JPH07102990B2 - Beta-alumina sintered body and method for producing the same - Google Patents
Beta-alumina sintered body and method for producing the sameInfo
- Publication number
- JPH07102990B2 JPH07102990B2 JP3202137A JP20213791A JPH07102990B2 JP H07102990 B2 JPH07102990 B2 JP H07102990B2 JP 3202137 A JP3202137 A JP 3202137A JP 20213791 A JP20213791 A JP 20213791A JP H07102990 B2 JPH07102990 B2 JP H07102990B2
- Authority
- JP
- Japan
- Prior art keywords
- oxide
- weight
- beta
- sintered body
- alumina
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Classifications
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/10—Energy storage using batteries
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- Compositions Of Oxide Ceramics (AREA)
- Secondary Cells (AREA)
Description
【０００１】[0001]
【産業上の利用分野】本発明は、固体電解質であるベー
タアルミナ質焼結体およびその製造方法に関するもので
あり、特にナトリウム−硫黄二次電池に用いるベータア
ルミナ質焼結体およびその製造方法に関するものであ
る。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a beta-alumina sintered body which is a solid electrolyte and a method for producing the same, and more particularly to a beta-alumina sintered body used for a sodium-sulfur secondary battery and a method for producing the same. It is a thing.
【０００２】[0002]
【従来の技術】ベータアルミナ質焼結体は、高いナトリ
ウムイオン伝導性を有するため、ナトリウム−硫黄二次
電池において陽極物質である溶融硫黄と陰極物質である
溶融ナトリウムとを隔離するための固体電解質として利
用できる。そして、このナトリウム−硫黄電池では内部
抵抗の大部分を固体電解質が占める。従って、電池の放
電時の出力低下および充電時の電力損失を小さく抑える
ためには、固体電解質であるベータアルミナ質焼結体の
使用温度範囲、たとえば350 ℃における比抵抗を低くす
ることが望ましい。またナトリウム- 硫黄電池の寿命
は、固体電解質の寿命に依存するため、ベータアルミナ
質焼結体は高強度であることが望ましい。2. Description of the Related Art Beta-alumina sintered bodies have high sodium ion conductivity, and therefore, are solid electrolytes for separating molten sulfur, which is an anode material, and molten sodium, which is a cathode material, in a sodium-sulfur secondary battery. Available as Then, in this sodium-sulfur battery, the solid electrolyte occupies most of the internal resistance. Therefore, in order to suppress the output reduction during discharge of the battery and the power loss during charge, it is desirable to lower the specific resistance in the operating temperature range of the beta-alumina sintered body which is the solid electrolyte, for example, 350 ° C. Since the life of the sodium-sulfur battery depends on the life of the solid electrolyte, it is desirable that the beta-alumina sintered body has high strength.
【０００３】[0003]
【発明が解決しようとする課題】従来、ベータアルミナ
質焼結体の比抵抗を小さくする方法として、焼結体の結
晶相をβアルミナに比較してナトリウムイオン伝導に有
利なβ″アルミナとすることがこれまで行われてきた。
これは、酸化マグネシウム、酸化リチウム等の２価以下
の金属イオンの酸化物を含有させ、β″アルミナ相を安
定化させることにより可能になる。しかしこの方法によ
って得られる比抵抗の値は、組成を最適化したとして35
0 ℃で3.0 Ω・cm程度である。さらに低い抵抗値は、粒
成長を促進させ粒界抵抗を下げることにより可能になる
が、強度が大きく低下して実用に適さなくなる。Conventionally, as a method of reducing the specific resistance of a beta-alumina sintered body, the crystal phase of the sintered body is β ″ alumina which is more advantageous in sodium ion conduction than β-alumina. Things have been done so far.
This can be achieved by stabilizing the β ″ alumina phase by incorporating an oxide of a metal ion having a valence of 2 or less, such as magnesium oxide or lithium oxide. However, the specific resistance value obtained by this method is Optimized as 35
It is about 3.0 Ω · cm at 0 ° C. A lower resistance value can be achieved by promoting grain growth and lowering the grain boundary resistance, but the strength is greatly reduced and it becomes unsuitable for practical use.
【０００４】また、ベータアルミナの耐久性を向上させ
るため、特公昭52-3411 号公報、特公昭52-40325号公報
において、タンタルをベータアルミナ中に添加し、タン
タルまたは酸化タンタルを粒界に存在せしめる技術も開
示されている。しかしながら、この方法で得られるベー
タアルミナは、耐久性は向上するがタンタル成分が異相
として粒界に析出し、粒界抵抗が上昇して比抵抗が高く
なる問題があった。In order to improve the durability of beta-alumina, in Japanese Patent Publication Nos. 52-3411 and 52-40325, tantalum is added to beta-alumina and tantalum or tantalum oxide is present at the grain boundaries. A technology for making a mistake is also disclosed. However, the beta-alumina obtained by this method has a problem that although the durability is improved, the tantalum component is precipitated as a different phase in the grain boundaries, the grain boundary resistance is increased, and the specific resistance is increased.
【０００５】本発明の目的は上述した課題を解消して、
高いナトリウムイオン伝導特性を示しなおかつ高強度の
ベータアルミナ質焼結体およびその製造法を提供しよう
とするものである。The object of the present invention is to solve the above problems,
An object of the present invention is to provide a high strength beta-alumina sintered body that exhibits high sodium ion conductivity and a method for producing the same.
【０００６】[0006]
【課題を解決するための手段】本発明のベータアルミナ
質焼結体は、酸化ナトリウム８〜10重量％、酸化マグネ
シウム3.0 〜5.5 重量％および／または酸化リチウム
0.1〜２重量％、酸化タンタル0.01〜0.5 重量％、残部
が酸化アルミニウムから実質的になり、タンタル成分が
粒界に析出していないことを特徴とするものである。The beta-alumina sintered body of the present invention comprises 8 to 10% by weight of sodium oxide, 3.0 to 5.5% by weight of magnesium oxide and / or lithium oxide.
It is characterized in that 0.1 to 2% by weight, tantalum oxide 0.01 to 0.5% by weight, and the balance being substantially aluminum oxide, and that the tantalum component is not precipitated at the grain boundaries.
【０００７】また、本発明のベータアルミナ質焼結体の
製造法は、酸化ナトリウム８〜10重量％、酸化マグネシ
ウム3.0 〜5.5 重量％および／または酸化リチウム 0.1
〜２重量％、酸化タンタル0.01〜0.5 重量％、残部が酸
化アルミニウムから実質的になるように原料粉末を混合
し、この混合物を成形、焼成することにより、タンタル
成分が粒界に析出していないベータアルミナ焼結体を得
ることを特徴とするものである。The method for producing a beta-alumina sintered body of the present invention is 8-10% by weight of sodium oxide, 3.0-5.5% by weight of magnesium oxide and / or 0.1% of lithium oxide.
.About.2% by weight, tantalum oxide 0.01 to 0.5% by weight, raw material powders are mixed so that the balance is substantially aluminum oxide, and the mixture is molded and fired, so that the tantalum component is not precipitated at the grain boundaries. It is characterized in that a beta-alumina sintered body is obtained.
【０００８】[0008]
【作用】本発明では、酸化タンタルの添加量は0.5 重量
％を越えず、タンタル成分が粒界に析出しないことを規
定している。この理由は、酸化タンタルを過剰に加える
ことによりタンタル成分が異相として粒界に析出してく
るようになると、本発明の目的である高いナトリウムイ
オン伝導性を供しなくなるからである。In the present invention, the addition amount of tantalum oxide does not exceed 0.5% by weight, and the tantalum component does not precipitate at the grain boundaries. The reason for this is that if the tantalum component begins to precipitate at the grain boundaries as a different phase due to excessive addition of tantalum oxide, the high sodium ion conductivity, which is the object of the present invention, will not be provided.
【０００９】本発明のベータアルミナ質焼結体は、酸化
ナトリウム、酸化マグネシウムおよび／または酸化リチ
ウム、酸化タンタルおよび酸化アルミニウムの原料粉末
を所定の割合で混合し、この混合物を所定温度で仮焼し
てβ″アルミナ粉末としてから、成形し焼成することに
より得られる。また酸化タンタルの添加時期であるが、
各原料粉末の混合時に添加するか、あるいは酸化ナトリ
ウム、酸化マグネシウムおよび／または酸化リチウム、
酸化アルミニウムの混合粉末を仮焼してβ″アルミナ粉
末としてから添加する、そのいずれの方法でも構わな
い。In the beta-alumina sintered body of the present invention, raw material powders of sodium oxide, magnesium oxide and / or lithium oxide, tantalum oxide and aluminum oxide are mixed in a predetermined ratio, and the mixture is calcined at a predetermined temperature. It can be obtained by shaping it into β ″ alumina powder, and then firing it. It is time to add tantalum oxide.
Add at the time of mixing each raw material powder, or sodium oxide, magnesium oxide and / or lithium oxide,
Any method may be used, in which the mixed powder of aluminum oxide is calcined to form β ″ alumina powder and then added.
【００１０】なお、酸化タンタル、酸化マグネシウム、
酸化リチウム、酸化アルミニウムは、焼成において酸化
物に変化するものであれば、他の形態たとえば炭酸塩、
硝酸塩、硫酸塩、塩化物として添加してもよい。また焼
成温度は、緻密化してなおかつ粒径が均一微細に維持さ
れ曲げ強度を低下させない温度条件を選択する。酸化タ
ンタルの添加量を増やしていくにつれ、最適焼成温度は
第１表に示すように低下する傾向にある。この焼結体の
結晶相であるが、主にβ″アルミナからなっており、小
量のβアルミナ、アルミン酸ナトリウムを含むこともあ
る。Incidentally, tantalum oxide, magnesium oxide,
Lithium oxide and aluminum oxide may be in any other form, such as carbonate, as long as they can be converted into oxides by firing.
You may add as a nitrate, a sulfate, and a chloride. Further, the firing temperature is selected such that it is densified and the grain size is kept uniform and fine so that the bending strength is not lowered. As the addition amount of tantalum oxide increases, the optimum firing temperature tends to decrease as shown in Table 1. The crystal phase of this sintered body is mainly composed of β ″ alumina and may contain a small amount of β alumina and sodium aluminate.
【００１１】化学組成の範囲を上記のように限定した理
由は、酸化ナトリウムが８重量％より少ないと充分に焼
結せず、10重量％より多いと結晶相中に過剰のアルミン
酸ナトリウムが残存し、比抵抗が高くなるからである。
また、酸化マグネシウムが３重量％より少ない場合、高
抵抗のβアルミナ相が増えて比抵抗が高くなり、5.5重
量％より多い場合結晶相中にスピネルが生じ、緻密化を
阻害し比抵抗も高くなるからである。さらに、酸化リチ
ウムが0.1 重量％より少ないと、高抵抗のβアルミナ相
が増えて比抵抗が高くなり、２重量％より多いと、粒成
長しやすくなり強度が低下するからである。また酸化タ
ンタルについては、0.5 重量％を越えると前に述べたよ
うにベータアルミナ結晶中に固溶しきれなくなったタン
タル成分が異相として粒界に析出し、粒界抵抗が上昇し
て比抵抗が高くなるからである。また、この固溶反応促
進のため、酸化タンタル原料の粒径は小さい方が好まし
く、特に10μｍ以下のものが好ましい。The reason why the range of the chemical composition is limited as described above is that when the amount of sodium oxide is less than 8% by weight, it does not sinter sufficiently, and when it exceeds 10% by weight, excess sodium aluminate remains in the crystal phase. However, the specific resistance increases.
Further, when the magnesium oxide content is less than 3% by weight, the high-resistance β-alumina phase increases and the specific resistance becomes high, and when it is more than 5.5% by weight, spinel is generated in the crystal phase, which inhibits densification and the specific resistance is high. Because it will be. Further, if the lithium oxide content is less than 0.1% by weight, the high-resistance β-alumina phase is increased to increase the specific resistance, and if it is more than 2% by weight, grain growth is likely to occur and the strength is lowered. As for tantalum oxide, when it exceeds 0.5% by weight, as described above, the tantalum component, which cannot be completely dissolved in the beta-alumina crystal, precipitates as a different phase at the grain boundary, increasing the grain boundary resistance and increasing the specific resistance. Because it will be higher. Further, in order to promote this solid solution reaction, it is preferable that the particle size of the tantalum oxide raw material is small, and particularly preferably 10 μm or less.
【００１２】一例として、第４図、第５図に、本発明範
囲内のベータアルミナ質焼結体の微構造写真、及び本発
明範囲外の粒成長したベータアルミナ質焼結体の微構造
写真をそれぞれ示した。第５図に示すように粒成長した
場合には強度が低下する。酸化マグネシウムおよび／ま
たは酸化リチウム、酸化タンタルをそれぞれ本発明範囲
内で含有することにより、各添加物の相互作用により、
高いナトリウムイオン伝導性を有し、なおかつ粒径微細
で強度の高いベータアルミナ質焼結体を製造することが
可能になる。As an example, FIGS. 4 and 5 show microstructure photographs of a beta-alumina sintered body within the scope of the present invention, and microstructure photographs of a grain-grown beta-alumina sintered body outside the scope of the present invention. Are shown respectively. As shown in FIG. 5, when grains grow, the strength decreases. By containing magnesium oxide and / or lithium oxide and tantalum oxide within the scope of the present invention, the interaction of each additive causes
It becomes possible to manufacture a beta-alumina sintered body having a high sodium ion conductivity, a fine grain size, and high strength.
【００１３】[0013]
【実施例】純度99.9％以上のα- アルミナ粉末、Na2CO3
粉末、MgO 粉末、Li2O粉末、Ta2O5 粉末とを、第１表記
載の組成で調合し、エタノールを媒体にしてボールミル
で粉砕混合を行い、1200℃で４時間仮焼してβ″アルミ
ナ粉末原料を合成した。さらに本粉末をエタノールでボ
ールミル粉砕して、造粒し、長さ50mm、幅25mm、厚さ７
mmの角板を金型予備成形した。さらに2.5ton/cm2で静水
圧成形し、MgOるつぼで雰囲気保護して所定の温度で１
時間保持して焼成した。[Example] α-alumina powder having a purity of 99.9% or more, Na 2 CO 3
Powder, MgO powder, Li 2 O powder, and Ta 2 O 5 powder were prepared according to the composition shown in Table 1, pulverized and mixed in a ball mill using ethanol as a medium, and calcined at 1200 ° C. for 4 hours to β ″ Alumina powder raw material was synthesized. Furthermore, this powder was ball-milled with ethanol and granulated, and the length was 50 mm, the width was 25 mm, and the thickness was 7 mm.
A square plate of mm was preformed with a die. Furthermore, hydrostatic pressure molding was performed at 2.5 ton / cm 2 , and the atmosphere was protected with a MgO crucible and the temperature was set to 1 at the specified temperature.
It was held for a time and baked.
【００１４】このようにして得たベータアルミナ質焼結
体の角板について、ブタノールを用いた浮力法により嵩
密度を測定した。また角板から棒状試料を切り出し、35
0 ℃における比抵抗及び４点曲げ強度を測定した。比抵
抗は、NaNO3-NaNO2 の共融塩を電極として、４端子によ
る複素インピーダンス法で測定した。本発明範囲内にお
ける焼結体の結晶相は主にβ″アルミナで、少量のβア
ルミナあるいはアルミン酸ナトリウムを含むものもあっ
た。上記測定結果を表１に示す。本発明範囲外の測定結
果も、比較例として示した。The bulk density of the thus-obtained beta-alumina sintered plate was measured by the buoyancy method using butanol. Also, cut out a rod-shaped sample from the square plate and
The specific resistance and 4-point bending strength at 0 ° C. were measured. The specific resistance was measured by a 4-terminal complex impedance method using a eutectic salt of NaNO 3 —NaNO 2 as an electrode. The crystal phase of the sintered body within the scope of the present invention was mainly β ″ alumina, and some contained a small amount of β alumina or sodium aluminate. The above measurement results are shown in Table 1. Measurement results outside the scope of the present invention Is also shown as a comparative example.
【００１５】[0015]
【表１】 [Table 1]
【００１６】表１から明らかなように、本発明の実施例
は350 ℃における比抵抗が３Ω・cm以下、しかも４点曲
げ強度が150MPa以上という特徴を有している。特に酸化
ナトリウム8.7 〜9.7 重量％、酸化マグネシウム3.5 〜
5.0 重量％および／または酸化リチウム0.5 〜1.5 重量
％、酸化タンタル0.01〜0.5重量％、残部が酸化アルミ
ニウムの化学組成では、比抵抗2.5 Ω・cm以下、しかも
４点曲げ強度200MPa以上と、著しく高いナトリウムイオ
ン伝導特性と曲げ強度の特性を有している。比較例に示
すように、化学組成が本発明範囲から外れると、比抵抗
が高い、あるいは曲げ強度が低い等の特性を示す。また
本発明の範囲外である酸化タンタルが0.5 重量％より多
い組成では、結晶相としてタンタル成分を含む異相が生
じる。EPMA装置により、Ta2O5 の添加量が0.5 重量％を
越えると、ベータアルミナ中に固溶しきれなくなったタ
ンタル元素が粒界中に存在していることが確認されてお
り、異相は粒界に析出したタンタル成分を含む化合物で
ある。同定の結果、化合物の結晶相はタンタル酸ナトリ
ウムであった。As is apparent from Table 1, the examples of the present invention are characterized in that the specific resistance at 350 ° C. is 3 Ω · cm or less and the four-point bending strength is 150 MPa or more. Especially sodium oxide 8.7-9.7% by weight, magnesium oxide 3.5-
5.0% by weight and / or 0.5 to 1.5% by weight of lithium oxide, 0.01 to 0.5% by weight of tantalum oxide, and the balance of aluminum oxide, the specific resistance is 2.5 Ω · cm or less and 4-point bending strength is 200 MPa or more, which is extremely high. It has characteristics of sodium ion conduction and bending strength. As shown in Comparative Examples, when the chemical composition deviates from the range of the present invention, characteristics such as high specific resistance or low bending strength are exhibited. Further, in a composition containing more than 0.5% by weight of tantalum oxide, which is outside the scope of the present invention, a hetero phase containing a tantalum component as a crystal phase occurs. It was confirmed by an EPMA device that when the amount of Ta 2 O 5 added exceeds 0.5% by weight, the tantalum element, which cannot be completely dissolved in beta-alumina, exists in the grain boundaries, and the heterogeneous phase It is a compound containing a tantalum component deposited in the boundary. As a result of the identification, the crystal phase of the compound was sodium tantalate.
【００１７】図１に実施例No.6a のベータアルミナ質焼
結体のＸ線回折チャート、図２に比較例No. 1dのタンタ
ル酸ナトリウムを生じているベータアルミナ質焼結体の
Ｘ線回折チャートを示す。実施例No. 6a, 6b，6c、比較
例No. 1a, 1C, 1dは、Na2O,MgO 量一定として酸化タン
タルの添加量を変化させた時の測定結果である。図３
に、酸化タンタルの添加量とタンタル酸ナトリウム(20
2) ピークのそれぞれ同条件で測定したＸ線回折チャー
トにおけるピーク強度の関係を示す。また、Ta2O5 量に
対する比抵抗の関係を図４に示す。比抵抗はTa2O5 量が
0.5 重量％までは一定の値をとり、無添加に比較すると
ナトリウムイオン伝導度は約35％向上している。Ta2O5
量が0.5 重量％を越えると、粒界に析出したタンタル酸
ナトリウムによると考えられる比抵抗の上昇があった。FIG. 1 is an X-ray diffraction chart of the beta-alumina sintered body of Example No. 6a, and FIG. 2 is an X-ray diffraction of the beta-alumina sintered body of Comparative Example No. 1d producing sodium tantalate. A chart is shown. Example Nos. 6a, 6b and 6c and Comparative Examples Nos. 1a, 1C and 1d are the measurement results when the addition amount of tantalum oxide was changed while keeping the Na 2 O and MgO amounts constant. Figure 3
The amount of tantalum oxide added and sodium tantalate (20
2) The relationship between the peak intensities in the X-ray diffraction chart measured under the same conditions is shown. FIG. 4 shows the relationship of the specific resistance with respect to the amount of Ta 2 O 5 . The resistivity is Ta 2 O 5
It has a constant value up to 0.5% by weight, and the sodium ion conductivity is improved by about 35% as compared with the case of no addition. Ta 2 O 5
When the amount exceeds 0.5% by weight, there is an increase in the specific resistance, which is considered to be due to sodium tantalate precipitated at the grain boundaries.
【００１８】また図５に、本発明例No. 6aの微構造写
真、第６図に比較例No. 1bの微構造写真をそれぞれ示し
た。比較例No. 1bは、1aの化学組成で焼成温度を上げ粒
成長させた結果である。粒成長させたことによりナトリ
ウムイオン伝導度は約20％向上したが、強度が約60％低
下した。FIG. 5 shows a microstructure photograph of the invention sample No. 6a, and FIG. 6 shows a microstructure photograph of the comparative sample No. 1b. Comparative Example No. 1b is the result of increasing the firing temperature and growing grains with the chemical composition of 1a. The grain growth increased the sodium ion conductivity by about 20%, but decreased the strength by about 60%.
【００１９】[0019]
【発明の効果】以上述べたとおり、本発明によれば、高
いナトリウムイオン伝導度を有し、なおかつ粒径微細で
曲げ強度の高いベータアルミナ質焼結体を得ることがで
き、ナトリウム−硫黄二次電池に用いる固体電解質であ
るベータアルミナ質焼結体の製造方法として、極めて有
用なものである。As described above, according to the present invention, it is possible to obtain a beta-alumina sintered body having a high sodium ion conductivity, a fine grain size and a high bending strength. It is extremely useful as a method for producing a beta-alumina sintered body that is a solid electrolyte used in the next battery.
【図１】本発明No.6a のベータアルミナ質焼結体のＸ線
回折チャートを示す図である。FIG. 1 is a view showing an X-ray diffraction chart of a beta-alumina sintered body of the present invention No. 6a.
【図２】比較例No.1d のベータアルミナ質焼結体のＸ線
回折チャートを示す図である。FIG. 2 is a view showing an X-ray diffraction chart of a beta-alumina sintered body of Comparative Example No. 1d.
【図３】酸化タンタルの添加量とタンタル酸ナトリウム
(202) ピークとの関係を示すグラフである。FIG. 3: Addition amount of tantalum oxide and sodium tantalate
It is a graph which shows the relationship with a (202) peak.
【図４】酸化タンタルの添加量と比抵抗との関係を示す
グラフ、FIG. 4 is a graph showing the relationship between the added amount of tantalum oxide and the specific resistance,
【図５】本発明No.6a の結晶の構造を示す顕微鏡写真で
ある。FIG. 5 is a micrograph showing the structure of the crystal of the present invention No. 6a.
【図６】比較例No.1b の結晶の構造を示す顕微鏡写真で
ある。FIG. 6 is a micrograph showing a structure of a crystal of Comparative Example No. 1b.
Claims (2)
ネシウム3.0〜5.5重量％および／または酸化リチウム
0.1〜２重量％、酸化タンタル0.01〜0.5 重量％、残部
が酸化アルミニウムから実質的になり、タンタル成分が
粒界に析出していないことを特徴とするベータアルミナ
質焼結体。1. Sodium oxide 8-10% by weight, magnesium oxide 3.0-5.5% by weight and / or lithium oxide
A beta-alumina sintered body characterized by comprising 0.1 to 2% by weight, tantalum oxide of 0.01 to 0.5% by weight, and the balance being substantially aluminum oxide, with no tantalum component precipitating at grain boundaries.
ネシウム3.0〜5.5重量％および／または酸化リチウム
0.1〜２重量％、酸化タンタル0.01〜0.5 重量％、残部
が酸化アルミニウムから実質的になるように原料粉末を
混合し、この混合物を成形、焼成することにより、タン
タル成分が粒界に析出していないベータアルミナ質焼結
体を得ることを特徴とするベータアルミナ質焼結体の製
造法。2. Sodium oxide 8-10% by weight, magnesium oxide 3.0-5.5% by weight and / or lithium oxide
0.1 to 2% by weight, 0.01 to 0.5% by weight of tantalum oxide, the raw material powders are mixed so that the balance is substantially aluminum oxide, and the mixture is molded and fired, whereby the tantalum component is precipitated at the grain boundaries. A method for producing a beta-alumina-based sintered body, which comprises obtaining a beta-alumina-based sintered body.
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3202137A JPH07102990B2 (en) | 1990-08-13 | 1991-07-18 | Beta-alumina sintered body and method for producing the same |
| DE1991615166 DE69115166T2 (en) | 1990-08-13 | 1991-08-09 | Beta alumina sintered body and process for its production. |
| EP19910307362 EP0471523B1 (en) | 1990-08-13 | 1991-08-09 | Beta alumina sintered body and method of manufacturing the same |
| CA 2048948 CA2048948C (en) | 1990-08-13 | 1991-08-12 | Beta alumina sintered body and method of manufacturing the same |
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21153890 | 1990-08-13 | ||
| JP2-211538 | 1990-08-13 | ||
| JP3202137A JPH07102990B2 (en) | 1990-08-13 | 1991-07-18 | Beta-alumina sintered body and method for producing the same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH054862A JPH054862A (en) | 1993-01-14 |
| JPH07102990B2 true JPH07102990B2 (en) | 1995-11-08 |
Family
ID=26513208
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3202137A Expired - Lifetime JPH07102990B2 (en) | 1990-08-13 | 1991-07-18 | Beta-alumina sintered body and method for producing the same |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07102990B2 (en) |
-
1991
- 1991-07-18 JP JP3202137A patent/JPH07102990B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH054862A (en) | 1993-01-14 |
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