WO2003043111A1 - Oxyde composite pour piles a combustible a oxyde solide, et procede de preparation - Google Patents
Oxyde composite pour piles a combustible a oxyde solide, et procede de preparation Download PDFInfo
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- WO2003043111A1 WO2003043111A1 PCT/JP2002/011949 JP0211949W WO03043111A1 WO 2003043111 A1 WO2003043111 A1 WO 2003043111A1 JP 0211949 W JP0211949 W JP 0211949W WO 03043111 A1 WO03043111 A1 WO 03043111A1
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- composite oxide
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- fuel cell
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Definitions
- the present invention relates to a composite oxide used as an electrolyte or an air electrode of a fuel cell using a solid electrolyte, and a method for producing the same. More specifically, the present invention relates to a composite oxide for a solid oxide fuel cell having a bevelskite structure and having oxygen ion conductivity, and an industrially suitable production method thereof.
- SOFC solid oxide fuel cells
- stabilized zirconia is used as the electrolyte in this fuel cell.
- stabilized zirconia electrolytes have low ionic conductivity at low temperatures and are used at high temperatures above 1000 ° C.
- expensive ceramics must be used instead of metals for fuel cell components.
- a perovskite electrolyte of LaGa ⁇ 3 has recently been developed that can be used at lower temperatures than stabilized zirconia.
- L a S r GaMg0 3 has been reported to show good performance (KHu an g, RS T ic hy, and JB Goodenough, J. Am. C er am. So c., 81 , 2565 (1998), U.S. Patent No. 6004688, JP-A-11-335164, JP-A-11-665165).
- the compounds of this L AGa_ ⁇ 3 system hardly set to G a Gabe perovskite structure is a typical element
- the firing tends to remain impurities heterogeneous phases other than is object assembly formed needed at high temperatures is there.
- the impurity heterogeneous phases below the melting point of the perovskite has a melting point of about 1400 ° C, Oxygen ion conductivity is low LaS rGa0 4, and melting point of 1600 ° C or higher, and oxygen ions lower L a S r Ga 3 ⁇ 7 conductive is typical.
- oxides, carbonates or hydroxides of each metal are used as raw materials. Pulverize, mix and fire as is. As a result, it becomes easy to cause microscopic non-uniformity of the mixed state, so that an impurity foreign phase tends to remain. Firing at a high temperature of 150 ° C. or higher was necessary to synthesize perovskite with a small impurity heterophase.
- the solid composite oxide powder when forming the synthesized solid composite oxide powder into an electrolyte or an electrode for a fuel cell, the solid composite oxide powder is usually press-molded and heated to 130 to 160 ° C. In this way, the sintered body is sintered.
- the oxide powder synthesized by the solid-phase synthesis method is molded and pressed for sintering, the impurity foreign phase contained in the oxide powder is melted, and the voids in the sintered body become oxygen ion conductive. It was difficult to form a uniform electrode body because it was covered with impurities having a low impurity phase.
- the temperature becomes high in a state in which the target composition and the intermediates and the synthesis raw materials are mixed during firing, so that The part may be melted and remain in the final product as a foreign phase of impurities.
- Japanese Patent Publication No. 08-130 018, etc. include yttrium-alkaline earth metal-transition metal composite oxide, bismuth-alkaline earth metal-transition metal composite oxide, lanthanum
- a method for synthesizing citric acid of a non-strontium-cobalt complex oxide or a lanthanum-cobalt-iron complex oxide is disclosed. All of the resulting oxides have low electric conductivity in a low temperature range of 600 to 800 ° C, and are not suitable as materials for a low-temperature operation type solid electrolyte fuel cell.
- an object of the present invention is to enable firing at a relatively low temperature, It is an object of the present invention to provide a high-performance, low-temperature-operation type composite oxide for a solid oxide fuel cell, which has a small amount of impurity foreign phases other than the chemical composition, and an industrially advantageous production method thereof. Disclosure of the invention
- the present inventors reacted a specific raw material compound under specific conditions by a citric acid synthesis method, whereby an intermediate or a target velovskite-type composition (composite oxide) was formed at a low temperature at which an intermediate or a synthesis raw material was not melted. It has been found that the composite oxide finally obtained can produce a composition close to an almost single phase in which the constituent elements are homogeneously dispersed and have a small number of different phases different from the perovskite phase. By using the composite acid, it is possible to improve the performance of the low-temperature operation type solid fuel cell electrode.
- the present invention has the following gist.
- Ln is at least one element selected from the group consisting of lanthanum, cerium, praseodymium, neodymium, samarium, gadolinium, and dysprosium
- A is selected from the group consisting of strontium, calcium, and barium
- B is at least one element selected from the group consisting of magnesium, aluminum and indium
- C is at least one element selected from the group consisting of iron, cobalt, nickel and manganese.
- the present invention relates to a method for producing a composite oxide for a solid oxide fuel cell having a belovskite-type crystal structure represented by the above formula (1), wherein the raw material of a metal element constituting the composite oxide is provided.
- a metal compound of a hydroxide, an acid or a carbonate and thermally decomposes a complex citrate which is a reaction product of the reaction of the metal compound with citric acid.
- FIG. 1A is an X-ray analysis pattern of the composite oxide of Example 1 according to the present invention.
- Fig. 1 (c) This is an image obtained by cutting and enlarging a portion without a void in Fig. 1 (b) by about 8.8 square microns and then performing image processing.
- FIG. 2 X-ray analysis pattern of the composite oxide of Example 2 according to the present invention.
- FIG. 3 is an X-ray analysis pattern of the composite oxide of Example 3 according to the present invention.
- FIG. 4 X-ray analysis pattern of the composite oxide of Example 4 according to the present invention.
- Fig. 5 (c) This is an image obtained by cutting and enlarging a part without a void in Fig. 5 (b) by about 22 square microns and then performing image processing.
- Figure 6 X-ray analysis pattern of the composite oxide of Comparative Example 2 by the conventional method.
- Equation (1) which represents the decoding oxide of the present invention
- the condition of 0.05.ltoreq.x.ltoreq.0.4, 0.02.ltoreq.y.0.4.40, 0.10.ltoreq.y + z.ltoreq.0.45 Is necessary to obtain a perovskite structure.
- ⁇ satisfies 0 ⁇ 1. If ⁇ is out of this range, the perovskite structure becomes unstable, which is not preferable.
- Ln lanthanoid rare earth metal
- A alkaline earth metal
- B non-transition metal
- C transition metal
- all metal ions are converted to citrate in a raw material slurry obtained by mixing a carbonate, oxide or hydroxide of a metal element contained in the composite oxide in water. 25-100%, preferably 60-100%, of the required chemical equivalent of citric acid is added, preferably 25-100 ° C, particularly preferably 50-100 ° C.
- a hydroxide as the Ln lanthanide-based rare earth element raw material in order to obtain a uniform composite citrate in which constituent elements are uniformly dispersed.
- gallium hydroxide as gallium in order to reduce the hetero phase.
- the alkaline earth metal of the component A it is preferable to use a carbonate in order to reduce a heterogeneous phase.
- thermal decomposition and calcination After the reaction with citric acid, drying and dehydration are performed, followed by thermal decomposition and calcination. In this case, it is also possible to perform the thermal decomposition and the calcination in a single-stage calcination. It should be noted that if thermal decomposition and calcining are performed at the same time, it is difficult to equalize the temperature of the reaction system. Therefore, it is preferable to perform thermal decomposition and calcining separately in two stages.
- the formed composite citrate is preferably thermally decomposed at 350 to 500 ° C, and then calcined at 900 to 147 ° C.
- the baking may be carried out as it is in the form of powder, or may be carried out after molding with a press or the like. If the calcination temperature is less than 900 ° C, sintering is insufficient and a dense powder cannot be obtained, which is not preferable. On the other hand, the firing temperature was 1470. If the temperature exceeds C, the furnace body material is deteriorated, and the heat consumption increases.
- the calcination temperature is more preferably from 120 to 140 ° C, particularly preferably from 130 to 140 ° C.
- the heat separation angle and the firing atmosphere may be either an oxidizing atmosphere such as air or an inert atmosphere. Crushing may be performed after thermal decomposition. After firing, it may be pulverized by a jet mill, a pole mill, or the like.
- the grinding method is not particularly limited. According to the present invention, there can be obtained a composite oxide in which the proportion of the different phase different from the phase having the belovskite structure in the sintered body structure is 0.3% or less in terms of area fraction. If the proportion of the heterophase is more than 0.3%, the melting point is lowered, the toughness of the sintered body is lowered, and the electric conductivity is lowered. Particularly preferably, the proportion of the different phases is 0.15% or less, more preferably 0.1% or less.
- Heterophase structure in belovskite composite oxide can be detected by X-ray diffraction spectrum when the fraction of heterophase is high, but can be quantified by reflected electron image with a scanning electron microscope when the fraction of heterophase is low. it can.
- the quantification of the heterophase in the belovskite composite oxide is performed by image analysis of a backscattered electron image.
- L a S r G a 0 4 impurity heterogeneous phases is small, such as, because it formed a single crystal structure, the melting point of preferably 1470 ° C or more, particularly preferably 1500 ° It has a feature of C or more. If the melting point is less than 1470 ° C, it is not preferable because it is easy to melt during molding.
- the composite oxide according to the present invention has an advantage that a tough molded body can be easily obtained as compared with a composite oxide obtained by a conventional solid phase method.
- the conventional solid oxide-based composite oxide it has the characteristic that fine powder is less likely to be generated when the powder is burned.
- the tap density of the powder after milling can be increased, so that there is an advantage that a dense molded body can be easily obtained.
- the tap density of the composite oxide according to the present invention is preferably 1.0 cm 3 or more. If the tap density is less than 1.0 gZcm 3, it is difficult to obtain a dense and high-strength molded body, which is not preferable.
- tap density of 1.2 g / cm 3 or more can be obtained.
- the composite oxide according to the present invention preferably has a weight average particle size of 0.4 to 2 m. If the weight average particle size is less than 0.4, it is not preferable because it is difficult to obtain a dense electrode molded body. On the other hand, if the weight average particle size exceeds 2.0 / im, the strength of the molded body is undesirably reduced. A particularly preferred range of the weight average particle size is 0.8 to 1.3 / m.
- a composite oxide powder was molded at 2 t pressure ZCM 2 in isostatic pressing in a mold, 1450 ° C for 6 hours to obtain a solid electrolyte sintered body, then obtain a 2000 ⁇ image of the sintered body by scanning electron microscopy, and use a high-speed image processor (Carl Zeiss VI DAS (P 1 us) using high-speed image processing software (KS400 manufactured by Carl Zeiss) to sample one sample from 5 fields of view (width 2902 Urn 2 ), calculate the average value, and calculate the average value. The average area fraction was calculated.
- the temperature was set to 70 ° C, and the reaction was performed by adding citric acid necessary for converting all metal ions to citric acid.
- FIG. 1 (b) A sintered body was prepared from this powder, and an image observed with a scanning electron microscope at a magnification of 2000 is shown in FIG. 1 (b).
- Figure 1 (c) shows the image of Fig. 1 (b) that has no chemical (black holes) cut out and enlarged to about 8.8 square microns and then image-processed and binarized. . Only the white part was measured based on Fig. 1 (c).
- the area fraction of the different phases was determined for the five visual fields from the number of particles per unit area and the average particle size, and was found to be 0.292%, 0.172%, 0.141%, 0.065%, 0% .082%, and the average area ratio of the different phases was 0.150%.
- the temperature was set to 70 ° C, and the reaction was performed by adding citric acid necessary for converting all metal ions to citric acid.
- the resultant was dried at 120 ° C. and pulverized, and preliminarily calcined at 400 ° C. for 6 hours to perform thermal decomposition. Thereafter, the mixture was further pulverized and mixed, and baked at 1350 for 12 hours. The shape after firing was white powder. After firing, the mixture was ground with a pole mill for 6 hours. The weight average particle diameter of the obtained composite oxide powder was 0.49 m, and the evening-up density was 1.21 gZcm 3 .
- the results of the crystal structure analysis are shown in FIG. 2, and the state after sintering, the melting point, and the results of X-ray diffraction identification are shown in Table 1.
- the average area ratio of the different phases of the sintered body determined in the same manner as in Example 1 was 0.159%.
- La 0. 8 S r 0 . 2 Ga 0, 6 Mg 0. 2 Co 0. 2 0 3 ⁇ become as Formulated and dispersed in water.
- the temperature was set to 70 ° C, and citric acid necessary for converting all the metal ions to citric acid was added to react.
- the resultant was dried at 120 ° C. and pulverized, and preliminarily calcined at 400 ° C. for 6 hours to perform thermal decomposition. Thereafter, the mixture was further pulverized and mixed, and baked at 1450 ° C for 12 hours. The shape after firing was black powder. After firing, the mixture was ground with a pole mill for 6 hours. The weight average particle size of the protected composite oxide powder was 0.86 m, and the evening-up density was 1.34 g / cm 3 .
- Figure 3 shows the results of the crystal structure analysis, and Table 1 shows the state after firing, melting point, and X-ray diffraction identification results. The average area ratio of the different phases of the sintered body determined in the same manner as in Example 1 was 0.107%.
- the mixture was dried (TC) and pulverized for 12 hours, pre-calcined at 400 ° C for 6 hours, and thermally decomposed. Thereafter, the mixture was further pulverized and mixed, and calcined at 1350 ° C for 12 hours. after the shape was a white powder. baking was milled for 6 hours in ball mill. the resulting weight average particle size of the composite oxide powder with 0. 66 m, evening-up density 1. was 22 gZcm 3 The results of the crystal structure analysis are shown in Fig. 4, and the state after sintering, the melting point and the results of X-ray diffraction identification are shown in Table 1. Average area ratio of different phases of the sintered body obtained in the same manner as in Example 1. Was 0.168%.
- the shape after firing was a brown lump. After firing, the mixture was ground with a pole mill for 6 hours.
- the weight average particle diameter of the obtained composite oxide powder was 2.21 am, and the evening-up density was 0.98 g / cm 3 .
- the results of the crystal structure analysis are shown in Fig. 5 (a), and the state after sintering, the melting point and the results of X-ray diffraction identification are shown in Table 1.
- FIG. 5 (b) shows a 2000 ⁇ scanning electron microscope image observed in the same manner as in Example 1.
- Figure 5 (c) shows a binarized image obtained by cutting out and enlarging a portion without matter (black holes) in the image of Fig. 5 (b) by about 22 square microns and performing image processing. Only the white part was measured based on Fig. 5 (c).
- the heterophasic area fraction was determined for the five visual fields in the same manner as in Example 1, and found to be 0.770%, 0.406%, 0.547%, 1.234%, and 0.596%.
- the average area ratio of the different phases was 0.711%.
- the shape after firing was a black lump. After firing, the mixture was ground with a pole mill for 6 hours.
- ⁇ The obtained composite oxide powder had a weight average particle size of 2.11 im and a tap density of 0.92 g / cm 3 .
- Figure 6 shows the results of the crystal structure analysis, and Table 1 shows the state after sintering, the melting point, and the results of X-ray diffraction identification. No perovskite phase identified
- an extremely uniform and high-performance composite oxide for a low-temperature operation type solid oxide fuel cell which can be fired at a relatively low temperature, has a small amount of impurities other than the target composition, and has a small amount.
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Description
Claims
Priority Applications (4)
Application Number | Priority Date | Filing Date | Title |
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EP02781798A EP1450425A4 (en) | 2001-11-15 | 2002-11-15 | COMPOUND OXIDE FOR A SOLID OXIDE FUEL CELL AND METHOD FOR THE PRODUCTION THEREOF |
CA002467120A CA2467120A1 (en) | 2001-11-15 | 2002-11-15 | Composite oxide for solid oxide fuel cell and process for its production |
US10/494,372 US7368095B2 (en) | 2001-11-15 | 2002-11-15 | Composite oxide for solid oxide fuel cell and method for preparation thereof |
KR10-2004-7007274A KR20040066118A (ko) | 2001-11-15 | 2002-11-15 | 고체산화물 연료전지용 복합산화물 및 그 제조방법 |
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JP2001-350372 | 2001-11-15 | ||
JP2001350372A JP4393027B2 (ja) | 2001-11-15 | 2001-11-15 | 固体酸化物燃料電池用複合酸化物およびその製造方法 |
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WO2003043111A1 true WO2003043111A1 (fr) | 2003-05-22 |
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PCT/JP2002/011949 WO2003043111A1 (fr) | 2001-11-15 | 2002-11-15 | Oxyde composite pour piles a combustible a oxyde solide, et procede de preparation |
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US (1) | US7368095B2 (ja) |
EP (1) | EP1450425A4 (ja) |
JP (1) | JP4393027B2 (ja) |
KR (1) | KR20040066118A (ja) |
CN (1) | CN1285138C (ja) |
CA (1) | CA2467120A1 (ja) |
WO (1) | WO2003043111A1 (ja) |
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EP1749326A1 (en) | 2004-05-31 | 2007-02-07 | Pirelli & C. S.p.A. | Electrochemical device with a lsgm-electrolyte |
CN1315211C (zh) * | 2005-11-30 | 2007-05-09 | 浙江大学 | 固体氧化物燃料电池粉体的制备方法和用途 |
CN100399611C (zh) * | 2006-05-19 | 2008-07-02 | 中国矿业大学(北京) | 固体氧化物燃料电池阴极负载型半电池的制备方法 |
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KR101210509B1 (ko) * | 2007-01-31 | 2012-12-10 | 테크니칼 유니버시티 오브 덴마크 | 고체 산화물 전지에 전극 물질로 사용하기 적합한 복합 물질 |
FR2930075B1 (fr) * | 2008-04-14 | 2011-03-18 | Commissariat Energie Atomique | Titanates de structure perovskite ou derivee et ses applications |
CN101445358B (zh) * | 2008-12-23 | 2011-07-20 | 合肥学院 | 一种NiO-SDC金属氧化物复合粉体的制备方法 |
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EP3203563B1 (en) | 2014-09-30 | 2019-05-01 | LG Chem, Ltd. | Electrolyte membrane, fuel cell including same, battery module including fuel cell, and method for manufacturing electrolyte membrane |
US10115973B2 (en) | 2015-10-28 | 2018-10-30 | Lg Fuel Cell Systems Inc. | Composition of a nickelate composite cathode for a fuel cell |
CN105449227B (zh) * | 2016-01-02 | 2018-07-06 | 红河学院 | 一种层状钙钛矿燃料电池阴极材料及其制备方法 |
TWI799569B (zh) * | 2018-04-17 | 2023-04-21 | 日商三井金屬鑛業股份有限公司 | 固體電解質接合體 |
WO2020008731A1 (ja) * | 2018-07-05 | 2020-01-09 | 株式会社村田製作所 | セラミック部材及び電子素子 |
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CN110729492A (zh) * | 2019-12-06 | 2020-01-24 | 福州大学 | 一种高性能的纳米结构含钴复合阴极材料的共合成方法 |
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CN114634208A (zh) * | 2022-04-13 | 2022-06-17 | 桂林电子科技大学 | 一种氧化物复合材料及其制备方法和应用 |
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JP2003151579A (ja) | 2003-05-23 |
US20050031518A1 (en) | 2005-02-10 |
KR20040066118A (ko) | 2004-07-23 |
CN1586020A (zh) | 2005-02-23 |
CA2467120A1 (en) | 2003-05-22 |
EP1450425A4 (en) | 2009-01-28 |
JP4393027B2 (ja) | 2010-01-06 |
CN1285138C (zh) | 2006-11-15 |
US7368095B2 (en) | 2008-05-06 |
EP1450425A1 (en) | 2004-08-25 |
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