JP2012104407A - Electrolyte-electrode assembly, and method for manufacturing the same - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide an electrolyte-electrode assembly (MEA) which comprises an electrolyte made of a zirconium-based oxide and held between an anode side electrode and a cathode side electrode, and an intermediate layer made of a cerium-based oxide and set between the cathode side electrode and the solid electrolyte, and shows excellent electrical properties.SOLUTION: The MEA10, for example, comprises a solid electrolyte 16 made of a zirconium-based oxide such as 8YSZ and held between an anode side electrode 12 and a cathode side electrode 14. An intermediate layer 18 made of a cerium-based oxide is set between the solid electrolyte 16 and the cathode side electrode 14. The intermediate layer 18 may contain Zr diffused from the solid electrolyte 16, and the amount of diffusion is 40 atom% at the maximum. The cathode side electrode 14 formed on the intermediate layer 18 comprises, for example, a first layer 22a adjacent to the intermediate layer 18, and a second layer 22b adjacent to the first layer 22a.

Description

  The present invention relates to an electrolyte / electrode assembly and a manufacturing method thereof, and more specifically, an electrolyte / electrode assembly suitable for constituting a unit cell of a fuel cell interposed between a pair of separators and a manufacturing method thereof. About.

A unit cell of a solid oxide fuel cell (SOFC) is basically composed of an electrolyte, which is configured by sandwiching a solid electrolyte between an anode side electrode and a cathode side electrode, as described in Patent Documents 1 and 2, etc. An electrode assembly (MEA) is interposed between a pair of separators. As the material of the anode side electrode, Ni-Y ₂ O ₃ stabilized ZrO ₂ (YSZ) cermet is mainly used. In addition, as the material of the solid electrolyte, a material having high oxide ion (O ²⁻ ) conductivity is adopted, and YSZ is particularly preferably selected.

On the other hand, the cathode side electrode has both high ionic conductivity and electronic conductivity, has an electrode reaction that occurs on the cathode side electrode of oxygen, that is, has a catalytic activity for oxygen dissociation reaction, thermodynamically It is stable and does not easily react with other substances (oxidant gas, solid electrolyte, etc.), is porous to allow sufficient circulation of oxidant gas, is difficult to sinter during power generation, and has mechanical strength. High is required. From this point of view, a perovskite type complex oxide represented by LaMO ₃ (M = Mn, Co, Fe) may be selected as the material of the cathode side electrode.

In this type of perovskite-type composite oxide, LaCoO _{3 or, La x Sr 1-x CoO} 3 where a portion of La was substituted by Sr (the so-called "LSC"), La _x a part of Co substituted with Fe When the cathode side electrode is formed using Sr _1-x Co _y Fe _1-y O ₃ (so-called “LSCF”), the overvoltage of the SOFC can be reduced. In Patent Document 2, a portion of La was substituted by Sr (La, Sr) constitutes the cathode from MnO _3.

  By the way, there is a possibility that La and Sr in LSC or LSCF react with Zr in YSZ forming a solid electrolyte when firing is performed in the MEA manufacturing process or during operation of SOFC, that is, at a high temperature. is there. When such a situation occurs, a high-resistance reaction product layer is formed and the conductivity is lowered.

In order to avoid this, as described in Patent Document 3 and Non-Patent Document 1, an intermediate layer as a reaction preventing layer is interposed. In Patent Document 3 and Non-Patent Document 1, CeO ₂ oxide (for example, CeO ₂ doped with Sm ₂ O ₃ ) is selected as the material of the intermediate layer.

European Patent No. 0722193 Japanese Patent Publication No.7-118327 JP 2003-331866 A

Solid Oxide Fuel Cell: Development of SOFC Published by CMC Publishing Co., Ltd. Page 171 October 31, 2005

Although not particularly mentioned in Patent Document 3 and Non-Patent Document 1, CeO ₂ -based oxides include Ni—YSZ forming an anode side electrode, YSZ forming a solid electrolyte, and the perovskite type complex oxide forming a cathode side electrode. It is a hardly sinterable substance that is difficult to sinter. The firing temperature is not sufficient, and for this reason, when the intermediate layer is formed as a porous body containing many pores, there are pores opened at the end face of the intermediate layer facing the cathode side electrode. As a result, the contact area between the intermediate layer and the cathode side electrode is reduced, and the mutual conductive paths are reduced.

In order to avoid such problems, for example, when an anode side electrode, a solid electrolyte, and an intermediate layer are formed and then subjected to a firing treatment at the same time, the intermediate layer made of CeO ₂ oxide is sufficiently sintered. The temperature is set appropriately for densification.

  However, even when a dense intermediate layer is formed in this way, an electrolyte / electrode assembly that does not exhibit the expected electrical characteristics may be obtained. That is, when an electrolyte / electrode assembly having a zirconium-based oxide as a solid electrolyte and a cerium-based oxide as an intermediate layer is manufactured, a product with insufficient electrical characteristics may be produced in some cases. Has become apparent.

  The present invention has been made to solve the above-described problems, and an object of the present invention is to provide an electrolyte / electrode assembly exhibiting good electrical characteristics and a method for producing the same.

  The present inventor, when forming a dense intermediate layer, when conducting a firing process in the process of earnestly examining the reason for producing an electrolyte / electrode assembly that does not exhibit the expected electrical characteristics The present inventors have found that Zr contained in the solid electrolyte is activated and diffuses into the intermediate layer. Based on this knowledge, it was inferred that when the cathode side electrode was baked, a reaction product layer having a high resistance was formed by the constituent elements of the cathode side electrode and Zr diffused in the intermediate layer.

  Further studies have been made from the viewpoint of avoiding excessive diffusion of Zr contained in the solid electrolyte into the intermediate layer, and the present invention has been made.

That is, the present invention provides an electrolyte / electrode in which a solid electrolyte made of a zirconium-based oxide is sandwiched between an anode-side electrode and a cathode-side electrode, and an intermediate layer is interposed between the solid electrolyte and the cathode-side electrode. A joined body,
The cathode side electrode is represented by at least Ba _x Sr _1-x Co _y Fe _1-y O ₃ , La _x Sr _1-x Co _y Fe _1-y O ₃ , or La _x Sr _1-x CoO _3. And a first layer adjacent to the intermediate layer,
The intermediate layer is made of a cerium-based oxide, and the amount of Zr diffused from the solid electrolyte is 40 atomic% or less.

  That is, in the present invention, the diffusion amount of Zr contained in the intermediate layer made of cerium-based oxide is set to 40 atomic% or less. In this case, since the amount of Zr present on the surface of the intermediate layer serving as the interface with the cathode side electrode is small, a reaction product layer having a high resistance is formed by the constituent elements of the cathode side electrode and Zr diffused in the intermediate layer. Is avoided. Even if a reaction product layer is formed, the amount is small.

  Therefore, a decrease in the conductivity of the MEA is avoided. For this reason, MEA which shows the outstanding electrical property can be comprised.

  The cathode side electrode may have a single layer structure composed of only the first layer. In this case, the first layer preferably has a thickness of 5 to 50 μm and a porosity of 20 to 30%. As a result, the oxidant gas can be easily diffused in the cathode side electrode (first layer).

The cathode side electrode may have a multi-layer structure including the first layer and a second layer adjacent to the first layer. In this case, the second layer is represented by _{Ba x Sr 1-x Co y} Fe 1-y O 3, La x Sr 1-x Co y Fe 1-y O 3, or La _x Sr _1-x CoO ₃ The perovskite complex oxide may be used.

  In this case, the relative density of the first layer is preferably 95% or more. When the relative density of the first layer is excessively small, there is a concern that the contact area between the intermediate layer and the first layer is not sufficient. In addition, about 0.2-10 micrometers is enough for the thickness of a 1st layer.

  Moreover, since the second layer substantially functions as a gas diffusion layer, it is preferable that the second layer has a thickness and a porosity that allow the oxidant gas to be easily diffused. From this viewpoint, it is preferable to set the thickness of the second layer to 5 to 50 μm and the porosity to 20 to 30%.

  The intermediate layer may be a porous body. In this case, pores opened at the end surface facing the first layer in the intermediate layer are filled with the first layer. Therefore, also in this case, a contact area between the intermediate layer and the first layer is ensured.

  The thickness of the intermediate layer is not particularly limited as long as the interaction between the solid electrolyte and the cathode electrode can be prevented, and specifically, 0.1 to 5 μm is preferable.

The present invention also provides an electrolyte / electrode in which a solid electrolyte composed of a zirconium-based oxide is sandwiched between an anode side electrode and a cathode side electrode, and an intermediate layer is interposed between the solid electrolyte and the cathode side electrode. A method for manufacturing a joined body, comprising:
An anode side electrode is provided directly on one end surface of the solid electrolyte or via an intermediate layer, and then the remaining other end surface of the solid electrolyte is provided via an intermediate layer made of a cerium-based oxide or on the anode side electrode. After providing the solid electrolyte directly on one end face or via an intermediate layer, the cathode side electrode is at least Ba _x Sr _1-x via an intermediate layer made of a cerium-based oxide on the solid electrolyte. _{Co y Fe 1-y O 3} , La x Sr 1-x Co y Fe 1-y O 3, or expressed by La _x Sr _1-x CoO ₃ consists perovskite complex oxide and adjacent to the intermediate layer Having a step of forming as having a first layer,
The amount of Zr diffused from the solid electrolyte and contained in the intermediate layer made of the cerium-based oxide is 40 atomic% or less.

  As described above, by suppressing the amount of Zr contained in the intermediate layer made of a cerium-based oxide to 40 atomic% or less, an MEA exhibiting excellent electrochemical characteristics can be obtained.

  When the cathode side electrode has a single layer structure composed of only the first layer, it is preferable to form a layer having a thickness of 5 to 50 μm and a porosity of 20 to 30%. This is because the oxidant gas easily diffuses in the cathode side electrode (first layer) having such a configuration.

Further, when the cathode side electrode is formed as a multi-layer structure having the first layer and the second layer adjacent to the first layer, the second layer is formed of Ba _x Sr _1-x Co _y Fe _{1-y. O 3, La x Sr 1-} x Co y Fe 1-y O 3, or La _x Sr _1-x CoO may be provided from the perovskite-type composite oxide represented by _3.

  In this case, it is preferable to make the first layer dense, while making the second layer a porous body having a thickness that allows the oxidant gas to easily diffuse. From this viewpoint, the first layer is formed with a relative density of 95% or more and a thickness of about 0.2 to 10 μm, and the second layer has a thickness of 5 to 50 μm and a porosity of 20 to 30%. It is preferable to form as a thing.

  In order to obtain the dense first layer and the porous second layer as described above, for example, a material having a small particle size is selected as the starting material for the first layer, and a large particle is used as the starting material for the second layer. What is necessary is just to select the diameter. As a specific example in this case, when the first layer is formed, particles having primary particles of 20 to 80 nm and secondary particles of 0.1 to 0.2 μm are used, and the second layer is formed. In some cases, it is possible to use particles having an average particle diameter of 0.5 to 1.2 μm.

  As described above, the intermediate layer may be a porous body. In this case, the intermediate layer can be obtained by first providing a compact from the particles and then pre-sintering the compact. And the open pore which exists in the end surface of this intermediate | middle layer should just be filled with the said 1st layer.

  Furthermore, it is preferable to set the thickness of the intermediate layer to 0.1 to 5 μm from the viewpoint of preventing the interaction between the solid electrolyte and the first layer and not increasing the electric resistance of the electrolyte / electrode assembly.

  According to the present invention, the amount of Zr that diffuses from the electrolyte and reaches the intermediate layer made of a cerium-based oxide and adjacent to the cathode side electrode is suppressed to 40 atomic% or less. It is avoided that a reaction product layer having a high resistance is formed between the cathode side electrode and the cathode side electrode. For this reason, an increase in the internal resistance of the electrolyte / electrode assembly is avoided, so that the charges move quickly in the electrolyte / electrode assembly. As a result, excellent electrical characteristics are exhibited in the electrolyte / electrode assembly.

  The intermediate layer is preferably formed by screen printing or sputtering. This is because an electrolyte / electrode assembly with better electrical characteristics tends to be obtained than when an intermediate layer is formed from a sheet-like molded body.

1 is a schematic entire cross-sectional explanatory view of an electrolyte / electrode assembly (MEA) according to an embodiment of the present invention. It is a principal part enlarged view of MEA of FIG. It is a principal part enlarged view of MEA of a site | part different from FIG. It is a schematic whole cross-sectional explanatory drawing of MEA which concerns on another embodiment. It is a schematic whole cross-sectional explanatory drawing of MEA which concerns on another embodiment. 4 is a chart showing physical properties of an intermediate layer and a cathode side electrode in MEAs of Examples 1 to 4 and Comparative Examples 1 and 2; It is a current density-discharge voltage curve of each MEA of Examples 2 and 3 and Comparative Examples 1 and 2. 4 is a Cole-Cole plot of MEAs of Example 2 and Comparative Example 2. FIG. 11 is a chart showing complex impedances in each of the first part, the second part, and the third part of the Cole-Cole plot shown in FIG. 10 and their total values. It is a definition explanatory drawing explaining the definition of the 1st part of Drawing 9, the 2nd part, and the 3rd part.

  Hereinafter, preferred embodiments of the electrolyte / electrode assembly and the manufacturing method thereof according to the present invention will be described in detail with reference to the accompanying drawings. In addition, all the numerical values of the porosity in the following show the value after reducing nickel oxide.

  FIG. 1 is a schematic overall cross-sectional explanatory view of an electrolyte / electrode assembly (MEA) 10 according to the present embodiment. This MEA 10 is configured by interposing a solid electrolyte 16 between an anode side electrode 12 and a cathode side electrode 14, and an anode side electrode supporting type (so-called ““ ASC "). An intermediate layer 18 is interposed between the cathode side electrode 14 and the solid electrolyte 16.

As the material of the anode side electrode 12, cermet of Ni and Y ₂ O ₃ stabilized ZrO ₂ (YSZ) is preferably selected. Or cermet of Ni and Sc ₂ O ₃ stabilized ZrO ₂ (SSZ), cermet of Ni and Y ₂ O ₃ doped CeO ₂ (YDC), cermet of Ni and Sm ₂ O ₃ doped CeO ₂ (SDC) A cermet of Ni and Gd ₂ O ₃ doped CeO ₂ (GDC) may be used.

  The thickness of the anode side electrode 12 of the ASC made of such a material is set to about 200 to 800 μm, preferably about 600 μm.

The solid electrolyte 16 is made of, for example, Y ₂ O ₃ stabilized ZrO ₂ (8YSZ) to which 8 mol% of Y ₂ O ₃ is added.

  The intermediate layer 18 serves to prevent the elements contained in the cathode side electrode 14 from diffusing into the solid electrolyte 16, in other words, preventing the cathode side electrode 14 and the solid electrolyte 16 from interacting with each other. That is, the intermediate layer 18 functions as a reaction preventing layer. The thickness of the intermediate layer 18 only needs to be sufficient to perform this reaction prevention function, and specifically, about 0.1 to 5 μm is sufficient.

The material of the intermediate layer 18 is not particularly limited as long as it has such a function, but is preferably Sm ₂ O ₃ doped CeO ₂ (SDC), Y ₂ O ₃ doped CeO ₂ (YDC). ), Gd ₂ O ₃ doped CeO ₂ (GDC), La ₂ O ₃ doped CeO ₂ (LDC). In particular, CeO ₂ (10 to ₂₀ SDC) doped with 10 to 20 mol% of Sm ₂ O ₃ is used.

  The intermediate layer 18 may contain Zr. The reason for this is presumed to be that Zr contained in the solid electrolyte 16 is activated and diffused into the intermediate layer 18 by heating when baking the intermediate layer 18.

When Zr is excessively contained in the intermediate layer 18, as described above, since the cathode electrode 14 is a perovskite complex oxide such as LSC or LSCF, La, Sr, and the like may react with Zr. . For this reason, the intermediate layer 18 is preferably selected to have a Zr diffusion amount of 40 atomic% or less obtained by an analytical instrument such as XPS. The diffusion amount of Zr in the intermediate layer 18 is calculated by the following formula (1).
Zr diffusion amount = Zr / (Ce + Zr) (1)

  The diffusion amount of Zr can be controlled by, for example, the firing temperature when the intermediate layer 18 is baked. That is, if the firing temperature is excessively high, the degree of Zr activation increases and the amount of diffusion into the intermediate layer 18 increases. On the contrary, when the firing temperature is low, Zr is not activated so much, and the amount of diffusion into the intermediate layer 18 is reduced.

Therefore, the firing temperature of the intermediate layer 18 is set to a range in which the amount of Zr diffused into the intermediate layer 18 can be suppressed to 40 atomic% or less and the intermediate layer 18 can be densified as much as possible. In many cases, the intermediate layer 18 obtained by performing the baking treatment in such a temperature range is a porous body including pores 20 as schematically shown in FIG. This is because the CeO ₂ oxide forming the intermediate layer 18 is hardly sinterable.

  The pore diameter of the intermediate layer 18 made of a porous body is defined as the average value of the major axis and the minor axis of the opening diameter of a two-dimensional cross section that is confirmed as a field of view of a scanning electron microscope (SEM). The pore diameter defined as described above is about 3 μm at the maximum. The porosity of the intermediate layer 18 is about 25%, and about 40% at the maximum.

  As shown in FIG. 2, some of the pores 20 open at the end face facing the cathode side electrode 14. As described above, since the pore diameter is about 3 μm at the maximum, the diameter of the opened pore 20 is also about 3 μm at the maximum.

  On the intermediate layer 18, the cathode side electrode 14 is laminated (see FIG. 1). In the present embodiment, the cathode side electrode 14 is composed of a laminate in which the first layer 22a and the second layer 22b are laminated in this order from the intermediate layer 18 side. Accordingly, the intermediate layer 18 is adjacent to the first layer 22a.

  One end of the first layer 22a (downward in FIG. 2) fills the pores 20 opened at the end face of the intermediate layer 18 facing the cathode side electrode. For this reason, the contact area between the intermediate layer 18 and the first layer 22a is increased.

  A preferable thickness of the first layer 22a is 0.2 to 10 μm. If it is less than 0.2 μm, it is not easy to fill the open pores 20 with the first layer 22a. Moreover, when it exceeds 10 micrometers, there exists a possibility that a crack may generate | occur | produce at the time of a baking process.

Here, the first layer 22a is represented by _{Ba x Sr 1-x Co y} Fe 1-y O 3, La x Sr 1-x CoO 3 or _{La x Sr 1-x Co y} Fe 1-y O 3 Perovskite complex oxide, that is, so-called BSCF, LSC or LSCF, and is formed as a dense body having a relative density larger than that of the second layer 22b. The preferred relative density of the first layer 22a is 95% or more.

  In order to obtain such a dense first layer 22a, a readily sinterable starting material such as BSCF may be used. Further, particles having a high BET specific surface area may be used. This is because particles having a high BET specific surface area are also easily sinterable.

  As described above, due to the fact that the first layer 22a fills the pores 20 opened in the intermediate layer 18 and the first layer 22a is a dense body, from the intermediate layer 18 to the first layer 22a. The conductive path is sufficiently secured.

  As shown in FIG. 3, the first layer 22a has a concave portion 24 as an open pore on the upper end surface (upper side in FIG. 3) facing the second layer 22b. In some cases, the recess 24 penetrates the second layer 22 b, so that the upper end surface of the intermediate layer 18 may be exposed in the recess 24. In FIG. 3, the first layer 22a is shown as a simple layer and the second layer 22b is shown to indicate that the first layer 22a is a dense body and the second layer 22b is a porous body. Shows grain boundaries.

  The presence of the recess 24 is confirmed by two-dimensionally observing the upper end surface of the first layer 22a with an SEM. In this case, when the area of the entire upper end surface of the first layer 22a is 100%, the ratio of the total area of all the recesses 24 existing on the upper end surface is about 10 to 30%. In other words, in the first layer 22a, the area ratio of the densified portion is 70 to 90%.

  The convex part 26 which protruded from the lower end part (downward in FIG. 3) of the second layer 22b enters the concave part 24. That is, the open pores (recesses 24) of the first layer 22a are filled with the second layer 22b. For this reason, the contact area between the first layer 22a and the second layer 22b increases. As a result, a sufficient conductive path from the first layer 22a to the second layer 22b is secured.

  As understood from the above, in the present embodiment, a sufficient conductive path is formed from the intermediate layer 18 to the second layer 22b. This is because the contact area between the intermediate layer 18 and the first layer 22a is sufficiently large, and the contact area between the first layer 22a and the second layer 22b is also sufficiently large.

  In FIG. 3, the actual contact interface between the first layer 22 a and the second layer 22 b including the concave portion 24 and the convex portion 26 is indicated by a thick solid line, and the concave portion 24 and the convex portion 26 are not present. A boundary line drawn between the part and the part other than the convex portion 26 is indicated by a thick broken line. Hereinafter, the former is referred to as an actual contact interface, the latter is referred to as a virtual boundary line, and the respective reference numerals are L1 and L2.

  The preferred length of the actual contact interface L1 is 140 to 200% of the length of the virtual boundary line L2. If it is less than 140%, the contact area between the first layer 22a and the second layer 22b may not be sufficient. Further, exceeding 200% means that there are excessively many recesses 24, in other words, there are excessive pores in the first layer 22a. In this case, the contact area between the first layer 22a and the intermediate layer 18 may not be sufficient.

  The second layer 22 b functions as a gas diffusion layer for diffusing the oxidant gas supplied to the cathode side electrode 14. Therefore, the second layer 22b is provided as a porous body having a porosity of about 20 to 30%. Note that if the porosity is less than 20%, it is not easy for the oxidant gas to diffuse. Moreover, since intensity | strength will fall when it exceeds 30%, there exists a possibility that a failure | damage may occur.

  The preferred thickness of the second layer 22b is 5 to 50 μm. If it is less than 5 μm, the amount of oxidant gas that can be supplied is reduced. On the other hand, when it exceeds 50 μm, it becomes difficult for the oxidant gas to diffuse.

  The second layer 22b configured as described above can be formed of the above-described perovskite complex oxide such as BSCF, LSCF, or LSC.

  The MEA 10 according to the present embodiment is basically configured as described above. Next, its operational effects will be described in relation to a fuel cell (SOFC) including the MEA 10.

  When configuring an SOFC, a unit cell may be formed by sandwiching the above-described MEA 10 with a separator, and a predetermined number of unit cells may be stacked to form a stack. After that, the unit cells located at both ends of the stack are sandwiched between a pair of end plates, and these end plates are fastened with tie rods or the like to form an SOFC.

  Prior to the operation of the SOFC, NiO-YSZ constituting the anode side electrode 12 is subjected to an initial reduction process to change NiO to Ni. Accordingly, an anode side electrode 12 made of Ni—YSZ is obtained, and the MEA 10 can generate power.

  When operating the SOFC, after raising the SOFC to a predetermined temperature, a fuel gas containing hydrogen is supplied to the anode side electrode 12 of each unit cell, and an oxidant gas containing oxygen is supplied to the cathode side electrode 14. Supplied. In the second layer 22b constituting the cathode side electrode 14, an ionization reaction of oxygen occurs, and oxide ions generated thereby move to the anode side electrode 12 side through the first layer 22a, the intermediate layer 18 and the solid electrolyte 16. .

  Here, as described above, in the present embodiment, the diffusion amount of Zr in the intermediate layer 18 is suppressed to 40 atomic% or less, so that Zr contained in the intermediate layer 18 and the constituent elements of the first layer 22a Is prevented from reacting. That is, the formation of a high-resistance reaction product layer between the intermediate layer 18 and the first layer 22a is avoided. Of course, since the intermediate layer 18 is interposed, it is possible to prevent the reaction product layer from being formed due to the mutual reaction between the first layer 22a and the solid electrolyte 16.

  In addition, the open pores (concave portion 24) of the first layer 22a are filled with the convex portions 26 of the second layer 22b, and the open pores 20 of the intermediate layer 18 are filled with the first layer 22a. For this reason, the contact area between the second layer 22b and the first layer 22a is increased, and the contact area between the first layer 22a and the intermediate layer 18 is increased.

  As a result, the interface resistance between the second layer 22b and the first layer 22a and the interface resistance between the first layer 22a and the solid electrolyte 16 are reduced. Moreover, the first layer 22a is preferably formed of dense BSCF. For this reason, electrical conductivity is large. Similar results can be obtained when the first layer 22a is made of LSCF or LSC.

  As described above, since the amount of Zr diffused in the intermediate layer 18 is suppressed to a predetermined amount or less, the formation of a high-resistance reaction product layer is avoided, and the intermediate layer 18 to the second layer are prevented. Combined with the formation of a sufficient conductive path up to 22b, the voltage drop of the MEA 10 is reduced. Therefore, even when the SOFC is discharged at a large current density, a relatively large discharge voltage can be obtained.

  Next, a method for manufacturing MEA 10 according to the present embodiment will be described.

  In order to obtain the MEA 10 which is ASC, first, the anode side electrode 12 is formed. In this case, for example, a mixed particle in which NiO particles and YSZ particles are mixed at a volume ratio of 1: 1, a binder such as polyvinyl butyral or acrylic, and a pore former such as PMMA resin or carbon. A paste is prepared by adding. In this preparation, NiO particles and YSZ particles have a predetermined particle size and a BET specific surface area so that the shrinkage rate associated with the firing treatment of the anode-side electrode 12 formed as a sheet-like molded body is within a predetermined range. Are selected, and the amount of binder added is set.

For example, when the particle diameter of the NiO particles and the BET specific surface area are 1 to ² μm and 6 to 9 m ² / g, and the particle diameter of the YSZ particles and the BET specific surface area are 0.5 to 3 μm and 4 to 8 m ² / g The binder addition ratio is preferably 40 to 65% by volume. In this case, the shrinkage rate of the anode side electrode 12 accompanying the firing process can be controlled to 8 to 30%.

  Next, the anode side electrode 12 as a sheet-like molded body is formed by the doctor blade method using the paste prepared as described above. The thickness of the sheet-like molded body is set so that the thickness of the anode-side electrode 12 after being subjected to pressure bonding by a hot press or the like and baking treatment is preferably 200 to 800 μm. When the thickness after the baking treatment is smaller than 200 μm, the strength as the support substrate is not sufficient, and the fuel gas supplied to the anode side electrode 12 is not easily diffused. On the other hand, if it is larger than 800 μm, the dimension of the MEA 10 in the stacking direction (thickness direction) becomes large, and the SOFC becomes large for this reason. Further, since the fuel gas flow distance along the thickness direction of the anode-side electrode 12 becomes longer during the operation of the SOFC, there is a concern that the amount of fuel gas leakage along the thickness direction increases.

  Thereafter, a degreasing process is performed on the anode side electrode 12 as necessary. By this degreasing treatment, the pore former disappears, and closed pores and open pores having a diameter corresponding to the average particle diameter of the pore former are formed in the disappearance trace. In addition, when not performing a degreasing process, a pore making material lose | disappears at the time of a baking process.

  At this point, the anode side electrode 12 is made of NiO—YSZ.

  Meanwhile, a paste that is a starting material for the solid electrolyte 16 and the intermediate layer 18 is prepared. The solid electrolyte 16 paste can be prepared by adding 8YSZ powder together with a binder as described above to a solvent, and the intermediate layer 18 paste can be prepared by adding 10-20 SDC powder together with a binder as described above to a solvent. Can be prepared.

  Thereafter, for example, a sheet-like molded body of the solid electrolyte 16 is formed by a doctor blade method. In addition, it can replace with a doctor blade method and can form each sheet-like molded object of desired thickness also by performing an extrusion molding method, a roll coating method, etc.

  Next, this sheet-like molded body (that is, the solid electrolyte 16) is laminated on the anode side electrode 12. Thereafter, a laminated body including the anode-side electrode 12 and the solid electrolyte 16 is obtained by performing pressure bonding by hot pressing or the like.

  Next, a firing treatment is performed on the laminate. What is necessary is just to set the temperature in this case to 1100-1400 degreeC, for example. By this firing treatment, the anode side electrode 12 and the solid electrolyte 16 cause thermal contraction.

  In the present embodiment, after the sheet-like molded bodies are laminated, the anode side electrode 12 and the solid electrolyte 16 are applied with a temperature and a pressure so as to be bonded to each other. As a result, the adjacent layers firmly adhere to each other, so that the layers are hardly separated during the firing process.

  Next, the paste of the intermediate layer 18 is applied on the solid electrolyte 16 of the laminate by screen printing. As a result, a laminate composed of the anode side electrode 12, the solid electrolyte 16, and the intermediate layer 18 is obtained.

  Alternatively, sputtering is performed using a target made of a material that can form the intermediate layer 18, whereby the intermediate layer 18 is formed on the solid electrolyte 16 of the laminate composed of the anode side electrode 12 and the solid electrolyte 16. Also good.

  Next, the laminated body of the anode side electrode 12, the solid electrolyte 16 and the intermediate layer 18 is subjected to a firing process. What is necessary is just to set the temperature in this case to 1100-1400 degreeC similarly to the above, for example. By this firing treatment, the anode side electrode 12, the solid electrolyte 16 and the intermediate layer 18 undergo thermal contraction.

In the above temperature range, the anode electrode 12 and the solid electrolyte 16 are well densified, but the intermediate layer 18 made of a hardly sinterable material such as CeO ₂ oxide is not easily densified. Therefore, the intermediate layer 18 becomes a porous body having many pores 20 as shown in FIG.

  Further, in the temperature range as described above, it is avoided that Zr contained in the solid electrolyte 16 diffuses into the intermediate layer 18. That is, Zr contained in the intermediate layer 18 can be suppressed to 40 atomic% or less.

  Next, the cathode-side electrode 14 is laminated on the intermediate layer 18 of the laminate thus obtained.

  That is, pastes are prepared as starting materials for the first layer 22a and the second layer 22b, respectively. For example, the pastes of the first layer 22a and the second layer 22b can be prepared by adding BSCF and LSCF powders together with a binder as described above to a solvent, respectively.

In order to obtain a dense layer as the first layer 22a, an easily sinterable one such as one having a large BET specific surface area is selected as the BSCF powder. The preferred BET specific surface area of the BSCF powder that can promote sintering is 20 to 35 m ² / g.

  And the paste used as the 1st layer 22a is printed on the intermediate | middle layer 18 with a screen printing method. Here, the thickness of the first layer 22a corresponds to the thickness of the screen mesh plate. That is, as the screen mesh plate, one having a thickness capable of obtaining the first layer 22a having a desired thickness is selected. In this printing, the excess paste fills the pores 20 opened at the end face of the intermediate layer 18.

  Then, a baking process is performed. In this firing treatment, the temperature may be increased at a temperature increase rate of 100 to 200 ° C./hour and then held at 800 to 1100 ° C. for 1 to 4 hours. After that, it is allowed to cool naturally until it reaches room temperature. In this process, the recess 24 is formed.

  Next, the paste to be the second layer 22b is printed on the first layer 22a in accordance with the above. By this printing, the excess paste fills the pores opened at the end face of the first layer 22a, that is, the recesses 24.

  Then, a baking process is performed. Also in this firing process, the temperature is increased at a temperature increase rate of 100 to 200 ° C./hour as in the case of the first layer 22a, and then held at 800 to 1100 ° C. for 1 to 4 hours. Just let it cool naturally. As a result, the MEA 10 including the cathode-side electrode 14 having the first layer 22a and the second layer 22b is obtained.

  The anode side electrode 12, the solid electrolyte 16 and the intermediate layer 18 are fired at the same time, and then the cathode side electrode 14 is formed by screen printing or the like and then dried and fired. The side electrode 12 and the solid electrolyte 16 are fired at the same time, then the intermediate layer 18 is formed by screen printing or the like and then fired, and further, the cathode side electrode 14 is formed by screen printing or the like and then dried and fired. May be applied.

  The present invention is not limited to the embodiments described above, and various modifications can be made without departing from the spirit of the present invention.

  For example, an intermediate layer may be interposed between the anode side electrode 12 and the solid electrolyte 16. This intermediate layer plays a role of flattening by filling or filling irregularities on the side facing the solid electrolyte 16 in the anode side electrode 12 which is a porous body. That is, this intermediate layer functions as a planarization layer.

  Further, as shown in FIG. 4, an electrolyte supporting (ESC) MEA 30 manufactured using the solid electrolyte 16 as a substrate may be used. In this case, the thickness of the solid electrolyte 16 is maximized in the layers constituting the MEA 30. A suitable thickness of the solid electrolyte 16 is about 70 to 100 μm.

  When the MEA 30 that is an ESC is manufactured, the anode-side electrode 12 is provided on one end face of the solid electrolyte 16, and the intermediate layer 18 and the cathode-side electrode 14 are provided on the remaining one end face in this order. Of course, the cathode side electrode 14 is formed as a laminated body having the first layer 22a and the second layer 22b. In ESC, the thickness of the anode side electrode 12 is set to about 50 to 100 μm, preferably about 90 μm.

  The cathode side electrode may have a single layer structure. That is, as illustrated in FIG. 5 exemplifying the MEA 40 that is an ASC, the cathode side electrode may be configured by only the first layer 22c. In this case, it is preferable to form the first layer 22c having a thickness of 5 to 50 μm and a porosity of 20 to 30%, similarly to the second layer 22b of the MEA 10 shown in FIG.

  In the MEA 40, it is desirable to make the intermediate layer 18 as dense as possible. This is because the contact area between the intermediate layer 18 and the relatively porous first layer 22c is ensured.

  Of course, the cathode side electrode having a single-layer structure may be similarly formed in the ESC.

  Furthermore, although the said manufacturing method has illustrated and demonstrated the case where a sheet | seat body is produced, it is not specifically limited to this. For example, after the anode-side electrode 12 or the solid electrolyte 16 is formed by any known method, the remaining layer may be provided by printing, film formation by CVD or PVD, coating by spin coating, dip, or the like. Good.

  Furthermore, a third layer may be laminated on the second layer. In this case, the third layer preferably has an electron diffusion function. That is, it is preferable to form the third layer as an electron diffusion layer.

As the material of the third layer that performs such a function, a material that has a higher electron conductivity than the material that forms the cathode side electrode at the operating temperature of the SOFC and that can reduce oxygen is selected. . As a preferable example of this substance, a complex oxide containing a rare earth element A, a transition metal element C, and oxygen O and having a composition formula represented by ACO ₃ can be given.

Preferred examples of the rare earth element A include at least one selected from the group of La, Sm, Nd, and Pr. On the other hand, suitable examples of the transition metal element C include Co, Fe, and the like. , Ni, Cr, Mn, and Ga. At least one selected from the group of Ga can be used. A specific example is LaCoO ₃ .

  Or you may make it comprise a 3rd layer by LSCF, LSC, etc. FIG.

  And the intermediate | middle layer 18 may be formed from the sheet-like molded object. Similar to the solid electrolyte 16, such a sheet-like molded body can be obtained by performing an appropriate molding method such as a doctor blade method using a paste.

  The MEA 10 having the intermediate layer 18 formed from the sheet-like molded body in this way also exhibits sufficiently excellent electrical characteristics as compared with the MEA according to the conventional technology.

  In accordance with the above, a sheet-like molded body made of NiO-YSZ and having a thickness of 100 μm and a sheet-like molded body made of 8YSZ and having a thickness of 10 μm were prepared, and then laminated in this order and subjected to a firing treatment, whereby the anode-side electrode and the solid An electrolyte laminate was obtained. Further, by performing sputtering, an intermediate layer was formed on the solid electrolyte in the laminate, and then a firing treatment was performed to obtain a sintered body. At this time, the thickness of the intermediate layer was 0.2 μm, and the diffusion amount of Zr determined by the above formula (1) was 8 atomic%.

On the other hand, a powder containing Ba _0.5 Sr _0.5 Co _0.8 Fe _0.2 O ₃ having an average primary particle diameter of 20 to 80 nm and an average secondary particle diameter of _{0.1 to 0.2} μm as BSCF. 1 paste and a second paste containing La _0.5 Sr _0.5 CoO ₃ powder having an average particle diameter of 0.7 μm as LSC were prepared.

  The 1st paste in this was printed on the intermediate | middle layer by screen printing. This was dried and fired at 900 ° C. to obtain a first layer having a thickness of 5 μm, a relative density of 97% (porosity of 3%), and an area ratio of 78%.

  Next, the second paste was printed on the first layer by screen printing. This was dried and then fired at 900 ° C. to obtain a second layer having a thickness of 10 μm and a porosity of 25%. As a result, an MEA having a cathode-side electrode composed of the first layer and the second layer was obtained. The length of the actual contact interface L1 between the first layer and the second layer in this MEA was 150% of the length of the virtual boundary line L2. This is Example 1.

  An intermediate layer having a thickness of 1 to 3 μm and a diffusion amount of Zr of 20 atomic% is formed on the solid electrolyte of the laminate by screen printing, and then subjected to a firing treatment. An MEA including a cathode side electrode having a first layer and a second layer was obtained. This is Example 2.

  An intermediate layer having a thickness of 1 to 3 μm and a Zr diffusion amount of 37 atomic% is formed. On the intermediate layer, a second paste is printed by screen printing, dried, and then fired at 900 ° C. Treatment was performed to form a cathode-side electrode having a single layer structure composed of a layer having a thickness of 10 μm and a porosity of 25%. As a result, an MEA having a cathode-side electrode composed only of the layer was obtained. This is Example 3.

  A layer having a thickness of 0.2 μm and a diffusion amount of Zr of 8 atomic% is formed as an intermediate layer, and the length of the actual contact interface L1 between the first layer and the second layer is 165 that is the length of the virtual boundary line L2. % MEA was obtained. This is Example 4.

  In addition, the length of the actual contact interface L1 with respect to the length of the virtual boundary line L2 was adjusted by changing the firing temperature of the first layer and the second layer.

Comparative Example 1

  An MEA was produced according to Examples 1 and 2 except that an intermediate layer having a thickness of 1 μm and a diffusion amount of Zr of 65 atomic% was formed. This is referred to as Comparative Example 1.

Comparative Example 2

  An MEA was produced according to Example 3 except that an intermediate layer having a thickness of 1 μm and a Zr diffusion amount of 65 atomic% was formed. This is referred to as Comparative Example 2.

  The physical properties of the intermediate layer, the first layer, and the second layer in the MEAs of Examples 1 to 4 and Comparative Examples 1 and 2 are shown in FIG. Here, the “length ratio” in FIG. 6 is a value calculated by multiplying the quotient obtained by dividing the length of the actual contact interface L1 by the virtual boundary line L2 by 100.

  Moreover, although the cathode side electrode in MEA of Example 3 and Comparative Example 3 has a single layer structure, the physical properties of the layer are shown in the column of the second layer for convenience.

  A unit cell was configured using the MEAs of Examples 1 to 4 and Comparative Examples 1 and 2, and the discharge was performed while variously changing the current density, thereby examining the relationship between the current density and the discharge voltage. Among these, the current density-discharge voltage curve of each MEA of Examples 2 and 3 and Comparative Examples 1 and 2 is shown in FIG.

  As can be seen from FIG. 7, both the MEAs of Examples 2 and 3 showed higher voltages than the MEAs of Comparative Examples 1 and 2. This means that the MEAs of Examples 2 and 3 can be discharged at a higher current density than the MEAs of Comparative Examples 1 and 2.

  Although not shown, the MEAs of Examples 1 and 4 also showed higher voltages than the MEAs of Comparative Examples 1 and 2.

  FIG. 8 is a Cole-Cole plot of the MEAs of Example 2 and Comparative Example 1. FIG. 8 shows that the complex impedance of the MEA of Example 2 is small, in other words, excellent conductivity is exhibited.

  FIG. 9 shows the complex impedances in each of the first part, the second part, and the third part of the Cole-Cole plot shown in FIG. Each of the first part, the second part, and the third part represents the IR loss (bulk resistance), the specific IR loss (interface resistance, etc.), and the resistance of the entire MEA.

  Also from FIG. 9, it is clear that the MEAs of Examples 1 to 4 have a low complex impedance and an excellent conductivity.

DESCRIPTION OF SYMBOLS 10, 30, 40 ... Electrolyte electrode assembly (MEA) 12 ... Anode side electrode 14 ... Cathode side electrode 16 ... Solid electrolyte 18 ... Intermediate | middle layer 20 ... Pore 22a, 22c ... 1st layer 22b ... 2nd layer 24 ... Recessed part 26 ... convex part

Claims (14)

An electrolyte / electrode assembly formed by sandwiching a solid electrolyte composed of a zirconium-based oxide between an anode side electrode and a cathode side electrode, and having an intermediate layer interposed between the solid electrolyte and the cathode side electrode,
The cathode side electrode is represented by at least Ba _x Sr _1-x Co _y Fe _1-y O ₃ , La _x Sr _1-x Co _y Fe _1-y O ₃ , or La _x Sr _1-x CoO _3. And a first layer adjacent to the intermediate layer,
The intermediate layer is made of a cerium-based oxide, and the amount of Zr diffused from the solid electrolyte is 40 atomic% or less, and is an electrolyte / electrode assembly.   2. The electrolyte-electrode assembly according to claim 1, wherein when the cathode-side electrode is composed of only the first layer, the first layer has a thickness of 5 to 50 μm and a porosity of 20 to 30%. Electrolyte / electrode assembly. 2. The electrolyte-electrode assembly according to claim 1, wherein the cathode side electrode is adjacent to the first layer, and Ba _x Sr _{1 -x} Co _y Fe _{1 -y} O ₃ , La _x Sr _{1 -x} Co _y Fe. An electrolyte / electrode assembly, further comprising a second layer made of a perovskite complex oxide represented by _1-y O ₃ or La _x Sr _1-x CoO ₃ .   4. The electrolyte / electrode assembly according to claim 3, wherein the first layer has a thickness of 0.2 to 10 μm and a relative density of 95% or more, and the second layer has a thickness of 5 to 50 μm and a porosity. The electrolyte / electrode assembly is characterized by being 20 to 30%.   5. The electrolyte / electrode assembly according to claim 1, wherein when the intermediate layer is a porous body, the first layer has an end face facing the first layer in the intermediate layer. Electrolyte / electrode assembly characterized by filling pores opened by.   The electrolyte / electrode assembly according to claim 1, wherein the intermediate layer has a thickness of 0.1 to 5 μm. A method for producing an electrolyte / electrode assembly in which a solid electrolyte made of a zirconium-based oxide is sandwiched between an anode side electrode and a cathode side electrode, and an intermediate layer is interposed between the solid electrolyte and the cathode side electrode. There,
An anode side electrode is provided directly on one end surface of the solid electrolyte or via an intermediate layer, and then the remaining other end surface of the solid electrolyte is provided via an intermediate layer made of a cerium-based oxide or on the anode side electrode. After providing the solid electrolyte directly on one end face or via an intermediate layer, the cathode side electrode is at least Ba _x Sr _1-x via an intermediate layer made of a cerium-based oxide on the solid electrolyte. _{Co y Fe 1-y O 3} , La x Sr 1-x Co y Fe 1-y O 3, or expressed by La _x Sr _1-x CoO ₃ consists perovskite complex oxide and adjacent to the intermediate layer Having a step of forming as having a first layer,
A method for producing an electrolyte-electrode assembly, wherein an amount of Zr diffused from the solid electrolyte and contained in the intermediate layer made of the cerium-based oxide is 40 atomic% or less.   8. The method according to claim 7, wherein the cathode-side electrode is formed of a single-layer structure composed of only a layer having a thickness of 5 to 50 μm and a porosity of 20 to 30%. Body manufacturing method. 8. The manufacturing method according to claim 7, wherein the cathode side electrode is adjacent to the first layer and the first layer, and Ba _x Sr _1-x Co _y Fe _1-y O ₃ , La _x Sr _1-x. And a second layer made of a perovskite complex oxide represented by Co _y Fe _1-y O ₃ or La _x Sr _1-x CoO _3. Method.   9. The manufacturing method according to claim 8, wherein the first layer has a thickness of 0.2 to 10 [mu] m and a relative density of 95% or more, and the second layer has a thickness of 5 to 50 [mu] m and pores A method for producing an electrolyte / electrode assembly, wherein a material having a rate of 20 to 30% is formed.   The manufacturing method according to claim 10, wherein the first layer is formed using particles having primary particles of 20 to 80 nm and secondary particles of 0.1 to 0.2 μm, and an average particle size of 0.1. A method for producing an electrolyte / electrode assembly, wherein the second layer is formed using particles having a size of 5 to 1.2 μm.   The manufacturing method according to any one of claims 7 to 11, wherein the intermediate layer is formed as a porous body by provisionally sintering the molded body after providing the molded body from particles. A method for producing an electrolyte-electrode assembly, wherein the first layer is filled with open pores existing on one end face of the intermediate layer.   The manufacturing method according to any one of claims 8 to 12, wherein the intermediate layer is formed with a thickness of 0.1 to 5 µm.   The method for producing an electrolyte-electrode assembly according to any one of claims 8 to 13, wherein the intermediate layer is formed by screen printing or sputtering.

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