JP4728811B2 - セラミックス焼結体、セラミックス焼結体の製造方法、金属蒸着用発熱体 - Google Patents
セラミックス焼結体、セラミックス焼結体の製造方法、金属蒸着用発熱体 Download PDFInfo
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Description
Al(s)+TiB2(s)→Al(l)+TiB2(l)
13Al(s)+12BN(s)→AlB12(s)+12AlN(s)
しかしながら、これらの改良にも関わらず、アルミニウム蒸着中の高温下では上記反応が徐々に進行し、長寿命化にはまだまだ改善の余地があった。
市販のBN粉末には、低結晶性のものから高結晶性のものまで幅広くあるが、これまで好適であるとされた高結晶性BN粉末を用いたのでは、耐食性の改善効果には限度があることがわかった。そこで、本発明では、酸素量が1.0〜2.5質量%かつC軸格子定数が6.690Å以下である、低酸素かつ低結晶性のBN粉末を用いることによって、従来の高結晶性BN粉末を用いた耐食性のレベルを凌ぐことができ、更にBN粉末の粒度を、累積平均径が4〜20μm、BET比表面積が25〜70m2/gとすることによって、この効果が助長される。
なお、焼結は、黒鉛製容器、窒化硼素製容器、窒化硼素で内張した容器に収納し、非酸化性雰囲気中で行うことが望ましい。ホットプレス法では、黒鉛又は窒化硼素製スリーブ、窒化硼素で内張したスリーブを用いて焼結する。
TiB2粉末(平均粒子径12μm、純度99.9質量%以上)、AlN粉末(平均粒子径10μm、純度98.5質量%)、CaO粉末(平均粒子径0.5μm、純度99.9質量%以上)、及び表1に示される各種のBN粉末を表1に示す割合で混合して種々の混合原料粉末を調整した。ここで、各種BN粉末は、硼砂と尿素の混合物をアンモニア雰囲気中で加熱して得られたBN粉末を、窒素雰囲気下、1100〜1300℃、3〜5時間の熱処理条件を種々変更し熱処理を行うことにより製造した。これを黒鉛ダイスに充填し、窒素雰囲気中、表2に示す条件でホットプレスを行ってセラミックス焼結体(直径200mm×高さ20mmの円柱形)を製造した。
また、セラミックス焼結体の相対密度、BNのC軸格子定数、酸素量、カルシウム化合物量、粒界相、及び上記X線ピーク強度比(TiN(200)面/BN(002)面)を以下に従って測定した。それらの結果を表2に示す。
Claims (7)
- 窒化硼素25.20〜55質量%、二硼化チタン45〜60質量%、窒化アルミニウム0〜26.60質量%、カルシウム化合物を含有し、粒界相に窒化チタンが存在する、相対密度が92%以上のセラミックス焼結体であり、上記カルシウム化合物の含有率がCaO換算として0.05〜0.8質量%であり、上記窒化チタンに由来する(200)面のX線回折によるピーク強度が、上記窒化硼素の(002)面のピーク強度に対して0.06〜0.15であるセラミックス焼結体。
- セラミックス焼結体に含まれる窒化硼素結晶のC軸格子定数が6.675Å以下であり、セラミックス焼結体の酸素量が1〜2質量%である請求項1記載のセラミックス焼結体。
- 窒化硼素と二硼化チタンの合計含有率が95質量%以上である請求項1記載のセラミックス焼結体。
- 窒化硼素、二硼化チタンおよび窒化アルミニウムの合計含有率が95質量%以上である請求項1記載のセラミックス焼結体。
- 請求項1〜4記載のいずれかのセラミックス焼結体で構成されてなることを特徴とする金属蒸着用発熱体。
- 窒化硼素粉末25.20〜55質量%、二硼化チタン粉末45〜60質量%、窒化アルミニウム粉末0〜26.60質量%、カルシウム系焼結助剤を含有してなる混合原料粉末を、非酸化性雰囲気中、温度1800〜2100℃で焼結する方法であって、上記窒化硼素粉末が、窒化硼素結晶のC軸格子定数が6.690Å以下、累積平均径が4〜20μm、BET比表面積が25〜70m2/g、酸素量が1.0〜2.5質量%の窒化硼素粉末であり、上記混合原料粉末中のカルシウム系焼結助剤の含有率がCaO換算として0.09〜0.8質量%であるセラミックス焼結体の製造方法。
- カルシウム系焼結助剤が、CaO、Ca(OH)2及びCaCO3から選ばれた少なくとも1種であることを特徴とする請求項6記載のセラミックス焼結体の製造方法。
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JP4937723B2 (ja) * | 2006-12-14 | 2012-05-23 | 電気化学工業株式会社 | 金属蒸発発熱体の製造方法 |
KR100838325B1 (ko) | 2007-12-27 | 2008-06-16 | 주식회사 이엠 인더스 | 이붕화티탄이 함유된 세라믹 제조방법 및 세라믹 |
US8821988B2 (en) * | 2012-10-01 | 2014-09-02 | Dayton T. Brown, Inc. | Method for modification of the surface and subsurface regions of metallic substrates |
CN103805822B (zh) * | 2013-09-26 | 2016-04-20 | 山东鹏程特种陶瓷有限公司 | 高性能四组分导电陶瓷蒸发舟及其生产工艺 |
CN104030690B (zh) * | 2014-06-09 | 2015-10-07 | 河海大学 | 一种氮化钛-二硼化钛-立方氮化硼复合材料的制备方法 |
US20190203344A1 (en) * | 2017-03-24 | 2019-07-04 | Kennametal Inc. | Evaporator boats for metallization installations |
WO2020139641A1 (en) * | 2018-12-27 | 2020-07-02 | Momentive Performance Materials Inc. | Ceramic composite heaters comprising boron nitride and titanium diboride |
CN117229066A (zh) * | 2019-01-31 | 2023-12-15 | 电化株式会社 | 陶瓷烧结体和其制造方法、以及喷嘴部件 |
JP6990338B2 (ja) * | 2019-12-16 | 2022-01-12 | 住友電気工業株式会社 | 立方晶窒化硼素焼結体 |
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- 2004-12-10 JP JP2005516254A patent/JP4728811B2/ja not_active Expired - Fee Related
- 2004-12-10 CN CN2004800369788A patent/CN1894171B/zh not_active Expired - Fee Related
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- 2004-12-10 BR BRPI0417078-4A patent/BRPI0417078A/pt not_active Application Discontinuation
- 2004-12-10 KR KR1020067011351A patent/KR100759178B1/ko active IP Right Grant
- 2004-12-10 US US10/582,627 patent/US7632768B2/en active Active
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JPS63201064A (ja) * | 1987-02-13 | 1988-08-19 | 三菱マテリアル株式会社 | 切削工具用立方晶窒化硼素基超高圧焼結体の製造法 |
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Also Published As
Publication number | Publication date |
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EP1719745A1 (en) | 2006-11-08 |
US20080020920A1 (en) | 2008-01-24 |
TWI292784B (ja) | 2008-01-21 |
US7632768B2 (en) | 2009-12-15 |
KR100759178B1 (ko) | 2007-09-14 |
WO2005056496A1 (ja) | 2005-06-23 |
CN1894171A (zh) | 2007-01-10 |
JPWO2005056496A1 (ja) | 2007-12-06 |
BRPI0417078A (pt) | 2007-03-13 |
CN1894171B (zh) | 2011-02-02 |
TW200526795A (en) | 2005-08-16 |
EP1719745A4 (en) | 2009-11-04 |
KR20070012321A (ko) | 2007-01-25 |
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