JPH01138170A - Low-temperature sintered alumina - Google Patents
Low-temperature sintered aluminaInfo
- Publication number
- JPH01138170A JPH01138170A JP62297100A JP29710087A JPH01138170A JP H01138170 A JPH01138170 A JP H01138170A JP 62297100 A JP62297100 A JP 62297100A JP 29710087 A JP29710087 A JP 29710087A JP H01138170 A JPH01138170 A JP H01138170A
- Authority
- JP
- Japan
- Prior art keywords
- weight
- frit
- alumina
- sintered
- composition
- 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.)
- Pending
Links
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 title claims abstract description 37
- 239000000203 mixture Substances 0.000 claims abstract description 27
- 230000008018 melting Effects 0.000 claims abstract description 12
- 238000002844 melting Methods 0.000 claims abstract description 12
- 238000005245 sintering Methods 0.000 claims abstract description 10
- 238000010586 diagram Methods 0.000 claims description 9
- 230000005496 eutectics Effects 0.000 claims description 2
- 229910011255 B2O3 Inorganic materials 0.000 abstract description 10
- 229910052593 corundum Inorganic materials 0.000 abstract description 5
- 229910001845 yogo sapphire Inorganic materials 0.000 abstract description 5
- ODINCKMPIJJUCX-UHFFFAOYSA-N calcium oxide Inorganic materials [Ca]=O ODINCKMPIJJUCX-UHFFFAOYSA-N 0.000 abstract 2
- 239000002245 particle Substances 0.000 description 20
- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Chemical compound [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 description 10
- 238000005452 bending Methods 0.000 description 9
- 239000010419 fine particle Substances 0.000 description 8
- 238000010438 heat treatment Methods 0.000 description 5
- 229910052697 platinum Inorganic materials 0.000 description 5
- 230000000694 effects Effects 0.000 description 4
- 239000011362 coarse particle Substances 0.000 description 3
- 230000008602 contraction Effects 0.000 description 3
- 238000010304 firing Methods 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 241000259633 Bagous frit Species 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000008020 evaporation Effects 0.000 description 1
- 238000001704 evaporation Methods 0.000 description 1
- 238000009766 low-temperature sintering Methods 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 230000000630 rising effect Effects 0.000 description 1
- 230000004580 weight loss Effects 0.000 description 1
Landscapes
- Compositions Of Oxide Ceramics (AREA)
Abstract
Description
【発明の詳細な説明】
産業上の利用分野
１２５０〜１３００’Ｃの低温で焼結することができ、
しかも曲げ強さの高い焼結体に関するものである。DETAILED DESCRIPTION OF THE INVENTION Industrial applications Can be sintered at low temperatures of 1250-1300'C;
Moreover, it relates to a sintered body with high bending strength.
従来の技術
アルミナは優れた特性を有しているため、広く工業製品
に使用されているが、焼結体を得るには高温とする必要
があった。Prior Art Alumina has excellent properties and is widely used in industrial products, but it is necessary to heat it to a high temperature to obtain a sintered body.
発明が解決しようとする問題点
従来のアルミナは焼結温度が１５００℃以上で非常に高
いため、工業化に対して１つの難点となっており、焼結
温度の１氏いかつ曲げ強度が大である焼結体が望まれて
いた。Problems to be Solved by the Invention Conventional alumina has a very high sintering temperature of 1500°C or higher, which poses a problem for industrialization. A sintered body was desired.
問題点を解決するための手段
本発明は、アルミナにＡ ｌ ２０３ 、 Ｃａｂ、
Ｂ２Ｏ３の３成分からなるものを熔融して作ったフリッ
トを添加した組成物を成形し、１２５０〜１３００℃の
低温で焼結することができる。低温焼結アルミナ焼結体
により前述の問題点を解決し得たものであり、特に、ア
ルミナに前記フリットを３〜８重量％添加してなる低温
焼結アルミナ焼結体により、就中、フリットが３成分組
成図においてＡｌ２Ｏ３とＣａＯとの共融点とＢ２Ｏ３
とを結ぶ線上にある組成割合、即ちＡ ｌ ２０３４３
．７０重量％。Means for Solving the Problems The present invention provides alumina with Al 203, Cab,
A composition to which a frit made by melting three components of B2O3 is added can be molded and sintered at a low temperature of 1250 to 1300°C. The above-mentioned problems can be solved by using a low-temperature sintered alumina sintered body, and in particular, a low-temperature sintered alumina sintered body made by adding 3 to 8% by weight of the frit to alumina can be used to solve the above-mentioned problems. In the ternary composition diagram, the eutectic point of Al2O3 and CaO and B2O3
The composition ratio on the line connecting A l 20343
．． 70% by weight.
Ｃａ０４１．９０重量％、Ｂ２Ｏ３１４．４０重量％の
組成割合のものを蝋石質坩堝で熔融してつくったＡｌ２
Ｏ３３２．５０重量％、 Ｃａ０３６．８０重量％、
Ｂ２Ｏ３８．９０重量％。Al2 made by melting a composition of 41.90% by weight of Ca0 and 14.40% by weight of B2O3 in a rotisserie crucible.
O332.50% by weight, Ca036.80% by weight,
B2O38.90% by weight.
５ｊＯ２１９，２０重量％組成のフリットである低温焼
結アルミナ焼結体により、前述の問題点を解決し得たも
のである。The above-mentioned problems can be solved by using a low temperature sintered alumina sintered body which is a frit having a composition of 5jO219 and 20% by weight.
作 用
前述のフリットをアルミナに添加することにより１２５
０〜１３００’Ｃの低温で液相を作り、該液相によりア
ルミナ粒子間の焼結を促進させ、低温焼結を可能とする
ものである。Effect By adding the above-mentioned frit to alumina, 125
A liquid phase is created at a low temperature of 0 to 1300'C, and the liquid phase promotes sintering between alumina particles, making low-temperature sintering possible.
実 施 例
以下、図面に示す予備試験例、実施例により本発明の構
成について説明する。EXAMPLES The structure of the present invention will be explained below with reference to preliminary test examples and examples shown in the drawings.
本発明のアルミナの添加に使用するフリットは第１図に
示す３成分組成において、Ａｌ２Ｏ３とＣａＯとの共融
点とＢ２Ｏ３とを結ぶ線上にある組成割合、即ちＡ ｌ
２０３４３．７０重１％、 Ｃａ０４１．９０重量、
Ｂ２Ｏ３１４．４０重量％の組成割合のものを蝋石質
坩堝で熔融してつくったＡ ｌ ２０３３２．５０重量
％、 Ｃａ０３６．８０重量％、 Ｂ２Ｏ３８．９０重
量％。The frit used for adding alumina in the present invention has a composition ratio of three components shown in FIG.
20343.70 weight 1%, Ca041.90 weight,
A1 20332.50% by weight, Ca0 36.80% by weight, and B2O38.90% by weight were produced by melting a composition of 14.40% by weight of B2O3 in a waxite crucible.
ＳｉＯ□１９．２０重量％組成のフリットである。This is a frit with a composition of 19.20% by weight of SiO□.
本試験を行うに先立って予備試験として白金坩堝で熔融
してつくったＡ ｌ ２０３４１．７５重量％。A1 20341.75% by weight was prepared by melting it in a platinum crucible as a preliminary test prior to conducting the main test.
Ｃａ０４１．５５重量％、Ｂ２Ｏ３１４．３０重量％、
５ｉＯ３０，９５重量％組成のフリットで行った。Ca041.55% by weight, B2O314.30% by weight,
A frit having a composition of 5iO30 and 95% by weight was used.
（１） 予備試験
、前述の、白金坩堝で熔融してつくったフリットを平均
粒子径５．５μｍ（粗粒）と、３．６μｍ（微粒）との
２種類とし、それぞれを平均粒子径０．５μｍのアルミ
ナに添加して試験を行った。(1) Preliminary test: Frits made by melting in a platinum crucible as described above were made into two types: one with an average particle size of 5.5 μm (coarse particles) and one with an average particle size of 3.6 μm (fine particles), each with an average particle size of 0.5 μm. Tests were conducted by adding it to 5 μm alumina.
以下平均粒子径５．５μｍのフリットを粗粒と、平均粒
子径３．６μｍのフリットを微粒と称する。Hereinafter, frits with an average particle diameter of 5.5 μm will be referred to as coarse particles, and frits with an average particle diameter of 3.6 μm will be referred to as fine particles.
前記粗粒には５μｍ以下の粒子が若干認められ、前記微
粒には５μｍ以上の粒子は認められず、１μｍ以下の粒
子が多く認められる。Some particles of 5 μm or less are observed in the coarse particles, no particles of 5 μm or more are observed in the fine particles, and many particles of 1 μm or less are observed.
前記フリットの昇温収縮曲線は第６図に示す通りであり
、加熱減量曲線は第７図に示す通りである。１３００″
Ｃで２時間放置した場合、減量率は約０．４％で、焼成
によるＢ２Ｏ３の蒸発は少く、焼成後も組成上は大きな
変化はな（ゝＯ
次に前記粗粒および微粒のフリットをそれぞれ平均粒子
径０．５μｍのアルミナに１５重量％添加した試料を１
５００℃まで加熱した場合の昇温収縮曲線を第８図に示
す。同図で明らかなように、粗粒よりも微粒のフリット
を使用する方がよく焼き締ることか予想される。The heating shrinkage curve of the frit is as shown in FIG. 6, and the heating loss curve is as shown in FIG. 7. 1300″
When left for 2 hours at C, the weight loss rate was about 0.4%, the evaporation of B2O3 during firing was small, and there was no major change in composition after firing (ゝO) Next, the coarse and fine frits were A sample containing 15% by weight of alumina with an average particle size of 0.5 μm was
FIG. 8 shows a heating shrinkage curve when heated to 500°C. As is clear from the figure, it is expected that the use of fine-grained frit will result in better baking performance than coarse-grained frit.
次に前記微粒フリットを１５重量％、平均粒子径０．５
μｍのアルミナに添加した試料を１２８０℃，１３００
℃，１３２０℃までそれぞれ昇温し、その後２時間保持
した場合の等温収縮曲線を第９図に示す。同図で明らか
なように、
１２８０″Ｃで２時間保持した場合は僅かに収縮が継続
し、膨張は起らない。１３００℃で２時間保持した場合
は約１時間は収縮が継続するが、その後は膨張する。１
３２０℃で２時間保持した場合は膨張に転する。膨張す
るものは好ましくない。Next, the fine frit was added at 15% by weight and the average particle size was 0.5.
A sample added to μm alumina was heated at 1280℃ and 1300℃.
FIG. 9 shows isothermal contraction curves obtained when the temperature was raised to 1320°C and then held for 2 hours. As is clear from the figure, when held at 1280°C for 2 hours, the shrinkage continues slightly and no expansion occurs.When held at 1300°C for 2 hours, the shrinkage continues for about 1 hour, but After that, it expands.1
When held at 320°C for 2 hours, it begins to expand. I don't like things that expand.
以下１３００℃以下の焼結について試験を行う。Below, a test will be conducted regarding sintering at 1300°C or lower.
平均粒子径０．５μｍのアルミナに５．１０゜１５重量
％のフリットをそれぞれ添加し、１０００ｋｇ／ ｃａ
の圧で成形し６℃／ｍｉｎの昇温で１２００”Ｃ、１２
５０″Ｃ、１３００’Ｃで焼結し、得られた焼結体を調
査の結果、第１表、第２表に示す結果を得た。Frit of 5.10° and 15% by weight was added to alumina with an average particle size of 0.5 μm, and 1000 kg/ca
molded at a pressure of 1200"C with a temperature increase of 6℃/min,
The sintered bodies were sintered at 50''C and 1300'C, and the results shown in Tables 1 and 2 were obtained as a result of investigating the obtained sintered bodies.
前述の結果から次の結論を得た。The following conclusions were drawn from the above results.
ｑ第１表に示す如く、微粒のフリットを１５重量％添加
したものは１３００℃焼結で曲げ強さ３８００ｋｇ／
ｃｒｌ 、 Ｘ密度３．６０．Ｆ／ｃＪ、微粒のフリッ
トを１０重量％添加したものは１３００℃焼結で曲げ強
さ３．３５０ｋｇ ／ ｃａ 。q As shown in Table 1, the material with 15% by weight of fine frit added has a bending strength of 3800 kg/kg when sintered at 1300°C.
crl, X density 3.60. F/cJ, the one with 10% by weight of fine frit added has a bending strength of 3.350 kg/ca when sintered at 1300°C.
嵩密度３．６０ ｐ ／ ｃａとなり共に良好な焼結体
となる。The bulk density is 3.60 p/ca, resulting in a good sintered body.
■第１表には示されていないが、フリット添加１５重量
％のものを１２５０’Ｃで焼結の熟成を充分に行ったも
の（１２５０℃で４時間熟成）は嵩密度３．６８ｐ／ｃ
ｔｌで、第１表記載の１３００℃で２時間熟成のものの
嵩密度３．６０ｇ／ｌｄのものより嵩密度が大で、良好
な焼結体となる。■Although it is not shown in Table 1, the bulk density of 15% frit-added material that has been sufficiently aged by sintering at 1250'C (aged for 4 hours at 1250°C) is 3.68 p/c.
tl, the bulk density was higher than that of the one aged at 1300° C. for 2 hours listed in Table 1, which had a bulk density of 3.60 g/ld, resulting in a good sintered body.
■粗粒の場合は、第２表に示す如く、嵩密度、曲げ強さ
共に低くいずれも不良である。(2) In the case of coarse grains, as shown in Table 2, both bulk density and bending strength are low and both are poor.
■フリットを添加しないアルミナ単体のものは１２００
℃、 １３００℃では全く焼結しない。焼結させうる温
度は１５００℃以上を必要とする。■Alumina alone without frit added is 1200
℃, no sintering occurs at 1300℃. The temperature required for sintering is 1500°C or higher.
前述の予備試験は、白金坩堝でつくったフリットを使用
しているため、実用化、工業化は難しい。The preliminary test mentioned above uses a frit made in a platinum crucible, so it is difficult to put it into practical use or industrialize.
（２）本試験
前述の予備試験の結果に基づき、前記
Ａ １２０３４３．７０重量％、Ｃａ０４１．９０重量
％、 Ｂ２Ｏ３１４．４０重量％の組成のものを蝋石質
坩堝で熔融してツくッたＡ １２０３３２．５０重量％
、ＣａＯ３６，８０重量％、 Ｂ２Ｏ３８．９０重量％
、 ５ｉＯ２１９，２０重量％のフリットを添加して本
試験を行った。(2) Main test Based on the results of the preliminary test mentioned above, A with the composition of A 120343.70% by weight, Ca041.90% by weight, and B2O3 14.40% by weight was melted in a rosite crucible. 120332.50% by weight
, CaO36.80% by weight, B2O38.90% by weight
, 5iO219, 20% by weight of frit was added for this test.
ａ、前述の組成の平均粒子径３．６μｍ（微粒）のフリ
ットを平均粒子径０．５μｍのアルミナに１５重量％添
加した場合の昇温収縮曲線を第３表および第２図に示す
。a. Table 3 and FIG. 2 show temperature-rise shrinkage curves when 15% by weight of frit having the above-described composition with an average particle size of 3.6 μm (fine particles) was added to alumina with an average particle size of 0.5 μm.
ｂ、平均粒子径３．６μｍ（微粒）の前述の組成のフリ
ットを平均粒子径０．５μｍのアルミナに３．５．８の
各重量％（３〜８重量％）添加し、それぞれを１１００
０ｔ ／ ｃａの圧で成形し、６℃／ｍｉｎの昇温で１
３００℃で焼結した。該焼結体の試験結果を第４表およ
び第３図、第４図、第５図に示す。b. Frits of the above composition with an average particle size of 3.6 μm (fine particles) were added to alumina with an average particle size of 0.5 μm in an amount of 3.5.8% by weight (3 to 8% by weight), and 1100% of each was added.
Molded at a pressure of 0t/ca and heated at a rate of 6°C/min.
It was sintered at 300°C. The test results of the sintered body are shown in Table 4 and FIGS. 3, 4, and 5.
尚、ＡＮ ２０３ ＣａＯＢ２Ｏ３の３成分からなる
前述の組成のものを白金坩堝で熔融してつくった平均粒
子径３．６μｍの微粒子フリットを平均粒子径０．５μ
ｍのアルミナに添加した組成物を１０００＆ｇ／ ｃｔ
ｌの圧で成形し１３００℃で焼結したところの、前記フ
リットを１０重量％添加した焼結体は曲げ強さ３．３５
０に９／（２１１％同じ＜１５重量％添加した焼結体は
曲げ強さ３８００＆ｇ／ ｃＡのいずれも高い曲げ強さ
のものとなるが、白金坩堝を使用するため工業化は難し
い。Furthermore, a fine particle frit with an average particle size of 3.6 μm made by melting the above-mentioned composition consisting of the three components of AN 203 CaOB2O3 in a platinum crucible was used as a fine particle frit with an average particle size of 0.5 μm.
Composition added to m alumina at 1000g/ct
The sintered body to which 10% by weight of the frit was added had a bending strength of 3.35 when molded at a pressure of 1 and sintered at 1300°C.
0 to 9/(211% Same <15% by weight) The sintered body has a high bending strength of 3800 g/cA, but it is difficult to commercialize it because a platinum crucible is used.
前述の通り本発明の、Ａｌ ２０３ ＣａＯＢ２Ｏ３
の３成分からなる第１図中Ｆ点の組成のもの、即ちＡ
１２０３４３．７０重量％、Ｃａ０４１．９０重量％、
Ｂ２Ｏ３１４．４０重量％の組成物を蝋石質坩堝で熔
融してつくったＡ７Ｉ２０３３２．５０重量％、 Ｃａ
０３６．８重量％、Ｂ２Ｏ３３，９０重量％、 ５ｉ（
ｈ１９．２０重量％の組成で、平均粒子径３．６μｍの
微粒子フリットを平均粒子径０．５μｍのアルミナに各
３．５．８重量％（３〜８重量％）添加し、１１００（
ｌａ／ ｃＪの圧で成形し１２５０’Ｃで焼結し熟成を
充分に行うか、１２５０℃より高く１３００℃までの範
囲の温度で焼結した焼結体は嵩密度が大で、気孔も殆ど
なく、第４表に示す通り、いずれも３０００ｋｇ／ ｃ
ｒＡ以上の曲げ強さを有する。As mentioned above, Al 203 CaOB2O3 of the present invention
The composition at point F in Figure 1 consists of three components, that is, A
120343.70% by weight, Ca041.90% by weight,
A7I20332.50% by weight, Ca made by melting a composition of 14.40% by weight of B2O3 in a waxy crucible
036.8% by weight, B2O33, 90% by weight, 5i(
h19. With a composition of 20% by weight, 3.5.8% by weight (3 to 8% by weight) of fine particle frit with an average particle size of 3.6 μm was added to alumina with an average particle size of 0.5 μm, and
A sintered body formed under a pressure of la/cJ and sintered at 1250'C for sufficient aging, or sintered at a temperature higher than 1250°C up to 1300°C has a high bulk density and almost no pores. As shown in Table 4, all of them are 3000kg/c.
It has a bending strength of rA or more.
アルミナ単体は１３００℃では全く焼結せず、１５００
℃以上の温度を必要とする。Alone alumina does not sinter at all at 1300°C, and at 1500°C
Requires a temperature of ℃ or higher.
発明の効果
本発明はＡｌ２Ｏ３，ＣａＯ９Ｂ２０３からなるものを
熔融してつくったフリットをアルミナに添加した組成物
を成形し、１２５０°〜１３００’ｃの低温で膨張する
ことなく嵩密度の高いものを焼結することができたもの
であり、アルミナ焼結体として焼結温度を２５０℃以上
下げることができ、しかも３０００／ｃｇ／ ｃａの曲
げ強さの焼結体を実現することができ、工業化も容易で
コスト［氏減も大きいという各種の効果を奏するもので
ある。Effects of the Invention The present invention molds a composition in which a frit made by melting Al2O3 and CaO9B203 is added to alumina, and sinters it at a low temperature of 1250° to 1300'c without expanding and having a high bulk density. It is possible to lower the sintering temperature by 250℃ or more as an alumina sintered body, and also to realize a sintered body with a bending strength of 3000/cg/ca, making it possible to industrialize it. It has various effects such as ease and cost reduction.
特にフリットを３〜８重量％添加することにより、就中
Ａｌ２Ｏ３４３．７０重量％、 Ｃａ０４１．９０重量
％、 Ｂ２Ｏ３１４．４０重量％の組成割合のものを蝋
石質坩堝で溶融してつくったフリットを添加することに
より前述の効果を確実に奏することができる。In particular, by adding 3 to 8% by weight of frit, a frit made by melting a composition of 43.70% by weight of Al2O3, 1.90% by weight of Ca04, and 14.40% by weight of B2O3 in a Rouseki crucible is added. By doing so, the aforementioned effects can be reliably achieved.
第１図はフリットと３成分組成図、第２図は実施例の昇
温収縮曲線図、第３図は同上フリット添加重量％−収縮
率線図、第４図は同上フリット添加重量％−嵩密度線図
、第５図は同上フリット添加重量％−曲げ強さ線図、第
６図は比較例（予備試験）の昇温収縮曲線図、第７図は
同上加熱減量曲線図、第８図は同上昇温収縮曲線図、第
９図は同上等温収縮曲線図である。Figure 1 is a frit and three component composition diagram, Figure 2 is a temperature-rise shrinkage curve diagram of the example, Figure 3 is a graph showing the frit addition weight % vs. shrinkage rate diagram, and Figure 4 is the frit addition weight % vs bulk. Density diagram, Figure 5 is the above frit addition weight % - bending strength diagram, Figure 6 is the heating shrinkage curve of the comparative example (preliminary test), Figure 7 is the heating loss curve of the same, Figure 8 9 is a rising temperature contraction curve diagram of the same, and FIG. 9 is an isothermal contraction curve diagram of the same.
Claims (3)
の３成分が熔融されてつくられたフリットが、添加され
てなる組成物の成形体が１２５０〜１３００℃で焼結さ
れて得られる低温焼結アルミナ焼結体。1. Alumina, Al_2O_3CaO, B_2O_3
A low-temperature sintered alumina sintered body obtained by sintering a molded body of a composition to which a frit made by melting the three components is sintered at 1250 to 1300°C.
範囲第１項記載の低温焼結アルミナ焼結体。2. The low-temperature sintered alumina sintered body according to claim 1, wherein 3 to 8% by weight of frit is added.
とＣａＯとの共融点とＢ＿２Ｏ＿３点とを結ぶ線上にあ
る組成割合である、Ａｌ＿２Ｏ＿３４３．７０重量％，
ＣａＯ４１．９０重量％、Ｂ＿２Ｏ＿３１４．４０重量
％の組成割合のものが蝋石質坩堝で熔融されてつくられ
たフリットである特許請求の範囲第１項または第２項記
載の低温焼結アルミナ焼結体。3. The frit is Al_2O_3 in the three-component composition diagram.
Al_2O_343.70% by weight, which is the composition ratio on the line connecting the eutectic point of and CaO and the B_2O_3 point,
The low-temperature sintered alumina sintered body according to claim 1 or 2, which is a frit made by melting a composition of 41.90% by weight of CaO and 314.40% by weight of B_2O_ in a waxite crucible. .
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62297100A JPH01138170A (en) | 1987-11-25 | 1987-11-25 | Low-temperature sintered alumina |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62297100A JPH01138170A (en) | 1987-11-25 | 1987-11-25 | Low-temperature sintered alumina |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH01138170A true JPH01138170A (en) | 1989-05-31 |
Family
ID=17842202
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP62297100A Pending JPH01138170A (en) | 1987-11-25 | 1987-11-25 | Low-temperature sintered alumina |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH01138170A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03174354A (en) * | 1989-11-30 | 1991-07-29 | Kyocera Corp | Aluminum oxide-based sintered body and production thereof |
| EP0810189A1 (en) * | 1996-05-28 | 1997-12-03 | Max-Planck-Gesellschaft zur Förderung der Wissenschaften e.V. | Liquid phase sintering process for alumina ceramics |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS4864587A (en) * | 1971-12-08 | 1973-09-06 | ||
| JPS61222957A (en) * | 1985-03-29 | 1986-10-03 | 株式会社住友金属セラミックス | Low temperature burnt ceramics |
-
1987
- 1987-11-25 JP JP62297100A patent/JPH01138170A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS4864587A (en) * | 1971-12-08 | 1973-09-06 | ||
| JPS61222957A (en) * | 1985-03-29 | 1986-10-03 | 株式会社住友金属セラミックス | Low temperature burnt ceramics |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03174354A (en) * | 1989-11-30 | 1991-07-29 | Kyocera Corp | Aluminum oxide-based sintered body and production thereof |
| EP0810189A1 (en) * | 1996-05-28 | 1997-12-03 | Max-Planck-Gesellschaft zur Förderung der Wissenschaften e.V. | Liquid phase sintering process for alumina ceramics |
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