JP4144184B2 - Manufacturing method of heat-resistant Al alloy wire for electric conduction - Google Patents
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【０００１】
【発明の属する技術分野】
本発明は、導電用耐熱Ａｌ合金線材の製造方法に係り、特に、架空送電線に用いられる耐熱Ａｌ合金線材の製造方法に関するものである。
【０００２】
【従来の技術】
近年、架空送電線においては、電力需要の増加に伴って送電容量の増加が要求されている。送電容量を増加させる最も簡単な方法は、架空送電線の導体断面積を大きくすればよいが、重量増加を招くため、既設の鉄塔の許容強度を超えてしまうという問題が生じる。
【０００３】
そこで、導体断面積を変えずに送電容量を増加させるべく、耐熱性に優れ、かつ、導電率の高いＡｌ合金線材を導体に使用している。これらの要求を満たすＡｌ合金として、従来、Ｚｒを０．１ｗｔ％程度含有したＡｌ−Ｚｒ合金が使用されてきた。このＡｌ−Ｚｒ系合金においては、耐熱性を向上させるべく、Ｚｒの含有量を多くすると、逆に導電性の低下を招いてしまう。このため、Ａｌ−Ｚｒ系合金に第３元素としてＦｅ、Ｍｇ、Ｓｉなどを含有させ、その後、極めて長時間の熱処理（時効処理）を施すことで、耐熱性および導電性に優れた導電用耐熱Ａｌ合金線材を得ている。
【０００４】
しかし、Ｆｅ、Ｍｇ、Ｓｉなどの第３元素を添加したＡｌ−Ｚｒ系合金は、長時間（例えば、約１００〜２００時間）の熱処理を必要とするため、生産性に劣り、製造コストの上昇を招いていた。このため、Ａｌ−Ｚｒ系合金に微量のＢｅを第３元素として含有させることで、熱処理（時効処理）時間の短縮を図った導電用耐熱Ａｌ合金（Ａｌ−Ｚｒ−Ｂｅ系合金）線が開発され、架空送電線に適用されている状況にある。
【０００５】
【発明が解決しようとする課題】
しかしながら、Ａｌ−Ｚｒ−Ｂｅ系合金は、熱処理に要する時間を短くすることはできるものの、Ｂｅが高価な金属であるため、原料コストの上昇を招くという問題がある。
【０００６】
また、従来の導電用耐熱Ａｌ合金線材の合金組成および製造方法では、従来の導電用耐熱Ａｌ合金線材の耐熱性、導電性、および強度を大きく上回る導電用耐熱Ａｌ合金線材を得ることは期待できない。
【０００７】
そこで本発明は、上記課題を解決し、従来の導電用耐熱Ａｌ合金線材と比較して、熱処理時間が短いと共に、製造コストが安価であり、かつ、耐熱性、導電性、および強度に優れた導電用耐熱Ａｌ合金線材の製造方法を提供することにある。
【０００８】
【課題を解決するための手段】
上記課題を解決するために請求項１の発明は、Ｚｒを０．１０〜０．５０ｗｔ％、Ｓｃを０．０５〜０．５０ｗｔ％、Ｓｉを０．０５〜０．１０ｗｔ％、Ｆｅを０．０５〜０．３０ｗｔ％、Ｔｉを０．０１〜０．１０ｗｔ％、Ｂを０．００３〜０．０２ｗｔ％含有し、残部がＡｌ及び不可避不純物であるＡｌ合金溶湯を用いて線材を形成した後、その線材に２００℃〜２５０℃で４０〜６０時間の熱処理を施し、その後、その線材に断面積減少率５０％以上の冷間加工を施してなるものである。
【０００９】
請求項２の発明は、Ｚｒを０．１０〜０．５０ｗｔ％、Ｓｃを０．０５〜０．５０ｗｔ％、Ｓｉを０．０５〜０．１０ｗｔ％、Ｆｅを０．０５〜０．３０ｗｔ％、Ｔｉを０．０１〜０．１０ｗｔ％、Ｂを０．００３〜０．０２ｗｔ％含有し、残部がＡｌ及び不可避不純物であるＡｌ合金溶湯を用いて線材を形成した後、その線材に１５０℃〜２００℃で５〜１０時間の１次熱処理、４００〜４３０℃で３５〜４５時間の２次熱処理を施し、その後、その線材に断面積減少率５０％以上の冷間加工を施してなるものである。
【００１０】
請求項３の発明は、Ｚｒを０．１０〜０．５０ｗｔ％、Ｓｃを０．０５〜０．５０ｗｔ％、Ｓｉを０．０５〜０．１０ｗｔ％、Ｆｅを０．０５〜０．３０ｗｔ％、Ｔｉを０．０１〜０．１０ｗｔ％、Ｂを０．００３〜０．０２ｗｔ％含有し、残部がＡｌ及び不可避不純物であるＡｌ合金溶湯を用いて線材を形成した後、その線材に２００℃〜２５０℃で４０〜６０時間の熱処理を施し、その後、その線材に断面積減少率５０％以上の冷間加工を施し、その後、その冷間加工材に３５０〜４００℃×１〜１０時間の熱処理を施してなるものである。
【００１１】
請求項４の発明は、Ｚｒを０．１０〜０．５０ｗｔ％、Ｓｃを０．０５〜０．５０ｗｔ％、Ｓｉを０．０５〜０．１０ｗｔ％、Ｆｅを０．０５〜０．３０ｗｔ％、Ｔｉを０．０１〜０．１０ｗｔ％、Ｂを０．００３〜０．０２ｗｔ％含有し、残部がＡｌ及び不可避不純物であるＡｌ合金溶湯を用いて線材を形成した後、その線材に１５０℃〜２００℃で５〜１０時間の１次熱処理、４００〜４３０℃で３５〜４５時間の２次熱処理を施し、その後、その線材に断面積減少率５０％以上の冷間加工を施し、その後、その冷間加工材に３５０〜４００℃×１〜１０時間の熱処理を施してなるものである。
【００１２】
請求項５の発明は、Ｚｒを０．１０〜０．５０ｗｔ％、Ｓｃを０．０５〜０．５０ｗｔ％、Ｓｉを０．０５〜０．１０ｗｔ％、Ｆｅを０．０５〜０．３０ｗｔ％、Ｔｉを０．０１〜０．１０ｗｔ％、Ｂを０．００３〜０．０２ｗｔ％、Ｂｅを０．００５〜０．０５ｗｔ％含有し、残部がＡｌ及び不可避不純物であるＡｌ合金溶湯を用いて線材を形成した後、その線材に２００℃〜２５０℃で４０〜６０時間の熱処理を施し、その後、その線材に断面積減少率５０％以上の冷間加工を施すことを特徴とする導電用耐熱Ａｌ合金線材の製造方法である。
【００１３】
請求項６の発明は、Ｚｒを０．１０〜０．５０ｗｔ％、Ｓｃを０．０５〜０．５０ｗｔ％、Ｓｉを０．０５〜０．１０ｗｔ％、Ｆｅを０．０５〜０．３０ｗｔ％、Ｔｉを０．０１〜０．１０ｗｔ％、Ｂを０．００３〜０．０２ｗｔ％、Ｂｅを０．００５〜０．０５ｗｔ％含有し、残部がＡｌ及び不可避不純物であるＡｌ合金溶湯を用いて線材を形成した後、その線材に１５０℃〜２００℃で５〜１０時間の１次熱処理、４００〜４３０℃で３５〜４５時間の２次熱処理を施し、その後、その線材に断面積減少率５０％以上の冷間加工を施すことを特徴とする導電用耐熱Ａｌ合金線材の製造方法である。
【００１４】
請求項７の発明は、Ｚｒを０．１０〜０．５０ｗｔ％、Ｓｃを０．０５〜０．５０ｗｔ％、Ｓｉを０．０５〜０．１０ｗｔ％、Ｆｅを０．０５〜０．３０ｗｔ％、Ｔｉを０．０１〜０．１０ｗｔ％、Ｂを０．００３〜０．０２ｗｔ％、Ｂｅを０．００５〜０．０５ｗｔ％含有し、残部がＡｌ及び不可避不純物であるＡｌ合金溶湯を用いて線材を形成した後、その線材に２００℃〜２５０℃で４０〜６０時間の熱処理を施し、その後、その線材に断面積減少率５０％以上の冷間加工を施し、その後、その冷間加工材に３５０〜４００℃×１〜１０時間の熱処理を施すものである。
【００１５】
請求項８の発明は、Ｚｒを０．１０〜０．５０ｗｔ％、Ｓｃを０．０５〜０．５０ｗｔ％、Ｓｉを０．０５〜０．１０ｗｔ％、Ｆｅを０．０５〜０．３０ｗｔ％、Ｔｉを０．０１〜０．１０ｗｔ％、Ｂを０．００３〜０．０２ｗｔ％、Ｂｅを０．００５〜０．０５ｗｔ％含有し、残部がＡｌ及び不可避不純物であるＡｌ合金溶湯を用いて線材を形成した後、その線材に１５０℃〜２００℃で５〜１０時間の１次熱処理、４００〜４３０℃で３５〜４５時間の２次熱処理を施し、その後、その線材に断面積減少率５０％以上の冷間加工を施し、その後、その冷間加工材に３５０〜４００℃×１〜１０時間の熱処理を施すものである。
【００１６】
以上の方法によれば、従来の導電用耐熱Ａｌ合金線材の製造方法と比較して、熱処理時間が短いと共に、線材の製造コストが安価となる。
【００１７】
上記数値範囲の限定理由を以下に説明する。
【００１８】
Ｚｒ含有量を０．１０〜０．５０ｗｔ％、Ｓｃ含有量を０．０５〜０．５０ｗｔ％としたのは、Ｚｒ含有量が０．１０ｗｔ％未満又はＳｃ含有量が０．０５ｗｔ％未満の場合、従来の製造方法と比較して、導電率の向上は図れるものの、耐熱性の向上が望めなく、さらに強度の向上も図れないためである。また、Ｚｒ含有量が０．５０ｗｔ％より多い又はＳｃ含有量が０．５ｗｔ％より多い場合、従来の製造方法と比較して、耐熱性の向上は図れるものの、導電率の向上が図れないためである。
【００１９】
Ｓｉは、０．０５〜０．１０ｗｔ％の範囲で含有させることで、熱処理時におけるＡｌ3 Ｚｒ、Ａｌ3 Ｓｃ、およびＡｌ3 （Ｚｒ，Ｓｃ）の析出を促進する効果がある。
【００２０】
Ｆｅは、０．０５〜０．３０ｗｔ％の範囲で含有させることで、得られる線材の強度を向上させる効果がある。
【００２１】
ＴｉおよびＢは、それぞれ０．０１〜０．１０ｗｔ％、０．００３〜０．０２ｗｔ％の範囲で含有させることで、鋳造材の結晶粒を微細化すると共に、鋳造材の割れや傷の発生を抑制し、これによって製造時（鋳造時）の歩留りが大幅に向上する。
【００２２】
１００℃以上３００℃未満×１〜１００時間の熱処理を施す際、熱処理温度が１００℃未満だと析出物の核生成が生じにくく、３００℃よりも高いと析出物が粗大に成長するため好ましくない。また、熱処理時間が１時間未満だと析出物の核生成が不十分となり、１００時間よりも長いと析出物が粗大に成長するため好ましくない。
【００２３】
５０℃以上３００℃未満×１〜３０時間の１次熱処理を施す際、１次熱処理の温度が５０℃未満だと析出物の核生成が生じにくく、３００℃よりも高いと析出物が粗大に成長するため好ましくない。また、１次熱処理時間が１時間未満だと析出物の核生成が不十分となり、３０時間よりも長いと析出物の成長が生じるため好ましくない。
【００２４】
３００〜５００℃×１０〜６０時間の２次熱処理を施す際、２次熱処理の温度が３００℃未満だと析出物の成長が不十分となって導電性が回復せず、５００℃よりも高いと析出物が粗大に成長して耐熱性が低下するため好ましくない。また、２次熱処理時間が１０時間未満だと析出物の成長が十分でなく、６０時間よりも長いと析出物が粗大に成長して耐熱性が低下するため好ましくない。
【００２５】
断面積減少率が５０％未満の冷間加工の場合、冷間加工時の加工硬化によるＡｌ合金線材の強度特性（引張強度）の向上が期待できないためである。
【００２６】
冷間加工後に３００〜５００℃×１〜１００時間の熱処理（再結晶熱処理）を施す際、再結晶熱処理温度が３００℃未満だと再結晶粒の核生成が生じにくく、５００℃よりも高いと再結晶粒が粗大に成長するため好ましくない。また、再結晶熱処理時間が１時間未満だと再結晶粒の核生成が不十分となり、１００時間よりも長いと再結晶粒が粗大に成長するため好ましくない。
【００２７】
【発明の実施の形態】
以下、本発明の好適一実施の形態について説明する。
【００２８】
本発明の導電用耐熱Ａｌ合金線材の製造方法は、
Ｚｒ：０．１０〜０．５０ｗｔ％と、
Ｓｃ：０．０５〜０．５０ｗｔ％と、
Ｓｉ：０．０５〜０．１０ｗｔ％、Ｆｅ：０．０５〜０．３０ｗｔ％、Ｔｉ：０．０１〜０．１０ｗｔ％、Ｂ：０．００３〜０．０２ｗｔ％を含有、又は
Ｚｒ：０．１０〜０．５０ｗｔ％と、
Ｓｃ：０．０５〜０．５０ｗｔ％と、
Ｓｉ：０．０５〜０．１０ｗｔ％、Ｆｅ：０．０５〜０．３０ｗｔ％、Ｔｉ：０．０１〜０．１０ｗｔ％、Ｂ：０．００３〜０．０２ｗｔ％、Ｂｅ：０．００５〜０．０５ｗｔ％を含有し、
残部がＡｌ及び不可避不純物であるＡｌ合金からなる線材を形成した後、その線材に２００℃以上２５０℃未満４０〜６０時間の熱処理を施し、その後、その線材に断面積減少率５０％以上の冷間加工を施してなるものである。
【００２９】
第１の実施の形態の導電用耐熱Ａｌ合金線材の製造方法を説明する。
【００３０】
先ず、Ｚｒ：０．１０〜０．５０ｗｔ％、好ましくは０．１５〜０．４０ｗｔ％、特に好ましくは０．１８〜０．３７ｗｔ％と、
Ｓｃ：０．０５〜０．５０ｗｔ％、好ましくは０．０５〜０．３０ｗｔ％、特に好ましくは０．０５〜０．２０ｗｔ％と、
Ｓｉ：０．０５〜０．１０ｗｔ％と、
Ｆｅ：０．０５〜０．３０ｗｔ％、好ましくは０．１０〜０．２０ｗｔ％と、
Ｔｉ：０．０１〜０．１０ｗｔ％、好ましくは０．０５〜０．１０ｗｔ％と、
Ｂ：０．００３〜０．０２ｗｔ％、好ましくは０．００３〜０．０１ｗｔ％と、
Ｂｅ：０．００５〜０．０５ｗｔ％、好ましくは０．００５〜０．０２５ｗｔ％
を含有し、
残部がＡｌ及び不可避不純物という化学組成を有したＡｌ合金を溶製する。
【００３１】
次に、プロペルチ法、ヘズレー法、ＳＣＲ法などの周知の鋳造方法により、このＡｌ合金溶湯を用いて線材を形成し、Ａｌマトリックス中にＺｒおよびＳｃが固溶したＡｌ合金線材を形成する。
【００３２】
その後、このＡｌ合金線材に、２００〜２５０℃×４０〜６０時間の熱処理を施す。この熱処理によって、鋳造時にＡｌマトリックス中に固溶したＺｒとＳｃが、微細な析出物（Ａｌ3 Ｚｒ、Ａｌ3 Ｓｃ、およびＡｌ3 （Ｚｒ，Ｓｃ））として生成する。
【００３３】
次に、熱処理後のＡｌ合金線材に、断面積減少率５０％以上、好ましくは断面積減少率７５％以上、特に好ましくは断面積減少率９０％以上の冷間加工を施し、導電用耐熱Ａｌ合金線材を得る。熱処理時に生成・成長した析出物が、冷間加工時における加工組織を安定化させる。これによって、導電性を低下させることなく、冷間加工後のＡｌ合金線材の耐熱性および引張強度を著しく向上させることが可能となる。
【００３４】
従来の導電用耐熱Ａｌ合金線材は、Ａｌマトリックス中にＺｒのみを固溶させると共に、熱処理によりＡｌ3 Ｚｒを析出させて、導電性を低下させること無く、耐熱性を向上させたものであった。
【００３５】
これに対して、本発明の導電用耐熱Ａｌ合金線材は、Ａｌマトリックス中にＺｒおよびＳｃを固溶させると共に、熱処理によりＡｌ3 Ｚｒ、Ａｌ3 Ｓｃ、およびＡｌ3 （Ｚｒ，Ｓｃ）を析出させたものである。即ち、本発明の線材と、従来の線材とは、耐熱性又は導電性或いは強度の向上メカニズムが全く異なるものである。よって、従来の線材と比較して、導電性、耐熱性、および強度に優れた導電用耐熱Ａｌ合金線材を得ることができる。
【００３６】
また、本発明の導電用耐熱Ａｌ合金線材の製造方法によれば、従来材のＡｌ−Ｚｒ系合金およびＡｌ−Ｚｒ−Ｂｅ系合金と比較しても、短い熱処理時間で、耐熱性、導電性、および引張強度に優れたＡｌ合金線材を得ることができる。ここで、熱処理時間が短くなるため、導電用耐熱Ａｌ合金線材の生産性が向上し、製造コストの低減を図ることができる。
【００３７】
熱処理後に断面積減少率５０％以上の冷間加工を施すことで、熱処理時に生成・成長した析出物（Ａｌ3 Ｚｒ、Ａｌ3 Ｓｃ、およびＡｌ3 （Ｚｒ，Ｓｃ））が加工組織を安定化させ、導電性を低下させることなく、冷間加工後のＡｌ合金線材の耐熱性および引張強度を著しく向上させることが可能となる。
【００３８】
次に、本発明の他の実施の形態について説明する。
【００３９】
第２の実施の形態の導電用耐熱Ａｌ合金線材の製造方法は、
Ｚｒ：０．１０〜０．５０ｗｔ％と、
Ｓｃ：０．０５〜０．５０ｗｔ％と、
Ｓｉ：０．０５〜０．１０ｗｔ％、Ｆｅ：０．０５〜０．３０ｗｔ％、Ｔｉ：０．０１〜０．１０ｗｔ％、Ｂ：０．００３〜０．０２ｗｔ％を含有、又は
Ｚｒ：０．１０〜０．５０ｗｔ％と、
Ｓｃ：０．０５〜０．５０ｗｔ％と、
Ｓｉ：０．０５〜０．１０ｗｔ％、Ｆｅ：０．０５〜０．３０ｗｔ％、Ｔｉ：０．０１〜０．１０ｗｔ％、Ｂ：０．００３〜０．０２ｗｔ％、Ｂｅ：０．００５〜０．０５ｗｔ％を含有し、
残部がＡｌ及び不可避不純物であるＡｌ合金からなる線材を形成した後、その線材に１５０℃〜２００℃で５〜１０時間の１次熱処理、４００〜４３０℃で３５〜４５時間の２次熱処理を施し、その後、その線材に断面積減少率５０％以上の冷間加工を施してなるものである。
【００４０】
第２の実施の形態の導電用耐熱Ａｌ合金線材の製造方法を説明する。
【００４１】
先ず、前述した本発明の製造方法と同様の方法により、Ａｌ合金線材を形成する。
【００４２】
その後、このＡｌ合金線材に、１５０〜２００℃×５〜１０時間の１次熱処理を施す。次に、４００〜４３０℃×３５〜４５時間の２次熱処理を施す。１次熱処理および２次熱処理によって、鋳造時にＡｌマトリックス中に固溶したＺｒとＳｃが、微細な析出物（Ａｌ3 Ｚｒ、Ａｌ3 Ｓｃ、およびＡｌ3 （Ｚｒ，Ｓｃ））として生成する。１次熱処理によって、析出物の核生成が行われ、２次熱処理によって、析出物が所望の大きさに成長する。
【００４３】
次に、熱処理後のＡｌ合金線材に、断面積減少率５０％以上、好ましくは断面積減少率７５％以上、特に好ましくは断面積減少率９０％以上の冷間加工を施し、導電用耐熱Ａｌ合金線材を得る。
【００４４】
本実施の形態の導電用耐熱Ａｌ合金線材の製造方法においても、本発明の導電用耐熱Ａｌ合金線材の製造方法と同様の効果を有することは言うまでもない。
【００４５】
また、本実施の形態の導電用耐熱Ａｌ合金線材の製造方法によれば、Ａｌ合金線材に施す熱処理を２段階（１次熱処理および２次熱処理）にわけることで、本発明の導電用耐熱Ａｌ合金線材の製造方法と比較して、熱処理時間を更に短くすることができる。
【００４６】
次に、第３の実施の形態の導電用耐熱Ａｌ合金線材の製造方法を説明する。
【００４７】
第３の実施の形態の導電用耐熱Ａｌ合金線材の製造方法は、
Ｚｒ：０．１０〜０．５０ｗｔ％と、
Ｓｃ：０．０５〜０．５０ｗｔ％と、
Ｓｉ：０．０５〜０．１０ｗｔ％、Ｆｅ：０．０５〜０．３０ｗｔ％、Ｔｉ：０．０１〜０．１０ｗｔ％、Ｂ：０．００３〜０．０２ｗｔ％を含有、又は
Ｚｒ：０．１０〜０．５０ｗｔ％と、
Ｓｃ：０．０５〜０．５０ｗｔ％と、
Ｓｉ：０．０５〜０．１０ｗｔ％、Ｆｅ：０．０５〜０．３０ｗｔ％、Ｔｉ：０．０１〜０．１０ｗｔ％、Ｂ：０．００３〜０．０２ｗｔ％、Ｂｅ：０．００５〜０．０５ｗｔ％を含有し、
残部がＡｌ及び不可避不純物であるＡｌ合金溶湯を用いて線材を形成した後、その線材に２００℃〜２５０℃で４０〜６０時間の熱処理を施し、その後、その線材に断面積減少率５０％以上の冷間加工を施し、その後、その冷間加工材に３５０〜４００℃×１〜１０時間の熱処理を施してなるものである。
【００４８】
本実施の形態の導電用耐熱Ａｌ合金線材の製造方法を説明する。
【００４９】
前述した本発明の製造方法で得られた導電用耐熱Ａｌ合金線材に、３５０〜４００℃×１〜１０時間の再結晶熱処理（熱処理）を施し、本実施の形態の導電用耐熱Ａｌ合金線材を得る。この再結晶熱処理によって、再結晶粒の核生成・成長が生じ、冷間加工時に導入された格子欠陥の大部分が消滅する。
【００５０】
本実施の形態の導電用耐熱Ａｌ合金線材の製造方法によれば、本発明の導電用耐熱Ａｌ合金線材の製造方法と比較して、引張強度および導電率を殆ど低下させることなく、耐熱性を更に向上させることができる。
【００５１】
次に、第４の実施の形態の導電用耐熱Ａｌ合金線材の製造方法を説明する。
【００５２】
第４の実施の形態の導電用耐熱Ａｌ合金線材の製造方法は、
Ｚｒ：０．１０〜０．５０ｗｔ％と、
Ｓｃ：０．０５〜０．５０ｗｔ％と、
Ｓｉ：０．０５〜０．１０ｗｔ％、Ｆｅ：０．０５〜０．３０ｗｔ％、Ｔｉ：０．０１〜０．１０ｗｔ％、Ｂ：０．００３〜０．０２ｗｔ％を含有、又は
Ｚｒ：０．１０〜０．５０ｗｔ％と、
Ｓｃ：０．０５〜０．５０ｗｔ％と、
Ｓｉ：０．０５〜０．１０ｗｔ％、Ｆｅ：０．０５〜０．３０ｗｔ％、Ｔｉ：０．０１〜０．１０ｗｔ％、Ｂ：０．００３〜０．０２ｗｔ％、Ｂｅ：０．００５〜０．０５ｗｔ％を含有し、
その線材に１５０℃〜２００℃で５〜１０時間の１次熱処理、４００〜４３０℃で３５〜４５時間の２次熱処理を施し、その後、その線材に断面積減少率５０％以上の冷間加工を施し、その後、その冷間加工材に３５０〜４００℃×１〜１０時間の熱処理を施してなるものである。
【００５３】
本実施の形態の導電用耐熱Ａｌ合金線材の製造方法を説明する。
【００５４】
前述した第１の実施の形態の製造方法で得られた導電用耐熱Ａｌ合金線材に、第２の実施の形態と同様に、３５０〜４００℃×１〜１０時間の再結晶熱処理（熱処理）を施し、本実施の形態の導電用耐熱Ａｌ合金線材を得る。
【００５５】
本実施の形態の導電用耐熱Ａｌ合金線材によれば、第１の実施の形態の導電用耐熱Ａｌ合金線材と比較して、引張強度および導電率を殆ど低下させることなく、耐熱性を更に向上させることができる。
【００５６】
【実施例】
（実施例１）
先ず、Ｚｒ：０．３５ｗｔ％、Ｓｃ：０．２０ｗｔ％、Ｓｉ：０．０８ｗｔ％、Ｆｅ：０．１３ｗｔ％、Ｔｉ：０．０７ｗｔ％、Ｂ：０．００５ｗｔ％、残部がＡｌ及び不可避不純物という化学組成を有したＡｌ合金を溶製する。
【００５７】
その後、このＡｌ合金溶湯を用いてＡｌ合金インゴットを形成した後、このＡｌ合金インゴットにスェージャー加工を施して、外径１２ｍｍのＡｌ合金荒引線を形成する。
【００５８】
次に、このＡｌ合金荒引線に２５０℃×５０時間の熱処理を施し、その後、熱処理後のＡｌ合金線材に断面積減少率９３％の冷間加工を施し、外径３．２ｍｍの導電用耐熱Ａｌ合金線材を作製する。
（実施例２）
実施例１と同様にして形成したＡｌ合金荒引線に、２９５℃×５０時間の熱処理を施し、その後、熱処理後のＡｌ合金線材に断面積減少率９３％の冷間加工を施し、外径３．２ｍｍの導電用耐熱Ａｌ合金線材を作製する。
（実施例３）
実施例１と同様にして形成したＡｌ合金荒引線に、２００℃×７時間の１次熱処理、次いで、４２０℃×４０時間の２次熱処理を施し、その後、熱処理後のＡｌ合金線材に断面積減少率９３％の冷間加工を施し、外径３．２ｍｍの導電用耐熱Ａｌ合金線材を作製する。
（実施例４）
Ｚｒ：０．２０ｗｔ％、Ｓｃ：０．２０ｗｔ％、Ｓｉ：０．０８ｗｔ％、Ｆｅ：０．１３ｗｔ％、Ｔｉ：０．０７ｗｔ％、Ｂ：０．００５ｗｔ％、残部がＡｌ及び不可避不純物という化学組成を有したＡｌ合金を用いる以外は、実施例３と同様にして、外径３．２ｍｍの導電用耐熱Ａｌ合金線材を作製する。
（実施例５）
Ｚｒ：０．３５ｗｔ％、Ｓｃ：０．２０ｗｔ％、Ｓｉ：０．０８ｗｔ％、Ｆｅ：０．１３ｗｔ％、Ｔｉ：０．０７ｗｔ％、Ｂ：０．００５ｗｔ％、Ｂｅ：０．０１ｗｔ％、残部がＡｌ及び不可避不純物という化学組成を有したＡｌ合金を用いる以外は、実施例１と同様にして、外径３．２ｍｍの導電用耐熱Ａｌ合金線材を作製する。
（実施例６）
２９５℃×５０時間の熱処理を施す以外は、実施例５と同様にして、外径３．２ｍｍの導電用耐熱Ａｌ合金線材を作製する。
（実施例７）
２００℃×７時間の１次熱処理、次いで、４２０℃×４０時間の２次熱処理を
施す以外は、実施例５と同様にして、外径３．２ｍｍの導電用耐熱Ａｌ合金線材を作製する。
（実施例８）
Ｚｒ：０．２０ｗｔ％、Ｓｃ：０．２０ｗｔ％、Ｓｉ：０．０８ｗｔ％、Ｆｅ：０．１３ｗｔ％、Ｔｉ：０．０７ｗｔ％、Ｂ：０．００５ｗｔ％、Ｂｅ：０．０１ｗｔ％、残部がＡｌ及び不可避不純物という化学組成を有したＡｌ合金を用いる以外は、実施例７と同様にして、外径３．２ｍｍの導電用耐熱Ａｌ合金線材を作製する。
（実施例９）
実施例１と同様にして形成したＡｌ合金荒引線に、２００℃×７時間の１次熱処理、次いで、４２０℃×４０時間の２次熱処理を施し、その後、熱処理後のＡｌ合金線材に断面積減少率９３％の冷間加工を施して外径３．２ｍｍに形成した後、３５０℃×４時間の再結晶熱処理を施し、導電用耐熱Ａｌ合金線材を作製する。
（比較例１）
Ａｌ合金がＳｃを含有していない他は、全て実施例１と同様にして、外径３．２ｍｍの導電用耐熱Ａｌ合金線材を作製する。
（比較例２）
Ａｌ合金がＳｃを含有していない他は、全て実施例２と同様にして、外径３．２ｍｍの導電用耐熱Ａｌ合金線材を作製する。
（比較例３）
Ａｌ合金がＳｃを含有していない他は、全て実施例３と同様にして、外径３．２ｍｍの導電用耐熱Ａｌ合金線材を作製する。
（比較例４）
Ａｌ合金がＳｃを含有していない他は、全て実施例４と同様にして、外径３．２ｍｍの導電用耐熱Ａｌ合金線材を作製する。
（比較例５）
Ａｌ合金がＳｃを含有していない他は、全て実施例５と同様にして、外径３．２ｍｍの導電用耐熱Ａｌ合金線材を作製する。
（比較例６）
Ａｌ合金がＳｃを含有していない他は、全て実施例６と同様にして、外径３．２ｍｍの導電用耐熱Ａｌ合金線材を作製する。
（比較例７）
Ａｌ合金がＳｃを含有していない他は、全て実施例７と同様にして、外径３．２ｍｍの導電用耐熱Ａｌ合金線材を作製する。
（比較例８）
Ａｌ合金がＳｃを含有していない他は、全て実施例８と同様にして、外径３．２ｍｍの導電用耐熱Ａｌ合金線材を作製する。
（比較例９）
Ａｌ合金がＳｃを含有していない他は、全て実施例９と同様にして、外径３．２ｍｍの導電用耐熱Ａｌ合金線材を作製する。
【００５９】
実施例１〜９および比較例１〜９の導電用耐熱Ａｌ合金線材の化学組成および熱処理条件を表１に示す。
【００６０】
【表１】
次に、得られた実施例１〜９および比較例１〜９の導電用耐熱Ａｌ合金線材について、それぞれ引張強度（ＭＰａ）、導電率（％ＩＡＣＳ）、耐熱性（％）を測定した。その測定結果を表２に示す。
【００６２】
ここで、耐熱性（％）は、（得られた導電用耐熱Ａｌ合金線材に２８０℃で１時間加熱した後における引張強度／得られた導電用耐熱Ａｌ合金線材の引張強度）×１００で求められる値である。
【００６３】
【表２】
表２に示すように、本発明材である実施例１〜９の導電用耐熱Ａｌ合金線材においては、５０時間以内の熱処理で、２４０ＭＰａ以上の引張強度、５８％ＩＡＣＳ以上の導電率、および９５％以上の耐熱性を有しており、強度、導電性、および耐熱性に優れていた。従来の送電線用アルミ合金において、上述の特性を兼ね備えた材料は存在せず、発明者らが鋭意研究し、発見したものである。また、Ｂｅを含有した実施例１〜４の線材とＢｅを含有しない実施例５〜８の線材とを比較するに、強度、導電性、および耐熱性に大きな差異が無いことから、必ずしも、高価なＢｅをＡｌ合金原料として用いる必要はないことが伺える。
【００６５】
これに対して、比較例１〜９の導電用耐熱Ａｌ合金線材は、それぞれ、実施例１〜９の導電用耐熱Ａｌ合金線材と同じ熱処理を施したものであるが、Ａｌ合金中にＳｃを含有していない。このため、比較例１〜９の線材全てにおいて、引張強度、導電率、および耐熱性のいずれもが、実施例１〜９の線材よりも劣っていた。
【００６６】
以上、本発明の実施の形態は、上述した実施の形態に限定されるものではなく、他にも種々のものが想定されることは言うまでもない。
【００６７】
【発明の効果】
以上要するに本発明によれば、短い熱処理時間で、従来の線材と比較して、導電性、耐熱性、および強度に優れた導電用耐熱Ａｌ合金線材を得ることができるという優れた効果を発揮する。[0001]
BACKGROUND OF THE INVENTION
The present invention is a heat-resistant Al alloy wire for electrical conduction.MaterialHeat-resistant Al alloy wire used in overhead transmission lines, especially for manufacturing methodsMaterialIt relates to a manufacturing method.
[0002]
[Prior art]
In recent years, overhead transmission lines have been required to increase transmission capacity with an increase in power demand. The simplest method for increasing the power transmission capacity is to increase the conductor cross-sectional area of the overhead power transmission line. However, since this increases the weight, there is a problem that the allowable strength of the existing steel tower is exceeded.
[0003]
Therefore, in order to increase the power transmission capacity without changing the conductor cross-sectional area, an Al alloy wire having excellent heat resistance and high conductivity is used for the conductor. Conventionally, an Al—Zr alloy containing about 0.1 wt% Zr has been used as an Al alloy that satisfies these requirements. In this Al—Zr-based alloy, if the Zr content is increased in order to improve the heat resistance, conversely, the conductivity is lowered. For this reason, it is possible to contain Fe, Mg, Si, etc. as the third element in the Al—Zr alloy, and then to perform heat treatment (aging treatment) for an extremely long time. Al alloy wire is obtained.
[0004]
However, an Al—Zr-based alloy to which a third element such as Fe, Mg, Si or the like is added requires heat treatment for a long time (for example, about 100 to 200 hours), resulting in poor productivity and an increase in manufacturing cost. Was invited. For this reason, a heat-resistant Al alloy (Al-Zr-Be alloy) wire has been developed for shortening the heat treatment (aging treatment) time by adding a small amount of Be as a third element to the Al-Zr alloy. And is applied to overhead power transmission lines.
[0005]
[Problems to be solved by the invention]
However, although the Al—Zr—Be-based alloy can shorten the time required for the heat treatment, Be is an expensive metal, so that there is a problem that the raw material cost is increased.
[0006]
In addition, with the conventional alloy composition and manufacturing method of heat-resistant Al alloy wire for electric conduction, it is not expected to obtain heat-resistant Al alloy wire for electric conduction that greatly exceeds the heat resistance, conductivity, and strength of conventional heat-resistant Al alloy wire for electric conduction. .
[0007]
Therefore, the present invention solves the above-mentioned problems, and has a shorter heat treatment time, a lower manufacturing cost, and superior heat resistance, conductivity, and strength as compared with conventional heat-resistant Al alloy wires for electric conduction. Heat-resistant Al alloy wire for conductionMaterialIt is to provide a manufacturing method.
[0008]
[Means for Solving the Problems]
In order to solve the above problems, the invention of claim 1 is characterized in that Zr is 0.10 to 0.50 wt%, and Sc is 0.05 to 0.50 wt%., 0.05 to 0.10 wt% of Si, 0.05 to 0.30 wt% of Fe, 0.01 to 0.10 wt% of Ti, 0.003 to 0.02 wt% of BContains, the balance being Al and inevitable impurities AlUsing molten alloyAfter forming the wire, the wire40-60 hours at 200-250 ° CAfter that, the wire is subjected to cold working with a cross-sectional area reduction rate of 50% or more.
[0009]
Claim2In the present invention, Zr is 0.10 to 0.50 wt%, and Sc is 0.05 to 0.50 wt%., 0.05 to 0.10 wt% of Si, 0.05 to 0.30 wt% of Fe, 0.01 to 0.10 wt% of Ti, 0.003 to 0.02 wt% of BAfter forming the wire using Al alloy molten metal that contains and the balance is Al and inevitable impurities, the wire150 to 200 ° C for 5 to 10 hoursPrimary heat treatment of35 to 45 hours at 400 to 430 ° CNext, the wire is subjected to cold working with a cross-sectional area reduction rate of 50% or more.
[0010]
Claim3In the present invention, Zr is 0.10 to 0.50 wt%, and Sc is 0.05 to 0.50 wt%, 0.05 to 0.10 wt% of Si, 0.05 to 0.30 wt% of Fe, 0.01 to 0.10 wt% of Ti, 0.003 to 0.02 wt% of BAfter forming the wire using Al alloy molten metal that contains and the balance is Al and inevitable impurities, the wire40-60 hours at 200-250 ° CAfter that, the wire is subjected to cold working with a cross-sectional area reduction rate of 50% or more.350-400 ° C x 1-10 hoursThe heat treatment is performed.
[0011]
Claim4In the present invention, Zr is 0.10 to 0.50 wt%, and Sc is 0.05 to 0.50 wt%, 0.05 to 0.10 wt% of Si, 0.05 to 0.30 wt% of Fe, 0.01 to 0.10 wt% of Ti, 0.003 to 0.02 wt% of BAfter forming the wire using Al alloy molten metal that contains and the balance is Al and inevitable impurities, the wire150 to 200 ° C for 5 to 10 hoursPrimary heat treatment of35 to 45 hours at 400 to 430 ° CAfter that, the wire is subjected to cold working with a cross-sectional area reduction rate of 50% or more, and then the cold worked material is subjected to cold working.350-400 ° C x 1-10 hoursThe heat treatment is performed.
[0012]
In the invention of claim 5, Zr is 0.10 to 0.50 wt%, Sc is 0.05 to 0.50 wt%, Si is 0.05 to 0.10 wt%, and Fe is 0.05 to 0.30 wt%. , Using 0.01 to 0.10 wt% of Ti, 0.003 to 0.02 wt% of B, 0.005 to 0.05 wt% of Be, the balance being Al and molten Al alloy with inevitable impurities After forming the wire, the wire is subjected to heat treatment at 200 to 250 ° C. for 40 to 60 hours, and then subjected to cold working with a cross-sectional area reduction rate of 50% or more. This is a method for producing an Al alloy wire.
[0013]
In the invention of claim 6, Zr is 0.10 to 0.50 wt%, Sc is 0.05 to 0.50 wt%, Si is 0.05 to 0.10 wt%, and Fe is 0.05 to 0.30 wt%. , Using 0.01 to 0.10 wt% of Ti, 0.003 to 0.02 wt% of B, 0.005 to 0.05 wt% of Be, the balance being Al and molten Al alloy with inevitable impurities After forming the wire, the wire is subjected to a primary heat treatment at 150 ° C. to 200 ° C. for 5 to 10 hours, and a secondary heat treatment at 400 to 430 ° C. for 35 to 45 hours. % Is a method for producing a heat-resistant heat-resistant Al alloy wire characterized by performing cold working of at least%.
[0014]
In the invention of claim 7, Zr is 0.10 to 0.50 wt%, Sc is 0.05 to 0.50 wt%, Si is 0.05 to 0.10 wt%, and Fe is 0.05 to 0.30 wt%. , Using 0.01 to 0.10 wt% of Ti, 0.003 to 0.02 wt% of B, 0.005 to 0.05 wt% of Be, the balance being Al and molten Al alloy with inevitable impurities After forming the wire, the wire is subjected to heat treatment at 200 ° C. to 250 ° C. for 40 to 60 hours, and then the wire is subjected to cold working with a cross-sectional area reduction rate of 50% or more, and then the cold worked material. Is subjected to heat treatment at 350 to 400 ° C. for 1 to 10 hours..
[0015]
In the invention of claim 8, Zr is 0.10 to 0.50 wt%, Sc is 0.05 to 0.50 wt%, Si is 0.05 to 0.10 wt%, and Fe is 0.05 to 0.30 wt%. , Using 0.01 to 0.10 wt% of Ti, 0.003 to 0.02 wt% of B, 0.005 to 0.05 wt% of Be, the balance being Al and molten Al alloy with inevitable impurities After forming the wire, the wire is subjected to a primary heat treatment at 150 ° C. to 200 ° C. for 5 to 10 hours, and a secondary heat treatment at 400 to 430 ° C. for 35 to 45 hours. % Or more of cold work, and then heat treatment of the cold work material at 350 to 400 ° C. for 1 to 10 hours.
[0016]
According to the above method, the heat treatment time is shorter and the production cost of the wire is lower than that of the conventional method for producing a heat-resistant Al alloy wire for electrical conduction.
[0017]
The reason for limiting the numerical range will be described below.
[0018]
The reason why the Zr content is 0.10 to 0.50 wt% and the Sc content is 0.05 to 0.50 wt% is that the Zr content is less than 0.10 wt% or the Sc content is less than 0.05 wt%. In this case, the conductivity can be improved as compared with the conventional manufacturing method, but the heat resistance cannot be improved and the strength cannot be further improved. In addition, when the Zr content is more than 0.50 wt% or the Sc content is more than 0.5 wt%, the heat resistance can be improved as compared with the conventional manufacturing method, but the conductivity cannot be improved. It is.
[0019]
Si is contained in the range of 0.05 to 0.10 wt%, so that Al during heat treatmentThreeZr, AlThreeSc and AlThreeThere is an effect of promoting precipitation of (Zr, Sc).
[0020]
Fe is contained in the range of 0.05 to 0.30 wt%, and has an effect of improving the strength of the obtained wire.
[0021]
Ti and B are contained in the range of 0.01 to 0.10 wt% and 0.003 to 0.02 wt%, respectively, to refine the crystal grains of the cast material and to generate cracks and scratches on the cast material. As a result, the yield during production (casting) is greatly improved.
[0022]
When heat treatment is performed at 100 ° C. or more and less than 300 ° C. for 1 to 100 hours, if the heat treatment temperature is less than 100 ° C., nucleation of precipitates is difficult to occur, and if it is higher than 300 ° C., precipitates grow coarsely, which is not preferable. . Further, if the heat treatment time is less than 1 hour, the nucleation of precipitates becomes insufficient, and if it is longer than 100 hours, the precipitates grow coarsely, which is not preferable.
[0023]
When the primary heat treatment is performed at 50 ° C. or more and less than 300 ° C. × 1 to 30 hours, if the temperature of the primary heat treatment is less than 50 ° C., nucleation of precipitates is difficult to occur, and if the temperature is higher than 300 ° C., the precipitates are coarse. It is not preferable because it grows. Further, if the primary heat treatment time is less than 1 hour, the nucleation of precipitates is insufficient, and if it is longer than 30 hours, the growth of precipitates occurs, which is not preferable.
[0024]
When the secondary heat treatment at 300 to 500 ° C. × 10 to 60 hours is performed, if the temperature of the secondary heat treatment is less than 300 ° C., the growth of precipitates is insufficient and the conductivity is not recovered and is higher than 500 ° C. And the precipitate grows coarsely and heat resistance is lowered, which is not preferable. Further, if the secondary heat treatment time is less than 10 hours, the growth of the precipitate is not sufficient, and if it is longer than 60 hours, the precipitate grows coarsely and the heat resistance is lowered, which is not preferable.
[0025]
This is because in the case of cold working with a cross-sectional area reduction rate of less than 50%, improvement in strength characteristics (tensile strength) of the Al alloy wire by work hardening during cold working cannot be expected.
[0026]
When performing heat treatment (recrystallization heat treatment) at 300 to 500 ° C. for 1 to 100 hours after cold working, if the recrystallization heat treatment temperature is less than 300 ° C., nucleation of recrystallized grains is difficult to occur, and if it is higher than 500 ° C. Since recrystallized grains grow coarsely, it is not preferable. Further, if the recrystallization heat treatment time is less than 1 hour, nucleation of recrystallized grains becomes insufficient, and if it is longer than 100 hours, the recrystallized grains grow coarsely, which is not preferable.
[0027]
DETAILED DESCRIPTION OF THE INVENTION
Hereinafter, a preferred embodiment of the present invention will be described.
[0028]
Heat-resistant Al alloy wire for conduction of the present inventionManufacturing methodIs
Zr: 0.10 to 0.50 wt%,
Sc: 0.05-0.50 wt%,
Si: 0.05-0.10 wt%, Fe: 0.05-0.30 wt%, Ti: 0.01-0.10 wt%, B: 0.003-0.02 wt%Containing, or
Zr: 0.10 to 0.50 wt%,
Sc: 0.05-0.50 wt%,
Si: 0.05 to 0.10 wt%, Fe: 0.05 to 0.30 wt%, Ti: 0.01 to 0.10 wt%, B: 0.003 to 0.02 wt%, Be: 0.005 Contains 0.05 wt%And
After forming a wire made of an Al alloy with the balance being Al and inevitable impurities, the wire200 ° C or more and less than 250 ° C for 40 to 60 hoursAfter that, the wire is subjected to cold working with a cross-sectional area reduction rate of 50% or more.
[0029]
Of the first embodimentA method for producing a heat-resistant Al alloy wire for conduction will be described.
[0030]
First, Zr: 0.10 to 0.50 wt%, preferably 0.15 to 0.40 wt%, particularly preferably 0.18 to 0.37 wt%,
Sc: 0.05 to 0.50 wt%, preferably 0.05 to 0.30 wt%, particularly preferably 0.05 to 0.20 wt%,
Si: 0.05 to 0.10 wt%,
Fe: 0.05-0.30 wt%, preferably 0.10-0.20 wt%,
Ti: 0.01-0.10 wt%, preferably 0.05-0.10 wt%,
B: 0.003-0.02 wt%, preferably 0.003-0.01 wt%,
Be: 0.005 to 0.05 wt%, preferably 0.005 to 0.025 wt%
Containing
An Al alloy having the chemical composition of Al and inevitable impurities is melted.
[0031]
Next, a wire is formed using this Al alloy molten metal by a known casting method such as the Properti method, the Hazeley method, or the SCR method, and an Al alloy wire in which Zr and Sc are dissolved in an Al matrix is formed.
[0032]
Then, to this Al alloy wire2Heat treatment at 00 to 250 ° C. × 40 to 60 hours is performed. By this heat treatment, Zr and Sc dissolved in the Al matrix at the time of casting become fine precipitates (AlThreeZr, AlThreeSc and AlThree(Zr, Sc)).
[0033]
Next, the Al alloy wire after the heat treatment is subjected to cold working with a cross-sectional area reduction rate of 50% or more, preferably a cross-sectional area reduction rate of 75% or more, and particularly preferably a cross-sectional area reduction rate of 90% or more. Obtain alloy wire. Precipitates generated and grown during heat treatment stabilize the work structure during cold working. Thereby, it becomes possible to remarkably improve the heat resistance and tensile strength of the Al alloy wire after cold working without reducing the conductivity.
[0034]
The conventional heat-resistant Al alloy wire for conductive use is a solution in which only Zr is dissolved in an Al matrix and heat treated to produce Al.ThreeThe heat resistance was improved without precipitating Zr and reducing the conductivity.
[0035]
On the other hand, the heat-resistant Al alloy wire for electric conduction of the present invention dissolves Zr and Sc in the Al matrix and heat-treats Al.ThreeZr, AlThreeSc and AlThree(Zr, Sc) is precipitated. That is, the wire rod of the present invention and the conventional wire rod are completely different in heat resistance, conductivity, or strength improvement mechanism. Therefore, it is possible to obtain a heat-resistant heat-resistant Al alloy wire excellent in conductivity, heat resistance, and strength as compared with a conventional wire.
[0036]
In addition, according to the method for producing a heat-resistant Al alloy wire for conduction of the present invention, heat resistance and conductivity can be reduced in a short heat treatment time as compared with the conventional Al-Zr alloy and Al-Zr-Be alloy. And an Al alloy wire excellent in tensile strength can be obtained. Here, since the heat treatment time is shortened, the productivity of the heat-resistant Al alloy wire for conduction is improved, and the manufacturing cost can be reduced.
[0037]
By performing cold working with a cross-sectional area reduction rate of 50% or more after heat treatment, precipitates (AlThreeZr, AlThreeSc and AlThree(Zr, Sc)) stabilizes the processed structure and can significantly improve the heat resistance and tensile strength of the Al alloy wire after cold working without reducing the electrical conductivity.
[0038]
Next, another embodiment of the present invention will be described.
[0039]
First2Heat-resistant Al alloy wire for electric conduction in the embodimentManufacturing methodIs
Zr: 0.10 to 0.50 wt%,
Sc: 0.05-0.50 wt%,
Si: 0.05-0.10 wt%, Fe: 0.05-0.30 wt%, Ti: 0.01-0.10 wt%, B: 0.003-0.02 wt%Containing, or
Zr: 0.10 to 0.50 wt%,
Sc: 0.05-0.50 wt%,
Si: 0.05 to 0.10 wt%, Fe: 0.05 to 0.30 wt%, Ti: 0.01 to 0.10 wt%, B: 0.003 to 0.02 wt%, Be: 0.005 Contains 0.05 wt%And
After forming the wire consisting of Al and Al alloy with the balance being inevitable impurities,150 to 200 ° C for 5 to 10 hoursPrimary heat treatment of35 to 45 hours at 400 to 430 ° CNext, the wire is subjected to cold working with a cross-sectional area reduction rate of 50% or more.
[0040]
First2The manufacturing method of the heat-resistant heat-resistant Al alloy wire of the embodiment will be described.
[0041]
First, an Al alloy wire is formed by the same method as the manufacturing method of the present invention described above.
[0042]
Then, to this Al alloy wire1A primary heat treatment is performed at 50 to 200 ° C. for 5 to 10 hours. next4Secondary heat treatment at 00 to 430 ° C. × 35 to 45 hours is performed. By primary heat treatment and secondary heat treatment, Zr and Sc dissolved in the Al matrix at the time of casting become fine precipitates (AlThreeZr, AlThreeSc and AlThree(Zr, Sc)). The primary heat treatment causes nucleation of precipitates, and the secondary heat treatment causes the precipitates to grow to a desired size.
[0043]
Next, the Al alloy wire after the heat treatment is subjected to cold working with a cross-sectional area reduction rate of 50% or more, preferably a cross-sectional area reduction rate of 75% or more, and particularly preferably a cross-sectional area reduction rate of 90% or more. Obtain alloy wire.
[0044]
Heat-resistant Al alloy wire for conduction of this embodimentMaterialAlso in the manufacturing method, the heat-resistant Al alloy wire for conductive use of the present inventionMaterialNeedless to say, it has the same effect as the manufacturing method.
[0045]
Moreover, according to the manufacturing method of the heat-resistant Al alloy wire for electric conduction of the present embodiment, the heat-resistant Al alloy wire for electric conduction according to the present invention is divided into two stages (primary heat treatment and secondary heat treatment). Compared with the manufacturing method of an alloy wire, the heat treatment time can be further shortened.
[0046]
Next3The manufacturing method of the heat-resistant heat-resistant Al alloy wire of the embodiment will be described.
[0047]
First3Heat-resistant Al alloy wire for electric conduction in the embodimentManufacturing methodIs
Zr: 0.10 to 0.50 wt%,
Sc: 0.05-0.50 wt%,
Si: 0.05-0.10 wt%, Fe: 0.05-0.30 wt%, Ti: 0.01-0.10 wt%, B: 0.003-0.02 wt%Containing, or
Zr: 0.10 to 0.50 wt%,
Sc: 0.05-0.50 wt%,
Si: 0.05 to 0.10 wt%, Fe: 0.05 to 0.30 wt%, Ti: 0.01 to 0.10 wt%, B: 0.003 to 0.02 wt%, Be: 0.005 Contains 0.05 wt%And
After forming the wire using Al alloy molten metal with the balance being Al and inevitable impurities,40-60 hours at 200-250 ° CAfter that, the wire is subjected to cold working with a cross-sectional area reduction rate of 50% or more.350-400 ° C x 1-10 hoursThe heat treatment is performed.
[0048]
The manufacturing method of the heat-resistant Al alloy wire for electric conduction of this Embodiment is demonstrated.
[0049]
To the heat-resistant Al alloy wire for conduction obtained by the production method of the present invention described above3A recrystallization heat treatment (heat treatment) is performed at 50 to 400 ° C. for 1 to 10 hours to obtain the heat-resistant Al alloy wire for conduction of this embodiment. This recrystallization heat treatment causes nucleation / growth of recrystallized grains, and most of lattice defects introduced during cold working disappear.
[0050]
Heat-resistant Al alloy wire for conduction of the present embodimentManufacturing methodAccording to the present invention, the heat-resistant heat-resistant Al alloy wire of the present inventionManufacturing methodAs compared with, the heat resistance can be further improved without substantially reducing the tensile strength and the electrical conductivity.
[0051]
Next4The manufacturing method of the heat-resistant heat-resistant Al alloy wire of the embodiment will be described.
[0052]
First4Heat-resistant Al alloy wire for electric conduction in the embodimentManufacturing methodIs
Zr: 0.10 to 0.50 wt%,
Sc: 0.05-0.50 wt%,
Si: 0.05-0.10 wt%, Fe: 0.05-0.30 wt%, Ti: 0.01-0.10 wt%, B: 0.003-0.02 wt%Containing, or
Zr: 0.10 to 0.50 wt%,
Sc: 0.05-0.50 wt%,
Si: 0.05 to 0.10 wt%, Fe: 0.05 to 0.30 wt%, Ti: 0.01 to 0.10 wt%, B: 0.003 to 0.02 wt%, Be: 0.005 Contains 0.05 wt%And
To the wire150 to 200 ° C for 5 to 10 hoursPrimary heat treatment of35 to 45 hours at 400 to 430 ° CAfter that, the wire is subjected to cold working with a cross-sectional area reduction rate of 50% or more, and then the cold worked material is subjected to cold working.350-400 ° C x 1-10 hoursThe heat treatment is performed.
[0053]
The manufacturing method of the heat-resistant Al alloy wire for electric conduction of this Embodiment is demonstrated.
[0054]
Similar to the second embodiment, the heat-resistant Al alloy wire for electric conduction obtained by the manufacturing method of the first embodiment described above is used.3A recrystallization heat treatment (heat treatment) is performed at 50 to 400 ° C. for 1 to 10 hours to obtain the heat-resistant Al alloy wire for conduction of this embodiment.
[0055]
According to the heat-resistant Al alloy wire for electric conduction of this embodiment, compared with the heat-resistant Al alloy wire for electric conduction of the first embodiment, the heat resistance is further improved without substantially reducing the tensile strength and conductivity. Can be made.
[0056]
【Example】
Example 1
First, Zr: 0.35 wt%, Sc: 0.20 wt%, Si: 0.08 wt%, Fe: 0.13 wt%, Ti: 0.07 wt%, B: 0.005 wt%, the balance being Al and inevitable impurities An Al alloy having the chemical composition is melted.
[0057]
Thereafter, an Al alloy ingot is formed using the Al alloy molten metal, and then the Al alloy ingot is subjected to swage processing to form an Al alloy rough drawn wire having an outer diameter of 12 mm.
[0058]
Next, this Al alloy rough wire was subjected to a heat treatment at 250 ° C. for 50 hours, and then the Al alloy wire after the heat treatment was subjected to a cold working with a cross-sectional area reduction rate of 93%, and a heat resistance for conduction having an outer diameter of 3.2 mm. An Al alloy wire is produced.
(Example 2)
The Al alloy rough wire formed in the same manner as in Example 1 was subjected to a heat treatment at 295 ° C. for 50 hours, and then the Al alloy wire after the heat treatment was subjected to cold working with a cross-sectional area reduction rate of 93% to obtain an outer diameter of 3 A 2 mm conductive heat-resistant Al alloy wire is produced.
(Example 3)
The Al alloy rough wire formed in the same manner as in Example 1 was subjected to a primary heat treatment of 200 ° C. × 7 hours and then a secondary heat treatment of 420 ° C. × 40 hours, and then the cross-sectional area was applied to the Al alloy wire after the heat treatment. Cold working with a reduction rate of 93% is performed to produce a heat-resistant Al alloy wire for conduction having an outer diameter of 3.2 mm.
Example 4
Zr: 0.20 wt%, Sc: 0.20 wt%, Si: 0.08 wt%, Fe: 0.13 wt%, Ti: 0.07 wt%, B: 0.005 wt%, the balance being Al and inevitable impurities A heat-resistant Al alloy wire for conduction having an outer diameter of 3.2 mm is produced in the same manner as in Example 3 except that an Al alloy having a composition is used.
(Example 5)
Zr: 0.35 wt%, Sc: 0.20 wt%, Si: 0.08 wt%, Fe: 0.13 wt%, Ti: 0.07 wt%, B: 0.005 wt%, Be: 0.01 wt%, balance A conductive heat-resistant Al alloy wire having an outer diameter of 3.2 mm is produced in the same manner as in Example 1 except that Al alloy having a chemical composition of Al and inevitable impurities is used.
(Example 6)
A conductive heat-resistant Al alloy wire having an outer diameter of 3.2 mm is produced in the same manner as in Example 5 except that heat treatment at 295 ° C. × 50 hours is performed.
(Example 7)
Primary heat treatment at 200 ° C x 7 hours, then secondary heat treatment at 420 ° C x 40 hours
A conductive heat-resistant Al alloy wire having an outer diameter of 3.2 mm is produced in the same manner as in Example 5 except that it is applied.
(Example 8)
Zr: 0.20 wt%, Sc: 0.20 wt%, Si: 0.08 wt%, Fe: 0.13 wt%, Ti: 0.07 wt%, B: 0.005 wt%, Be: 0.01 wt%, balance A conductive heat-resistant Al alloy wire having an outer diameter of 3.2 mm is produced in the same manner as in Example 7, except that Al alloy having a chemical composition of Al and inevitable impurities is used.
Example 9
The Al alloy rough wire formed in the same manner as in Example 1 was subjected to a primary heat treatment of 200 ° C. × 7 hours and then a secondary heat treatment of 420 ° C. × 40 hours, and then the cross-sectional area was applied to the Al alloy wire after the heat treatment. A cold working with a reduction rate of 93% is performed to form an outer diameter of 3.2 mm, and then a recrystallization heat treatment is performed at 350 ° C. for 4 hours to produce a heat-resistant Al alloy wire for conduction.
(Comparative Example 1)
Except that the Al alloy does not contain Sc, a conductive heat-resistant Al alloy wire having an outer diameter of 3.2 mm is produced in the same manner as in Example 1.
(Comparative Example 2)
A conductive heat-resistant Al alloy wire having an outer diameter of 3.2 mm is manufactured in the same manner as in Example 2 except that the Al alloy does not contain Sc.
(Comparative Example 3)
Except that the Al alloy does not contain Sc, a conductive heat-resistant Al alloy wire having an outer diameter of 3.2 mm is produced in the same manner as in Example 3.
(Comparative Example 4)
Except that the Al alloy does not contain Sc, a conductive heat-resistant Al alloy wire having an outer diameter of 3.2 mm is produced in the same manner as in Example 4.
(Comparative Example 5)
Except that the Al alloy does not contain Sc, a conductive heat-resistant Al alloy wire having an outer diameter of 3.2 mm is produced in the same manner as in Example 5.
(Comparative Example 6)
Except that the Al alloy does not contain Sc, a conductive heat-resistant Al alloy wire having an outer diameter of 3.2 mm is produced in the same manner as in Example 6.
(Comparative Example 7)
Except that the Al alloy does not contain Sc, a conductive heat-resistant Al alloy wire having an outer diameter of 3.2 mm is produced in the same manner as in Example 7.
(Comparative Example 8)
Except that the Al alloy does not contain Sc, a conductive heat-resistant Al alloy wire having an outer diameter of 3.2 mm is produced in the same manner as in Example 8.
(Comparative Example 9)
Except that the Al alloy does not contain Sc, a conductive heat-resistant Al alloy wire having an outer diameter of 3.2 mm is produced in the same manner as in Example 9.
[0059]
Table 1 shows the chemical compositions and heat treatment conditions of the heat-resistant Al alloy wires for conduction in Examples 1 to 9 and Comparative Examples 1 to 9.
[0060]
[Table 1]
Next, the tensile strength (MPa), electrical conductivity (% IACS), and heat resistance (%) were measured about the obtained heat-resistant Al alloy wire for electroconductivity of Examples 1-9 and Comparative Examples 1-9, respectively. The measurement results are shown in Table 2.
[0062]
Here, the heat resistance (%) is obtained by (tensile strength after heating the obtained conductive heat-resistant Al alloy wire at 280 ° C. for 1 hour / tensile strength of the obtained conductive heat-resistant Al alloy wire) × 100. Value.
[0063]
[Table 2]
As shown in Table 2, in the heat-resistant Al alloy wire for conduction of Examples 1 to 9 which is the material of the present invention, the tensile strength of 240 MPa or more, the conductivity of 58% IACS or more and 95 after heat treatment within 50 hours. % Heat resistance and excellent strength, conductivity, and heat resistance. In the conventional aluminum alloy for power transmission lines, there is no material having the above-mentioned characteristics, and the inventors have conducted intensive research and discovery. Moreover, since there is no big difference in an intensity | strength, electroconductivity, and heat resistance when comparing the wire of Examples 1-4 containing Be and the wire of Examples 5-8 which does not contain Be, it is not necessarily expensive. It can be seen that it is not necessary to use neat Be as an Al alloy raw material.
[0065]
On the other hand, the heat-resistant Al alloy wire for conductive use in Comparative Examples 1 to 9 was subjected to the same heat treatment as the heat-resistant Al alloy wire for conductive use in Examples 1 to 9, but Sc was added to the Al alloy. Does not contain. For this reason, in all the wire materials of Comparative Examples 1 to 9, all of the tensile strength, conductivity, and heat resistance were inferior to those of Examples 1 to 9.
[0066]
As mentioned above, it cannot be overemphasized that embodiment of this invention is not limited to embodiment mentioned above, and various things are assumed in addition.
[0067]
【The invention's effect】
In short, according to the present invention, an excellent effect of being able to obtain a heat-resistant Al alloy wire for electric conduction having excellent conductivity, heat resistance and strength as compared with conventional wires can be obtained in a short heat treatment time. .
Claims (8)
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| CN103781926B (en) * | 2011-09-05 | 2016-08-17 | 大电株式会社 | Aluminum base conductive material and employ its electric wire and cable |
| JP5534241B2 (en) * | 2011-11-03 | 2014-06-25 | 日立金属株式会社 | Aluminum alloy wire and manufacturing method thereof |
| EP2736047B1 (en) * | 2012-11-22 | 2017-11-08 | Heraeus Deutschland GmbH & Co. KG | Aluminium alloy wire for bonding applications |
| JP2016035079A (en) * | 2012-12-27 | 2016-03-17 | 大電株式会社 | Aluminum-based conductive material and cable using the same |
| CN105274397A (en) * | 2015-10-23 | 2016-01-27 | 东北大学 | High-strength super-heat-resistant aluminum-alloy conductor and preparation method thereof |
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