JPH02221153A - Dielectric porcelain composition - Google Patents
Dielectric porcelain compositionInfo
- Publication number
- JPH02221153A JPH02221153A JP1042857A JP4285789A JPH02221153A JP H02221153 A JPH02221153 A JP H02221153A JP 1042857 A JP1042857 A JP 1042857A JP 4285789 A JP4285789 A JP 4285789A JP H02221153 A JPH02221153 A JP H02221153A
- Authority
- JP
- Japan
- Prior art keywords
- weight
- porcelain composition
- pts
- parts
- dielectric
- 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
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- 239000000203 mixture Substances 0.000 title claims abstract description 27
- 229910052573 porcelain Inorganic materials 0.000 title abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 239000000919 ceramic Substances 0.000 claims description 17
- 229910000272 alkali metal oxide Inorganic materials 0.000 claims description 5
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 abstract description 14
- UPWOEMHINGJHOB-UHFFFAOYSA-N oxo(oxocobaltiooxy)cobalt Chemical compound O=[Co]O[Co]=O UPWOEMHINGJHOB-UHFFFAOYSA-N 0.000 abstract description 14
- ZKATWMILCYLAPD-UHFFFAOYSA-N niobium pentoxide Chemical compound O=[Nb](=O)O[Nb](=O)=O ZKATWMILCYLAPD-UHFFFAOYSA-N 0.000 abstract description 12
- 229910052681 coesite Inorganic materials 0.000 abstract description 7
- 229910052906 cristobalite Inorganic materials 0.000 abstract description 7
- 239000000377 silicon dioxide Substances 0.000 abstract description 7
- 235000012239 silicon dioxide Nutrition 0.000 abstract description 7
- 229910052682 stishovite Inorganic materials 0.000 abstract description 7
- 229910052905 tridymite Inorganic materials 0.000 abstract description 7
- PLDDOISOJJCEMH-UHFFFAOYSA-N neodymium oxide Inorganic materials [O-2].[O-2].[O-2].[Nd+3].[Nd+3] PLDDOISOJJCEMH-UHFFFAOYSA-N 0.000 abstract description 4
- 239000003513 alkali Substances 0.000 abstract 2
- 229910019714 Nb2O3 Inorganic materials 0.000 abstract 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 abstract 1
- 239000000470 constituent Substances 0.000 abstract 1
- 229910044991 metal oxide Inorganic materials 0.000 abstract 1
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 239000003990 capacitor Substances 0.000 description 7
- 230000007423 decrease Effects 0.000 description 6
- MCMNRKCIXSYSNV-UHFFFAOYSA-N Zirconium dioxide Chemical compound O=[Zr]=O MCMNRKCIXSYSNV-UHFFFAOYSA-N 0.000 description 4
- 229910002113 barium titanate Inorganic materials 0.000 description 4
- 229910052783 alkali metal Inorganic materials 0.000 description 3
- 150000001340 alkali metals Chemical class 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000000843 powder Substances 0.000 description 3
- 229910003781 PbTiO3 Inorganic materials 0.000 description 2
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N Titan oxide Chemical compound O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 description 2
- WMWLMWRWZQELOS-UHFFFAOYSA-N bismuth(iii) oxide Chemical compound O=[Bi]O[Bi]=O WMWLMWRWZQELOS-UHFFFAOYSA-N 0.000 description 2
- 238000001704 evaporation Methods 0.000 description 2
- NUJOXMJBOLGQSY-UHFFFAOYSA-N manganese dioxide Chemical compound O=[Mn]=O NUJOXMJBOLGQSY-UHFFFAOYSA-N 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 238000005245 sintering Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 229910016063 BaPb Inorganic materials 0.000 description 1
- BQCADISMDOOEFD-UHFFFAOYSA-N Silver Chemical compound [Ag] BQCADISMDOOEFD-UHFFFAOYSA-N 0.000 description 1
- 229910010252 TiO3 Inorganic materials 0.000 description 1
- XTXRWKRVRITETP-UHFFFAOYSA-N Vinyl acetate Chemical compound CC(=O)OC=C XTXRWKRVRITETP-UHFFFAOYSA-N 0.000 description 1
- AYJRCSIUFZENHW-UHFFFAOYSA-L barium carbonate Inorganic materials [Ba+2].[O-]C([O-])=O AYJRCSIUFZENHW-UHFFFAOYSA-L 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 150000001622 bismuth compounds Chemical class 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000007606 doctor blade method Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000008020 evaporation Effects 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 239000003112 inhibitor Substances 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 229910052761 rare earth metal Inorganic materials 0.000 description 1
- 229910052709 silver Inorganic materials 0.000 description 1
- 239000004332 silver Substances 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
Landscapes
- Compositions Of Oxide Ceramics (AREA)
- Inorganic Insulating Materials (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は、高誘電率を有し、かつ広い温度範囲にわたっ
て容量温度特性が平坦である誘電体磁器組成物に間する
ものである。DETAILED DESCRIPTION OF THE INVENTION (Industrial Application Field) The present invention relates to a dielectric ceramic composition that has a high dielectric constant and flat capacitance-temperature characteristics over a wide temperature range.
（在米技術）
従来、高誘電率を有し、かつその容量温度特性が平坦な
誘電体磁器組成物としては、ＢａＴｉＯ３を主成分とし
、副成分としてＢｉ ２０３−Ｔｉ ０２等のビスマス
化合物と希土類元素酸化物を添加したものあるいは副成
分としてＭｇＯ，ＳｉＯ２を添加したものが知られてい
る。(U.S.-based technology) Conventionally, dielectric ceramic compositions with a high dielectric constant and flat capacitance-temperature characteristics include BaTiO3 as the main component, and bismuth compounds such as Bi 203-Ti 02 and rare earth elements as subcomponents. Those to which elemental oxides are added or those to which MgO and SiO2 are added as subcomponents are known.
しかしながら、前者は焼結時にＢｉ２Ｏ３が蒸発するこ
とによって得られる磁器が反ること、その電気特性にバ
ラツキが大きいなどの問題があった。また、高周波にお
ける誘電損失が大きく、積層コンデンサとして用いる場
合には、ＢｉｚＯ３とＰｄが反応するので内部電極とし
て高価なｐｔを使用せざるをえなかった。However, the former has problems such as warping of the resulting porcelain due to evaporation of Bi2O3 during sintering and large variations in its electrical properties. Furthermore, the dielectric loss at high frequencies is large, and when used as a multilayer capacitor, BizO3 and Pd react, making it necessary to use expensive PT as internal electrodes.
また、後者の組成を含めて、これらの組成系では誘電率
が高くなると、その容量温度変化率を平坦にすると誘電
率が低下するという傾向があり、誘電率増大による小型
、大容量化には限界があった。In addition, in these composition systems, including the latter composition, when the dielectric constant increases, flattening the capacitance temperature change rate tends to cause the dielectric constant to decrease. There was a limit.
そこでこのような問題点を解決するために、副成分とし
てＮｂ２Ｏ５，Ｃｏ２Ｏ３，Ｎｄ２Ｏ３，ＳｉＯ２を添
加することを特徴とする特開昭５９−１５２２８５号が
提案されている。In order to solve these problems, JP-A-59-152285 has been proposed, which is characterized in that Nb2O5, Co2O3, Nd2O3, and SiO2 are added as subcomponents.
（従来技術の問題点）
しかしながら、上述したＢａＴｉＯ３を主成分とした誘
電体磁器組成物においては、この誘電体磁器組成物を用
いて作製したコンデンサの容量温度特性が＋２５℃を基
準とした時、−５５℃〜→１２５℃の温度範囲では容量
変化率が１１５％であるが、＋１２５℃以上の温度にな
ると容量変化率が著しく大きくなるという問題点があっ
た。(Problems with the Prior Art) However, in the above-mentioned dielectric ceramic composition mainly composed of BaTiO3, when the capacitance-temperature characteristic of a capacitor manufactured using this dielectric ceramic composition is set at +25°C, The rate of change in capacity is 115% in the temperature range from -55°C to 125°C, but there is a problem in that the rate of change in capacity becomes significantly large at temperatures above +125°C.
そこで本発明は、上述した問題点を解決しようとしたも
のであり、高誘電率を有し、かつ容量温度特性が＋２５
℃を基準とした時、−５５℃〜＋１５０℃の温度範囲で
温度変化率が１１５％以内の誘電体磁器組成物を提供す
ることを目的とするものである。Therefore, the present invention is an attempt to solve the above-mentioned problems, and has a high dielectric constant and a capacitance temperature characteristic of +25
The object of the present invention is to provide a dielectric ceramic composition having a temperature change rate of within 115% in the temperature range of -55°C to +150°C.
（問題点を解決するための手段）
本発明の誘電性磁器組成物は、不純物としてのアルカリ
金属酸化物の含有量が全体で０．０４重量％以下であっ
て、（Ｂａ１−ｘＰｂｘ）ｙＴｉＯ３（ｘ”０．０１〜
０．０４゜ｙ＝Ｑ、 ９８〜１．０２）の式で表された
誘電体磁器組成物を主成分とし、この主成分１００重量
部に対して副成分としてＮｂ２Ｏ５を１．０〜２．５重
量部、Ｃｏ２Ｏ３を０．１〜０．８重量部およびＮｄ２
Ｏ３，ＳｉＯ２のうち少なくとも一方を０．０５〜１．
０重量部含有したことを特徴とする。(Means for Solving the Problems) The dielectric ceramic composition of the present invention has a total content of alkali metal oxides as impurities of 0.04% by weight or less, and (Ba1-xPbx)yTiO3( x”0.01~
The main component is a dielectric ceramic composition expressed by the formula: 0.04°y=Q, 98-1.02), and 1.0-2.0 parts by weight of Nb2O5 as a subcomponent based on 100 parts by weight of the main component. 5 parts by weight, 0.1 to 0.8 parts by weight of Co2O3 and Nd2
At least one of O3 and SiO2 is 0.05 to 1.
It is characterized by containing 0 parts by weight.
すなわち、本発明においてはＢａＴｉＯ３にＰｂＴｉＯ
３を固溶させることにより、ＢａＴｉＯ３のキュリー点
を高温側にシフトさせ、その結果、容量の温度特性が＝
５５℃〜＋１５０℃の範囲にわたって１１５％以内の誘
電体磁器組成物を得ることができる。That is, in the present invention, PbTiO is added to BaTiO3.
By dissolving 3 in solid solution, the Curie point of BaTiO3 is shifted to the high temperature side, and as a result, the temperature characteristic of the capacity becomes =
Dielectric ceramic compositions within 115% can be obtained over the range of 55°C to +150°C.
本発明において、ＰｂＴｉＯ３の固溶比率（ＢａＰｂ）
／Ｔｉモル比およびｔ＋ｂ２ｏ５等の酸化物の添加量を
上記した範囲に限定した理由は以下の通りである。In the present invention, the solid solution ratio of PbTiO3 (BaPb)
The reason why the /Ti molar ratio and the amount of oxide added such as t+b2o5 were limited to the above ranges is as follows.
（Ｂａ１−ｘＰｂｘ） 、ＴｉＯ３においてＸが０．０
１未満であれば、１５０℃での容量温度変化率が一１５
％以下に大きくはずれ、逆にＸが０．０４を越えるとキ
ュリー点での容量温度変化率が＋１５％以上にはずれる
ためである。また、ｙが１．０２を越えると焼結性が悪
くなり、緻密な焼結体が得られず、逆に０．９８未満に
なると過剰のＴｉＯ２が２次相を作りやすく、焼結性も
悪くなるためである。(Ba1-xPbx), X is 0.0 in TiO3
If it is less than 1, the capacitance temperature change rate at 150℃ is 115
% or less, and conversely, if X exceeds 0.04, the capacitance temperature change rate at the Curie point will deviate by more than +15%. In addition, if y exceeds 1.02, sinterability deteriorates and a dense sintered body cannot be obtained, and conversely, if y exceeds 0.98, excess TiO2 tends to form a secondary phase, resulting in poor sinterability. Because it gets worse.
また、本発明において、副成分として添加する酸化物の
添加量を上記のように限定したのは次の通りである。Further, in the present invention, the amount of the oxide added as a subcomponent is limited as described above.
Ｎｂ２Ｏ５は１．０重量部未満では焼結性が悪化し、ま
た容量温度変化率も大きくなり、ＥＩＡに規定する×７
Ｒ特性をも満足しなくなるのであり、また２、５重量部
を越えると誘電率が２３００以下と低下するためである
。If Nb2O5 is less than 1.0 parts by weight, sinterability will deteriorate and the capacity temperature change rate will increase, so
This is because the R characteristic is no longer satisfied, and if the amount exceeds 2.5 parts by weight, the dielectric constant decreases to 2300 or less.
Ｃｏ２Ｏ３は０．１重量部未満では容量温度変化率を小
さくする効果に乏しく、０．８重量部を越えると誘電率
の低下あるいは容量温度特性の悪化を招くからである。This is because if Co2O3 is less than 0.1 part by weight, it is not effective in reducing the capacitance temperature change rate, and if it exceeds 0.8 part by weight, it causes a decrease in dielectric constant or deterioration of capacitance temperature characteristics.
Ｎｄ２Ｏ３の含有量を０．０５〜１．０重量部とするの
は、その量が０６０５重量部未満では焼結性を向上させ
る効果に乏しく、また１、０重量部を越えると共に添加
するＣｏ２Ｏ３と関連してＣｏ２Ｏ３量が少ない場合に
は容量温度変化率が著しく大きくなってしまい、逆にＣ
ｏ２Ｏ３量が多い場合には誘電率が２３００以下と著し
く低下するためである。The reason why the content of Nd2O3 is set to 0.05 to 1.0 parts by weight is that if the amount is less than 0.605 parts by weight, the effect of improving sinterability is poor, and if it exceeds 1.0 parts by weight, the added Co2O3 Relatedly, when the amount of Co2O3 is small, the rate of change in capacitance with temperature increases significantly, and conversely
This is because when the amount of o2O3 is large, the dielectric constant decreases significantly to 2300 or less.
ＳｉＯ２は０．０５重量部未満では焼結性を向上させる
効果に乏しく、１．０重量部を越えると誘電率の低下を
招くことから０．０５〜１．０重量部の範囲とするもの
である。If SiO2 is less than 0.05 parts by weight, it will have little effect on improving sinterability, and if it exceeds 1.0 parts by weight, the dielectric constant will decrease, so the content should be in the range of 0.05 to 1.0 parts by weight. be.
なお、本発明において、その組成中に微量のＭｎＯ２，
Ｆｅ２Ｏ３などの還元防止剤を添加することは得られる
誘電体磁器組成物の特性を何ら損なうものではない。In addition, in the present invention, a trace amount of MnO2,
Addition of a reduction inhibitor such as Fe2O3 does not impair the properties of the resulting dielectric ceramic composition.
不純物としてのアルカリ金属酸化物の含有量を誘電体磁
器組成物全体の０．０４重量％以下としたのは、０．０
４重量％を越えると誘電率が２３００以下と低下するた
めである。The reason why the content of alkali metal oxide as an impurity is 0.04% by weight or less of the whole dielectric ceramic composition is 0.0
This is because if the content exceeds 4% by weight, the dielectric constant decreases to 2300 or less.
（発明の効果）
上述したように、本発明の誘電体磁器組成物は、容量の
温度特性が、２５℃を基準とした時、−５５℃〜＋１５
０℃の範囲において１１５％以内のものが得られるため
、今までの誘電体磁器組成物では容量の温度変化率が大
きいため使用が不可能であった自動車のエンジンルーム
内、あるいは熱を発生する電源回路等の高温下での使用
が可能とすることができる。(Effects of the Invention) As described above, the dielectric ceramic composition of the present invention has a capacitance temperature characteristic of -55°C to +15°C when 25°C is the standard.
Since it can be obtained within 115% in the 0°C range, it can be used in the engine room of a car or where heat is generated, which was impossible with conventional dielectric ceramic compositions due to the large temperature change rate of capacitance. It can be used under high temperature conditions such as power supply circuits.
以下に、本発明の誘電体磁器組成物の実施例を詳細に説
明する。Examples of the dielectric ceramic composition of the present invention will be described in detail below.
（実施例）
原料としてＢａＣ０３（アルカリ金属含有量０．０１重
量％以下）、ｐｂｏ（アルカリ金属は未検出）ｔＴｆ０
２（アルカリ金属は未検出）を用い、第１表に示すよう
な置換比率のＰｂＴｉＯ３となるように秤量し、ジルコ
ニアポールを用いたボールミルにて１６時時間式混合を
行った。次に、得られた混合物の水分を蒸発させた後、
１０００〜１１００℃で２時間保持して仮焼し、（Ｂａ
、 Ｐｂ）Ｔｉ０３の仮焼粉末を得た。(Example) Raw materials BaC03 (alkali metal content 0.01% by weight or less), pbo (alkali metal not detected) tTf0
2 (no alkali metal detected) was weighed so that PbTiO3 had a substitution ratio as shown in Table 1, and mixed for 16 hours in a ball mill using a zirconia pole. Then, after evaporating the water in the resulting mixture,
Calcined by holding at 1000-1100°C for 2 hours, (Ba
, Pb) A calcined powder of Ti03 was obtained.
次に、得られた仮焼粉末にＮｂ２Ｏ５，Ｎｄ２Ｏ３，Ｃ
ｏ２Ｏ３゜ＳｉＯ２を第１表に示す組成割合になるよう
に秤量し、再びジルコニアボールを用いたボールミルに
て１６時時間式混合を行って粉砕した後、水分を蒸発。Next, Nb2O5, Nd2O3, C
o2O3°SiO2 was weighed so as to have the composition ratio shown in Table 1, and mixed again for 16 hours in a ball mill using zirconia balls to be pulverized, and then water was evaporated.
乾燥して粉末を得た。It was dried to obtain a powder.
次に、得られた粉末を酢酸ビニル系バインダーにて混練
して造粒した後、２ｔｏｎ／Ｃｍ２の圧力でプレス成形
し、直径１０ｍｎ＋、厚さｉｍｍの円板状の成形体を得
た。そして、この成形体を第１表に示すような温度で２
時間焼成し、誘電体磁器を得た。Next, the obtained powder was kneaded with a vinyl acetate binder and granulated, and then press-molded at a pressure of 2 tons/Cm2 to obtain a disk-shaped compact with a diameter of 10 mm+ and a thickness of imm. Then, this molded body was heated for 2 hours at a temperature as shown in Table 1.
After firing for a period of time, dielectric porcelain was obtained.
次に、得られた誘電体磁器の両生表面に銀電極を焼付け
て、コンデンサを作製し、このコンデンサを試料として
温度２５℃２周波数ＩＫＨｚの条件で、誘電率（ε）、
誘電損失（ｔａｎδ）を測定した。Next, silver electrodes were baked on the amphibian surface of the obtained dielectric porcelain to prepare a capacitor. Using this capacitor as a sample, the dielectric constant (ε),
Dielectric loss (tan δ) was measured.
また、２５℃での容量を基準とした時の容量変化率ｆ：
Ｗ定し、第１表には、−５５℃、＋１５０℃での容量変
化率、および−５５℃〜÷１５０℃で絶対値として容量
変化率が最大である値（１△Ｃ／（：２５１ｍａｘ）を
示した。Also, the rate of change in capacity f based on the capacity at 25°C:
Table 1 shows the capacitance change rate at -55℃ and +150℃, and the value at which the capacitance change rate is maximum as an absolute value from -55℃ to ÷150℃ (1△C/(:251max )showed that.
なお、第１表中の×ζ印の試料番号は本発明の範囲外で
ある。Note that the sample numbers marked with ×ζ in Table 1 are outside the scope of the present invention.
また、試料番号２２はアルカリ金属酸化物含有量の比較
例として、原料であるＢａ ＣＯ３に０．０６重量％の
アルカリ金属酸化物を含有するものを用いた。In addition, as a comparative example of the alkali metal oxide content, sample number 22 contained 0.06% by weight of an alkali metal oxide in the raw material Ba CO3.
さらに、第１表に示したものはすべて単板コンデンサに
おいて得られた結果であるが、同じ組成物をドクターブ
レード法にてシート化し、積層された積層コンデンサに
おいても単板コンデンサと同等の特性が得られた。Furthermore, although all of the results shown in Table 1 were obtained for single-plate capacitors, the same composition was made into sheets using the doctor blade method, and a multilayer capacitor that was laminated had the same characteristics as a single-plate capacitor. Obtained.
（以下、余白）
第１表から明らかなように、本発明の誘電体磁器組成物
を用いた誘電体磁器は、−５５℃〜＋１５０℃の広い温
度範囲にわたって容量の温度変化率が±１５％以内と平
坦である。(Hereinafter, blank space) As is clear from Table 1, the dielectric ceramic using the dielectric ceramic composition of the present invention has a temperature change rate of ±15% in capacity over a wide temperature range of -55°C to +150°C. Within and flat.
また、平坦な容量の温度変化率であるにもかかわらず、
その誘電率が２３００以上と高い値を示していることが
わかる。Also, despite the flat capacitance temperature change rate,
It can be seen that the dielectric constant shows a high value of 2300 or more.
さらに、１２５０℃以下の低い焼成温度で焼結すること
も可能である。Furthermore, it is also possible to sinter at a low sintering temperature of 1250° C. or lower.
Claims (1)
０．０４重量％以下であって、（Ｂａ＿１＿−＿ｘＰｂ
＿ｘ）＿ｙＴｉＯ＿３（ｘ＝０．０１〜０．０４，ｙ＝
０．９８〜１．０２）の式で表された誘電体磁器組成物
を主成分とし、この主成分１００重量部に対して副成分
としてＮｂ＿２Ｏ＿５を１．０〜２．５重量部、Ｃｏ＿
２Ｏ＿３を０．１〜０．８重量部およびＮｄ＿２Ｏ＿３
，ＳｉＯ＿２のうち少なくとも一方を０．０５〜１．０
重量部含有したことを特徴とする誘電体磁器組成物。The total content of alkali metal oxides as impurities is 0.04% by weight or less, and (Ba_1_-_xPb
_x)_yTiO_3(x=0.01~0.04, y=
The main component is a dielectric ceramic composition expressed by the formula of 0.98 to 1.02), and 1.0 to 2.5 parts by weight of Nb_2O_5 and 1.0 to 2.5 parts by weight of Co_
0.1 to 0.8 parts by weight of 2O_3 and Nd_2O_3
, at least one of SiO_2 is 0.05 to 1.0
A dielectric ceramic composition characterized in that it contains part by weight.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1042857A JPH02221153A (en) | 1989-02-22 | 1989-02-22 | Dielectric porcelain composition |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1042857A JPH02221153A (en) | 1989-02-22 | 1989-02-22 | Dielectric porcelain composition |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH02221153A true JPH02221153A (en) | 1990-09-04 |
Family
ID=12647696
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1042857A Pending JPH02221153A (en) | 1989-02-22 | 1989-02-22 | Dielectric porcelain composition |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH02221153A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US7736433B2 (en) | 2000-12-15 | 2010-06-15 | Canon Kabushiki Kaisha | BaTiO3—PbTiO3 series single crystal and method of manufacturing the same, piezoelectric type actuator and liquid discharge head using such piezoelectric type actuator |
-
1989
- 1989-02-22 JP JP1042857A patent/JPH02221153A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US7736433B2 (en) | 2000-12-15 | 2010-06-15 | Canon Kabushiki Kaisha | BaTiO3—PbTiO3 series single crystal and method of manufacturing the same, piezoelectric type actuator and liquid discharge head using such piezoelectric type actuator |
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