JPH0624975B2 - Method for producing titanate powder - Google Patents
Method for producing titanate powderInfo
- Publication number
- JPH0624975B2 JPH0624975B2 JP9959687A JP9959687A JPH0624975B2 JP H0624975 B2 JPH0624975 B2 JP H0624975B2 JP 9959687 A JP9959687 A JP 9959687A JP 9959687 A JP9959687 A JP 9959687A JP H0624975 B2 JPH0624975 B2 JP H0624975B2
- Authority
- JP
- Japan
- Prior art keywords
- mol
- tio
- powder
- titanate
- particle size
- 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.)
- Expired - Lifetime
Links
- 239000000843 powder Substances 0.000 title claims description 21
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 title claims description 18
- 238000004519 manufacturing process Methods 0.000 title claims description 7
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 13
- 239000000203 mixture Substances 0.000 claims description 13
- 238000010438 heat treatment Methods 0.000 claims description 8
- 239000010419 fine particle Substances 0.000 claims description 5
- 238000002844 melting Methods 0.000 claims description 5
- 230000008018 melting Effects 0.000 claims description 5
- 238000001816 cooling Methods 0.000 claims description 4
- 229910052705 radium Inorganic materials 0.000 claims description 3
- 229910052712 strontium Inorganic materials 0.000 claims description 3
- 239000002253 acid Substances 0.000 claims description 2
- 229910020091 MgCa Inorganic materials 0.000 claims 1
- 101100003996 Mus musculus Atrn gene Proteins 0.000 claims 1
- 239000002245 particle Substances 0.000 description 21
- 238000000034 method Methods 0.000 description 12
- 239000003985 ceramic capacitor Substances 0.000 description 6
- 238000009826 distribution Methods 0.000 description 5
- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Substances [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 description 5
- 238000000354 decomposition reaction Methods 0.000 description 4
- 238000005245 sintering Methods 0.000 description 4
- QTBSBXVTEAMEQO-UHFFFAOYSA-N Acetic acid Chemical compound CC(O)=O QTBSBXVTEAMEQO-UHFFFAOYSA-N 0.000 description 3
- 238000010306 acid treatment Methods 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 238000010586 diagram Methods 0.000 description 3
- 238000007496 glass forming Methods 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 229910052697 platinum Inorganic materials 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 238000003746 solid phase reaction Methods 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- MUBZPKHOEPUJKR-UHFFFAOYSA-N Oxalic acid Chemical compound OC(=O)C(O)=O MUBZPKHOEPUJKR-UHFFFAOYSA-N 0.000 description 2
- 229910052790 beryllium Inorganic materials 0.000 description 2
- 229910052791 calcium Inorganic materials 0.000 description 2
- 238000006243 chemical reaction Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 229910052749 magnesium Inorganic materials 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 238000002156 mixing Methods 0.000 description 2
- 239000012071 phase Substances 0.000 description 2
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 238000001354 calcination Methods 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 239000003989 dielectric material Substances 0.000 description 1
- 238000004455 differential thermal analysis Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 239000011521 glass Substances 0.000 description 1
- 150000002978 peroxides Chemical class 0.000 description 1
- 238000010587 phase diagram Methods 0.000 description 1
- 238000010298 pulverizing process Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Inorganic Compounds Of Heavy Metals (AREA)
Description
【発明の詳細な説明】 〔発明の目的〕 （産業上の利用分野） 本発明は電子部品、特にセラミックコンデンサ等の材料
に適するチタン酸塩粉末の製造方法に関する。DETAILED DESCRIPTION OF THE INVENTION Object of the Invention (Field of Industrial Application) The present invention relates to a method for producing a titanate powder suitable for a material such as an electronic component, particularly a ceramic capacitor.
（従来の技術） 従来、電子部品用材料たとえばＢａＴｉＯ3，ＳｒＴｉ
Ｏ3などのチタン酸塩粉末の製造方法としては、固相反
応法が一般的に用いられている。固相反応法は、ＢａＴ
ｉＯ3を例にとるとＴｉＯ2とＢａＣＯ3を混合し電気炉
中で仮焼して得られるＢａＴｉＯ3焼結体を粉砕・後処
理して粉末とする方法である。この方法は経済性，量産
性に優れているが、得られる粉末の粒径が２〜３μｍと
比較的大きいうえに粒径分布幅も広い。(Prior Art) Conventionally, materials for electronic parts such as BaTiO 3 and SrTi
A solid-phase reaction method is generally used as a method for producing a titanate powder such as O 3 . The solid-phase reaction method is BaT
Taking iO 3 as an example, it is a method of pulverizing and post-treating a BaTiO 3 sintered body obtained by mixing TiO 2 and BaCO 3 and calcining in an electric furnace to obtain a powder. This method is excellent in economical efficiency and mass productivity, but the particle size of the obtained powder is relatively large as 2 to 3 μm and the particle size distribution width is wide.
また固相反応法以外にシュウ酸塩分解法、複合過酸化物
分解法、錯体分解法などが知られている。これらの方法
によって製造される粉末の粒径は、０．５〜１．５μｍ
程度でセラミックコンデンサ用には適するが、やはり前
者同様粒径分布が広く、ばらつきが大きい。In addition to the solid-phase reaction method, oxalate decomposition method, complex peroxide decomposition method, complex decomposition method and the like are known. The particle size of the powder produced by these methods is 0.5 to 1.5 μm.
Although it is suitable for ceramic capacitors to some extent, it also has a wide particle size distribution and large variations like the former.
（発明が解決しようとする問題点） 上記製造方法ではいずれも粒径の制御が難しく粒径のそ
ろった均一な粉末が得られない欠点があった。粒径が不
均一であると、焼結する際に焼結体の機械的強度が不安
定となり素子の寿命を短くする原因となる。(Problems to be Solved by the Invention) In any of the above-mentioned production methods, there is a drawback in that it is difficult to control the particle size and a uniform powder having a uniform particle size cannot be obtained. If the particle size is not uniform, the mechanical strength of the sintered body becomes unstable during sintering, which shortens the life of the device.
また近年、電子機器の小型化に伴いセラミックコンデン
サなどの素子も小型大容量のものが望まれている。小型
大容量化を実現するひとつの手段として積層セラミック
コンデンサがあり、積層数を増してさらに大容量化する
方法が知られている。しかし、積層数を増加させること
は誘電体層間に設けられる内部電極数をも増加させるこ
ととなり著しいコストの上昇をまねく。これは、現在の
積層セラミックコンデンサがＢａＴｉＯ3あるいは、Ｓ
ｒＴｉＯ3を主成分とするため焼結温度が１３００〜１
４００℃と高く、内部電極として高価なＰｔやＰｄを使
用せざるを得ないためである。これに対する解決策のひ
とつとして誘電体材料粉末を微細化して焼結温度を低下
させることによって、内部電極にＡｇ等比較的安価な材
料の使用を可能にする方法が考えられ、これに適した高
品位で微細な粉末が求められている。In recent years, along with the miniaturization of electronic devices, elements such as ceramic capacitors having small size and large capacity have been desired. There is a monolithic ceramic capacitor as one means for realizing a small size and a large capacity, and a method for increasing the capacity by increasing the number of laminated layers is known. However, increasing the number of stacked layers also increases the number of internal electrodes provided between the dielectric layers, resulting in a significant increase in cost. This is because the current monolithic ceramic capacitor is BaTiO 3 or S
Since rTiO 3 is the main component, the sintering temperature is 1300 to 1
This is because Pt or Pd, which has a high temperature of 400 ° C. and is expensive, must be used as the internal electrode. As one of the solutions to this problem, a method of making it possible to use a relatively inexpensive material such as Ag for the internal electrodes by making the dielectric material powder fine and lowering the sintering temperature is considered. Fine powder is required.
本発明は上記事情を考慮してなされたもので、微細で粒
径の均一なチタン酸塩粉末を安定して供給することを目
的とする。The present invention has been made in consideration of the above circumstances, and an object thereof is to stably supply a fine titanate powder having a uniform particle size.
（問題点を解決するための手段と作用） 本発明は上記目的を達成するために、ガラス形成物質に
チタン酸塩の基本成分を一定比率で混合し溶融した後、
その溶融物を急冷して得られる非晶質体に熱処理を施す
ことによって、目的にかなったチタン酸塩微粒子の結晶
を析出させるものである。(Means and Actions for Solving Problems) In order to achieve the above-mentioned object, the present invention comprises mixing a glass-forming substance with a basic component of titanate in a fixed ratio and melting the same.
By subjecting an amorphous body obtained by quenching the melt to a heat treatment, crystals of titanate fine particles suitable for the purpose are deposited.
すなわち本発明は、ＡＯ−ＴｉＯ2−Ｂ2Ｏ3系（ＡはＢ
ａ，Ｂｅ，Ｍｇ，Ｃａ，Ｓｒ，Ｒａから選ばれる少なく
とも一種の元素）三角成分図において、ＡＯ５０モル％
−Ｂ2Ｏ3５０モル％の点、ＴｉＯ2５５モル％−ＡＯ４
５モル％の点、ＴｉＯ2４５モル％−ＡＯ５５モル％の
点を結ぶ線で囲まれる組成領域内にある混合物を溶融
し、急速に冷却して非晶質体とする工程と、この非晶質
体に熱処理を施こして結晶化させる工程と、この焼結体
を希酸で処理してチタン酸塩の微粒子を抽出する工程と
を有するチタン酸塩粉末の製造方法である。That is, the present invention, AO-TiO 2 -B 2 O 3 system (A is B
a, Be, Mg, Ca, Sr, Ra, at least one element selected from) Trigonal component diagram, AO 50 mol%
-B 2 O 3 of 50 mol% point, TiO 2 55 mol% -AO4
A step of melting a mixture within a composition region surrounded by a line connecting points of 5 mol% and 45 mol% of TiO 2 -55 mol% of AO and rapidly cooling it to an amorphous body; It is a method for producing a titanate powder, which comprises a step of subjecting a body to a heat treatment for crystallization and a step of treating the sintered body with a dilute acid to extract fine particles of titanate.
ここで組成領域について説明する。上記非晶質体を熱処
理する際に、まずＡＢ2Ｏ4（あるいは、ＡＯ・Ｂ2Ｏ3）
相が析出する。これは示差熱分析Ｘ線回折の結果等から
チタン酸塩に優先して析出する。したがって、チタン酸
塩の原料であるＡＯがＢ2Ｏ3と等量モルより少ない場
合、ＡＯはＢ2Ｏ3と化合してＡＢ2Ｏ4となり易いため、
目的とするチタン酸塩の析出量が減少し、残部はＴｉＯ
2として析出する。ＴｉＯ2は後工程の希酸処理によって
除去することが困難であり、最終生成物であるチタン酸
塩中に混入するので好ましくない。また、Ｂ2Ｏ3量の増
加と共に溶融温度の上昇をまねき経済性が悪化する。以
上の影響を考慮すると第１図面に示したＡＯ，Ｔｉ
Ｏ2，Ｂ2Ｏ3を頂点とする三角成分図におけるａ−ｂ
線、すなわちＡＯ５０モル％−Ｂ2Ｏ3５０モル％の点と
ＴｉＯ2５５モル％−ＡＯ４５モル％の点を結んだ線よ
りもＡＯが過剰な領域であることが好ましい。Here, the composition region will be described. When heat-treating the amorphous body, first, AB 2 O 4 (or AO.B 2 O 3 )
The phase precipitates. This is preferentially deposited over the titanate based on the results of differential thermal analysis X-ray diffraction and the like. Therefore, when AO, which is a raw material of titanate, is less than an equimolar amount of B 2 O 3 , AO is likely to combine with B 2 O 3 to form AB 2 O 4 .
The amount of desired titanate precipitates is reduced, and the balance is TiO 2.
Precipitates as 2 . TiO 2 is difficult to remove by a dilute acid treatment in the subsequent step, and is mixed in the final product titanate, which is not preferable. Further, as the amount of B 2 O 3 increases, the melting temperature rises and the economic efficiency deteriorates. Considering the above influence, AO, Ti shown in the first drawing
Ab in the triangular component diagram with O 2 and B 2 O 3 as vertices
It is preferable that the AO region is in excess of the line, that is, the line connecting the point of AO 50 mol% -B 2 O 3 50 mol% and the point of TiO 2 55 mol% -AO 45 mol%.
一方、ＡＯがＢ2Ｏ3のモル数より大きい場合にはＡＯが
非晶質体中に残存し、ＡＢ2Ｏ4＋ＡＴｉＯ3＋ＡＯが生
成する。ＡＢ2Ｏ4およびＡＯは希酸処理によって除去で
きるが、ＡＯ量の増加に伴って目的とするチタン酸塩の
収率が低下し、希酸処理工程への負担が増大し生産性を
著しく損うため、少なくとも第１図面におけるａ−ｃ
線、すなわちＡＯ５０モル％−Ｂ2Ｏ3５０モル％の点と
ＴｉＯ2４５モル％−ＡＯ５５モル％の点を結んだ線よ
りも、ＴｉＯ2過剰領域であることが好ましい。On the other hand, when AO is larger than the number of moles of B 2 O 3 , AO remains in the amorphous body and AB 2 O 4 + ATiO 3 + AO is produced. AB 2 O 4 and AO can be removed by a dilute acid treatment, but the yield of the target titanate decreases as the amount of AO increases, increasing the burden on the dilute acid treatment process and significantly impairing productivity. Therefore, at least ac in FIG.
The TiO 2 excess region is more preferable than the line, that is, the line connecting the point of AO 50 mol% -B 2 O 3 50 mol% and the point of TiO 2 45 mol% -AO 55 mol%.
最も望ましくは第１図面における上記領域内でａ−ｄ線
で示したＡＯ５０モル％−Ｂ2Ｏ3５０モル％の点とＴｉ
Ｏ2５０モル％−ＡＯ５０モル％の点とを結んだ線上の
組成となる場合である。Most preferably, the point of AO 50 mol% -B 2 O 3 50 mol% indicated by a-d line and Ti in the above region in the first drawing.
This is the case where the composition is on the line connecting the points of 50 mol% O 2 and 50 mol% AO.
また上記組成領域すなわち第１図面の点ａ，ｂ，ｃを結
んだ線で囲まれる範囲内では、析出する粒子の粒径の熱
処理温度依存性がゆるやかであるため、熱処理条件また
は成分組成を変えることによって粒径の制御を容易に行
うことができる。Further, in the composition region, that is, in the range surrounded by the line connecting points a, b, and c in the first drawing, the heat treatment temperature or the component composition is changed because the grain size of the precipitated particles has a mild dependency on the heat treatment temperature. Therefore, the particle size can be easily controlled.
さらに本発明においては非晶質体を熱処理してガラス相
からチタン酸塩の結晶を析出させる。この反応は固相内
での原子拡散に支配されるためゆっくりとした反応とな
り、析出するチタン酸塩を非常に微細な粒子とすること
が可能である。Further, in the present invention, the amorphous body is heat-treated to precipitate titanate crystals from the glass phase. Since this reaction is controlled by atomic diffusion in the solid phase, it becomes a slow reaction, and the deposited titanate can be made into very fine particles.
（実施例） 次に本発明の一実施例についてＢａＴｉＯ3を例として
説明する。The BaTiO 3 for one embodiment (Example) of the present invention will be described below as an example.
本実施例ではガラス形成物質としてＢａＯ・Ｂ2Ｏ3を用
いた。また以下の説明では原料混合物を溶融・冷却して
得られる非晶質体において、ＢａＴｉＯ3：ＢａＯ・Ｂ2
Ｏ3がモル比で６０：４０のものを試料No.１，５０：５
０のものを試料No.２とする。In this example, BaO.B 2 O 3 was used as the glass forming substance. Further, in the following description, in an amorphous body obtained by melting and cooling a raw material mixture, BaTiO 3 : BaO.B 2
Samples No. 1 and 50: 5 with O 3 in a molar ratio of 60:40
Sample No. 2 is 0.
上記組成比となるように、それぞれＢａＣＯ3，Ｔｉ
Ｏ2，Ｈ3ＢＯ3を所定量混合して白金ルツボに収容し、
１３００〜１４００℃に加熱溶融した。この溶融物を白
金ルツボ底部のノズルから流出させ、水冷ローラにより
急速に冷却して薄板状の非晶質体とした。この非晶質体
をボールミルまたは振動ミルによって微粉砕し、所定の
容器に充填して電気炉内に収容し、７５０〜８５０℃で
５Ｈｒ熱処理を行いＢａＴｉＯ3結晶を含む焼結体を生
成させた。この焼結体を微粉砕した後、１０％酢酸溶液
で処理してガラス形成物質を溶解除去し、ＢａＴｉＯ3
微粒子を抽出分離した。BaCO 3 and Ti are used so that the above composition ratios are obtained.
O 2 and H 3 BO 3 are mixed in a predetermined amount and housed in a platinum crucible,
It was heated and melted at 1300 to 1400 ° C. The melt was discharged from the nozzle at the bottom of the platinum crucible and rapidly cooled by a water cooling roller to obtain a thin plate-like amorphous body. The amorphous body was finely pulverized by a ball mill or a vibration mill, filled in a predetermined container, housed in an electric furnace, and heat-treated at 750 to 850 ° C. for 5 hours to produce a sintered body containing BaTiO 3 crystals. . Thereafter the sintered body was finely pulverized, the glass-forming substance dissolved is removed by treatment with 10% acetic acid solution, BaTiO 3
The fine particles were extracted and separated.
得られたＢａＴｉＯ3粉末は、測定の結果、No.１の試料
が平均粒径０．２μｍ，粒度分布（３σ）０．０７、N
o.２の試料が平均粒径０．７μｍ，粒度分布（３σ）
０．１０であった。これに対し参考例として、シュウ酸
塩分解法によって製造されたＢａＴｉＯ3粉末について
同様の測定を行ったところ、平均粒径１．６μｍ，粒度
分布（３σ）０．１５であり、本発明の方法によるＢａ
ＴｉＯ3粉末が粒径のそろった極めて均一なものである
ことがわかった。As for the obtained BaTiO 3 powder, as a result of measurement, No. 1 sample had an average particle size of 0.2 μm, a particle size distribution (3σ) of 0.07, N
o.2 sample has an average particle size of 0.7 μm and particle size distribution (3σ)
It was 0.10. On the other hand, as a reference example, when BaTiO 3 powder produced by the oxalate decomposition method was subjected to the same measurement, the average particle size was 1.6 μm and the particle size distribution (3σ) was 0.15. Ba
It was found that the TiO 3 powder had a very uniform particle size.
このように均一な粒子粉末を用いたセラミックコンデン
サ用素子は均質で焼成後の焼結強度が高く、非常に安定
した長寿命の素子を得ることができる。As described above, the ceramic capacitor element using the uniform particle powder is homogeneous and has a high sintering strength after firing, and a very stable and long-life element can be obtained.
上記実施例では、同一の熱処理条件で組成範囲を変える
ことによって粒径を変化させたが、同一組成で熱処理条
件を変えることによっても容易に粒径を制御することが
できる。またこれらの組合せにより必要に応じて０．０
１〜数μｍの範囲で粒径を制御することが可能である。In the above embodiment, the grain size was changed by changing the composition range under the same heat treatment condition, but the grain size can be easily controlled by changing the heat treatment condition under the same composition. Also, depending on the combination of these, 0.0
It is possible to control the particle size in the range of 1 to several μm.
また上記においては、ＡＴｉＯ3のＡがＢａの例を示し
たが、ＡがＢｅ，Ｍｇ，Ｃａ，Ｓｒ，Ｒａの場合でも同
様の結果が得られた。Further, in the above, an example in which A of ATiO 3 is Ba is shown, but similar results were obtained even when A was Be, Mg, Ca, Sr, Ra.
以上のように本発明によれば、原料組成および熱処理条
件を変えることにより、チタン酸塩粉末の粒径制御が容
易にでき、しかも極めて粒度のそろった均一な粉末が得
られるため、希望する粒径の粉末を比較的大きいものか
ら、非常に微細なものまでコストを上げることなく安定
して供給することができるという効果がある。As described above, according to the present invention, the particle size of the titanate powder can be easily controlled by changing the raw material composition and the heat treatment condition, and moreover, a uniform powder having an extremely uniform particle size can be obtained. There is an effect that a powder having a large diameter can be stably supplied from a relatively large powder to a very fine powder without increasing the cost.
図面は本発明に係るＡＯ−ＴｉＯ2−Ｂ2Ｏ3系の相図
（三角成分図）である。The drawing is a phase diagram (triangular component diagram) of the AO—TiO 2 —B 2 O 3 system according to the present invention.
Claims (1)
ｅ，ＭｇＣａ，Ｓｒ，Ｒａから選ばれる少なくとも一種
の元素）三角成分図において、ＡＯ５０モル％−Ｂ2Ｏ3
５０モル％の点、ＴｉＯ2５５モル％−ＡＯ４５モル％
の点、ＴｉＯ2４５モル％−ＡＯ５５モル％の点を結ぶ
線で囲まれる組成領域内にある混合物を溶融し、急速に
冷却して非晶質体とする工程と、この非晶質体に熱処理
を施こして結晶化させる工程と、この焼結体を希酸で処
理してチタン酸塩の微粒子を抽出する工程とを有するチ
タン酸塩粉末の製造方法。1. AO-TiO 2 -B 2 O 3 system (A is Ba, B
e, MgCa, Sr, Ra, at least one element selected from A) 50% by mole-B 2 O 3
50 mol% point, TiO 2 55 mol% -AO 45 mol%
Point, TiO 2 45 mol% -AO 55 mol%, and the step of melting the mixture in the composition region surrounded by the line connecting the points and rapidly cooling it to an amorphous body. A method for producing a titanate powder, comprising: a step of subjecting to heat treatment to crystallize; and a step of treating the sintered body with a dilute acid to extract fine particles of titanate.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9959687A JPH0624975B2 (en) | 1987-04-22 | 1987-04-22 | Method for producing titanate powder |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9959687A JPH0624975B2 (en) | 1987-04-22 | 1987-04-22 | Method for producing titanate powder |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63265820A JPS63265820A (en) | 1988-11-02 |
| JPH0624975B2 true JPH0624975B2 (en) | 1994-04-06 |
Family
ID=14251478
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP9959687A Expired - Lifetime JPH0624975B2 (en) | 1987-04-22 | 1987-04-22 | Method for producing titanate powder |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0624975B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2005001989A (en) * | 2003-05-21 | 2005-01-06 | Asahi Glass Co Ltd | Method for producing barium titanate fine particles |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106861669B (en) * | 2017-02-27 | 2019-06-04 | 陕西科技大学 | A kind of porous layered structure titanate particle and preparation method thereof |
-
1987
- 1987-04-22 JP JP9959687A patent/JPH0624975B2/en not_active Expired - Lifetime
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2005001989A (en) * | 2003-05-21 | 2005-01-06 | Asahi Glass Co Ltd | Method for producing barium titanate fine particles |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS63265820A (en) | 1988-11-02 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US3195030A (en) | Glass and methods of devitrifying same and making a capacitor therefrom | |
| TWI598290B (en) | Dielectric film, capacitor element and electronic component | |
| US5795537A (en) | Method of producing composite oxide ceramics | |
| Budd et al. | Preparation of strontium titanate ceramics and internal boundary layer capacitors by the Pechini method | |
| WO1996000704A1 (en) | Layered bismuth oxide ferroelectric material | |
| JPH0624975B2 (en) | Method for producing titanate powder | |
| WO1989010800A1 (en) | Process for preparing a barium titanate film | |
| JP3526886B2 (en) | Method for producing composite oxide | |
| JP2010001180A (en) | Barium titanate fine particle, method for producing the same and multilayer capacitor | |
| JPH01219014A (en) | Production of dielectric material powder | |
| Jebli et al. | Effect of the substitution of titanium by niobium on the structural, electric and modulus properties in Ba0. 97La0. 02Ti (1-x) Nb4x/5O3 perovskites | |
| JPH0524863B2 (en) | ||
| JP2885599B2 (en) | Barium titanate-based powder composition and method for producing semiconductor porcelain composition using the same | |
| CN100358835C (en) | Method for high temperature quick synthesizing blender or compound titanate ceramic powder | |
| Gorokhovskii et al. | Synthesis of glass-ceramic materials in the BaO–PbO–B2O3–Al2O3–TiO2 system | |
| JPH035357A (en) | Manufacturing method of dielectric porcelain | |
| JPH0215607A (en) | Ceramic capacitor element | |
| CN114874009B (en) | Near-room temperature relaxation ferroelectric material Ba 4 SrBiTi 3 Nb 7 O 30 And preparation method and application thereof | |
| JPH02145423A (en) | Production of oxide-based superconductor | |
| JPS63315572A (en) | Production of superconductor | |
| JPH0733440A (en) | Production of porcelain composition | |
| JPH026330A (en) | Production of superconducting material and superconducting single crystal | |
| JP2555734B2 (en) | Production method of superconducting material | |
| JPH0826727A (en) | Production of perovskite material | |
| JPH03279216A (en) | Production of perovskite type oxide |