Base tube for fuel cell and material for base tube

Abstract: A base tube for a fuel cell produced by forming a film of a fuel electrode (2) and a film of an air electrode (4) on a surface of the base tube (1), the base tube comprising a mixture of a raw material for the base tube, and coarse particles, whereby the mixture shrinks nonuniformly when sintered to increase the porosity of the base tube. Thus, the gas permeability and the cell electrical efficiency can be increased.

Description: BACKGROUND OF THE INVENTION 1. Field of the Invention This invention relates to a base tube for a fuel cell, whose porosity and pore diameter are increased to improve the power generation characteristics of the resulting fuel cell, and a material for the. base tube. 2. Description of the Related Art Fig. 1 shows the outline of a base tube of a thermal spray type solid electrolyte fuel cell. As shown in Fig. 1, a thermal spray type solid electrolyte fuel cell (SOFC) is produced in the following manner: A thermit of Ni and yttria-stabilized zirconia (YSZ) is provided in a film formed by plasma spraying on a porous cylindrical base tube 1 of calcia-stabilized zirconia (CSZ) to serve as a fuel electrode 2. On this fuel electrode 2, oxygen ion-conductive YSZ is provided in a film form by plasma spraying to serve as an electrolyte 3. On this electrolyte 3, LaCoO 3 is provided in a film form by acetylene flame spraying to serve as an air electrode 4. In this manner, a fuel cell is constructed. Finally, the fuel electrode 2 and the air electrode 4 are connected together in series by an electrically conductive connecting material (interconnector) 5 in a film form composed of a thermit of NiAl and alumina. The production of a fuel cell by thermal spraying as an earlier technology is laborious and costly, and should be decreased in cost. Thus, a co-sinter type fuel cell, which is composed of a base tube, a fuel electrode and an electrolyte sintered integrally, and which requires a reduced number of sintering operations, has been developed. However, this type of fuel cell poses the problem of insufficient gas permeability of the base tube for achieving desired power generation characteristics. Another problem with the base tube of the earlier technology is marked deterioration at a rapid temperature raising and lowering rate during a heat cycle. In detail, with a temperature raising and lowering rate of not higher than 50°C/hour, the performance of the cell after the heat cycle does not differ from'its performance before the heat cycle. At a temperature raising and lowering rate in excess of 50°C/hour, on the other hand, an output drop of about 10% may occur per heat cycle. When fuel cells are used as a gathering, a temperature raising and lowering rate, if not made very slow, exceeds 50°C/hour in a part of the fuel cell gathering, thereby damaging the cell. Thus, there is a demand for a cell which is not damaged even at a rapid temperature raising and lowering rate of about 200°C/hour. Another challenge for the base tube is to improve the fuel utilization factor. The fuel utilization factor of the base tube according to the earlier technology is about 70% of fuel charged. An improvement achieved in the fuel utilization factor can lead to an increase in the efficiency of the fuel cell. Document US-A-4598028 addresses an improvement in the strength and in the gas transport (porosity) of support tubes of SOFCs. It describes a sintered porous support material for SOFCs, which contained from 3 - 45% of thermally stable oxide fibres, which do not react with a support oxide powder. Preferably, the support is a tube. Preferably, the powder consists of calcia-stabilized zirconia particles ranging in size from 1 - 100 µm and preferably from 4 - 20 µm. The fibres may be made of different materials, e.g. yttria or calcia-stabilized zirconia, alumina, alumina-silica, and should have 800 - 2400 µm in length and 0,5 - 20 µm in diameter. Preferably, the fibres contribute to 5 - 20 weight % of the whole composition. The powder and the fibres are blended together with auxiliary materials, needed and extruded to form a body, which is subsequently dried at 100°C and sintered at 1400 - 1700°C. Document EP-A-0921586, which addresses the problem of degradation of based tubes of SOFCs by fast changes in temperature, discloses a material for a base tube of a fuel battery, which in a second aspect of the invention comprises a three-component mixture composed of CaO, ZrO 2 NiO, with the NiO being present as particles having a size of ≤ 5 µm and representing ≤ 13% of the total weight. Also document JP-08250138A addresses a base material with an improved endurance for temperature cycling. The material consists of calcia-stabilized zirconia with a particle size of 30 µm and 10 - 30 volume % of NiO with a particle size of 0,8 µm. SUMMARY OF THE INVENTION It is an object of the present invention to further improve temperature cycling endurance and the fuel utilization factor. This object is attained by the features of claims 1, 3, 5, 7 or 8. Preferred embodiments of the invention are illustrated in the subclaims 2, 4, 6. BRIEF DESCRIPTION OF THE DRAWING The present invention will become more fully understood from the detailed description given hereinbelow and the accompanying drawing which is given by way of illustration only, and thus is not limitative of the present invention, and wherein: Fig. 1 is a schematic view of a base tube for a thermal spray type solid electrolyte fuel cell. DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS Preferred embodiments of the present invention will now be described, but it should be understood that the invention is not restricted thereby. (1) A composite material for the base tube of the invention comprises a mixture of a raw material for the base tube, and coarse particles, so that the mixture shrinks nonuniformly during sintering to increase the porosity of the resulting base tube. The invention, which makes shrinkage nonuniform during sintering to increase the porosity, improves gas permeability. According to this invention, not only the porosity of the base tube, but also. the mean pore diameter of the base tube can be increased, so that gas permeability can be further improved. The raw material for the base tube in the invention is fine particles of calcia-stabilized zirconia (CSZ) having a mean particle diameter of about 0.5 to 2 µm. The coarse particles mixed with the fine particles may be calcia-stabilized zirconia (CSZ) having a mean particle diameter of 5 µm or more, preferably about 10 µm.The raw material for the base tube is not restricted, and MgO-MgAl 2 O 4 , CaTiO 3 -MgAl 2 O 4 , MgTiO 3 -MgAl 2 O 4 , and BaTiO 3 -MgAl 2 O 4 can be exemplified instead of the calcia-stabilized zirconia (CSZ).The upper limit of the particle diameter of the coarse particles added is not limited, and even a particle diameter of about 500 µm enables the invention to exhibit the intended effect.The content of the coarse particles is not restricted, but it is preferably 10 to 40% by weight. If it is less than 10% by weight, the increase in the porosity will be small. If it is more than 40% by weight, a further increase in the porosity will not be achieved.The sintering temperature during production of the base tube of the invention is preferably 1,300 to 1,500°C. If it is lower than 1,300°C, the electrolyte and the interconnector will be insufficient in densification. With sintering at a temperature above 1,500°C, densification of the fuel electrode will be accelerated, producing unfavorable results. (2) Alternatively, the base tube of the invention comprises a mixture of the calcia-stabilized zirconia (CSZ) as the raw material for the base tube, and a metal oxide. Because of the addition of the metal oxide, the metal oxide is reduced and shrinks during power generation, thereby generating pores anew, increasing the pore diameters, and eventually improving the gas permeability. Since the porosity can be increased, and the mean pore diameter also increased, the gas permeability can be improved. The metal oxide added is fine particles of one or more members selected from the group consisting of NiO, CoO, FeO and Fe 2 O 3 . Since the metal oxide is added, shrinkage of the mixture can be made nonuniform at the time of sintering to increase the porosity.The particle diameter of the metal oxide may be 5 µm or more, preferably about 20 µm, rather than the same particle diameter as the particle diameter of the raw material. In this case, increases in the porosity and the pore diameter can be realized, owing to synergy between a shrinkage effect due to reduction of the added metal oxide during power generation and a shrinkage effect due to the increased particle diameter' of the added metal oxide during sintering.The content of the metal oxide is not restricted, but it is preferably 5 to 40% by weight, more preferably 10 to 30% by weight. If it is less than 5% by weight, the increase in the porosity will be small. If it.is more than 40% by weight, a further increase in the porosity will not be achieved.By adding fine particles and coarse particles of the metal oxide in predetermined proportions, the porosity can be increased, the electrical efficiency of the cell can be increased, a leak increase during a heat'cycle can be curbed, and the fuel utilization factor can be increased. That is, the material for the base tube according to the invention comprises a mixture of CaO-stabilized ZrO 2 as the raw material for the base tube, 5 to 30% by weight, based on the CaO-stabilized ZrO 2 , of fine particles having a mean particle diameter of 0.5 to 3 µm, the fine particles being one or more of NiO, CoO and Fe 2 O 3 , and 5 to 30% by weight, based on the CaO-stabilized ZrO 2 , of coarse particles having a mean particle diameter of 5 µm or more, the coarse particles being one or more of NiO, CoO, Fe 2 O 3 and CaO-stabilized ZrO 2 . Alternatively, the material for the base tube according'to the invention comprises a mixture of CaO-stabilized ZrO 2 as the raw material for the base tube, 5 to 30% by weight, based on the CaO-stabilized ZrO 2 , of one or more of titania-derived composite oxides, such as CaTiO 3 , SrTiO 3 , and BaTiO 3 , and CaO-stabilized ZrO 2 , each having a mean particle diameter of 0.5 µm or more, and 5 to 30% by weight, based on the CaO-stabilized ZrO 2 , of one or more of NiO, CoO, and Fe 2 O 3 having a mean particle diameter of 5 µm or more. The upper limit for the particle diameter of the metal oxide added is about 200 µm, if the metal oxide is NiO, CoO, FeO, or Fe 2 O 3 ; or about 500 to 700 µm, if the metal oxide is CaTiO 3 , SrTiO 3 , or BaTiO 3 , for the following reasons: In case of NiO, CoO, FeO, or Fe 2 O 3 , when the particle diameter is 200 µm or more, thermal shrinkage occurs even in a reducing atmosphere during power generation by the fuel cell, and the strength of the base tube decreases. In case of a titania-derived composite oxide such as CaTiO 3 , no thermal shrinkage takes place even in a reducing atmosphere during power generation. Thus, the base tube is consistent with the electrolyte film in terms of thermal expansion, so that the base tube does not decrease, in strength. consequently, the leak increase during heat cycle can be suppressed. According to the present invention, chromia-derived composite oxides such as Cr 2 O 3 , or chromium-based lanthanum composite oxides such as LaCrO 3 can be exemplified instead of the titania-derived composite oxides. EXAMPLES AND TEST EXAMPLES The present invention will be described in more detail with reference to Examples and Test Examples, which in no way limit the invention. [Test Example 1] 80% by weight of a CSZ raw material with a mean particle diameter of 1 µm, and 20% by weight of coarse CSZ particles with a particle diameter of 10 µm were mixed, and sintered at 1,350°C. [Test Example 2] 80% by weight of a CSZ raw material with a mean particle diameter of 1 µm, and 20% by weight of an NiO material with a particle diameter of 1 µm were mixed, and sintered at 1,350°C. [Test Example 3] 80% by weight of a CSZ raw material with a mean particle diameter of 1 µm, and 20% by weight of an NiO material with a particle diameter of 20 µm were mixed, and sintered at 1,350°C. [Referential Example 1] As a control, a CSZ raw material with a mean particle diameter of 1 µm was used alone, and sintered in the same way. The porosity, pore diameter, and cell electrical efficiency of each of the resulting sinters are shown in Table 1. CSZ raw material NiO material Porosity Pore diameter Cell electrical efficiency Ref. Ex.1 Particle diameter 1 µm: 100% None 15% 0.7 µm 0.12 Test Ex.1 Particle diameter 1 µm: 80% Particle diameter 10 µm: 20% None 20% 0.7 µm 0.31 Test Ex.2 Particle diameter 1 µm: 80% Particle diameter 1 µm: 20% 25% 0.7 µm 0.37 Test Ex.3 Particle diameter 1 µm: 80% Particle diameter 10 µm: 20% 30% 1.2 µm 0.44 As shown in Table 1, the base tubes of the Test Examples all increased in the porosity and improved in the cell electrical efficiency in comparison with the Referential Example. Furthermore, as shown in Test Example 3, the addition of the metal material and the associated further increase in the particle diameter synergistically resulted in. a further improvement in the cell electrical efficiency. <Test Examples 1 to 19, Comparative Examples 1 to 7, Examples 20 to 27, and Comparative Examples 8 to 11> Tables 2 and 3 show the compositions of a composite material for a base tube (base material portion) comprising a porous tube according to the present invention indicated in Fig. 1. On the surface of the base tube 1, there were laminated a 100 µm thick fuel electrode 2 comprising Ni-zirconia thermit, a 100 µm thick electrolyte 3 comprising YSZ, and a 1,000 µm thick air.electrode 4. comprising LaMnO 3 doped'with Sr in a proportion of 0.1. Further, a conductive connecting material 5 comprising LaCrO 3 was laminated for connecting the fuel electrode 2 with the air electrode 4 to make a cell. Rapid temperature raising and lowering cycles of the cell were repeated, and then changes in its leak were compared. The porosity and the cell electrical efficiency were also measured. The results are shown in Tables 2 and 3. The compositions in the Examples that are shown in Tables 2 and 3 successfully suppressed the.leak increase. The fuel utilization factor was also increased. In the present Examples, the materials indicated in Tables 2 and 3 were prepared for use as ceramic materials for the base tube 1. The base'tube 1 was prepared by extrusion. Methyl cellulose, glycerin, water, and a stearate emulsion as a lubricant were used as extrusion auxiliaries. The amounts of these auxiliaries used were 4 parts by weight, 5 parts by weight, 10 parts by weight, and 0.2 part by weight for 100 parts by weight of the ceramic materials. The stearate emulsion had a solids concentration of 15% by weight, and contained water as a dispersion medium. Production of the base tube according to the present Examples is described below. First, the ceramic materials and methyl cellulose were weighed in given proportions, placed in a high speed mixer, and mixed for 3 minutes. Then, water, glycerin, and a stearate emulsion were weighed, and added to the mixture, followed by mixing for 1 minute. Then, the mixture was kneaded by means of a twin screw kneader, and formed into a cylindrical product with the use of an extruder. After formation, the product was dried for 24 hours at 60°C, and coated with materials for electrodes. Then, the coated product was heat treated for 2 hours at 1,400°C to make a fuel cell. Each of the resulting cells was subjected to 5 cycles of temperature raising and lowering from room temperature to the power generation temperature and vice versa at a rate of 200°C/hour. Changes in cell performance were examined in this manner. The results of the Examples according to the invention'are shown in Tables 2 and 3, along with Comparative Examples outside the scope of the invention for elucidating the effects of the invention. Table 2 shows that the repetition of temperature raising and lowering did not lead to leak increases in Examples 1 to 19 involving the components within the scope of the invention. The fuel utilization factors were 80% or more, satisfactory values. The cell strengths were 3 kg/mm 2 or more, similarly satisfactory values. The role of NiO with a mean particle diameter of 0.5 to 3 µm is assumed to contribute to suppressing the leak increase during heat cycle. In Comparative Example 7 with a small content of NiO with a mean particle diameter of 0.5 to 3 µm, a leak increase during heat cycle was observed. This effect may be ascribed to an increase in the thermal expansion coefficient of the base tube. The same effect of suppressing the leak increase can be expected of CoO and Fe 2 O 3 . NiO with a mean particle diameter of 0.5 to 3 µm also has the action of densifying the base tube. The .Comparative Examples using the components outside the scope of the invention led to decreases in the fuel' utilization factor, as demonstrated by the results of. Comparative Examples 1 and 6. The role of NiO with a mean particle diameter of 5 to 200 µm is considered to contribute to increasing the fuel utilization factor. This is clear from the finding in Comparative Example 5 that when the amount of NiO with a mean particle diameter of 5 to 200 µm was small, the fuel utilization factor was low. NiO with a mean particle diameter of 5 to 200 µm is also effective in enhancing the cell strength. Deviation from the scope of the components of the invention leads to decreased strength, as demonstrated by Comparative Examples 2 to 3. Table 3 shows that the same effects as des.cribed above were confirmed in Examples 20 to 27 each of which used a base tube containing 5 to 30% by weight of one or more of NiO, CoO and Fe 2 O 3 with a mean particle diameter of 0.5 to 3 µm, and 5 to 30% by weight of one or more of NiO, CoO and Fe 2 O 3 with a mean particle diameter of 5 to 200 µm. By contrast, a decrease in cell strength was noted in Comparative Example 8 in which the content of the coarse particles added was outside the scope of the invention, while a decrease in fuel utilization factor was noted in Comparative Example 9 in which the content of the coarse particles added was outside the scope of the invention. Furthermore, the fuel utilization factor decreased in Comparative Example 10 in which the amount of the fine particles added was more than in the scope of the invention. A leak. increase during heat cycle was observed in-Comparative Example 11 in which the amount of the fine particles added was less than in the scope of the invention. <Examples 28 to 48, Comparative Examples 12 to 18, Examples 49 to 56, and Comparative Examples 19 to 22> Tables 4 and 5 show the compositions of a composite material for a base tube (base material portion) comprising a porous tube according to the present invention indicated in Fig. 1. On the surface of the base tube 1, there were laminated a 100 µm thick fuel electrode 2 comprising an Ni-zirconia thermit, a 100 µm thick electrolyte 3 comprising YSZ, and a 1,000 µm thick air electrode 4 comprising LaMnO 3 doped with Sr in a proportion of 0.1. Further, a conductive connecting material 5 comprising LaCrO 3 was laminated for connecting the fuel electrode 2 with the air electrode 4 to make a cell. Rapid temperature raising and lowering cycles of the cell were repeated, and then changes in its leak were compared. The porosity and the cell electrical efficiency were also measured. The results are shown in Tables 4 and 5. The compositions in the Examples that are shown in Tables 4 and 5 successfully suppressed the increase in leak. The fuel utilization factor was also increased. In the present Examples, the materials indicated in Tables 4 and 5 were prepared for use as ceramic materials for the base tube 1. The base tube 1 was prepared by extrusion. Methyl cellulose, glycerin, water, and a stearate emulsion as a lubricant were used as extrusion auxiliaries. The amounts of these auxiliaries used were 4 parts by weight, 5 parts by weight, 10 parts by weight, and 0.2 part by weight for 100 parts by weight of the ceramic materials. The stearate emulsion had a solids concentration of 15% by weight, and contained water as a dispersion medium. Production of the base tube according to the present Examples is described below. First, the ceramic materials and methyl cellulose were weighed in given proportions, placed in a high speed mixer, and mixed for 3 minutes. Then, water, glycerin, and a stearate emulsion were weighed, and added to the mixture, followed by mixing for 1 minute. Then, the mixture was kneaded by means of a twin screw kneader, and formed into a cylindrical product with the use of an extruder. After formation, the product was dried for 24 hours at 60°C, and coated with materials for electrodes. Then, the coated product was heat treated for 2 hours at 1,400°C to make a fuel cell. Each of the resulting cells was subjected to 5 cycles of temperature raising and lowering from room temperature to the power generation temperature and vice versa at a rate of 200°C/hour. Changes in cell performance were examined in this manner. The results of the Examples according to the invention are shown in Tables 4 and 5, along with the results of Comparative Examples outside the scope of the invention for elucidating the effects of the invention. Table 4 shows that the repetition of temperature raising and lowering did not lead to leak increases in Examples 28 to 48 involving the components within the scope of the invention. The fuel utilization factors were 80% or more, satisfactory values. The cell strengths were 3 kg/mm 2 or more, similarly satisfactory values. The role of CaTiO 3 with a mean particle diameter of 0.5 to 200 µm is assumed to contribute to suppressing the leak increase during heat cycle. This is evidenced by the finding that an increase in.leak during heat cycle was observed in Comparative Example 18 with a small content of CaTiO 3 with a mean particle diameter of 0.5 to 200 µm. This effect may be ascribed to an increase in the thermal expansion coefficient of the base tube. The same effect of suppressing the leak increase can be expected of SrTiO 3 , BaTiO 3 , CaO and MgO. CaTiO 3 with a mean particle diameter of 0.5 to 200 µm also has the action of densifying the base tube. Deviation from the scope of the components according to the invention leads to decreases in the fuel utilization factor, as demonstrated by the results of Comparative Examples 12 and 17. The role of NiO with a mean particle diameter of 5 to 200 µm is considered to contribute to increasing the fuel utilization factor. This is clear from the finding in Comparative Example 16 that when the amount of NiO with a mean particle diameter of 5 to 200 µm was small, the fuel utilization factor was low. NiO with a mean particle diameter of 5 to 200 µm is also effective in enhancing the cell strength. Deviation from the scope of the components of the invention leads to decreased strength, as demonstrated by Comparative Examples 13 to 15. The same effect can be expected of CoO and Fe 2 O 3 . Even with CaTiO 3 with mean particle diameters of 300 and 500 µm, as shown in Examples 44 and 45, increases in porosity and cell strength were both preferred. Table 5 shows that the same effects as described above were confirmed in Examples 49 to 56 each of which used a base tube containing 5 to 30% by weight of one or more of CaTiO 3 , SrTiO 3 , and BaTiO 3 with a mean particle diameter of 0.5 to 200 µm, and 5 to 30% by weight of one or more of NiO, CoO and Fe 2 O 3 with a mean particle diameter of 5 to 200 µm. By contrast, a decrease in cell strength was noted in Comparative Example 19 in which the content of the coarse particles added was outside the scope of the invention, while a decrease in fuel utilization factor was noted in Comparative Example 20 in which the content of the coarse particles added was outside the scope of the invention. Furthermore, the fuel utilization factor decreased in Comparative Example 21 in which the amount of the fine particles added was more than that within the scope of the invention. A leak increase during heat cycle was observed in Comparative Example 22 in which the amount of the fine particles added was less than that within the scope of the invention. <Examples 57 to 59> Table 6 shows the compositions of a composite material for a base tube (base material portion) 1 comprising a porous tube according to the present invention indicated in Fig. 1. In the present Examples, NiO was used as fine particles added, and calcia-stabilized zirconia (CSZ) was used as coarse particles added. On the surface of the base tube 1, there were laminated a 100 µm thick fuel electrode 2 comprising an Ni-zirconia thermit, a 100 µm thick electrolyte 3 comprising YSZ, and a 1,000 µm thick air electrode 4 comprising LaMnO 3 doped with Sr in a proportion of 0.1. Further, a conductive connecting material 5 comprising LaCrO 3 was laminated for connecting the fuel electrode 2 with the air electrode 4 to make a cell. Rapid temperature raising and lowering cycles of the cell were repeated, and then changes in its leak were compared. The porosity and the cell electrical efficiency were also measured. Table 6 shows that repetition of temperature raising and lowering in the base tubes of Examples 57 to 59 did not result in leak increases. The fuel utilization factors were 80% or more, satisfactory values. The cell strengths were 3 kg/mm 2 or more, similarly satisfactory values.

Claims: A base tube for a fuel cell, wherein: a raw material for the base tube is calciastabilized zirconia (CSZ) having a mean particle diameter of 0.5 to 2 µm, and coarse particles having particle diameters of 5 µm or more are mixed with the raw material, the coarse particles being selected from one or more of NiO, CoO, FeO, Fe 2 O 3 , CaTiO 3 , SrTiO 3 , and BaTiO 3 , whereby the mixture of the coarse particles and the raw material shrinks nonuniformly when sintered to increase the porosity of the base tube. The base tube for a fuel cell as claimed in claim 1, wherein: the mixture contains 10 to 40% by weight of the coarse particles. A base tube for a fuel cell, wherein: a raw. material for the base tube is calcia-stabilized zirconia (CSZ) having a mean particle diameter of 0.5 to 2 µm, and fine particles having particle diameters of 0.5 to 3 µm, and coarse particles having particle diameters of 5 µm or more are mixed with the raw material, the fine particles being selected from one or more of NiO, CoO, FeO, Fe 2 O 3 , CaTiO 3 , SrTiO 3 , and BaTiO 3 , and the coarse particles being selected from one or more of NiO, CoO, FeO, Fe 2 O 3 , CaTiO 3 , SrTiO 3 , and BaTiO 3 , whereby the mixture of the fine particles, the coarse particles and the raw material shrinks nonuniformly when sintered to increase the porosity of the.base tube. The base tube for a fuel cell as claimed in claim 3, wherein: the mixture contains 5 to 30% by weight of the fine particles and 5 to 30% by weight of the coarse particles. A material for a base tube for a solid electrolyte fuel cell, the solid electrolyte fuel cell being produced by laminating a film of a fuel electrode, a film of an electrolyte, and a film of an air electrode in this order on a surface of the base tube, said material for the base tube comprising: a mixture of a raw material for the base tube, and coarse particles, the raw material being calcia-stabilized zirconia (CSZ) having a mean particle diameter of 0.5 to 2 µm, and the coarse particles having particle diameters of 5 µm or more and being selected from one or more of NiO, CoO, FeO, Fe 2 O 3 , CaTiO 3 , SrTiO 3 , and BaTiO 3 . The base tube for a fuel cell as claimed in claim 5, wherein: the mixture contains 10 to 40% by weight of the coarse particles. A material for a base tube for a solid electrolyte fuel cell, the solid electrolyte fuel cell being produced by laminating a film of a fuel electrode, a film of an electrolyte, and a film of an air electrode in this order on a surface of the base tube, said material for the base tube comprising a mixture of : calcia-stabilized zirconia (CSZ) having a mean particle diameter of 0.5 to 2 µm, 5 to 30% by weight, based on the CSZ, of fine particles having a mean particle diameter of 0.5 to 3 µm, the fine particles being one or more of NiO, CoO and Fe 2 O 3 , and 5 to 30% by weight, based on the CSZ, of coarse particles having a mean particle diameter of 5 µm or more, the coarse particles being one or more of NiO, CoO, Fe 2 O 3 and CaO-stabilized ZrO 2 , whereby the mixture shrinks nonuniformly when sintered to increase the porosity of the base tube. A material for a base tube for a solid electrolyte fuel cell, the solid electrolyte fuel cell being produced by laminating a film of a fuel electrode, a film of an electrolyte, and a film of an air electrode in this order on a surface of the base tube, said material for the base tube comprising a mixture of: calcia-stabilized zirconia (CSZ) having a mean particle diameter of 0.5 to 2 µm; 5 to 30% by weight, based on the CSZ, of one or more of CaTiO 3 , SrTiO 3 , BaTiO 3 , and CaO-stabilized ZrO 2 having a mean particle diameter of 0.5 µm or more; and 5 to 30% by weight, based on the CSZ, of one or more of NiO, CoO, and Fe 2 O 3 having a mean particle diameter of 5 µm or more, whereby the mixture shrinks nonuniformly when sintered to increase the porosity of the base tube.

Inventors: HISATOME NAGAO, HOUJYOU TORU, KOSAKA KENICHIRO, TSUKUDA HIROSHI, WATANABE YOSHIHARU, YAMASHITA AKIHIRO, HISATOME, NAGAO, HOUJYOU, TORU, KOSAKA, KENICHIRO, TSUKUDA, HIROSHI, WATANABE, YOSHIHARU, YAMASHITA, AKIHIRO, Hisatome, Nagao, c/o Mitsubishi Heavy Ind., Ltd., Houjyou, Toru, c/o Choryo Engineering Co., Ltd., Kosaka, Kenichiro, c/o Mitsubishi Heavy Ind., Ltd., Tsukuda, Hiroshi, c/o Mitsubishi Heavy Ind., Ltd., Watanabe, Yoshiharu, c/o Mitsubishi Heavy Ind.Ltd., Yamashita, Akihiro, c/o Mitsubishi Heavy Ind.,Ltd.
Applicants: MITSUBISHI HEAVY IND LTD, MITSUBISHI HEAVY INDUSTRIES, LTD.
Application year: 2000
Main classification: H01M8
IPC codes: H01M8