prepared in step S1 And at least one of Li is added (step S2). The additive raw materials for the sintering aid components are V ₅ ⁺ , Ba ²⁺ and Li ⁺ using V ₂ O ₅ , Ba (C ₂ H ₃ O ₂ ) ₂ , and Li (C ₂ H ₃ O ₂ ), respectively. It can be added in the form of ions, such as there is no restriction in the type of additive raw material if it can add these components. For uniform mixing of LSGM powder and additive raw materials, ball mill is performed for 24 hours with alcohol as a solvent, followed by washing, drying and pulverization to obtain mixed LSGM powder to which sintering aid is added.

Next, after the disk is molded into a Φ 10 mm mold, it is appropriately molded by CIP (Cold Isostatic Pressing) at a pressure of 150 MPa, and sintered at a low temperature at 1200 ° C. to 1300 ° C. (step S3). At the time of sintering, the powder calcined at 1400 ° C. for 4 hours can be placed in a sintering furnace to be used as an atmosphere powder for sintering.

The sintered body thus obtained can be used as a solid electrolyte, and the anode material on one side and the anode material on the other side using a deposition method such as hand painting, screen printing or spray coating. The coating and heat treatment are used to produce a solid oxide fuel cell. On the other hand, the disk molding here has been selected for ease of experiment and evaluation, and may be advantageous to a molding method such as tape casting that can be made thin to apply to the solid electrolyte of the fuel cell.

As described in detail in the examples below, when the LSGM powder is sintered by adding the sintering aid according to the present invention, a very dense sintered body can be obtained even at a low temperature of 1200 ° C to 1300 ° C. In addition, the addition of sintering aid improves phase purity and density, and does not reduce electrical conductivity, compared to pure LSGM phase. As the low temperature sintering is possible, the buffer layer is unnecessary because the stability of the interface between the cathode and the electrolyte is secured when constructing the cathode support unit cell, and the anode and electrolyte are sintered at the same time, and only the anode is sintered in a separate process, or the cathode, electrolyte, and anode are Co-firing is also possible, in which the molds are formed sequentially and then all are sintered in one sintering process. Co-sintering not only shortens the process time and saves energy costs, but also eliminates the risk of thermal shocks on the molded part during sintering.

2 is a flowchart illustrating an example of a method of manufacturing a fuel cell using LSGM solid electrolyte using co-sintering according to the present invention, and FIG. 3 is a cross-sectional view thereof.

First, the negative electrode molded body 10 is made (step T1 of FIG. 2, FIG. 3 (a)).

For example, materials such as Ni-GDC, Ni-SDC, Ni-LDC, Ni-LSGM, and the like as the negative electrode material are molded according to a conventional ceramic molding process to form the molded body 10 having a thickness of about 1 mm. At this time, the molded body 10 may include a conventional organic binder (binder) to improve the molding strength.

Next, the solid electrolyte molded body 20 is formed and laminated on the prepared cathode molded body 10 (step T2 of FIG. 2 and FIG. 3B).

The method for making the solid electrolyte molded body 20 is the same from the method described above with reference to FIG. 1 until the process before sintering. In other words, LSGM powder is made of a mixed powder obtained by adding at least one component of V, Ba, and Li (the ions thereof, V ⁵⁺ , Ba ^2+, and Li ⁺ ) as a sintering aid unique to the present invention, and then molding the LSGM powder. To raise on the negative electrode molded body 10. Each of the negative electrode molded body 10 and the solid electrolyte molded body 20 may be formed by simply laminating a molded product separately or by pressing after lamination to achieve physical bonding to some extent, or by adding a negative electrode material powder and a sintering aid. It can also be made in one molding using LSGM powder.

Subsequently, the laminated structure of the negative electrode molded body 10 and the solid electrolyte molded body 20 is sintered at a low temperature (H1) at 1200 ° C to 1300 ° C to obtain a sintered body 30 (step T3 in Fig. 2, (c) in Fig. 2). . At this time, the powder calcined at 1400 ° C. for 4 hours can be placed in a sintering furnace to be used as an atmosphere powder for sintering.

Thereafter, the anode 40 having a thickness of about 10 to 100 μm is formed (step T4 of FIG. 2 and (d) of FIG. 2) by using a conventional ceramic powder coating method on the sintered body 30. 40) The material may be a conventional lanthanum-strontium-manganese oxide (LSM) or lanthanum-strontium-cobalt-iron oxide (LSCF), or a mixed composition of lanthanum-strontium-manganese oxide and lanthanum-strontium-cobalt-iron oxide. Can be.

Next, the sintered compact 30 and the anode 40 are heat-treated (H2) to obtain a fuel cell 50 (step T5 of FIG. 2, FIG. 3E).

On the other hand, although not described using a flowchart or a process cross-sectional view, a solid electrolyte fuel cell may be manufactured by sequentially forming the cathode-solid electrolyte-anode and then simultaneously sintering them all at once.

As such, simultaneous sintering is possible through low-temperature sintering of the solid electrolyte, and thus it is possible to manufacture a more economical solid oxide fuel cell by shortening process time and reducing energy cost.

Hereinafter, the present invention will be described in more detail with reference to the following specific examples, which are only intended to explain the present invention in more detail, and the scope of the present invention is in accordance with the gist of the present invention. It will be apparent to those skilled in the art that the present invention is not limited thereto.

In Examples, 1 mol% of Fe ²⁺ and Fe ³⁺ , Mn ²⁺ , V ⁵⁺ , Ba ²⁺ , Li ⁺ were added to the LSGM fine powder synthesized by the GNP method as a sintering aid, respectively, at 1200 ° C. for 4 hours and 1300. After sintering at 4 ° C. for 4 hours to prepare a sintered specimen, the optimum sintering aid was confirmed through XRD pattern, density, and impedance measurement. As a comparative example, the characteristics of the specimens sintered at 1200 ° C. and 1300 ° C. for 4 hours were analyzed using pure LSGM fine powder without sintering aid.

Example 1-1

1 mol% of Fe ²⁺ was added to the La _0.8 Sr _0.2 Ga _0.8 Mg _0.2 O _{3-δ (} LSGM) fine powder synthesized by GNP method and calcined at 1000 ° C. for 2 hours. Fe (C ₂ H ₃ O ₂ ) ₂ (Aldrich) was used as a raw material of the additive. For uniform mixing of the raw materials, ball milling was performed for 24 hours with alcohol as a solvent, followed by washing, drying and grinding to obtain mixed LSGM powder to which a sintering aid was added.

Next, the disks were formed into a Φ 10 mm mold, and then CIP was applied at 150 MPa pressure and sintered at 1200 DEG C and 1300 DEG C for 4 hours. At the time of sintering, the powder calcined at 1400 ° C. for 4 hours was used as the atmosphere powder for sintering.

After that, the XRD pattern analysis of the sintered specimens, the density measurement by the Archimedes method, and the resistivity measurement of the specimens were performed at 300 ° C. using an impedance analyzer.

[Example 1-2]

The other experimental conditions were the same as in [Example 1-1], and 1 mol% of Fe ³⁺ was added as a sintering aid. Fe (NO ₃ ) ₃ · 9H ₂ O (Aldrich) was used as a raw material of the additive.

[Example 1-3]

The other experimental conditions were the same as in [Example 1-1], and 1 mol% of Mn ²⁺ was added as a sintering aid. Mn (NO ₃ ) ₂ · 4H ₂ O (Sigma) was used as a raw material of the additive.

Example 1-4

The other experimental conditions were the same as in [Example 1-1], and 1 mol% of V ⁵⁺ was added as a sintering aid. V ₂ O ₅ (Junsei) was used as a raw material of the additive.

[Comparative Example 1-1]

The other experimental conditions were the same as in [Example 1-1], and pure LSGM powder without adding a sintering aid was used.

Example 2-1

The other experimental conditions were the same as in [Example 1-1], and 1 mol% of Ba ²⁺ was added as a sintering aid. Ba (C ₂ H ₃ O ₂ ) ₂ (Sigma-Aldrich) was used as a raw material of the additive.

Example 2-2

The other experimental conditions were the same as in [Example 1-1], and 1 mol% of Li ⁺ was added as a sintering aid. Li (C ₂ H ₃ O ₂ ) (Aldrich) was used as a raw material of the additive.

Comparative Example 2

It is the same as [Comparative Example 1].

4, 5, and 6 show the density, XRD pattern, and impedance analysis results of the sintered specimens prepared in Examples 1-1, 1-2, 1-3, 1-4, and Comparative Example 1, respectively.

First, referring to FIG. 4, as shown in the graph (a) and the result of sintering at 1200 ° C. for 4 hours and the graph at 4 ° C. at 1300 ° C., as compared with the pure LSGM sintered specimen of Comparative Example 1 (pure) It can be seen that in the case of Example 1-1, Example 1-3, and Example 1-4 specimens to which each of the Fe ²⁺ Mn ²⁺ and V ⁵⁺ sintering aids were added, it was confirmed that the density increased. On the other hand, in Example 1-2 where Fe ³⁺ was added, the density improvement of the sintered compact was hardly seen. Therefore, the sintering aids of Fe ²⁺ Mn ²⁺ and V ⁵⁺ are evaluated as excellent sintering aids in terms of density improvement.

5 shows the XRD pattern of the sintered specimen.

First, (a) and (b) of FIG. 5 are pure LSGM and XRD patterns of Example 1-1 sintered at 1200 ° C. and 1300 ° C. by adding 1 mol% of Fe ²⁺ as a sintering aid to pure LSGM powder. The XRD pattern of Comparative Example 1 sintered at only 1200 ° C and 1300 ° C is shown. In the case of Example 1-1, it can be seen that LaSrGaO _{4, which} is a secondary phase, is decreased as compared with Comparative Example 1.

Next, FIGS. 5 (c) and 5 (d) are graphs showing results of sintering at 1200 ° C. for 4 hours, and graphs showing results of sintering at 1300 ° C. for 4 hours, and graphs showing phase purity of the test specimens compared to pure LSGM phases. to be. Indices for checking the purity of the phase include the ratio of the intensity of the largest peak (2θ = 31.4, LaSrGaO ₄ (103) plane) among the secondary phases to the intensity of the main peak (2θ = 32.4, LSGM (112) plane) of the pure LSGM phase, That is, I (103) / I (112) was used. The smaller the I 103 / I 112, the greater the phase purity.

As shown in (c) and (d) of FIG. 5, in every case where Fe ²⁺ , Fe ³⁺ , Mn ²⁺ and V ⁵⁺ are added according to the inventive examples 1-1 to 1-4, You can see this improvement. Therefore, the sintering aid of Fe ²⁺ , Fe ³⁺ , Mn ²⁺ , V ⁵⁺ is evaluated as an excellent sintering aid in terms of phase purity.

6 shows the impedance measurement results of the sintered specimen.

First, (a) and (b) of FIG. 6 are pure LSGM phases and the impedance data of Example 1-1 sintered at 1200 ° C and 1300 ° C by adding 1 mol% of Fe ²⁺ as a sintering aid to pure LSGM powder. Impedance data of Comparative Example 1 sintered at 1200 ° C. and 1300 ° C. are shown (ρ _gi : specific grain resistance, ρ _gb : grain boundary resistivity). In the case of Example 1-1, it can be seen that the specific resistance is reduced and the conductivity is improved as compared with Comparative Example 1.

6 (c) and 6 (d) are graphs showing results of sintering at 1200 ° C. for 4 hours and results of sintering at 1300 ° C. for 4 hours. It is a graph showing the specific resistance value (ρ _tot = ρ _gi + ρ _gb ). The change of the grain resistivity by the addition of the sintering aid was hardly observed, while the grain boundary resistivity decreased except for the addition of Mn ²⁺ , and the increase in grain boundary resistivity was not significant even when Mn ²⁺ was added. Therefore, the addition of Fe ²⁺ and V ⁵⁺ in Examples 1-1 and 1-4 showed three effects, such as an increase in sintered density of LSGM solid electrolyte, an improvement in phase purity, and a decrease in total specific resistance. In the case of the addition of Mn ^{2+ of} -3, the density and phase purity are improved, and in the case of the addition of Fe ³⁺ of Example 1-2, the total specific resistance is effectively reduced.

7, 8 and 9 show the density, XRD pattern, and impedance analysis results of the sintered specimens prepared in Examples 2-1, 2-2 and Comparative Example 2. FIG.

As shown in FIG. 7, when the Ba ²⁺ and Li ⁺ sintering aids were added as compared with Comparative Example 2, which is a pure LSGM sintered specimen, (a) 1200 ° C. And (b) it can be seen that the density increases both at 1300 ℃ sintering temperature.

8 shows the XRD pattern of the sintered specimen. Compared to the pure LSGM phase, the phase purity of the (a) 1200 ° C. sintered specimen and (b) the 1300 ° C. sintered specimen was shown. After adding Ba ²⁺ and Li ⁺ , the sintering at 1200 ° C. improved the phase purity, and when the sintering temperature was increased to 1300 ° C., the phase purity was improved only for Ba ²⁺ .

9 shows the impedance measurement results of the sintered specimen. Comparing the case of adding pure LSGM and sintering aid, the particle size, grain boundary, and total resistivity (ρ _gi , ρ _gb , ρ _tot ) of (a) 1200 ° C sintered specimens and (b) 1300 ° C sintered specimens were shown. In Figure 9 it can be seen that the total specific resistance is not significantly changed by the addition of Ba ²⁺ and Li ⁺ .

Taken together, the addition of Fe ²⁺ and V ⁵⁺ has three effects: increasing the sintered density of LSGM solid electrolytes, improving the phase purity, and reducing the total specific resistance. Mn ²⁺ _, Ba ²⁺ , Li ^In the case of ⁺ addition, the density and phase purity are improved, and in the case of Fe ³⁺ addition, the total specific resistance is effectively reduced. Therefore, if the sintering aid of the composition containing at least any one of Fe, Mn, V, Ba, and Li are mixed and sintered, at least one of the density, the ordinary purity, and the total resistivity characteristic can be improved.

In the above, the present invention has been described in detail with reference to preferred embodiments, but the present invention is not limited to the above embodiments, and various modifications are possible by those skilled in the art within the technical idea of the present invention. Is obvious. Embodiments of the invention have been considered in all respects as illustrative and not restrictive, which include the scope of the invention as indicated by the appended claims rather than the detailed description therein, the equivalents of the claims and all modifications within the means. I want to.

1 is a flow chart of the LSGM solid electrolyte production method according to the present invention.

FIG. 2 is a flowchart for explaining an example of a method of manufacturing a fuel cell using LSGM solid electrolyte using co-sintering, and FIG. 3 is a cross-sectional view thereof.

4, 5, and 6 show the density, XRD pattern, and impedance analysis results of the sintered specimens prepared in Examples 1-1, 1-2, 1-3, 1-4, and Comparative Example 1, respectively.

7, 8 and 9 show the density, XRD pattern and impedance analysis results of the sintered specimens prepared in Examples 2-1, 2-2 and Comparative Example 2, respectively.

<Explanation of symbols for the main parts of the drawings>

10.cathode molded body

20.Solid electrolyte molded body

H1 ... Low Temperature Sintering

30 ... sintered

40.Anode

H2 ... heat treatment

50.Fuel cell

Claims (5)

A solid electrolyte for a solid oxide fuel cell, comprising: sintering after molding by mixing a sintering aid having a composition containing at least one of V, Ba, and Li with a raw powder having La, Sr, Ga, and Mg components Manufacturing method. The solid electrolyte fuel cell manufacturing method of claim 1, wherein the composition of the raw material powder is La _0.8 Sr _0.2 Ga _0.8 Mg _0.2 O _2.8 . The solid electrolyte fuel cell manufacturing method of claim 1, wherein the sintering temperature is in a range of 1200 to 1300 ° C. 3. The solid electrolyte fuel cell manufacturing method of claim 1, wherein the sintering aid is mixed with 0.1 to 2 mol% based on the raw material powder. Stacking the solid electrolyte compact on the anode compact; And Simultaneously sintering the negative electrode molded body and the solid electrolyte molded body at 1200 ~ 1300 ℃, Forming the solid electrolyte molded body A method for producing a solid oxide fuel cell, characterized by mixing and molding a raw powder having La, Sr, Ga, and Mg components with a sintering aid having a composition comprising at least one of V, Ba, and Li.

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