JPH0717436B2 - Method for producing highly insulating and highly alumina-based porcelain composition - Google Patents
Method for producing highly insulating and highly alumina-based porcelain compositionInfo
- Publication number
- JPH0717436B2 JPH0717436B2 JP60272209A JP27220985A JPH0717436B2 JP H0717436 B2 JPH0717436 B2 JP H0717436B2 JP 60272209 A JP60272209 A JP 60272209A JP 27220985 A JP27220985 A JP 27220985A JP H0717436 B2 JPH0717436 B2 JP H0717436B2
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- Prior art keywords
- alumina
- sintered body
- additive
- highly
- porcelain composition
- Prior art date
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Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は高絶縁性を有する高アルミナ質磁器組成物の製
造方法に関するものであり、特に自動車等の内燃機関用
の点火栓として用いられて有効なものである。TECHNICAL FIELD The present invention relates to a method for producing a high-alumina porcelain composition having high insulation properties, and is particularly used as an ignition plug for an internal combustion engine of an automobile or the like. It is valid.
〔従来の技術〕 高アルミナ質磁器は、耐熱性を含めて化学的に極めて安
定であり、機械的強度が優れ、しかも製造法が量産に適
しているため内燃機関用点火栓等の電気絶縁材として広
く実用化されている。[Prior Art] High-alumina porcelain is chemically extremely stable including heat resistance, has excellent mechanical strength, and its manufacturing method is suitable for mass production. Has been widely used as.
一方、近年内燃機関の高性能化のために、点火栓に対す
る要求電圧は益々高まる傾向にあり、点火栓の絶縁碍子
に対する耐電圧特性の向上が要求されてきている。On the other hand, in recent years, the required voltage for the spark plug has been increasing more and more due to higher performance of the internal combustion engine, and it has been required to improve the withstand voltage characteristic of the insulator of the spark plug.
これに対して点火栓に使用される従来のSiO2‐MgO-CaO
系のガラス質フラックスを有する焼結体において、アル
ミナの含有率を高めることによりフラックスを少なくし
て耐電圧を改善したものが知られているが、上記要求に
対してはまだ十分とは言えないのが現状である。In contrast, conventional SiO 2 -MgO-CaO used for spark plugs
It is known that, in a sintered body having a glassy flux of the system, the flux is reduced by increasing the alumina content to improve the withstand voltage, but it cannot be said to be sufficient for the above requirements. is the current situation.
そこで、本発明者等は耐電圧の向上を目的として絶縁破
壊のメカニズムを詳細に検討した結果、絶縁破壊が以下
の2つの原因の奏合により発生することが明らかとなっ
た。Therefore, as a result of detailed study of the mechanism of the dielectric breakdown for the purpose of improving the withstand voltage, the present inventors have found that the dielectric breakdown occurs due to the combination of the following two causes.
すなわち、第1の原因は、第4図の焼結体組織図に示す
如く絶縁破壊が焼結体表面に発生するボイドと呼ばれる
凹部Bや焼結体内部の粒界A中に存在する気孔C等の欠
陥に、高電圧印加により電界が集中し、この集中電界に
よりイオン電流が流れて絶縁破壊に至というものであ
る。That is, the first cause is the voids C called voids where dielectric breakdown occurs on the surface of the sintered body and the pores C existing in the grain boundaries A inside the sintered body as shown in the sintered body structure diagram of FIG. An electric field is concentrated on such defects as a high voltage is applied, and an ion current flows due to this concentrated electric field, leading to dielectric breakdown.
また、第2の原因は、従来用いられていたSiO2‐MgO-Ca
O系の焼結助剤は比較的低融点の粒界Aを形成し、前記
イオン電流により容易に溶融して絶縁破壊に至るという
点である。The second cause is the previously used SiO 2 -MgO-Ca.
The O-based sintering aid forms a grain boundary A having a relatively low melting point, and is easily melted by the ion current to cause dielectric breakdown.
以上の実験観察の結果に基づき、本発明者等は焼結体の
粒界組織の改良に着目して耐絶縁性を高めることを目的
とする。Based on the results of the above-described experimental observations, the present inventors focus on the improvement of the grain boundary structure of the sintered body and aim to enhance the insulation resistance.
Y2O3、ZrO2、La2O3より選ばれた少なくとも一つの添加
物、若しくは、Y2O3、ZrO2、La2O3より選ばれた少なくと
も一つの添加物とアルミナとの固溶体複合酸化物の何れ
かと、 粒径0.5μm以下のアルミナ徹粒粉とから構成された混
合原料粉末を成形、焼成することによって、焼結体とす
るにあたり、 前記添加物としての含有量が、前記焼結体に対して0.5
〜10重量%であることを特徴とする高絶縁性高アルミナ
質磁器組成物の製造方法、或いは、 Y2O3、ZrO2、La2O3より選ばれた少なくとも一つの添加
物、若しくは、Y2O3、ZrO2、La2O3より選ばれた少なくと
も一つの添加物とアルミナとの固溶体複合酸化物の何れ
かと、 SiO2‐CaO-MgO系の焼結助剤と、 粒径0.5μm以下のアルミナ徹粉粒とから構成された混
合原料粉末を成形、焼成することによって焼結体とする
にあたり、 前記添加物としての含有量が、前記焼結体に対して0.5
〜4.5重量%であり、さらに前記焼結助剤としての含有
量が、前記焼結体に対して、0.5〜4.5重量%であること
を特徴とする高絶縁性高アルミナ質磁器組成物の製造方
法を採用するものである。Y 2 O 3 , at least one additive selected from Z r O 2 and La 2 O 3 , or at least one additive selected from Y 2 O 3 , Z r O 2 and La 2 O 3. In the case of forming a sintered body by molding and firing a mixed raw material powder composed of any one of solid solution complex oxides of alumina and alumina powder having a particle size of 0.5 μm or less, the content as the additive is included. The amount is 0.5 with respect to the sintered body.
Method for producing a highly insulating high alumina ceramic composition, which is a 10 wt%, or, Y 2 O 3, Z r O 2, La least one additive from the selected 2 O 3, or, either of Y 2 O 3, Z r O 2, at least one additive was La selected from 2 O 3 solid solution composite oxide of alumina, and sintering aid SiO 2 -CaO-MgO-based When a mixed raw material powder composed of alumina powder having a particle diameter of 0.5 μm or less is molded and fired into a sintered body, the content of the additive is 0.5 with respect to the sintered body.
To 4.5% by weight, and the content as the sintering aid is 0.5 to 4.5% by weight, based on the sintered body, for producing a highly insulating and highly alumina-based porcelain composition. The method is adopted.
上記手段によれば、アルミナの原料粉末の粒径を0.5μ
m以下とすることにより焼結体中の気孔や表面のボイド
をなくすことができるとともに、Y2O3,ZrO2,La2O3より
選ばれた添加物が、焼結体組織中の粒界部分の融点を高
めイオン電流の発生を抑制することが可能となる。According to the above means, the particle size of the raw material powder of alumina is 0.5μ.
When it is m or less, voids in the sintered body and voids on the surface can be eliminated, and the additive selected from Y 2 O 3 , ZrO 2 and La 2 O 3 is a grain in the sintered body structure. It is possible to increase the melting point of the boundary portion and suppress the generation of ion current.
従って、本発明によれば、高アルミナ質磁器組成物の耐
絶縁性を大巾に向上させることができ、高電圧の印加さ
れる部品の絶縁体として有効に使用できる。Therefore, according to the present invention, the insulation resistance of the high-alumina porcelain composition can be greatly improved, and it can be effectively used as an insulator for parts to which a high voltage is applied.
以下本発明を実施例に基づいて詳細に説明する。 Hereinafter, the present invention will be described in detail based on examples.
純度99.9%以上で粒径0.25μmに調整されたAl2O3から
なる主成分を93wt%,SiO2‐MgO-CaO系の焼結助剤粉末
(組成比がSiO250%,MgO10%,CaO40%)2wt%、本発明
の添加物としてY2O3粉末5wt%を混合した原料粉末に適
宜の量の水を加えてアルミナボールを用いて湿式で混合
粉砕を行った。粉砕後造粒のためポリビニルアルコール
(PVA)の10wt%水溶液を原料粉末に対し10wt%添加し
再混合した後乾燥を行った。次にこの乾燥造粒原料をさ
らに粗粉砕し、60メッシュの目の粗さのふるいにかける
ことにより、粒径のそろった原料粉末を作製した。93 wt% of the main component consisting of Al 2 O 3 with a purity of 99.9% or more and a particle size of 0.25 μm, SiO 2 -MgO-CaO system sintering aid powder (composition ratio SiO 2 50%, MgO 10%, CaO 40%) 2 wt% and Y 2 O 3 powder 5 wt% as an additive of the present invention were mixed with an appropriate amount of water, and wet mixing and grinding were performed using alumina balls. For pulverization after granulation, 10 wt% aqueous solution of polyvinyl alcohol (PVA) was added to the raw material powder in an amount of 10 wt%, re-mixed, and then dried. Next, this dry granulated raw material was further coarsely pulverized and passed through a sieve with a mesh size of 60 mesh to prepare raw material powder having a uniform particle size.
この原料粉末を金型に入れ面圧500kg/cm2で加圧して直
径30mmの円盤状に成形した後、耐熱アルミナ製容器中に
粉径0.1〜0.5mmのAl2O3の粉末を分散させた上へ、成形
体を載置し、電気炉中で100℃/hrの昇温率で1650℃まで
昇温、1650℃で2時間保持、その後100℃/hrで降温する
ことによりかさ比重3.72g/cm3、相対密度(かさ比重の
真比重に占める割合)94%の焼結体が得られた(組織図
を第1図に示す)。This raw material powder is put into a mold and pressed at a surface pressure of 500 kg / cm 2 to form a disk shape with a diameter of 30 mm, and then a powder of Al 2 O 3 having a powder diameter of 0.1 to 0.5 mm is dispersed in a heat-resistant alumina container. The molded product is placed on top of it, heated up to 1650 ° C at a heating rate of 100 ° C / hr in an electric furnace, kept at 1650 ° C for 2 hours, and then cooled at 100 ° C / hr to obtain a bulk specific gravity of 3.72. A sintered body having a g / cm 3 and a relative density (ratio of the bulk specific gravity to the true specific gravity) of 94% was obtained (structure chart is shown in FIG. 1).
次にこの焼結体をダイヤモンド砥粒等を用いた研磨盤を
用いて厚さ1.0±0.05mmの研磨加工を施し、第2図に示
す耐電圧測定装置にて耐電圧を実測した。すなわち焼結
体10の一面に電極11を導電ペースト等により貼り付けシ
リコンオイル12中に浸漬する。そして焼結体10の電極11
の対向する面に、先端をニードル状に尖らせたプローブ
13を固定し、この状態で電極11とプローブ13との間に定
電圧電源14から発振器15とコイル16により発生させた高
電圧を、高電圧プローブ17とオシロスコープ18でモニタ
ーしながら30cycle/秒の周波数で毎秒0.2kvづつ電圧を
上昇させ試料の破壊した電圧をその焼結体試料の耐電圧
とした。Next, this sintered body was polished to a thickness of 1.0 ± 0.05 mm using a polishing machine using diamond abrasive grains and the withstand voltage was measured with a withstand voltage measuring device shown in FIG. That is, the electrode 11 is attached to one surface of the sintered body 10 by a conductive paste or the like and immersed in the silicon oil 12. And the electrode 11 of the sintered body 10
Probes with needle-like tips on opposite surfaces of the
13 is fixed, and in this state, the high voltage generated by the oscillator 15 and the coil 16 from the constant voltage power supply 14 between the electrode 11 and the probe 13 is monitored at the high voltage probe 17 and the oscilloscope 18 for 30 cycles / sec. The breakdown voltage of the sample was defined as the withstand voltage of the sintered sample by increasing the voltage by 0.2 kv per second at the frequency.
第1表は主成分のアルミナ,焼結助剤としてのSiO2‐Ca
O-MgO,Y2O3,ZrO2,La2O3の添加物の含有量を変化させた
原料粉末から作製した焼結体サンプルの耐電圧を示す実
験結果である。Table 1 shows the main component of alumina and SiO 2 -Ca as a sintering aid.
5 is an experimental result showing the withstand voltage of a sintered body sample prepared from raw material powders in which the contents of additives of O-MgO, Y 2 O 3 , ZrO 2 , and La 2 O 3 were changed.
従来品は平均粒径2.5μmのアルミナ95wt%とSiO2‐MgO
-CaO系焼結助剤(SiO250%,MgO10%,CaO40%)5wt%と
からなる原料粉末から上記と同様の方法により作製した
もので、本発明のものは最高で40%を超える耐電圧の向
上が達成されている(サンプルNo.2,6)。 The conventional product is 95 wt% alumina with an average particle size of 2.5 μm and SiO 2 -MgO
-CaO-based sintering aid (SiO 2 50%, MgO 10%, CaO 40%) 5 wt% was prepared by the same method as above. The present invention has a maximum resistance of more than 40%. Improvement of voltage has been achieved (Sample Nos. 2 and 6).
なお、ここでアルミナの粒系が0.5μmを超えると相対
密度が小さくなり耐電圧が向上しないことが確かめられ
た。またSiO2‐MgO-CaO系の焼結助剤は5wt%以上では、
焼結性が悪く緻密な焼結体が得られず、5wt%ではやや
過ぎることが表より明らかとなり、4.5wt%以下程度が
好ましい。なお、このSiO2‐MgO-CaO系の焼結助剤はな
くてもかまわない。またY2O3,ZrO2,La2O3の添加物の添
加量は0.5wt%以下では耐電圧の向上効果がなく、SiO2
‐MgO-CaO系の焼結助剤を加えたものでは、5wt%を超え
ると耐電圧が低下しはじめる。また、SiO2‐MgO-CaO系
の焼結助剤を加えない場合は、これらの添加物は10wt%
程度まで加えても耐電圧は低下しない。Here, it was confirmed that when the grain size of alumina exceeds 0.5 μm, the relative density decreases and the withstand voltage does not improve. Moreover, when the SiO 2 -MgO-CaO system sintering aid is 5 wt% or more,
The sinterability was poor and a dense sintered body could not be obtained, and it became clear from the table that it was a little too high at 5 wt%, and it is preferably about 4.5 wt% or less. It should be noted that this SiO 2 —MgO—CaO based sintering aid may be omitted. The Y 2 O 3, ZrO 2, the addition amount of the additive of La 2 O 3 has no effect of improving the withstand voltage is below 0.5 wt%, SiO 2
-With the addition of the MgO-CaO system sintering aid, the withstand voltage begins to decrease when it exceeds 5 wt%. If SiO 2 -MgO-CaO system sintering additive is not added, these additives are 10wt%.
The withstand voltage does not decrease even if added to a certain degree.
Y2O3,ZrO2,La2O3等の添加物は、それら自身の粉末とし
て原料粉末中に添加してもよいが、いったんこれらをAl
2O3との固溶体混合酸化物として原料粉末中に添加して
もよく、こうすることによって添加物が非常に少量であ
る場合は分散性よく前記添加物を混合させることができ
る。Additives such as Y 2 O 3 , ZrO 2 and La 2 O 3 may be added to the raw material powder as their own powder, but once these are added to Al
It may be added to the raw material powder as a solid solution mixed oxide with 2 O 3, and by doing so, the above additives can be mixed with good dispersibility when the amount of the additives is very small.
次に本発明の高絶縁性高アルミナ質磁器組成物が好適に
用いられる内燃機関用点火栓の構造を第3図に基づいて
説明する。Next, the structure of an ignition plug for an internal combustion engine, in which the highly insulating and highly alumina-based ceramic composition of the present invention is preferably used, will be described with reference to FIG.
点火栓20はエンジンのシリンダ内に置かれ高電圧を発生
するコイルからの印加電圧によって中心電極21と接地電
極22の間に放電を行わせる事によってガソリンと空気の
混合気を着火させる働きをもつ。ハウジング23は接地電
極22と同じ電位であるためハウジング23と中心電極21間
の放電が生じないように絶縁碍子24が置かれる。燃料が
通常空燃比よりも小さい場合や他の着火しにくい燃料で
は中心電極21と接地電極22の間に通常より高電圧を印加
しないと良好な着火を生じさせることができない。しか
るに電圧がある大きさ以上になると絶縁碍子24の一部が
破壊されピンホールが生ずる。この状態になると接地電
極22と中心電極21間に生ずべき放電がハウジング23と中
心電極21間で生じてしまい失火を起こす。The spark plug 20 is placed in the cylinder of the engine and has a function of igniting a mixture of gasoline and air by causing discharge between the center electrode 21 and the ground electrode 22 by an applied voltage from a coil that generates a high voltage. . Since the housing 23 has the same potential as the ground electrode 22, the insulator 24 is placed so that the discharge between the housing 23 and the center electrode 21 does not occur. If the fuel is smaller than the normal air-fuel ratio or other fuel that is difficult to ignite, good ignition cannot be generated unless a higher voltage than usual is applied between the center electrode 21 and the ground electrode 22. However, when the voltage exceeds a certain level, a part of the insulator 24 is destroyed and a pinhole is generated. In this state, a discharge that should occur between the ground electrode 22 and the center electrode 21 is generated between the housing 23 and the center electrode 21, causing misfire.
従来の絶縁碍子材であるAl2O3にSiO2‐MgO-CaO系の焼結
助剤を添加した材料はすでに説明したように第4図の如
く表面にボイドと呼ばれる凹部Bや、粒界に気孔Cが多
く存在する。これに高電圧が印加されると、これらの欠
陥に電位が集中しその電位勾配によって粒界A、に存在
する動きやすいイオンによる電流が流れ、この電流によ
る発熱がさらに可動イオン数を増加させる事によりさら
に電流が流れて発熱するというサイクルを繰り返す。こ
の発熱量がアルミナの分解エネルギーよりも過大となっ
た時に破壊が生ずる。As described above, the material obtained by adding a SiO 2 -MgO-CaO-based sintering aid to Al 2 O 3 which is a conventional insulator material, as described above, has a concave portion B called a void and a grain boundary as shown in FIG. There are many pores C in the. When a high voltage is applied to this, a potential concentrates on these defects, and the potential gradient causes a current to flow due to the easily moving ions existing in the grain boundary A, and the heat generated by this current further increases the number of mobile ions. Then, a cycle in which an electric current further flows to generate heat is repeated. When this calorific value becomes larger than the decomposition energy of alumina, destruction occurs.
本発明者等は破壊が最初粒界にあるガラス成分から始ま
る事を見出し、この結果より粒界を高融点材料とし、か
つ緻密にAl2O3を焼結させる添加剤を検討した結果、本
発明に至ったものであり、アルミナの粒径を小さくする
ことと、Y2O3,ZrO2,La2O3等の添加物を加えることで達
成されたものである。The present inventors found that the fracture first started from the glass component at the grain boundary, and as a result of examining the additive which makes the grain boundary a high melting point material and sinters Al 2 O 3 densely as a result, The present invention has been achieved by reducing the particle size of alumina and adding additives such as Y 2 O 3 , ZrO 2 , and La 2 O 3 .
第1図は本発明の製造方法により製造された高絶縁性高
アルミナ質磁器組成物の組織を示す模式図、第2図は耐
電圧測定装置を示す系統図、第3図は本発明の製造方法
による高絶縁性高アルミナ質磁器組成物が好適に用いら
れる点火栓の構造を示す部分断面図、第4図は従来の高
アルミナ質磁器組成物の組織を示す模式図である。 A……粒界。FIG. 1 is a schematic diagram showing the structure of a highly insulating and highly alumina-based porcelain composition produced by the production method of the present invention, FIG. 2 is a system diagram showing a withstand voltage measuring device, and FIG. 3 is the production of the present invention. FIG. 4 is a partial cross-sectional view showing the structure of an ignition plug in which a highly insulating and highly alumina-based ceramic composition is preferably used, and FIG. 4 is a schematic diagram showing the structure of a conventional highly-alumina-based ceramic composition. A ... Grain boundary.
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 昭59−156961(JP,A) 特開 昭56−96777(JP,A) 特開 昭60−21854(JP,A) 特開 昭48−91112(JP,A) ─────────────────────────────────────────────────── ─── Continuation of front page (56) Reference JP-A-59-156961 (JP, A) JP-A-56-96777 (JP, A) JP-A-60-21854 (JP, A) JP-A-48- 91112 (JP, A)
Claims (2)
も一つの添加物、若しくは、Y2O3、ZrO2、La2O3より選ば
れた少なくとも一つの添加物とアルミナとの固溶体複合
酸化物の何れかと、 粒径0.5μm以下のアルミナ徹粒粉とから構成された混
合原料粉末を成形、焼成することによって、焼結体とす
るにあたり、 前記添加物としての含有量が、前記焼結体に対して0.5
〜10重量%であることを特徴とする高絶縁性高アルミナ
質磁器組成物の製造方法。1. A Y 2 O 3, Z r O 2, La 2 O 3 , at least one additive was more chosen, or selected from Y 2 O 3, Z r O 2, La 2 O 3 At least one additive and one of solid solution composite oxides of alumina, and a mixed raw material powder composed of alumina grain-penetrating powder having a particle size of 0.5 μm or less is molded and fired to obtain a sintered body, The content as the additive is 0.5 with respect to the sintered body.
-10% by weight, a method for producing a highly insulating and highly alumina-based porcelain composition.
も一つの添加物、若しくは、Y2O3、ZrO2、La2O3より選ば
れた少なくとも一つの添加物とアルミナとの固溶体複合
酸化物の何れかと、 SiO2‐CaO-MgO系の焼結助剤と、 粒径0.5μm以下のアルミナ徹粉粒とから構成された混
合原料粉末を成形、焼成することによって焼結体とする
にあたり、 前記添加物としての含有量が、前記焼結体に対して0.5
〜4.5重量%であり、さらに前記焼結助剤としての含有
量が、前記焼結体に対して、0.5〜4.5重量%であること
を特徴とする高絶縁性高アルミナ質磁器組成物の製造方
法。Wherein Y 2 O 3, Z r O 2, La 2 O 3 , at least one additive was more chosen, or selected from Y 2 O 3, Z r O 2, La 2 O 3 A mixed raw material powder composed of at least one additive and a solid solution composite oxide of alumina, a SiO 2 -CaO-MgO-based sintering aid, and an alumina powder having a grain size of 0.5 μm or less. In forming a sintered body by molding and firing, the content as the additive is 0.5 with respect to the sintered body.
To 4.5% by weight, and the content as the sintering aid is 0.5 to 4.5% by weight, based on the sintered body, for producing a highly insulating and highly alumina-based porcelain composition. Method.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP60272209A JPH0717436B2 (en) | 1985-12-03 | 1985-12-03 | Method for producing highly insulating and highly alumina-based porcelain composition |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP60272209A JPH0717436B2 (en) | 1985-12-03 | 1985-12-03 | Method for producing highly insulating and highly alumina-based porcelain composition |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS62132765A JPS62132765A (en) | 1987-06-16 |
JPH0717436B2 true JPH0717436B2 (en) | 1995-03-01 |
Family
ID=17510626
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP60272209A Expired - Lifetime JPH0717436B2 (en) | 1985-12-03 | 1985-12-03 | Method for producing highly insulating and highly alumina-based porcelain composition |
Country Status (1)
Country | Link |
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JP (1) | JPH0717436B2 (en) |
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EP1104062A1 (en) | 1999-11-29 | 2001-05-30 | Ngk Spark Plug Co., Ltd | Insulator for spark plug and spark plug comprising same |
JP2007510617A (en) * | 2003-11-12 | 2007-04-26 | フェデラル−モーグル コーポレイション | Ceramic with advanced high temperature electrical properties for use as a spark plug insulator |
WO2009119098A1 (en) | 2008-03-27 | 2009-10-01 | 日本特殊陶業株式会社 | Spark plug and process for producing the spark plug |
JP4508439B2 (en) * | 2001-02-16 | 2010-07-21 | 日本特殊陶業株式会社 | Spark plug |
US8749125B2 (en) | 2009-07-03 | 2014-06-10 | Ngk Spark Plug Co., Ltd. | Spark plug |
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JP3339989B2 (en) * | 1995-05-31 | 2002-10-28 | 京セラ株式会社 | Low dielectric loss material |
JP2999395B2 (en) * | 1995-07-06 | 2000-01-17 | 品川白煉瓦株式会社 | Basic refractories |
JP4748693B2 (en) * | 1998-11-24 | 2011-08-17 | 日本特殊陶業株式会社 | High voltage endurance alumina-based sintered body and method for producing the same |
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JP5017298B2 (en) | 2009-03-11 | 2012-09-05 | 株式会社日本自動車部品総合研究所 | Alumina sintered body, manufacturing method thereof, and spark plug using the same |
JP5478404B2 (en) * | 2010-07-23 | 2014-04-23 | 日本カーバイド工業株式会社 | Manufacturing method of alumina ceramic |
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Family Cites Families (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5430002B2 (en) * | 1971-12-10 | 1979-09-27 | ||
JPS5696777A (en) * | 1979-12-29 | 1981-08-05 | Matsushita Electric Ind Co Ltd | Alumina ceramic composition for electronic parts |
JPS59156961A (en) * | 1983-02-24 | 1984-09-06 | 松下電器産業株式会社 | Manufacture of alumina sintered substrate |
JPS6021854A (en) * | 1983-07-15 | 1985-02-04 | 松下電器産業株式会社 | Manufacture of alumina sintered substrate |
-
1985
- 1985-12-03 JP JP60272209A patent/JPH0717436B2/en not_active Expired - Lifetime
Cited By (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
EP1104062A1 (en) | 1999-11-29 | 2001-05-30 | Ngk Spark Plug Co., Ltd | Insulator for spark plug and spark plug comprising same |
JP4508439B2 (en) * | 2001-02-16 | 2010-07-21 | 日本特殊陶業株式会社 | Spark plug |
JP2007510617A (en) * | 2003-11-12 | 2007-04-26 | フェデラル−モーグル コーポレイション | Ceramic with advanced high temperature electrical properties for use as a spark plug insulator |
WO2009119098A1 (en) | 2008-03-27 | 2009-10-01 | 日本特殊陶業株式会社 | Spark plug and process for producing the spark plug |
US8390183B2 (en) | 2008-03-27 | 2013-03-05 | Ngk Spark Plug Co., Ltd. | Spark plug and method for manufacturing spark plug |
US8749125B2 (en) | 2009-07-03 | 2014-06-10 | Ngk Spark Plug Co., Ltd. | Spark plug |
Also Published As
Publication number | Publication date |
---|---|
JPS62132765A (en) | 1987-06-16 |
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