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JPS6212671A - 繊維強化セラミツクス - Google Patents

繊維強化セラミツクス

Info

Publication number
JPS6212671A
JPS6212671A JP60150248A JP15024885A JPS6212671A JP S6212671 A JPS6212671 A JP S6212671A JP 60150248 A JP60150248 A JP 60150248A JP 15024885 A JP15024885 A JP 15024885A JP S6212671 A JPS6212671 A JP S6212671A
Authority
JP
Japan
Prior art keywords
fibers
whiskers
fiber
sic
ceramic
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.)
Granted
Application number
JP60150248A
Other languages
English (en)
Other versions
JPH0569789B2 (ja
Inventor
広志 坂本
忠彦 三吉
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Hitachi Ltd
Original Assignee
Hitachi Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Hitachi Ltd filed Critical Hitachi Ltd
Priority to JP60150248A priority Critical patent/JPS6212671A/ja
Priority to EP86305288A priority patent/EP0209320B1/en
Priority to DE8686305288T priority patent/DE3682129D1/de
Publication of JPS6212671A publication Critical patent/JPS6212671A/ja
Priority to US07/453,925 priority patent/US5057465A/en
Priority to US07/453,928 priority patent/US5055430A/en
Publication of JPH0569789B2 publication Critical patent/JPH0569789B2/ja
Granted legal-status Critical Current

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    • C04B35/71—Ceramic products containing macroscopic reinforcing agents
    • C04B35/78—Ceramic products containing macroscopic reinforcing agents containing non-metallic materials
    • C04B35/80—Fibres, filaments, whiskers, platelets, or the like
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Abstract

(57)【要約】本公報は電子出願前の出願データであるた
め要約のデータは記録されません。

Description

【発明の詳細な説明】 〔発明の利用分野〕 本発明は構造部品などに使用するに適した繊維強化セラ
ミックスに関する。
〔発明の背景〕 セラミックスの持つ耐熱性、耐酸化性、高強度。
耐摩耗性などの特徴を生かして、金属に替って構造部品
や機械部品などへ適用しようとする試みが活発におこな
われている。特にセラミックスのうちでも、高温強度が
大きいこと、耐酸化性にすぐれていることから、Ｓｉ３
Ｎ、、ＳＬ、、ｘＡＱ、Ｏ，Ｎ、−。
（０〈ｚ≦４）（ルーカス社商品名サイアロン。
以下単にサイアロンと云う）、ＳｉＣなとのケイ素系セ
ラミックスが注目されている。しかしながら、これらの
セラミックスにはもろいという欠点があり、これが実用
化のための最大の障害となっている。
セラミックスのもろさを克服して破壊しん性を向上させ
る手段の一つとしては、セラミックス中゛に高強度の繊
維を分散させて、繊維強化する手段も提案されている。
この方法は例えば、ジエー・ジエー・ブレンナン、ケイ
・エム・プリュウ；ジャーナル・オン・マテリアルス・
サイエンス（Ｊ。
Ｊ　、Ｂｒｅｎｎａｎ、　Ｋ、Ｍ、Ｐｒｅｗｏ、　Ｊ　
、Ｍａｔｅｒ、Ｓｃｉ、　１７　＋２３７１−２３８３
　（１９８２）　］に見られるように、ガラスを母材と
した時には特に有効であって、Ｋ１゜で評価した破壊じ
ん性が１５　Ｍ　Ｎ　／　ｍ　”’　を越える材料も知
られている。しかしながら、このようなガラスを母材と
した材料は耐熱性が一般にセラミックスよりも劣り、高
温で長時間荷重を加えると変形してしまう欠点があった
。
一方、セラミックスを繊維強化した例も知られているが
１例えば機端：サンシャインジャーナル１９８２　Ｖｏ
ｌ、３．Ｎａ４．Ｐ、２０〜２８に見られるように、そ
の破壊しん性値は充分には大きくならず、機械的な信頼
性の点で問題があった。
さらに、ビー・ニー・ベンダー（Ｂ　、　Ａ　、　Ｂ　
ｅｎｄｅｒ）らはプロシーデインゲ　オン　ｓｔｈ　　
アンニュアル　コンフエレンス　オン　コンポジイッテ
スアンド　アトバンド　セラミック　マテリアルス（Ｐ
ｒｏｃ、ｏｆ　８ｔｈ　Ａｒ＋ｎｕａｌ　Ｃｏｎｆｅｒ
ｅｎｃｅ　ｏｎＣｏｍｐｏｓｉｔａｇ　ａｎｄ　Ａｄｖ
ａｎｕｄ　Ｃｅｒａｍｉｃ　Ｍａｔｅｒｉａｌｓ）Ｐ、
５１３〜５２９．１月１５−１８　（１９８４）　　に
おいて、ＳｉＣ繊維で強化したＺｒＯ□やムライト、コ
ージライトについて報告している。これらのセラミック
ス中には比較的破壊靭性値の大きいものもあるが、強度
は８０〜１８０ＭＰａ程度とセラミックスとしては小さ
い、また、セラミックスが酸化物であるために、高温で
は軟化による強度低下が考えられる。なお、同じ報告で
は３０％のＢＮを含むムライトとＳｉＣ繊維との界面に
炭素から成る膜状の反応相が存在することが述べられて
いるが、この反応相は靭性向上には寄与しておらず、セ
ラミックスの靭性は小さい。
さらに、同じ報告にはＳｉＣ繊維で強化したガラスにつ
いての報告もあるが、これらの試料においても強度は小
さいか、大きくても高温では軟化して強度低下する欠点
があり、構造用材料として要望されている高温高強度、
かつ、高靭性のセラミックスは得られていない。
〔発明の目的〕
本発明の目的は、耐熱性及び機械的強度を必要とされる
構造部品材料として適した、高温で高強度かつ高靭性の
繊維強化セラミックスを提供することを目的としている
。
〔発明の概要〕
本発明は、セラミックス母材中にセラミックス繊維又は
ウィスカを分散した複合セラミックスにおいて、上記セ
ラミックス繊維又はウィスカの表面に、上記セラミック
ス母材との直接の接触を阻止するための被覆膜を設ける
ことにより、その破壊靭性値が大幅に向上することに基
づいている。
また、セラミックス母材及び繊維又はウィスカるのが良
いことを見出した。
本発明者達の検討の結果、 ■例えば１０００℃を越えるような高温で長時間安定に
使用でき、かつ、高強度、高靭性の要求を満足するため
には、セラミックス母材中ヘセラミックス繊維やウィス
カを分散した材料が最もすぐれており、具体的材料とし
ては５ｉ（ＪＩＳＩ３Ｎ４又はサイアロンが良いこと、 ■従来の繊維強化セラミックスにおいては、母材のセラ
ミックスの焼結時に、母材と繊維やウィスカが接触、反
応するために、破壊しん性が充分大きくならないことが
判明した。
すなわち、母材セラミックスの焼結時に、母材と繊維や
ウィスカが直接接触すると、間者が反応して繊維やウィ
スカの強度が低下するばかりでなく、一般に焼結時に繊
維やウィスカは焼成収縮しないため、母材の焼成収縮の
邪魔になったり、母材と繊維やウィスカの界面に大きな
歪が発生し、その歪が原因で母材中にクラックが発生し
たりする。これらの結果、繊維強化セラミックスの強度
や破壊しん性が充分大きくならない、また、一般に繊維
強化セラミックスにおいて特に大きな破壊しん性の向上
をもたらす要因は破壊時の繊維やウィスカの引抜けによ
るエネルギー消費であるが、母材と繊維やウィスカが密
着しているとこの引抜は効果が働きにくく、むしろ母材
と繊維やウィスカが一体となって破壊するために、破壊
じん性が充分大きなものとはならない。
本発明の繊維強化セラミックスにおいては、繊維やウィ
スカの表面に母材との直接の接触をさけるための被覆膜
を設けて、上述のような母材セラミックスの焼結時に繊
維やウィスカが劣化したり。
焼成収縮による歪が母材と繊維やウィスカとの界面で発
生することを防止している。また、母材と繊維やウィス
カとが直接接触していないため、破断時には確実にこれ
らの界面ではがれ、繊維やウィスカが引抜かれる。この
結果・、本発明の繊維強化やセラミックスでは大きな破
壊じん性がもたらされる。
繊維やウィスカの表面に設ける被覆膜は母材セラミック
スと焼結時に強固に密着しすぎないことが必要であり、
これに適した材料は母材によって異る。母材として、１
５００℃を越えるような特に高温での使用が期待される
ＳｉＣを用いた場合は。
被覆膜としてはＢＮを主体としたものが良い。また、１
２００℃程度の温度ではあるが、特に高強度が要求され
る用途にＳｉ３Ｎ、やサイアロン（Ｓ　ｉ　、、Ａ　Ｑ
　、０．Ｎ、、、　Ｑ　（Ｚ≦４）を母材として用いた
場合、被覆膜としてはＢ、ＢＮ又はＣを主体とするもの
が良い、なお、被覆膜としてＣを用いた時には繊維やウ
ィスカが適度の力で引抜けるため引抜けの効果が大きく
、特に破壊靭性が向上しやすい。一方、被覆膜としてＢ
、ＢＮを用いた時にはセラミックスの空気中での熱処理
に対し特に安定である。
これらの被覆膜はＣＶＤ、蒸着、スパッタなどの気相法
や溶液、樹脂などの塗布２分解のような湿式法によって
、繊維やウィスカ上に形成できる。
また、その厚さとしては０．１〜５μｍであることが望
ましい。被覆膜が薄すぎると、母材との反応阻止、歪の
除去や引抜けの効果が低下し、一方、厚すぎると母材と
繊維やウィスカとの界面か弱すぎて、繊維強化セラミッ
クスとしての強度が充分得られない。
母材中に分散する繊維やウィスカとしては、母材セラミ
ックスの焼結温度でも安定であることが不可欠である。
具体的には、母材がＳｉＣを主成分とする時はＳｉＣを
主体とするもの、母材がＳＬ３Ｎ、やサイアロン主成分
とする時はＳｉＣ又は５Ｌ３Ｎ、を主体とするものを繊
維やウィスカとして用いることができる。
これらのうちでも、とくにＣまたはＳｉＣｗｔ維上にＳ
ｉＣをＣＶＤした繊維は高温まで高強度であること、破
壊時に母材と繊維との界面から引抜けるばかりでなく、
繊維内のＣ繊維やＳｉＣ繊維とＳｉＣ膜との界面からも
引抜けるため、靭性向上に特に有効である。
有機珪素化合物から作製した長繊維上へＳｉＣやＳｉ３
Ｎ４をＣＶＤして得られる繊維を用いると、その強化セ
ラミックスの靭性が向上すると共に、耐熱性、耐酸化性
に優れた特性が得られるのでこれらは特に好ましい。
また、用いる繊維やウィスカとしてはアスペクト比（長
軸と短軸の比）が２０以上のものが引抜けによるエネル
ギー消費に有効であり、また、その存在量としては繊維
やウィスカが母材中にランダムに分散している場合には
１５〜５０ｖｏΩ％の範囲が、更にまた繊維やウィスカ
の長軸方向が１次元、２次元又は３次元的に並んで配向
している時は５〜３５ｖｏｌ２％の範囲が良く、これら
は特に高強度、高靭性のセラミックスを与える。
上記含有量よりも少なすぎると添加の効果がなく、逆に
多すぎると靭性が向上しないばかりでなく、強度が低下
するという欠点を生じる。
ターボチャージャロータやガスタービンロータのような
特に高信頼性を要求される構造部品にセラミックスを用
いる場合、その破壊靭性は応力拡大係数に１ｏで１０　
Ｍ　Ｎ　／　ｍ　””以上であることが望ましい。この
場合、セラミックスの表面や内部に１００μｍ程度の欠
陥が存在したとしても、その強度は約３０ｋｇ／ｍｓ”
以上となり、上記ロータの強度設計の許容値を満足する
ため、使用時の破損などの問題はおこらない、また、セ
ラミックスの欠陥として１００μｍ以上の欠陥が存在し
たとしても、それらの欠陥はＸ線透過法、超音波探傷法
、目視法などの手段により、製造ラインで非破壊的に容
易に発見でき、除去することがある。このように、に１
ｅが１０　Ｍ　Ｎ　／　ｍ””以上のセラミックスを用
いれば、セラミックスに不可避の内部欠陥や表面傷など
による破損事故を防止することができ、セラミックス構
造部品の信頼性を大幅に高めることができる。さらに、
に１゜が大きいセラミックスではセラミックス中に存在
するクラックが成長するのに大きなエネルギーが必要と
なり。
結果としてクラックの成長が阻止されるため゛、セラミ
ックスの特性が長期にわたって安定で、信頼性の高いも
のとなる。Ｋ、ｃが１０　Ｍ　Ｎ　／　ｍ　””以上の
セラミックスのクラック成長のためのエネルギーは、３
〜６ＭＮ／ｍ””程度のに１゜を待った従来のセラミッ
クスの３〜１０倍と大きく、それだけ、構造用部品とし
て高強度、高信頼性のものとなる。さらに、本発明の特
に望ましい範囲のセラミックスのに１ｏは１５　Ｍ　Ｎ
　／　ｍ　””以上に達する。このセラミックスを破壊
するに必要なエネルギーは従来のセラミックスの６〜２
５倍と、著しく大きなものとなり、特に高強度、高信頼
性となる。
〔発明の実施例〕
実施例１ 粒径０．５〜２μｍのＳｉ３Ｎ４．　Ａ　ｆｌ　Ｎ＊　
Ｓ　ｉ　Ｏ。
及びＡＱ、○、を所定量加え、ＳＬ、−、Ａ　Ｑ　ｘｏ
ｘＮａ−ｘ（ｚ　：　０．０．５．４）　　の組成を持
つ混合粉末を調製した。次にこれに１粒径１〜２μｍの
Ｙ２Ｏ３を０．５〜５ｖｏ　９％と５％ポリビニールア
ルコール水溶液を適量添加した後、ふるいを用いて整粒
した。
一方、繊維としては直径３５μｍのＣ繊維上にＳｉＣを
ＣＶＤ　Ｌ、た直径１４０μｍの繊維（ＳｉＣ繊維と称
す）上にさらにＣ膜をＣＶＤ　Ｌ、たものを用いた。
上記ＳｉＣ繊維を長さ５０ｍｍに切断し、等間隔に一方
向に並べて配列した。厚さ方向の間隔は原料粉末とこの
ＳｉＣ繊維を交互に型へ入れ、この時の粉末の量を変え
て制御した。その後、金型プレスで４００　ｋｇ／　Ｃ
ａＩ２　の圧力で５０ｍｍ角Ｘ６ｍｍｔに成形し、これ
を黒鉛ダイスに入れ、窒素ガス１０気圧中３００　ｋｇ
／　ｃ＋ａ”　の圧力下で１７５０〜１９００℃でホッ
トプレス焼結した。この焼結体より、ＳｉＣ繊維の配列
方向と平行に切断して、３ｍｍＸ４ｍａ＋Ｘ５０ｍｍの
試験片を採取した。これを研摩した後、中心部に幅３０
μｍ、深さ０．５＋＋＋ｍの切込みを試験片と直角に入
れ、シングル　エツジ　ノッチド　ビーム（Ｓ　ｉｎｇ
ｌａ　　Ｅ　ｄｇｅ　Ｎ　ｏｔｃｈｅｄ　Ｂ　ａｅａ＋
）法により破壊靭性値に１゜を求めた。
第１図及び第２図はＳｉＣ繊維添加［２０ｖｏＱ％のＳ
ｉ３Ｎ４の破断面の組織を示す顕微鏡写真である。ｓｉ
ｃ繊維１がＳｉ３Ｎ４母材５から引抜けている様子を示
している。
また、第３図はＳｉＣ繊維添加量とに１．、の関係、第
４図はＣ膜厚とに１゜の関係である。
なお、第３図の試料のうち５ｉＣ４ｌ維添加量が３５ｖ
ｏＱ％以下の試料の４点曲げ強度は全て５０〜１００　
ｋｇ／　＋１１１１１”であったが、添加量５０ｖｏＱ
％の試料の強度は２５　ｋｇ　／　ｍ＋ｓ”　と小さか
った。
同様な方法により、５ｉＣＪｌ雑の配列方向を交互に９
０°変え、繊維を２次元に配向した試料を作製した。こ
の試料においても、第３図と同様にＳｉＣ繊維添加量５
〜３５ｖｏＱ％の範囲では大きなに１ｏと曲げ強度が得
られた。
また、上記Ｃ繊維上へＳｉＣをＣＶＤＬ、さらにこの上
にＢＮをスパッタリングして得たＳｉＣ繊維を用いて得
られた繊維強化セラミックスにおいても、ＳｉＣ繊維添
加量５〜３５ｖｏｆ１％の範囲で大きなに１ｏと５０−
１００ｋｇ／＋＋＋＋ａ”の曲げ強度）が得られた。第
５図はこの試料のＢＮ膜厚とに□。
との関係を示したものである。
また、直径約１０μｍのＳｉＣ長繊維上へＳｉＣをＣＶ
ＤＬ、た直径約５０μｍのＳｉＣ［維（但し表面にはＢ
Ｎ膜１μｍ形成）を前記繊維の代りに用いたものも１０
　Ｍ　Ｎ　／　ｍ””以上のに、。を示した。また、空
気中１０００℃、　ｔｏｏｏｈ熱処理しても特性は全く
変化しなかった。更に、繊維表面ＢＮ膜の代りにＢ膜を
形成したものも同様の結果が得られた。
実施例２ 実施例１で用いたＳｉＣ繊維と同様に表面にＣ膜（厚さ
１μｍ）をＣＶＤ法により形成したＳｉＣ繊維（直径７
０μｍ）を３次元的に織り重ねたものを、ポリカルボシ
ランの１０％キシレン溶液に浸漬し、引上げてアルゴン
ガス中１２００℃で熱分解してＳｉＣを形成する工程を
くり返す方法により、ＳｉＣ母相中に３次元的にＳｉＣ
繊維が配列した繊維強化セラミックスを形成した。この
試料のに、。とＳｉＣ繊維添加量の関係を第６図に示す
。
実施例３ 市販の直径０．５〜１μｍのＳｉＣウィスカをふつ化水
素につけてＳ　ｉ　Ｏ，を除去し、洗浄した後、水に良
く分散し、沈降法により、長さくアスペクト比）の異る
ウィスカ毎に分取した１次に、このウィスカの集合体に
Ｂ、Ｈ，及びＮＨ３の混合ガスを流しながら加熱し、ウ
ィスカの表面に０．１〜０．２μｍ厚のＢＮ膜を設けた
。
次に、平均粒径０．５μｍのα−８ｉＣ粉末に０．５〜
３ｖｏＱ％のＡ１２Ｎ及び上述のＳｉＣウィスカを加え
、混合、成形の後、　２０００℃でホットプレス焼結し
た。得られた焼結体のウィスカ添加量とに１（ｌの関係
を第７図に、ウィスカのアスペクト比とに１ｏの関係を
第８図に示す。
なお、第７図の試料のうちウィスカ添加量が５０ｖｏＱ
％以下の試料の曲げ強度は４０〜８０ｋｇ／ｍｍ”であ
ったが、添加量７５ｖｏＱ％の試料では強度は１５ｋｇ
／ｍｓ”　に低下した。
実施例４ 平均粒径２μｍのＳｉ３Ｎ４粉末に粒径０．５〜１μｍ
のＡＱ、Ｏｓ　２ｖｏＱ％１粒径２〜５μｍのＹ、０．
５ｖｏｎ％及び実施例３に用いたＳｉＣウィスカを加え
、混合、成形の後３Ｎ２中１８００℃でホットプレス焼
結した。得られた焼結体のウィスカ添加量とに□０の関
係を第９図、ウィスカのアスペクト比とに、。の関係を
第１０図に示す。
なお、第９図の試料のうち、ウィスカ添加量が５０ｖｏ
Ｑ％以下の試料の曲げ強度は５０〜８０ｋｇ／ａｍ”で
あったが、添加量７５ｖｏＱ％の試料では強度は１５〜
２０ｋｇ／＋ｍ”　に低下した。
実施例５ 実施例１と同様に母材にサイアロン （Ｓ　ｉｓ、ｓＡ　Ｑａ、ｓＯｏ、ｓＮｓ、ｓ）を用い
、これに市販のＳＬ３Ｎ４ウイスカ（直径０．３〜１　
ｐ　ｍ）　、アスペクト比３０〜１００）の表面に真空
中でＣ膜を約０．２　μｍコーティングしたものを加え
３Ｎ２中１８００℃でホットプレス焼結した。得られた
焼結体のウィスカ添加量とに１゜及び曲げ強度の関係を
第１１図に示す。
このように、本発明の強靭性セラミックスは破壊エネル
ギーが大きいため、従来のセラミックスに較べて特に機
械衝撃や熱衝撃に強い特徴を持つ。
したがって、ガスタービン部品（ノズル、ロータ）、タ
ーボチャージャロータ、ベアリング、軸受。
切削工具（バイト、ノコギリなど）及び開閉時に衝撃の
加わる配管用の弁などにも使用できる。
第１２図は耐摩耗性や耐機械衝撃性の要求される原子力
配管の弁用ディスクヘッドに本発明の強靭性セラミック
スを用いた例を示す。
〔発明の効果〕
以上説明して来たように、本発明によれば破壊靭性値が
ＩＯＭＮ／ｍ”’以上と大きく、かつ。
高強度のセラミックスが得られ、これを用いた構造部品
の信頼性を大幅に向上することができる。
【図面の簡単な説明】
第１図及び第２図は本発明の実施例で得られた試料断面
の粒子構造を示す顕微鏡写真、第３図〜第１１図は本発
明の実施例で得られた試料の特性を示す特性曲線図、第
１２図は本発明のセラミックスを用いて得られる原子力
配管の横断面図である。

Claims (1)

  1. 【特許請求の範囲】 １、セラミックス母材中に繊維または／およびウィスカ
    が分散含有された繊維強化セラミックスにおいて、上記
    セラミックス母材がＳｉＣ、Ｓｉ＿３Ｎ＿４またはＳｉ
    ＿６＿−＿ｚＡｌ＿ｚＯ＿ｚＮ＿３＿−＿ｚ（但し０＜
    ｚ≦４）を主成分とし、前記繊維およびウィスカがＳｉ
    Ｃ、Ｓｉ＿３Ｎ＿４およびＳｉ＿６＿−＿ｚＡｌ＿ｚＯ
    ＿ｚＮ＿３＿−＿ｚ（但し０＜ｚ≦４）から選ばれる少
    なくとも１種であり、上記繊維、ウィスカはその表面に
    Ｃ、ＢまたはＢＮの被覆膜を有することを特徴とする繊
    維強化セラミックス。 ２、特許請求の範囲第１項において、前記被覆膜の厚さ
    が０．１〜５μｍであることを特徴とする繊維強化セラ
    ミックス。 ３、特許請求の範囲第１項または第２項において、前記
    繊維またはウィスカのアスペクト比が２０以上であるこ
    とを特徴とする繊維強化セラミックス。 ４、特許請求の範囲第１項〜第３項のいずれかにおいて
    、前記繊維または／およびウィスカがセラミックス母材
    中にランダムに配向していることを特徴とする繊維強化
    セラミックス。 ５、特許請求の範囲第４項において、前記繊維または／
    およびウィスカの含有量が１５〜５０ｖｏｌ％であるこ
    とを特徴とする繊維強化セラミックス。 ６、特許請求の範囲第１項〜第３項において前記繊維ま
    たは／およびウィスカの繊維長軸方向が１次元、２次元
    または３次元に配向して含有されていることを特徴とす
    る繊維強化セラミックス。 ７、特許請求の範囲第６項において、前記繊維または／
    およびウィスカの含量量が５〜３５ｖｏｌ％であること
    を特徴とする繊維強化セラミックス。 ８、特許請求の範囲第１項〜第７項のいずれかにおいて
    、前記セラミックス母材がＳｉ＿３Ｎ＿４またはＳｉ＿
    ６＿−＿ｚＡｌ＿ｚＯ＿ｚＮ＿３＿−＿ｚ（但し０＜ｚ
    ≦４）を主成分とするとき、前記繊維または／およびウ
    ィスカはＳｉＣ、Ｓｉ＿３Ｎ＿４であることを特徴とす
    る繊維強化セラミックス。 ９、特許請求の範囲第１項〜第７項のいずれかにおいて
    、前記セラミックス母材がＳｉＣを主成分とするとき、
    前記繊維または／およびウィスカがＢＮ被覆膜を有する
    ＳｉＣであることを特徴とする繊維強化セラミックス。 １０、特許請求の範囲第１項〜第９項のいずれかにおい
    て、前記繊維または／およびウィスカがＣ繊維を心とし
    たＳｉＣ繊維であることを特徴とする繊維強化セラミッ
    クス。
JP60150248A 1985-07-10 1985-07-10 繊維強化セラミツクス Granted JPS6212671A (ja)

Priority Applications (5)

Application Number Priority Date Filing Date Title
JP60150248A JPS6212671A (ja) 1985-07-10 1985-07-10 繊維強化セラミツクス
EP86305288A EP0209320B1 (en) 1985-07-10 1986-07-09 Fiber-reinforced ceramics
DE8686305288T DE3682129D1 (de) 1985-07-10 1986-07-09 Faserverstaerkte keramikwerkstoffe.
US07/453,925 US5057465A (en) 1985-07-10 1989-12-20 Ceramic matrices reinforced with SiC, Si3 N4 or SiAlON fibers having a coating of C, B or BN containing SiC or Si3 N4
US07/453,928 US5055430A (en) 1985-07-10 1989-12-20 Carbon coated silicon carbide, silicon nitride or sialon fibers in a ceramic matrix

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
JP60150248A JPS6212671A (ja) 1985-07-10 1985-07-10 繊維強化セラミツクス

Publications (2)

Publication Number Publication Date
JPS6212671A true JPS6212671A (ja) 1987-01-21
JPH0569789B2 JPH0569789B2 (ja) 1993-10-01

Family

ID=15492794

Family Applications (1)

Application Number Title Priority Date Filing Date
JP60150248A Granted JPS6212671A (ja) 1985-07-10 1985-07-10 繊維強化セラミツクス

Country Status (4)

Country Link
US (2) US5057465A (ja)
EP (1) EP0209320B1 (ja)
JP (1) JPS6212671A (ja)
DE (1) DE3682129D1 (ja)

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JPS63277563A (ja) * 1987-05-08 1988-11-15 Ishikawajima Harima Heavy Ind Co Ltd 繊維強化炭化けい素セラミックスおよびその製造方法
JPS63281408A (ja) * 1987-05-13 1988-11-17 Hitachi Ltd 薄膜磁気ヘツド用スライダおよびその製法
JPS6437470A (en) * 1987-07-31 1989-02-08 Mazda Motor Sliding member made of ceramic
JPS6461355A (en) * 1987-09-01 1989-03-08 Riken Kk Titanium carbide/silicon carbide whisker/zirconia based complex sintered material and production thereof
JPS6476972A (en) * 1987-09-18 1989-03-23 Toshiba Corp Fiber reinforced silicon nitride-based ceramic and production thereof
JPH01188475A (ja) * 1988-01-19 1989-07-27 Toshiba Ceramics Co Ltd ＢＮ被覆ＳｉＣウイスカー及びその製造方法
JPH01188476A (ja) * 1988-01-19 1989-07-27 Toshiba Ceramics Co Ltd アルミナ被覆ＳｉＣウイスカー及びＳｉＣウイスカー強化セラミツクス複合材料
JPH0226876A (ja) * 1988-07-14 1990-01-29 Agency Of Ind Science & Technol 粒子分散強化した繊維強化セラミックス複合材及びその製造方法
JPH02116682A (ja) * 1988-10-25 1990-05-01 Ube Ind Ltd β型窒化珪素ウイスカー複合材料及びその製法
JPH02204373A (ja) * 1989-01-31 1990-08-14 Tonen Corp 繊維強化セラミックス複合材料
US5091344A (en) * 1988-01-30 1992-02-25 Ibiden Corporation Fiber reinforced ceramics of calcium phosphate series compounds and method of producing the same
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Cited By (17)

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Publication number Priority date Publication date Assignee Title
JPS6345190A (ja) * 1986-06-19 1988-02-26 サンドビック　アクティエボラーグ 被覆されたウィスカ−強化セラミックス焼結体
JPH0551558B2 (ja) * 1986-06-19 1993-08-02 Sandvik Ab
JPS63277566A (ja) * 1987-05-08 1988-11-15 Ishikawajima Harima Heavy Ind Co Ltd 繊維強化炭化けい素セラミックスおよびその製造方法
JPS63277563A (ja) * 1987-05-08 1988-11-15 Ishikawajima Harima Heavy Ind Co Ltd 繊維強化炭化けい素セラミックスおよびその製造方法
JPS63281408A (ja) * 1987-05-13 1988-11-17 Hitachi Ltd 薄膜磁気ヘツド用スライダおよびその製法
JPS6437470A (en) * 1987-07-31 1989-02-08 Mazda Motor Sliding member made of ceramic
JPS6461355A (en) * 1987-09-01 1989-03-08 Riken Kk Titanium carbide/silicon carbide whisker/zirconia based complex sintered material and production thereof
JPS6476972A (en) * 1987-09-18 1989-03-23 Toshiba Corp Fiber reinforced silicon nitride-based ceramic and production thereof
JPH01188476A (ja) * 1988-01-19 1989-07-27 Toshiba Ceramics Co Ltd アルミナ被覆ＳｉＣウイスカー及びＳｉＣウイスカー強化セラミツクス複合材料
JPH01188475A (ja) * 1988-01-19 1989-07-27 Toshiba Ceramics Co Ltd ＢＮ被覆ＳｉＣウイスカー及びその製造方法
US5091344A (en) * 1988-01-30 1992-02-25 Ibiden Corporation Fiber reinforced ceramics of calcium phosphate series compounds and method of producing the same
US5273941A (en) * 1988-01-30 1993-12-28 Ibiden Co., Ltd. Fiber reinforced silicon carbide ceramics and method of producing the same
JPH0226876A (ja) * 1988-07-14 1990-01-29 Agency Of Ind Science & Technol 粒子分散強化した繊維強化セラミックス複合材及びその製造方法
JPH0582349B2 (ja) * 1988-07-14 1993-11-18 Kogyo Gijutsuin
JPH02116682A (ja) * 1988-10-25 1990-05-01 Ube Ind Ltd β型窒化珪素ウイスカー複合材料及びその製法
JPH02204373A (ja) * 1989-01-31 1990-08-14 Tonen Corp 繊維強化セラミックス複合材料
US5194409A (en) * 1990-07-23 1993-03-16 Tokai Carbon Co., Ltd. Process for producing bn-coated SiC whisker and process for producing ceramic comprising said bn-coated SiC whisker as reinforcement

Also Published As

Publication number Publication date
EP0209320A1 (en) 1987-01-21
US5055430A (en) 1991-10-08
DE3682129D1 (de) 1991-11-28
JPH0569789B2 (ja) 1993-10-01
US5057465A (en) 1991-10-15
EP0209320B1 (en) 1991-10-23

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