KR20130055939A - Solid oxide fuel cell - Google Patents

Abstract

PURPOSE: A solid oxide fuel cell is provided to form a thin and dense zirconia-based electrolyte on a ceria-based electrolyte membrane and to expand electrolyte region without degrading ion conductivity, thereby improving performance of the solid oxide fuel cell. CONSTITUTION: A solid oxide fuel cell(1) comprises a negative electrode(10); a first electrolyte membrane(20) on the negative electrode; a second electrolyte membrane(30) which is located on the first electrolyte membrane and is thin; and a positive electrode(40) located in the second electrolyte membrane. The thickness ratio of the second electrolyte membrane to the first electrolyte membrane is determined by average ion conductivity and ion transportability of the membranes. The ion transportability is 0.9 or more. The average ion conductivity is 90% or more of the first electrolyte membrane.

Description

Solid Oxide Fuel Cell {SOLID OXIDE FUEL CELL}

The present invention relates to a solid oxide fuel cell.

In general, a solid oxide fuel cell includes a fuel electrode, an air electrode, and an electrolyte membrane therebetween. Although a ceria-based electrolyte membrane having high ion conductivity has been proposed as the electrolyte membrane, the ceria-based electrolyte membrane has a problem in that open circuit electromotive force is small because the oxygen partial pressure of the anode is out of the electrolyte region.

In order to solve the above problems, the present invention provides a solid oxide fuel cell with improved performance.

A solid oxide fuel cell according to embodiments of the present invention includes a cathode, a first electrolyte membrane disposed on the cathode, a second electrolyte membrane disposed on the first electrolyte membrane, and having a thickness thinner than that of the first electrolyte membrane, And an anode disposed on the second electrolyte membrane.

The thickness ratio of the first electrolyte membrane to the second electrolyte membrane may be determined by the average number of ions and the average ion conductivity of the first and second electrolyte membranes. The average ion number may be 0.9 or more, and the average ion conductivity may be 90% or more of the ion conductivity of the first electrolyte membrane. The lower limit of the thickness ratio of the first electrolyte membrane to the second electrolyte membrane may be determined by the average ion number, and the upper limit of the thickness ratio may be determined by the average ion number.

The thickness ratio may be 1: 8.6 × 10 ⁻⁵ to 1: 0.22 at 800 to 1000 ° C. The thickness ratio is 1 eseo ^{800 ℃: 8.6 × 10 -5 ~} 1: 9.5 × 10 -2 and 1 eseo ^{900 ℃: 3.0 × 10 -4 ~} 1: 0.14 , and 1 eseo 1000 ℃: 1.0 × 10 ^{- 3} to 1: 0.22. The thickness ratio may be 1: 1.0 × 10 ⁻³ .

The first electrolyte membrane may be a ceria-based electrolyte membrane, and the second electrolyte membrane may be a zirconia-based electrolyte membrane.

The ceria-based electrolyte membrane may have a chemical formula of Ce _{1 - x} M ¹ _x O _{2 -x / 2} , and the zirconia-based electrolyte membrane may have a chemical formula of Zr _{1 - x} M ² _x O _{2 -x / 2} , In the above formula, M ¹ may be Gd, Sm, Tb, or Y, and M ² may be Y or Sc.

The first electrolyte membrane may include at least one selected from Gd (Doped Ceria), SDC (Sm-Doped Ceria), and Y-Doped Bismuth oxide (YDB), and the second electrolyte membrane may be Yittria Stablized Zirconia (YSZ). ) May be included.

The negative electrode and the positive electrode may have a porous structure, and the first electrolyte membrane and the second electrolyte membrane may have a dense structure.

According to embodiments of the present invention, by forming a dense and thin zirconia-based electrolyte membrane on the anode side of the ceria-based electrolyte membrane, the electrolyte region may be expanded without deteriorating ion conductivity, thereby improving performance of the solid oxide fuel cell.

1 illustrates a solid oxide fuel cell according to embodiments of the present invention.
Figure 2 shows the relationship between the ion number and conductivity for the oxygen partial pressure in the oxygen ion electrolyte region.
3 shows the zirconia-based and ceria-based oxygen ion electrolyte regions.
4 shows a double electrolyte membrane according to an embodiment of the present invention.
5 shows the oxygen partial pressure at the interface according to the thickness ratio of the YSZ film to the GDC film.
6A to 6C show the average ion number of the double electrolyte membrane according to the thickness ratio of the YSZ membrane to the GDC membrane.
7A to 7C show average ion conductivity of the double electrolyte membrane according to the thickness ratio of the YSZ membrane to the GDC membrane.
8 shows XRD of a double electrolyte membrane prepared according to an embodiment of the present invention.
9 is a SEM photograph of a double electrolyte membrane prepared according to an embodiment of the present invention.
10 shows the electrical conductivity according to the oxygen partial pressure of the double electrolyte membrane prepared according to an embodiment of the present invention.
FIG. 11 shows electron conductivity according to oxygen partial pressure of a double electrolyte membrane, a GDC single membrane, and an YSZ single membrane prepared according to an embodiment of the present invention.
12 shows a method for determining the oxygen partial pressure at which the electron conductivity and the ion conductivity are the same.
13 and 14 illustrate a comparison between electrolyte regions of a double electrolyte membrane prepared according to an embodiment of the present invention, a GDC single membrane, and an YSZ single membrane.

Hereinafter, the present invention will be described in more detail with reference to the following examples. The objects, features and advantages of the present invention will be easily understood by the following embodiments. The present invention is not limited to the embodiments described herein, but may be embodied in other forms. The embodiments disclosed herein are provided so that the disclosure may be thorough and complete, and that those skilled in the art will be able to convey the spirit of the invention to those skilled in the art. Therefore, the present invention should not be limited by the following examples.

When it is mentioned that a layer is on another layer or another element, it means that it can be formed directly on another layer or another element or a third layer can be interposed therebetween. In the drawings, the thickness of layers or regions may be exaggerated for clarity. In the drawings, the size of elements, or the relative sizes between elements, may be somewhat exaggerated for a clearer understanding of the present invention. In addition, the shape of the elements shown in the drawings may be somewhat changed by variations in the manufacturing process. Accordingly, the embodiments disclosed herein are not to be limited to the shapes shown in the drawings unless specifically stated, it should be understood to include some modification.

As used herein, the term " dense " may refer to a case in which the density of the thin film in the thin film is 95% or more of the theoretical density value, and may indicate a structure of the thin film having a density capable of sealing gas. .

<Solid Oxide Fuel Cell>

1 illustrates a solid oxide fuel cell according to embodiments of the present invention.

Referring to FIG. 1, the solid oxide fuel cell 1 includes a cathode 10, a first electrolyte membrane 20, a second electrolyte membrane 30, and an anode 40. The first electrolyte membrane 20 is disposed on the cathode 10, the second electrolyte membrane 30 is disposed on the first electrolyte membrane 20, and the anode 40 is disposed on the second electrolyte membrane 30. .

The cathode 10 may be referred to as a fuel electrode as an electrode that generates an oxidation reaction and emits electrons. Cathode 10 may be provided with a fuel that can be oxidized, such as hydrogen, hydrocarbons, alcohols, and the like. The negative electrode 10 may have a porous structure, and may include Ni—Zr _1-x Y _x O _{2-x / 2} , Ni-Ce _1-x Gd _x O _{2-x / 2} , and the like.

The first electrolyte membrane 20 may be a ceria-based electrolyte membrane having a dense structure. The ceria-based electrolyte membrane may have a chemical formula of Ce _{1 - x} M ¹ _x O _{2 -x / 2} , in which M ¹ may be Gd, Sm, Tb, or Y. The first electrolyte membrane 20 may include one or more selected from Gd-Doped Ceria (GDC), Sm-Doped Ceria (SDC), and Y-Doped Bismuth oxide (YDB).

The second electrolyte membrane 30 may be a zirconia-based electrolyte membrane having a dense structure. The zirconia-based electrolyte membrane may have a chemical formula of Zr _{1 - x} M ² _x O _{2- x / 2} , in which M ² may be Y or Sc. The second electrolyte membrane 30 may include Yttria Stablized Zirconia (YSZ).

The thickness Lz of the second electrolyte membrane 30 is thinner than the thickness Lc of the first electrolyte membrane 20. The thickness ratio Lz / Lc of the first electrolyte membrane 20 to the second electrolyte membrane 30 may be determined by the average number of ions and the average ion conductivity of the first and second electrolyte membranes 20 and 30. have. The lower limit of the thickness ratio Lz / Lc of the first electrolyte membrane 20 to the second electrolyte membrane 30 may be determined by the average ion number, and preferably, the average ion number may be 0.9 or more. . The upper limit of the thickness ratio Lz / Lc may be determined by the average ion number, and preferably, the average ion conductivity may be 90% or more of the ion conductivity of the first electrolyte membrane 20. The thickness ratio Lz / Lc may be 1: 8.6 × 10 ⁻⁵ to 1: 0.22 at 800 to 1000 ° C. For example, the thickness ratio is 1: 8.6 × 10 ⁻⁵ to 1: 9.5 × 10 ⁻² at 800 ° C., 1: 3.0 × 10 ⁻⁴ to 1: 0.14 at 900 ° C., and 1: 1 at 1000 ° C. 1.0 × 10 ⁻³ to 1: 0.22. Preferably, the thickness ratio may be 1: 1.0 × 10 ⁻³ .

The anode 40 may be referred to as an air electrode as an electrode which receives a electron by causing a reduction reaction. The anode 10 may be provided with an oxidizing agent, for example air. A positive electrode 40 may have a porous structure, La _{1 -,} and the like _{y FeyO 3 - x Sr x MnO} 3, La 1 - x Sr x Co 1.

Oxygen ion electrolyte area

Figure 2 shows the relationship between the ion number and conductivity for the oxygen partial pressure in the oxygen ion electrolyte region.

Referring to FIG. 2, the ion number of the oxygen partial pressure and the open circuit electromotive force (OCV) in the oxygen ion electrolyte region may be represented by Equations 1 and 2, respectively.

[Equation 1]

In Equation 1, sigma _i represents ion conductivity and sigma _e represents electron conductivity (conductivity by electrons or holes).

&Quot; (2) &quot;

The oxygen partial pressure at which the electron conductivity and the ion conductivity are the same is Pn, and Pp is the oxygen partial pressure at which the electron conductivity and the ion conductivity are the same, and the ion number (t _ion ) is 0.5 at the Pn and Pp. The wider the area of the electrolyte by holes, the closer the average ion number is to 1, and the narrower the area of the electrolyte, the smaller the average ion number is. In general, in the case of an electrolyte for a solid oxide fuel cell, the number of ions in the air electrode is 1, and the number of ions in the fuel electrode is smaller than 1 due to an increase in electron conductivity due to metal reduction. In this manner, when the average number of ion numbers becomes smaller than 1, the open circuit electromotive force is reduced. Since the ion conductivity of the solid electrolyte is directly proportional to the magnitude of the ion current of the solid oxide fuel cell, the solid oxide fuel cell has excellent performance as the electrolyte region and the size of the ion conductivity are larger.

Zirconia  And Ceria  Oxygen ion electrolyte area

3 shows the zirconia-based and ceria-based oxygen ion electrolyte regions. FIG. 3 shows the electrical conductivity of the zirconia-based oxygen ion electrolyte region and the ceria-based oxygen ion electrolyte region and the oxygen partial pressure at the fuel electrode (expressed as fuel) and the air electrode (expressed as air) under the driving conditions of the solid oxide fuel cell.

Referring to FIG. 3, in the case of the zirconia-based oxygen ion electrolyte region, since the oxygen partial pressures of the anode and the cathode are located in the electrolyte region, there is no reduction in open circuit electromotive force compared to the ideal value. However, in the case of the ceria-based oxygen ion electrolyte region, since the partial pressure of oxygen of the anode is out of the electrolyte region, the open circuit electromotive force appears smaller than the ideal value. On the other hand, in the case of ion conductivity, ceria-based electrolytes are known to be several times higher than zirconia-based electrolytes.

The In embodiments  According to the electrolyte area

4 shows an electrolyte membrane according to an embodiment of the present invention.

Referring to FIG. 4, the electrolyte membrane may include a double electrolyte membrane of a GDC membrane in contact with the anode (10 in FIG. 1) and an YSZ membrane in contact with the cathode (40 in FIG. 1). Lc represents the thickness of the GDC film, and Lz represents the thickness of the YSZ film. If the thickness ratio of the double electrolyte membrane to the GDC membrane is t, the thickness ratio Lz / Lc of the YSZ membrane to the GDC membrane may be represented by (1-t) / t.

In the double electrolyte membrane, the amount of oxygen passing through each membrane per unit time in the steady state is equal to the following Equation 3.

&Quot; (3) &quot;

If the oxygen partial pressure of the anode is Po ₂ ′, the oxygen partial pressure at the interface between the GDC film and the YSZ film is Po ₂ '', and the oxygen partial pressure of the air electrode is Po ₂ '', the following Equation 4 Can be.

&Quot; (4) &quot;

If ln (Po ₂ / Po ₂ ^* ) is arranged as x in Equation 4, Equation 5 may be derived. Po ₂ ^* denotes an oxygen partial pressure in which electron conductivity by electrons and electron conductivity by holes are the same.

[Equation 5]

In Equation 5, the subscript C represents GDC, Z represents YSZ, and σ _{el and m} represent electron conductivity by electrons or holes in Po ₂ ^* .

5 shows the oxygen partial pressure at the interface according to the thickness ratio of the YSZ film to the GDC film.

Referring to FIG. 5, the partial pressure of oxygen at the interface according to the thickness ratio Lz / Lc of the YSZ film to the GDC film at 800, 900, and 1000 ° C. can be calculated from Equations 3 to 5 above.

The average ion number t _ion ^bilayer of the double electrolyte membrane according to the thickness ratio Lz / Lc of the YSZ membrane to the GDC membrane may be calculated using FIG. 5, and may be represented by Equation 6 below.

&Quot; (6) &quot;

6A to 6C show average ion counts calculated by Equation 6 above. Figure 6a shows the average ion number of the double electrolyte membrane in accordance with the thickness ratio of the YSZ membrane to GDC membrane at 800 ℃, Figure 6b shows the average ion number of the double electrolyte membrane in accordance with the thickness ratio of the YSZ membrane to GDC membrane at 900 ℃, 6C shows the average ion number of the double electrolyte membrane according to the thickness ratio of the YSZ membrane to the GDC membrane at 1000 ° C.

6A to 6C, when a dense YSZ membrane having a thickness of about 1/1000 of the thickness of the GDC membrane is coated on the GDC membrane, the average ion number of the double electrolyte membrane is about 0.99 at 800 ° C. In the case of the GDC single layer, the open circuit electromotive force is improved by more than 35% compared to the average ion number of 0.72. In addition, at 900 ° C. and 1000 ° C., the average ion carry number of the double electrolyte membrane is 0.96 and 0.90, respectively, and the open circuit electromotive force can be improved by 48% and 61%, respectively, compared with the average ion carry number of the GDC single membrane.

Since the double electrolyte membrane is an electrically series circuit of the GDC membrane and the YSZ membrane, since the ionic resistance is in series connection and the conductivity is proportional to the inverse of the resistance, the average ion conductivity (σ _i ^bilayer ) of the double electrolyte membrane may be represented by the following equation.

[Equation 7]

7A to 7C show average ion conductivity calculated by Equation (7). FIG. 7A shows the average ion conductivity of the double electrolyte membrane according to the thickness ratio of the YSZ membrane to the GDC membrane at 800 ° C., FIG. 7B shows the average ion conductivity of the double electrolyte membrane according to the thickness ratio of the YSZ membrane to the GDC membrane at 900 ° C., FIG. 7C Shows the average ion conductivity of the double electrolyte membrane according to the thickness ratio of the YSZ membrane to the GDC membrane at 1000 ° C.

7A to 7C, when the dense YSZ film having a thickness of about 1/1000 of the GDC film is coated on the GDC film, the average ion conductivity of the double electrolyte membrane is reduced to 1% or less compared to the average ion conductivity of the GDC film. It can be seen.

As described above, in the case of coating a very thin and dense YSZ film on the GDC film on the cathode side (for example, Lz / Lc = 1/1000), the electron conductivity is greatly suppressed compared to the GDC single film, and the open circuit electromotive force is greatly improved. Since the ion conductivity is reduced to 1% or less, it can be seen that the performance of the electrolyte including the double electrolyte membrane is greatly improved.

<Fabrication of Solid Oxide Fuel Cells>

Referring back to FIG. 1, the first electrolyte membrane 20, the second electrolyte membrane 30, and the anode 40 are formed on the cathode 10.

The cathode 10 may be formed by a thin film forming process, for example, a pulsed laser deposition (PLD) method, a screen print method, a spin coating method, and a dip coating method. The cathode 10 may be formed to have a porous structure made of a material such as Ni—Zr _{1 - x} Y _x O _{2 -x / 2} , Ni-Ce _{1 - x} Gd _x O _{2 -x / 2,} and the like.

The first electrolyte membrane 20 may be formed by a thin film forming process, for example, a pulsed laser deposition (PLD) method, a screen print method, a spin coating method, or a dip coating method. Can be. The first electrolyte membrane 20 may be formed to have a dense structure as a ceria-based electrolyte membrane. The ceria-based electrolyte membrane may have a chemical formula of Ce _{1 - x} M ¹ _x O _{2 -x / 2} , in which M ¹ may be Gd, Sm, Tb, or Y. The first electrolyte membrane 20 may be formed of at least one selected from Gd (Doped Ceria), Sm-Doped Ceria (SDC), and Y-Doped Bismuth oxide (YDB).

The second electrolyte membrane 30 may be formed by a thin film forming process, for example, a pulsed laser deposition (PLD) method, a screen print method, a spin coating method, or a dip coating method. Can be. The second electrolyte membrane 30 may be formed to have a dense structure as a zirconia-based electrolyte membrane. The zirconia-based electrolyte membrane may have a chemical formula of Zr _{1 -x} M ² _x O _{2-x / 2} , wherein M ² may be Y or Sc. The second electrolyte membrane 30 may be formed of Yttria Stablized Zirconia (YSZ).

The second electrolyte membrane 30 is formed thinner than the first electrolyte membrane 20. The thickness ratio Lz / Lc of the first electrolyte membrane 20 to the second electrolyte membrane 30 may be determined by the average number of ions and the average ion conductivity of the first and second electrolyte membranes 20 and 30. have. The lower limit of the thickness ratio Lz / Lc of the first electrolyte membrane 20 to the second electrolyte membrane 30 may be determined by the average ion number, and preferably, the average ion number may be 0.9 or more. . The upper limit of the thickness ratio Lz / Lc may be determined by the average ion number, and preferably, the average ion conductivity may be 90% or more of the ion conductivity of the first electrolyte membrane 20. The thickness ratio Lz / Lc may be 1: 8.6 × 10 ⁻⁵ to 1: 0.22 at 800 to 1000 ° C. For example, the thickness ratio is 1: 8.6 × 10 ⁻⁵ to 1: 9.5 × 10 ⁻² at 800 ° C., 1: 3.0 × 10 ⁻⁴ to 1: 0.14 at 900 ° C., and 1: 1 at 1000 ° C. 1.0 × 10 ⁻³ to 1: 0.22. Preferably, the thickness ratio may be 1: 1.0 × 10 ⁻³ .

The anode 40 may be formed by a thin film forming process, for example, a pulsed laser deposition (PLD) method, a screen print method, a spin coating method, and a dip coating method. The anode 10 may be formed to have a porous structure with a material such as La _{1 - x} Sr _x MnO ₃ and La _{1 - x} Sr _x Co _{1 - y} FeyO ₃ .

double Electrolyte membrane Manufacturing example

An YSZ film of about 1 mu m was deposited on the GDC film of about 1 mm by the PLD method. FIG. 8 illustrates X-ray diffraction (XRD) of a double electrolyte membrane prepared according to an embodiment of the present invention, and FIG. 9 illustrates a scanning electron microscopy (SEM) photograph of the double electrolyte membrane prepared according to an embodiment of the present invention. Indicates.

double Electrolyte membrane  Ionic conductivity measurement

Ionic conductivity of the double electrolyte membrane was measured using a semi-4 probe impedance spectroscopy.

10 illustrates ion conductivity according to oxygen partial pressure of a double electrolyte membrane prepared according to an embodiment of the present invention.

Referring to FIG. 10, the ion conductivity of the double electrolyte membrane has a value similar to that of the GDC single membrane.

double Electrolyte membrane  Electronic conductivity measurement

Electron conductivity of the double electrolyte membrane was measured using Hebb-Wagner polarization method.

FIG. 11 shows electron conductivity according to oxygen partial pressure of a double electrolyte membrane, a GDC single membrane, and an YSZ single membrane prepared according to an embodiment of the present invention.

Referring to FIG. 11, the electron conductivity of the double electrolyte membrane is about 10 to 100 times smaller than the electron conductivity of the GDC single membrane.

Determine electrolyte area

12 shows a method of determining the oxygen partial pressure Pn at which the electron conductivity and the ion conductivity are the same. It can be understood that the smaller the Pn value, the wider the electrolyte region.

13 and 14 illustrate a comparison between electrolyte regions of a double electrolyte membrane prepared according to an embodiment of the present invention, a GDC single membrane, and an YSZ single membrane.

Referring to FIG. 13, it can be seen that Pn of the double electrolyte membrane is smaller than Pn of the GDC single membrane and larger than Pn of the YSZ single membrane.

Referring to FIG. 14, since the Pn of the GDC is higher than the oxygen partial pressure (purple solid line) of the general solid oxide fuel cell fuel, the size of the open circuit electromotive force is smaller than the Nernst voltage of 1 ion number. However, since the Pn of the double electrolyte membrane (GDC / YSZ Bilayer) is lower than the oxygen partial pressure of a general solid oxide fuel cell fuel, the open circuit electromotive force of the double electrolyte membrane shows a theoretical value of Nernst electromotive force.

As in the double electrolyte membrane according to the embodiment of the present invention, when the electrolyte region is narrow but the thin YSZ is densely coated on the cathode side on the GDC membrane having high ion conductivity, the ion conductivity of the double electrolyte membrane is close to the ion conductivity of the GDC single membrane. Pn appears to be about 1 million times smaller than GDC. Since this value is lower than the partial pressure of oxygen of the solid oxide fuel cell fuel, the open circuit electromotive force of the double electrolyte membrane is larger than that of the GDC single membrane. In other words, it can be seen that the YSZ film closely coated on the cathode side greatly expands the electrolyte region without lowering the high ion conductivity of the GDC film.

Hereinafter, specific embodiments of the present invention have been described. It will be understood by those skilled in the art that various changes in form and details may be made therein without departing from the spirit and scope of the invention as defined by the appended claims. Therefore, the disclosed embodiments should be considered in an illustrative rather than a restrictive sense. The scope of the present invention is defined by the appended claims rather than by the foregoing description, and all differences within the scope of equivalents thereof should be construed as being included in the present invention.

1: solid oxide fuel cell 10: negative electrode
20: first electrolyte membrane 30: second electrolyte membrane
40: anode

Claims (10)

cathode;
A first electrolyte membrane disposed on the cathode;
A second electrolyte membrane disposed on the first electrolyte membrane and having a thickness thinner than that of the first electrolyte membrane; And
A solid oxide fuel cell comprising an anode disposed on the second electrolyte membrane. The method of claim 1,
The thickness ratio of the first electrolyte membrane to the second electrolyte membrane is determined by the average number of ions and the average ion conductivity of the first and second electrolyte membranes,
The average ion number is 0.9 or more,
The average ion conductivity is a solid oxide fuel cell, characterized in that more than 90% of the ion conductivity of the first electrolyte membrane. 3. The method of claim 2,
The lower limit of the thickness ratio of the first electrolyte membrane to the second electrolyte membrane is determined by the average ion number;
And the upper limit of the thickness ratio is determined by the average ion number. 3. The method of claim 2,
The thickness ratio is a solid oxide fuel cell, characterized in that 1: 8.6 × 10 ^-5 to 1: 0.22 at 800 to 1000 ° C. The method of claim 4, wherein
The thickness ratio,
1: 8.6 × 10 ⁻⁵ to 1: 9.5 × 10 ⁻² at 800 ° C.,
1: 3.0 × 10 ⁻⁴ to 1: 0.14 at 900 ° C.,
Solid oxide fuel cell, characterized in that 1: 1.0 × 10 ^-3 ~ 1: 0.22 at 1000 ℃. 3. The method of claim 2,
The thickness ratio is 1: 1.0 × 10 ^- a solid oxide fuel cell, characterized in that ^3. The method of claim 1,
The first electrolyte membrane is a ceria-based electrolyte membrane,
And the second electrolyte membrane is a zirconia-based electrolyte membrane. The method of claim 1,
The ceria-based electrolyte membrane has a chemical formula of Ce _{1 - x} M ¹ _x O _{2 -x / 2} ,
The zirconia-based electrolyte membrane has a chemical formula of Zr _{1 - x} M ² _x O _{2- x / 2} ,
In the formula, M ¹ is Gd, Sm, Tb, or Y, M ² is Y or Sc solid oxide fuel cell, characterized in that. The method of claim 1,
The first electrolyte membrane includes one or more selected from Gd-Doped Ceria (GDC), Sm-Doped Ceria (SDC), and Y-Doped Bismuth oxide (YDB),
The second electrolyte membrane comprises YSZ (Yittria Stablized Zirconia) solid oxide fuel cell, characterized in that. The method of claim 1,
The anode and the anode has a porous structure,
And the first electrolyte membrane and the second electrolyte membrane have a dense structure.

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