JP4022491B2

JP4022491B2 - Aluminum alloy bat

Info

Publication number: JP4022491B2
Application number: JP2003085726A
Authority: JP
Inventors: 学中井; 典史細田; 武比古江藤; 高弘野瀬
Original assignee: Kobe Steel Ltd
Current assignee: Kobe Steel Ltd
Priority date: 2002-03-27
Filing date: 2003-03-26
Publication date: 2007-12-19
Anticipated expiration: 2023-03-26
Also published as: JP2004002983A

Description

【０００１】
【発明の属する技術分野】
本発明は、熱処理型7000系アルミニウム合金押出材からなり、打撃感や耐食性に優れた、アルミニウム合金製野球用バットに関するものである。
【０００２】
【従来の技術】
従来から、ソフトボールや軟式野球、あるいは硬式野球などのアルミニウム合金製野球用バットとしては、熱処理型7000系アルミニウム合金押出材が汎用されている。この7000系アルミニウム合金としては、Al-Zn-Mg-Cu 系のJIS 7050、7075、7055等が使用されている。
これら熱処理型7000系アルミニウム合金押出材からなるバットは、通常、溶解鋳造後のビレットを、均質化熱処理後、熱間押出後、必要に応じて冷間抽伸ならびに焼鈍を繰り返して、所定のサイズの管にした後、バット形状へ加工された後、溶体化処理および焼き入れ後、最終的なバット形状へ冷間矯正された後、人工時効処理 (人工時効硬化処理) して制作される。
【０００３】
そして、これら、熱処理型7000系アルミニウム合金押出材からなるバットは、打球部の構造が単一層の金属部材からなるバットとして、SG規格の強度を満足し、かつ、圧縮の縦弾性率が高いため、打球部の肉厚を薄くし、バット本体の打球部を大きく撓ませることができる点で、打球の反発特性が良好な金属製バットを提供することができる (特許文献１参照) 。また、打球部の構造がアルミニウム合金押出材の単一層からなるため、製造コストが安価な金属製バットを提供することができる。
【０００４】
【特許文献１】
特開平11-267257 号公報
【０００５】
【発明が解決しようとする課題】
しかし、これら優れた特徴を有する熱処理型7000系アルミニウム合金押出材からなるバットも、耐食性に起因する耐久性には、今だ改良の余地があった。即ち塗装されて使用するにせよ、裸で使用するにせよ、バットは必然的に、応力や衝撃が負荷された状態で使用される。このため、熱処理型7000系アルミニウム合金では、特に、Zn、Mgなどの元素含有量が高いことと合わせ、バット表面乃至アルミニウム合金押出材表面が腐食しやすくなる。ここにおいて、問題となるのは、耐SCC 応力特性 (耐応力腐食割れ性) と耐剥離腐食性である。そして、これらの耐蝕性が劣る場合、バットに必要なSG規格を満足する引張強度や伸びなどの引張特性や、打球の反発特性に必要な耐力や縦弾性率などの圧縮特性、更には、損失係数で表現される打撃感も低くなる。
【０００６】
この様な事情に鑑み、本発明は、耐蝕性に優れ、バットに必要な前記引張特性や前記圧縮特性、更には、損失係数で表現される打撃感も優れた、熱処理型7000系アルミニウム合金押出材からなるアルミニウム合金製バットを提供しようとするものである。
【０００７】
【課題を解決するための手段】
この目的を達成するために、本発明アルミニウム合金製バットの第一の要旨は、熱処理型7000系アルミニウム合金押出材からなるバットであって、7000系アルミニウム合金押出材が、Zn:5.7〜8.5%、Mg:1.2〜2.6%、Cu:1.9〜2.6%、Zr:0.08 〜0.15% を含み、かつ、Si: 0.12% 以下、Fe:0.15%以下、Mn:0.30%以下、Cr:0.20%以下、V:0.05% 以下、Ti:0.10%以下とし、残部Alおよび不可避的不純物からなるとともに、この7000系アルミニウム合金押出材が、115 〜145 ℃で12〜48時間の人工時効処理後に、160 〜190 ℃で6 〜12時間の再人工時効処理される2 段階の時効処理を、溶体化処理および焼き入れ後に施されており、引張強度が540MPa以上、伸びが10% 以上の引張特性と、耐力が540MPa以上、縦弾性率が70000MPa以上の圧縮特性とを有し、かつ、耐SCC 応力が180MPa以上、剥離腐食性がEXCOランクでEB以上の耐蝕性を有し、更に、損失係数が周波数700Hz の1 次モードで0.017 以下および周波数3800Hzの3 次モードで0.010 以上である打撃感を有することとする。
【０００８】
更に、この目的を達成するために、本発明アルミニウム合金製バットの第二の要旨は、熱処理型7000系アルミニウム合金押出材からなるバットであって、7000系アルミニウム合金押出材が、Zn:5.7〜8.5%、Mg:1.2〜2.6%、Cu:1.9〜2.6%、Zr:0.08 〜0.15% を含み、かつ、Si: 0.12% 以下、Fe:0.15%以下、Mn:0.30%以下、Cr:0.20%以下、V:0.05% 以下、Ti:0.10%以下とし、残部Alおよび不可避的不純物からなるとともに、この7000系アルミニウム合金押出材が、115 〜145 ℃で12〜48時間の人工時効処理後に、170 〜190 ℃で1 〜4 時間の復元処理され、更に115 〜145 ℃で12〜48時間の再人工時効処理される3 段階の時効処理を、溶体化処理および焼き入れ後に施されており、引張強度が540MPa以上、伸びが10% 以上の引張特性と、耐力が540MPa以上、縦弾性率が70000MPa以上の圧縮特性とを有し、かつ、耐SCC 応力が180MPa以上、剥離腐食性がEXCOランクでEB以上の耐蝕性を有し、更に、損失係数が周波数700Hz の1 次モードで0.017 以下および周波数3800Hzの3 次モードで0.010 以上である打撃感を有することとする。
【０００９】
特定組成の熱処理型7000系アルミニウム合金押出材を溶体化処理および焼き入れ後に、上記2 段階あるいは3 段階の特定の人工時効処理を施すことによって、この人工時効処理後のミクロ組織として、結晶粒界上のη相の間隔を大きくでき、結晶粒内のη' 相のサイズを微細化できる。この結果、耐蝕性に優れ、バットに必要な上記引張特性や上記圧縮特性、更には、上記損失係数で表現される打撃感も優れた、熱処理型7000系アルミニウム合金押出材からなるバットを提供することができる。なお、本発明のアルミニウム合金製バットの上記特性の規定は、全て、上記人工時効処理後について規定している。
【００１０】
上記ミクロ組織について、まず、結晶粒界上のη相はアノディックであり溶出し易い。このため、η相の最小間隔が小さい場合、η相が連続化して、バットなどの腐食環境下では、特に連続して溶出し易くなる。この結果、耐SCC 応力および耐剥離腐食性が著しく低くなる。
【００１１】
また、結晶粒内のη' 相のサイズが粗大化した場合、粒内の強度に寄与するGPゾーンの割合が少なくなり、強度が著しく低くなる。このため、バットに必要な上記引張特性や上記圧縮特性、更には、上記損失係数で表現される打撃感も得られない。
【００１２】
このため、熱処理型7000系アルミニウム合金押出材を、バットに成形加工後かまたはバットに成形加工される前に溶体化処理および焼入れ後、上記2 段階あるいは3 段階の特定の人工時効処理を施す。即ち、これら人工時効処理における、時効処理、復元処理および再時効処理の各条件は、結晶粒界上のη相の間隔、結晶粒内のη相のサイズを制御して、上記した、バットに必要な耐蝕性、引張特性や圧縮特性、更には、上記損失係数で表現される打撃感に優れたものとするための最適な条件を設定している。
【００１３】
【発明の実施の形態】
まず、バット素材である押出材の押出方法は、常法にて可であり、上記特定組成の7000系アルミニウム合金を溶解鋳造にてビレット等の鋳塊にした後、均質化熱処理し、熱間押出を行う。その後、通常は、溶体化および水焼入れ処理を行った後、必要に応じてストレッチ等で引張加工し、目的に応じた熱処理 (焼鈍など) が行われる。その後、これら押出材はバットに成形加工され、本発明の熱処理 (人工時効処理) が行われる。そして、その後製品バットに仕上げられる。
【００１４】
熱処理型7000系アルミニウム合金は析出硬化型の合金であり、溶体化処理および焼入れ後、例えば通常の120 ℃で24hrなどの条件で人工時効処理すると、粒内にGPゾーンが微細に析出するため、強度は高くなる。しかし、一方で、粒界上にはη相が連続的に析出するようになる。このη相はアノディックであり、バットなどの腐食環境下では特に溶出し易い。このため、前記通常の条件で人工時効処理すると、耐SCC 応力および耐層状腐食特性が低くなる。例えば、ASTM-G47に従った耐SCC 試験において、耐SCC 応力（ST方向）は48N /mm²以下と極めて低い。また、ASTM-G34に従った剥離試験において、耐剥離腐食性はランクEC〜EDと極めて低い。
【００１５】
これに対し、本発明の第一の要旨のように、上記特定組成の熱処理型7000系アルミニウム合金押出材を、115 〜145 ℃で12〜48時間人工時効処理後、更に160 〜190 ℃で6 〜12時間の過時効条件側での再人工時効処理する2 段階(T76) の熱処理法では、粒内のGPゾーンの割合を出来るだけ増やすことで高い強度を得ることができる。また、粒内のη' 相の割合を増やすことと、粒界上のη相の間隔を拡げることで高耐食性を実現できる。即ち、溶体化および焼入れ処理後の最初の時効処理で生じた粒内のGPゾーンは、復元処理で一部復元するが、高耐食性に寄与するη' 相の析出を促進する。一方、粒界上では、時効処理で生じたη相は、復元処理で粗大化し、間隔が広がるために不連続化し、耐SCC 性および剥離腐食特性等の耐食性は高くなる。
【００１６】
また、本発明の第二の要旨のように、上記特定組成の熱処理型7000系アルミニウム合金押出材を、溶体化処理および焼き入れ後に、115 〜145 ℃で12〜48時間の人工時効処理後、170 〜190 ℃で1 〜4 時間の復元処理し、更に115 〜145 ℃で12〜48時間の再人工時効処理する3 段階の熱処理法(T77) によって、粒内ではGPゾーンの割合が減少し、η' 相の割合が高くなり、またη' 相のサイズも大きくなる。GPゾーンの割合が低くなり、η' 相の割合が高くなること、またη' 相のサイズが大きくなることで、強度は前記通常の人工時効処理に比して低下する。しかしながら、粒界上のη相は粗大化することによって、間隔が広がるために不連続化する。このため、η相は溶出しにくくなり、粒界腐食感受性は低くなり、さらにまた、耐SCC 性ならびに剥離腐食性は高くなる。なお、第1 段目と第2 段目との間の加熱速度、ならびに第2 段目と第3 段目との間の冷却速度が低速であると、実質的に第2 段目の熱処理時間が長時間となる。従って、第1 段目と第2 段目との間の加熱速度、また第2 段目と第3 段目との間の冷却速度は、50℃/hr 以上であることが望ましい。
【００１７】
前記復元処理においては、前記範囲を外れて、温度が高すぎたり処理時間が長すぎると、GPゾーンの復元が進行するとともに、粗大なη' 相およびη相が析出してしまい、その後の再時効処理を行っても高い強度を得ることは困難である。また、バットに必要な上記引張特性や上記圧縮特性、更には、上記損失係数で表現される打撃感を得ることは困難である。一方、前記範囲を外れて、温度が低すぎたり処理時間が短すぎると粒界上にはη相が連続的に析出するようになり、耐SCC 応力および耐層状腐食特性等の耐食性が低下する。
【００１８】
また、各人工時効処理においても、温度が高すぎる、あるいは時間が長すぎるなどで、粒内に粗大なη' 相およびη相が析出する状態にまで時効析出を進行させてはならない。そのような状態まで時効析出が進行すると、復元処理時に復元するGPゾーンの量が減るため、再時効処理時に最終的に析出するGPゾーンが減り、十分な強度は得られない。逆に、温度が低すぎる、あるいは時間が短すぎるなどで、時効処理が不十分でGPゾーンが僅かしか析出しない場合、この状態で次の復元処理を行っても、上述したように復元処理時に復元するGPゾーンの量が減るため、再時効処理時に最終的に析出するGPゾーンが減る。このため十分な強度は得られない。このように時効処理時には、復元処理時に復元するGPゾーンを十分に析出させる必要があり、前記温度と時間の規定した条件範囲内とする。
【００１９】
最初の時効処理温度が高いと短時間で、また時間が長すぎても、η相および粗大なη相が析出しやすくなり、その分GPゾーンが減る。このためバットに必要な上記引張特性や上記圧縮特性、更には、上記損失係数で表現される打撃感は得られない。一方、各時効処理温度が低くても時間が短くても、十分なGPゾーンが析出しない。このため、最初の時効処理は上記特定条件範囲とする。なお、第1 段目と第2 段目との間の加熱速度が、また第2 段目と第3 段目との間の冷却速度が低速であると、実質的に第2 段目の熱処理が長時間となる。従って、第1 段目と第2 段目との間の加熱速度、ならびに、第2 段目と第3 段目との間の冷却速度は50℃/hr 以上であることが望ましい。
【００２０】
また、各再時効処理においても、粒内にη相および粗大なη相が析出する状態にまで時効析出を進行させてはならず、時効処理温度が高くて、また時間が長すぎて、そのような状態にまで時効析出が進行すると、上記引張特性や上記圧縮特性、更には、上記損失係数で表現される打撃感強度は得られない。また、逆に各時効処理温度が低くても時間が短くても、時効処理が不十分となり、GPゾーンが僅かにしか析出しない。この場合も、上記引張特性や上記圧縮特性、更には、上記損失係数で表現される打撃感強度は得られない。このため、各再時効処理においても、上記特定条件範囲とする。
【００２１】
これら溶体化や時効処理などに使用される熱処理炉はバッチ炉、連続焼鈍炉、溶融塩浴炉のいずれを用いてもよいが、結晶粒径を微細にするには５℃／分以上の昇温速度で加熱することがなお望ましい。また焼入れは水浸漬、水噴射、空気噴射のいずれを用いてもよい。更に、溶体化処理および焼入れ後に行われる時効処理、復元処理および再時効処理はバッチ炉、連続焼鈍炉、熱風ファン、オイルバス、温湯浴槽等のいずれを用いてもよい。
【００２２】
アルミニウム合金製バットの結晶粒は、等軸状の結晶粒ではなく、熱間押出材とすることで、押出方向に長く伸長した繊維状結晶粒組織とすることができ、バットに必要な上記引張特性や上記圧縮特性、更には、上記損失係数で表現される打撃感を基本的に保証できる。ただ、バット (押出材) のミクロ結晶粒組織を押出方向に長く伸長した繊維状結晶粒組織とミクロ組織としても、バット (押出材) 表面には、押出に際して、必然的に等軸状の結晶粒である再結晶層が生じる。そして、この再結晶層の厚さが500 μm を越えた場合、耐SCC 応力および耐層状腐食特性が著しく低くなり、耐蝕性や、ひいてはバットに必要な上記引張特性や上記圧縮特性、更には、上記損失係数で表現される打撃感も確保できない可能性がある。このため、バット (押出材) 表面の再結晶層の厚さは500 μm 以下とすることが好ましい。なお、前記繊維状結晶粒か等軸状結晶粒かの判別や、バット (押出材) 表面の再結晶層の厚さ測定は、バット (押出材) 組織の光学顕微鏡による観察によって、簡便にできる。
【００２３】
次に、本発明バット (押出材) 用アルミニウム合金組成は、上記人工時効処理によって、上記ミクロ組織となって、上記引張特性と圧縮特性、耐蝕性とを各々有し、更に、上記打撃感を得られるものとする。このための7000系アルミニウム合金押出材の組成は、Zn:5.7〜8.5%、Mg:1.2〜2.6%、Cu:1.9〜2.6%、Zr:0.08 〜0.15% を主要元素として含み、かつ、Si: 0.12% 以下、Fe:0.15%以下、Mn:0.30%以下、Cr:0.20%以下、V:0.05% 以下、Ti:0.10%以下に各々規制した、残部Alおよび不可避的不純物からなる組成とする。なお、本発明における元素量の% 表示は全て質量% である。
【００２４】
Zn、Mg、Cu、Zrの含有量が、各々上記含有量範囲の下限未満では、上記人工時効処理によっても、アルミニウム合金製バットとしての上記引張特性と圧縮特性、更に上記打撃感が各々得られない。また、上記含有量範囲の上限を越えて各々含有した場合アルミニウム合金製バットとしての上記耐蝕性が得られない。
そして、Si、Fe、Mn、Cr、V 、Tiを、上記各含有量上限を越えて各々含有した場合、アルミニウム合金製バットとしての上記耐蝕性が得られない。また、上記引張特性や圧縮特性なども低下する。
【００２５】
【実施例】
次に、本発明の実施例を説明する。表１に示す組成を含み残部不純物とアルミニウムとからなる7000系アルミニウム合金を、溶湯中水素濃度0.02ml/100mlアルミニウムまで脱ガス後，溶解鋳造しφ400 mmの鋳塊ビレットとした。次に450 ℃で24hrの均熱処理を施した後，φ380mm まで面削した後、430 ℃に再加熱し、外径85mmφ×内径75mmφ、肉厚10mmt の断面形状に押し出した。その後、400 ℃×2hr の焼鈍で軟質材とした後、冷間抽伸で外径73.8mmφ×内径67mmφにし、さらに400 ℃×2hr の焼鈍で軟質材とした。
【００２６】
その後、打球部の肉厚が3mm のバットの形状に加工した。溶体化処理は、硝石炉で450 ℃×40分間保持した後、水焼き入れした。焼き入れによる歪みを冷間矯正で修正した後、表2 中の人工時効条件（１段階〜３段階）の熱処理を行った。表2 の合金番号は表1 の合金番号である。ここで、本発明の第一の要旨の115 〜145 ℃で12〜48時間人工時効処理後、更に160 〜190 ℃で6 〜12時間の過時効条件側での再人工時効処理する2 段階の熱処理法は発明T76 と言う。また、本発明の第二の要旨のように、115 〜145 ℃で12〜48時間の人工時効処理後、170 〜190 ℃で1 〜4 時間の復元処理し、更に115 〜145 ℃で12〜48時間の再人工時効処理する3 段階の熱処理法は発明T77 と言う。また、従来のT6およびT77 の熱処理法は従来T6および従来T77 として、これらの調質種別を各々表2 に示す。なお、焼き入れ後、人工時効までの室温での経過時間は12〜72時間である。なお、これらの複合人工時効処理時の加熱および冷却速度は、試料の実体で100 ℃/hr で行った。
【００２７】
これらの複合人工時効処理後のアルミニウム合金製バットの、引張強度と伸びの引張特性、圧縮耐力と縦弾性率の圧縮特性、耐SCC 応力と剥離腐食性の耐蝕性、損失係数による打撃感を調査、測定した。これらの結果を表3 に示す。なお、これらの複合人工時効処理後のバット( 押出材) 表面の再結晶層の厚さは、全て500 μm 以下であった。
【００２８】
0.2%耐力(MPa) と伸び(%) の引張特性は、アルミニウム合金製バット打撃部（外径67mm、肉厚3.0 mm）より、長さ150mm （バット長手方向）のJIS 12B 試験片を採取し、JIS-Z2241 の引張試験法に従い、引張特性を測定した。なお、引張試験片の平行部中央部はバット先端（打撃部）から80mmの位置となる。
【００２９】
圧縮耐力と縦弾性率の圧縮特性は、アルミニウム合金製バット打撃部（外径67mm、肉厚3.0 mm）より、長さ15mm（バット長手方向）、幅8mm （バット円周方向）、厚さ３mm（肉厚）の試料を採取した後、長さ15mm（バット長手方向），幅８mm（バット円周方向），厚2.5mm （肉厚）の直方体の試料に加工した。そして、この試料の15mm×8 mmの中央部両面に、歪ゲージを接着し、8mm ×2.5mm の面に円周方向に圧縮力を付加し、歪および応力値より縦弾性率（圧縮）ならびに耐力（圧縮）を測定した。なお、測定点は、バット先端（打撃部）から80mmの位置である。
【００３０】
耐SCC 応力の測定は、クロム酸促進法による耐SCC(応力腐食割れ) 試験によって、円周方向(LT)に引っ張り応力を付加して行った。即ち、アルミニウム合金製バット打撃部（外径67mm、肉厚3.0mm ）より，幅15mmのC リング状の試験片を採取し、所定の引張応力値を付加した後、直ちに、沸騰したSCC 試験溶液に360 分浸漬し、割れの発生しない試料を○、割れの発生した試料を×として評価した。なお、応力の付加は、ボルトとナットを締めますことで、試料外表面に引張応力を発生させ、応力値はこの外表面に接着した歪ゲージを用いて、各試料毎に測定した。また、SCC 試験溶液（1 リットル当たり）、食塩3g、2 クロム酸カリウム30g 、酸化クロム36g に蒸留水に加えることで作製した。C リングは、バット先端（打球部）から50〜110mm の範囲で採取した。
【００３１】
剥離腐食性試験は、アルミニウム合金製バット打撃部（外径67mm、肉厚3.0mm ）より、長さ60mm（バット長手方向）、幅30mm（バット円周方向）、厚３mm（肉厚）の試料を採取し、ASTM-G34-90 剥離腐食性試験によるEXCOテストを実施し、試験完了後、ASTM-G34-90 に定める腐食程度の基準（最も優れるＮから順に、Ｐ、ＥＡ、ＥＢ、ＥＣ、ＥＤ）を用いて、各試料を評価した。EC、ED以下が特に剥離腐食性が劣ると評価される。なお、試料は、バット先端（打球部）から50〜110mm の範囲で採取した。
【００３２】
打撃感は、周波数約700Hz の1 次モードでの損失係数が大きいことと、周波数約3800Hzの3 次モードでの損失係数が小さいことで評価される。アルミニウム合金製バット打撃部（外径67mm、肉厚3.0mm ）より、長さ124mm （バット長手方向）、幅12mm（バット円周方向）、厚3mm （肉厚）の試料を採取し、室温大気中にて、中央加振法で、周波数5000Hzまでの伝達関数を測定し、これより、周波数約700Hz の1 次モード、周波数約3800Hzの3 次モードでの損失係数を測定、評価した。なお、中央加振法で試料を保持する位置は、試料中心部となり、この位置は、バット先端（打撃部）から80mmの位置である。
【００３３】
本発明組成を満足する表1 の発明例1 〜8 までのアルミニウム合金製バットは表2 の通り本発明条件で発明T76 または発明T77 の複合人工時効処理されており、表3 の通り、引張強度が540MPa以上、伸びが10% 以上の引張特性と、耐力が540MPa以上、縦弾性率が70000MPa以上の圧縮特性とを有し、かつ、耐SCC 応力が180MPa以上、剥離腐食性がEXCOランクでEB以上の耐蝕性を有し、更に、損失係数が周波数700Hz の1 次モードで0.017 以下および周波数3800Hzの3 次モードで0.010 以上である打撃感を有する。
【００３４】
一方、比較例において、表1 の通り、Mn、Zrの含有量が高すぎる比較例9 、Si、Feの含有量が高すぎる比較例10、Znの含有量が高すぎる比較例12、Mgの含有量が高すぎる比較例14は、各々表2 の通り本発明条件での複合人工時効処理T77 あるいはT76 が施されているにも関わらず、表3 の通り、各々アルミニウム合金製バットとしての耐SCC 応力や剥離腐食性が、発明例に比して著しく劣る。また、各々上記引張特性と圧縮特性、打撃感なども低い。
【００３５】
また、Zrの含有量が低すぎる比較例11、Znの含有量が低過ぎる比較例13、Mgの含有量が低過ぎる比較例15、Cuの含有量が低過ぎる比較例16は、各々表2 の通り本発明条件での複合人工時効処理されているにも関わらず、表3 の通り、各々上記引張特性と圧縮特性、打撃感なども発明例に比して著しく低い。更に、本発明条件から外れる従来のT77 の人工時効処理されている比較例17は、本発明範囲内の合金8 を用いているにもかかわらず、T77 における復元処理温度が高すぎ、アルミニウム合金製バットとしての耐SCC 応力や剥離腐食性が発明例に比して著しく劣る。また、上記引張特性と圧縮特性、打撃感なども発明例に比して劣る。
【００３６】
したがって、以上の結果から、本発明要件の臨界的な意義が分かる。
【００３７】
【表１】

【００３８】
【表２】

【００３９】
【表３】

【００４０】
【発明の効果】
本発明によれば、耐蝕性に優れ、バットに必要な前記引張特性や前記圧縮特性、更には、損失係数で表現される打撃感も優れた、熱処理型7000系アルミニウム合金押出材からなるアルミニウム合金製バットを提供することができる。したがって、熱処理型7000系アルミニウム合金押出材の用途の拡大を図ることができる点で、多大な工業的な価値を有するものである。[0001]
BACKGROUND OF THE INVENTION
The present invention relates to an aluminum alloy baseball bat made of a heat treatment type 7000 series aluminum alloy extruded material and excellent in hit feeling and corrosion resistance.
[0002]
[Prior art]
Conventionally, heat treatment type 7000 series aluminum alloy extruded materials have been widely used as baseball bats made of aluminum alloy such as softball, soft baseball, and hard baseball. As this 7000 series aluminum alloy, Al-Zn-Mg-Cu series JIS 7050, 7075, 7055, etc. are used.
These heat treatment type 7000 series aluminum alloy extrudate batts usually have a predetermined size of billet after melting and casting, after homogenization heat treatment, after hot extrusion, and repeated cold drawing and annealing as necessary. After being formed into a tube, processed into a bat shape, subjected to solution treatment and quenching, cold-corrected to a final bat shape, and then produced by artificial aging treatment (artificial age hardening treatment).
[0003]
And these bats made of heat treated 7000 series aluminum alloy extruded material satisfy the SG standard strength and have a high compressive longitudinal elastic modulus as the bat made of a single layer metal member with a hitting ball structure. In addition, it is possible to provide a metal bat that has good rebound characteristics of the hit ball in that the hit ball portion can be made thin and the hit ball portion of the bat body can be greatly deflected (see Patent Document 1). Moreover, since the structure of the hitting ball portion is made of a single layer of an aluminum alloy extruded material, a metal bat can be provided at a low manufacturing cost.
[0004]
[Patent Document 1]
Japanese Patent Laid-Open No. 11-267257 [0005]
[Problems to be solved by the invention]
However, bats made of heat treated 7000 series aluminum alloy extruded material having these excellent characteristics still have room for improvement in durability due to corrosion resistance. That is, whether it is painted or used naked, the bat is inevitably used in a state where stress or impact is applied. For this reason, in the heat treatment type 7000 series aluminum alloy, especially the high content of elements such as Zn and Mg, the bat surface or the extruded surface of the aluminum alloy tends to corrode. The problems here are SCC stress resistance (stress corrosion cracking resistance) and exfoliation corrosion resistance. And if these corrosion resistances are inferior, tensile properties such as tensile strength and elongation satisfying the SG standard required for bats, compressive properties such as proof stress and longitudinal elastic modulus required for ball rebound characteristics, and loss The hit feeling expressed by the coefficient is also low.
[0006]
In view of such circumstances, the present invention is excellent in the corrosion resistance, the tensile properties and the compression properties necessary for the bat, and also has a good feeling of impact expressed by a loss factor. An aluminum alloy bat made of a material is to be provided.
[0007]
[Means for Solving the Problems]
In order to achieve this object, the first gist of the aluminum alloy bat of the present invention is a bat made of heat-treatable 7000 series aluminum alloy extruded material, and the 7000 series aluminum alloy extruded material contains Zn: 5.7 to 8.5%. Mg: 1.2-2.6%, Cu: 1.9-2.6%, Zr: 0.08-0.15%, and Si: 0.12% or less, Fe: 0.15% or less, Mn: 0.30% or less, Cr: 0.20% or less, V: 0.05% or less, Ti: 0.10% or less, consisting of the balance Al and inevitable impurities, and this 7000 series aluminum alloy extruded material is 160-190 after artificial aging treatment at 115-145 ° C. for 12-48 hours Two-stage aging treatment, which is re-artificial aging treatment for 6-12 hours at ℃, is applied after solution treatment and quenching, tensile strength of 540 MPa or more, elongation of 10% or more, and yield strength It has compression characteristics of 540MPa or more, longitudinal modulus of elasticity of 70000MPa or more, SCC stress resistance of 180MPa or more, exfoliation corrosion resistance is EB in EXCO rank Having corrosion resistance above, further, the loss factor is to have a striking feeling is 0.010 or more third mode of 0.017 or less and the frequency 3800Hz in the primary mode frequency 700 Hz.
[0008]
Furthermore, in order to achieve this object, the second gist of the aluminum alloy bat of the present invention is a bat made of a heat treatment type 7000 series aluminum alloy extruded material, wherein the 7000 series aluminum alloy extruded material has Zn: 5.7 to 8.5%, Mg: 1.2-2.6%, Cu: 1.9-2.6%, Zr: 0.08-0.15%, Si: 0.12% or less, Fe: 0.15% or less, Mn: 0.30% or less, Cr: 0.20% In the following, V: 0.05% or less, Ti: 0.10% or less, and the balance Al and inevitable impurities, and this extruded 7000 series aluminum alloy is 170-145 ° C. after artificial aging treatment for 12 to 48 hours, 170 Three-stage aging treatment is applied after solution treatment and quenching, which are re-treated for 1 to 4 hours at ~ 190 ° C and re-artificial aging treatment at 115 to 145 ° C for 12 to 48 hours. It has a tensile property with a strength of 540 MPa or more, an elongation of 10% or more, a compressive property with a yield strength of 540 MPa or more, and a longitudinal elastic modulus of 70000 MPa or more, and SCC stress is 180MPa or more, exfoliation corrosion resistance is EXCO rank and EB or more corrosion resistance, and loss coefficient is 0.017 or less in the primary mode with frequency 700Hz and 0.010 or more in the tertiary mode with frequency 3800Hz It has a feeling.
[0009]
After the solution heat treatment type 7000 series aluminum alloy extruded material with a specific composition is subjected to solution treatment and quenching, the above-mentioned two-stage or three-stage specific artificial aging treatment is performed, and as a microstructure after this artificial aging treatment, the grain boundary The interval between the upper η phases can be increased, and the size of the η ′ phase in the crystal grains can be reduced. As a result, there is provided a bat made of a heat treatment type 7000 series aluminum alloy extrudate that has excellent corrosion resistance, excellent tensile properties and compressive properties necessary for the bat, and excellent impact feeling expressed by the loss factor. be able to. The above-mentioned characteristics of the aluminum alloy bat of the present invention are all defined after the artificial aging treatment.
[0010]
Regarding the above microstructure, first, the η phase on the crystal grain boundary is anodic and easily eluted. For this reason, when the minimum interval of the η phase is small, the η phase becomes continuous, and it becomes easy to elute continuously particularly in a corrosive environment such as a vat. As a result, the SCC stress resistance and peel corrosion resistance are significantly reduced.
[0011]
Further, when the size of the η ′ phase in the crystal grains is coarsened, the ratio of GP zones contributing to the strength in the grains is reduced, and the strength is remarkably lowered. For this reason, the above-mentioned tensile characteristics and compression characteristics required for the bat, and also the hit feeling expressed by the loss factor cannot be obtained.
[0012]
For this reason, the heat treatment type 7000 series aluminum alloy extruded material is subjected to the above-described two-stage or three-stage specific artificial aging treatment after the solution treatment and quenching after being molded into the bat or before being molded into the bat. That is, in these artificial aging treatments, the aging treatment, restoration treatment, and reaging treatment conditions are controlled by controlling the interval between η phases on the grain boundaries and the size of the η phases in the crystal grains. Optimum conditions are set in order to achieve the necessary corrosion resistance, tensile properties, compression properties, and the impact feeling expressed by the loss factor.
[0013]
DETAILED DESCRIPTION OF THE INVENTION
First, the extrusion method of the extruded material, which is a bat material, can be performed by a conventional method. After the 7000 series aluminum alloy having the above specific composition is made into an ingot such as a billet by melt casting, it is subjected to a homogenization heat treatment and hot. Extrude. Thereafter, after solution treatment and water quenching treatment are usually performed, stretching is performed by stretching or the like as necessary, and heat treatment (annealing or the like) according to the purpose is performed. Thereafter, these extruded materials are molded into bats and subjected to the heat treatment (artificial aging treatment) of the present invention. Then, it is finished into a product bat.
[0014]
Heat treatment type 7000 series aluminum alloy is a precipitation hardening type alloy, and after solution treatment and quenching, when artificial aging treatment is performed under conditions such as normal 120 ° C. for 24 hours, the GP zone precipitates finely in the grains. Strength increases. However, on the other hand, the η phase is continuously precipitated on the grain boundaries. This η phase is anodic and is particularly easily eluted in a corrosive environment such as a bat. For this reason, when the artificial aging treatment is performed under the normal conditions, the SCC stress resistance and the layered corrosion resistance are lowered. For example, in the SCC resistance test according to ASTM-G47, the SCC stress resistance (ST direction) is extremely low, 48 N / mm ² or less. Further, in the peel test according to ASTM-G34, the peel corrosion resistance is extremely low as rank EC to ED.
[0015]
On the other hand, as in the first aspect of the present invention, the heat treatment type 7000 series aluminum alloy extruded material having the above specific composition was subjected to artificial aging treatment at 115 to 145 ° C. for 12 to 48 hours, and further at 160 to 190 ° C. In the two-step (T76) heat treatment method in which re-artificial aging treatment is performed on the overaging condition side for ˜12 hours, high strength can be obtained by increasing the proportion of GP zones in the grains as much as possible. Moreover, high corrosion resistance is realizable by increasing the ratio of the (eta) 'phase in a grain, and expanding the space | interval of the (eta) phase on a grain boundary. That is, the intra-granular GP zone generated by the first aging treatment after the solution treatment and quenching treatment is partially restored by the restoration treatment, but promotes the precipitation of the η ′ phase that contributes to high corrosion resistance. On the other hand, on the grain boundary, the η phase generated by the aging treatment is coarsened by the restoration treatment and becomes discontinuous because the interval is widened, and the corrosion resistance such as SCC resistance and exfoliation corrosion characteristics becomes high.
[0016]
Further, as in the second aspect of the present invention, the heat treatment type 7000 series aluminum alloy extruded material having the above specific composition is subjected to solution treatment and quenching, and after artificial aging treatment at 115 to 145 ° C. for 12 to 48 hours, A three-stage heat treatment method (T77) in which restoration is performed at 170 to 190 ° C for 1 to 4 hours and then re-artificial aging treatment at 115 to 145 ° C for 12 to 48 hours reduces the percentage of GP zones in the grains. , The proportion of the η ′ phase is increased, and the size of the η ′ phase is also increased. The strength decreases as compared with the normal artificial aging treatment because the GP zone ratio decreases, the η ′ phase ratio increases, and the η ′ phase size increases. However, the η phase on the grain boundaries becomes discontinuous due to coarsening due to widening of the interval. For this reason, the η phase is difficult to elute, the intergranular corrosion susceptibility is low, and the SCC resistance and exfoliation corrosion resistance are also high. If the heating rate between the first stage and the second stage and the cooling rate between the second stage and the third stage are low, the heat treatment time of the second stage is substantially reduced. Becomes a long time. Accordingly, it is desirable that the heating rate between the first stage and the second stage and the cooling rate between the second stage and the third stage be 50 ° C./hr or more.
[0017]
In the restoration process, when the temperature is out of the range and the temperature is too high or the treatment time is too long, the restoration of the GP zone proceeds, and coarse η ′ phase and η phase are precipitated, and the subsequent re-treatment. It is difficult to obtain high strength even after aging treatment. In addition, it is difficult to obtain the feeling of impact expressed by the above-described tensile characteristics and compression characteristics required for the bat, and further, the loss factor. On the other hand, if the temperature is out of the range and the temperature is too low or the treatment time is too short, the η phase will continuously precipitate on the grain boundaries, and the corrosion resistance such as SCC stress resistance and lamellar corrosion resistance will decrease. .
[0018]
Also, in each artificial aging treatment, aging precipitation must not proceed to a state where coarse η ′ phase and η phase are precipitated in the grains due to the temperature being too high or the time being too long. When aging precipitation progresses to such a state, the amount of GP zone restored at the time of restoration treatment decreases, so that the GP zone that finally precipitates at the time of reaging treatment decreases, and sufficient strength cannot be obtained. On the other hand, if the aging treatment is insufficient and the GP zone precipitates only slightly because the temperature is too low or the time is too short, even if the next restoration process is performed in this state, Since the amount of GP zones to be restored is reduced, the number of GP zones that eventually precipitate during re-aging treatment is reduced. For this reason, sufficient strength cannot be obtained. Thus, at the time of aging treatment, it is necessary to sufficiently precipitate the GP zone to be restored at the time of restoration treatment, and the temperature and time are within the specified condition range.
[0019]
If the initial aging temperature is high, the η phase and the coarse η phase are likely to precipitate in a short time and if the time is too long, and the GP zone is reduced accordingly. For this reason, it is not possible to obtain the feeling of impact expressed by the above-mentioned tensile characteristics and compression characteristics necessary for the bat, and furthermore, the above-mentioned loss factor. On the other hand, even if the aging treatment temperature is low or the time is short, a sufficient GP zone does not precipitate. For this reason, the first aging treatment is within the specific condition range. If the heating rate between the first stage and the second stage is low, and the cooling rate between the second stage and the third stage is low, the second stage heat treatment is substantially performed. Becomes a long time. Therefore, it is desirable that the heating rate between the first stage and the second stage and the cooling rate between the second stage and the third stage be 50 ° C./hr or more.
[0020]
Also, in each re-aging treatment, the aging precipitation must not proceed to a state where the η phase and coarse η phase precipitate in the grains, the aging treatment temperature is high, and the time is too long. When aging precipitation progresses to such a state, the tensile properties and the compression properties as well as the impact strength expressed by the loss factor cannot be obtained. Conversely, even if the aging treatment temperature is low or the time is short, the aging treatment is insufficient and the GP zone is only slightly precipitated. In this case as well, the impact strength expressed by the tensile characteristics, the compression characteristics, and the loss factor cannot be obtained. For this reason, it is set as the specific condition range in each re-aging process.
[0021]
The batch heat treatment furnace, continuous annealing furnace, or molten salt bath furnace may be used as the heat treatment furnace used for solution treatment or aging treatment. To increase the crystal grain size, the temperature is increased by 5 ° C./min or more. It is still desirable to heat at a temperature rate. Moreover, quenching may use any of water immersion, water injection, and air injection. Furthermore, any of a batch furnace, a continuous annealing furnace, a hot air fan, an oil bath, a hot water bath, etc. may be used for the aging treatment, the restoration treatment, and the reaging treatment performed after the solution treatment and quenching.
[0022]
The crystal grain of the aluminum alloy bat is not an equiaxed crystal grain, but can be made into a fibrous crystal grain structure elongated in the extrusion direction by using a hot extruded material. The impact feeling expressed by the characteristics, the compression characteristics, and the loss factor can be basically guaranteed. However, even if the microcrystalline structure and microstructure of the bat (extruded material) are elongated in the direction of extrusion, the surface of the bat (extruded material) inevitably has equiaxed crystals. A recrystallized layer which is a grain is formed. When the thickness of the recrystallized layer exceeds 500 μm, the SCC stress and the lamellar corrosion resistance are remarkably lowered, and the corrosion resistance and, as a result, the tensile and compression characteristics required for the bat, There is a possibility that the hit feeling expressed by the above loss factor cannot be secured. Therefore, the thickness of the recrystallized layer on the surface of the bat (extruded material) is preferably 500 μm or less. The discrimination between the fibrous crystal grains and the equiaxed crystal grains and the measurement of the thickness of the recrystallized layer on the surface of the bat (extruded material) can be easily performed by observing the structure of the bat (extruded material) with an optical microscope. .
[0023]
Next, the aluminum alloy composition for the bat (extruded material) of the present invention becomes the microstructure by the artificial aging treatment, has the tensile properties, the compression properties, and the corrosion resistance, respectively, and further has the impact feeling. Shall be obtained. The composition of the 7000 series aluminum alloy extruded material for this purpose includes Zn: 5.7 to 8.5%, Mg: 1.2 to 2.6%, Cu: 1.9 to 2.6%, Zr: 0.08 to 0.15% as main elements, and Si: The composition is composed of the balance Al and inevitable impurities, which are respectively controlled to 0.12% or less, Fe: 0.15% or less, Mn: 0.30% or less, Cr: 0.20% or less, V: 0.05% or less, and Ti: 0.10% or less. In the present invention, the% display of the element amount is all mass%.
[0024]
When the contents of Zn, Mg, Cu, and Zr are less than the lower limit of each of the above content ranges, the above-described tensile and compression characteristics as an aluminum alloy bat can be obtained by the artificial aging treatment, and the impact feeling can be obtained. Absent. Further, when each content exceeds the upper limit of the content range, the corrosion resistance as an aluminum alloy bat cannot be obtained.
When Si, Fe, Mn, Cr, V, and Ti are contained in excess of the above respective content upper limits, the above corrosion resistance as an aluminum alloy bat cannot be obtained. In addition, the tensile characteristics and compression characteristics are also deteriorated.
[0025]
【Example】
Next, examples of the present invention will be described. A 7000 series aluminum alloy containing the composition shown in Table 1 and consisting of the remaining impurities and aluminum was degassed to a hydrogen concentration of 0.02 ml / 100 ml aluminum in the molten metal, and then melt cast to obtain an ingot billet of φ400 mm. Next, it was soaked at 450 ° C for 24 hours, then chamfered to φ380mm, reheated to 430 ° C, and extruded into a cross-sectional shape with an outer diameter of 85mmφ x inner diameter of 75mmφ and a wall thickness of 10mmt. After that, a soft material was obtained by annealing at 400 ° C. × 2 hr, and then cold drawing to an outer diameter of 73.8 mmφ × inner diameter of 67 mmφ, and further annealed at 400 ° C. × 2 hr to obtain a soft material.
[0026]
Thereafter, the ball was processed into a bat shape with a wall thickness of 3 mm. The solution treatment was carried out by water quenching after holding at 450 ° C. for 40 minutes in a glass stone furnace. After correcting the distortion due to quenching by cold correction, heat treatment was performed under the artificial aging conditions (1 to 3 steps) in Table 2. The alloy numbers in Table 2 are the alloy numbers in Table 1. Here, after the artificial aging treatment at 115 to 145 ° C. for 12 to 48 hours according to the first aspect of the present invention, the re-artificial aging treatment at the overaging condition side at 160 to 190 ° C. for 6 to 12 hours is further performed. The heat treatment method is referred to as Invention T76. Further, as in the second aspect of the present invention, after artificial aging treatment at 115 to 145 ° C. for 12 to 48 hours, restoration treatment is performed at 170 to 190 ° C. for 1 to 4 hours, and further at 115 to 145 ° C. for 12 to 12 hours. A three-stage heat treatment method with 48 hours of re-artificial aging treatment is called Invention T77. The conventional T6 and T77 heat treatment methods are the conventional T6 and the conventional T77, and these tempering types are shown in Table 2, respectively. In addition, the elapsed time at room temperature after quenching until artificial aging is 12 to 72 hours. The heating and cooling rates during the composite artificial aging treatment were 100 ° C./hr for the sample.
[0027]
Investigate the tensile properties of tensile strength and elongation, compression properties of compressive strength and longitudinal elastic modulus, corrosion resistance of SCC stress and exfoliation corrosion resistance, and impact feeling by loss factor of these aluminum alloy bats after combined artificial aging treatment ,It was measured. These results are shown in Table 3. The thickness of the recrystallized layer on the surface of the vat (extruded material) after these composite artificial aging treatments was 500 μm or less.
[0028]
The tensile properties of 0.2% proof stress (MPa) and elongation (%) were obtained by taking a JIS 12B test piece with a length of 150 mm (bat longitudinal direction) from an aluminum alloy bat striking part (outer diameter 67 mm, wall thickness 3.0 mm). The tensile properties were measured according to the tensile test method of JIS-Z2241. The central part of the parallel part of the tensile test piece is located 80 mm from the butt tip (striking part).
[0029]
The compression characteristics of compression strength and longitudinal elastic modulus are 15mm in length (bat longitudinal direction), 8mm in width (bat circumferential direction), 3mm in thickness from the butt striking part (outer diameter 67mm, wall thickness 3.0mm) made of aluminum alloy. After collecting a (thickness) sample, it was processed into a rectangular parallelepiped sample having a length of 15 mm (bat longitudinal direction), a width of 8 mm (bat circumferential direction), and a thickness of 2.5 mm (thickness). A strain gauge was attached to both sides of the 15mm x 8mm center of this sample, and a compressive force was applied to the 8mm x 2.5mm surface in the circumferential direction. Yield strength (compression) was measured. The measurement point is 80 mm from the butt tip (striking part).
[0030]
The SCC stress resistance was measured by applying tensile stress in the circumferential direction (LT) by an SCC (stress corrosion cracking) test by the chromic acid acceleration method. In other words, a 15-mm wide C-ring-shaped test piece was taken from an aluminum alloy butt striking section (outer diameter 67 mm, wall thickness 3.0 mm), and after adding a predetermined tensile stress value, immediately boiled SCC test solution The sample in which no crack was generated was evaluated as ○, and the sample in which crack was generated was evaluated as ×. In addition, the stress was applied by generating a tensile stress on the outer surface of the sample by tightening the bolt and nut, and the stress value was measured for each sample using a strain gauge adhered to the outer surface. It was prepared by adding SCC test solution (per liter), 3 g of sodium chloride, 30 g of potassium chromate and 36 g of chromium oxide to distilled water. The C-ring was sampled within a range of 50 to 110 mm from the tip of the bat (ball hitting portion).
[0031]
The peel corrosion test is a sample with a length of 60 mm (bat longitudinal direction), width 30 mm (bat circumferential direction), and thickness 3 mm (thickness) from an aluminum alloy bat striking part (outer diameter 67 mm, wall thickness 3.0 mm). The EXCO test by ASTM-G34-90 exfoliation corrosion test was conducted, and after the test was completed, the standard of corrosion degree defined in ASTM-G34-90 (P, EA, EB, EC, Each sample was evaluated using ED). Below EC and ED, it is evaluated that peeling corrosion is inferior. The sample was collected in the range of 50 to 110 mm from the tip of the bat (ball hitting portion).
[0032]
The hit feeling is evaluated by a large loss factor in the first-order mode with a frequency of about 700 Hz and a small loss factor in the third-order mode with a frequency of about 3800 Hz. A sample of 124mm in length (bat longitudinal direction), 12mm in width (bat circumferential direction), and 3mm in thickness (thickness) is collected from an aluminum alloy bat striking part (outer diameter 67mm, wall thickness 3.0mm), and air at room temperature. In the middle, the transfer function up to a frequency of 5000 Hz was measured by the central excitation method, and from this, the loss factor was measured and evaluated in the first-order mode with a frequency of about 700 Hz and the third-order mode with a frequency of about 3800 Hz. Note that the position where the sample is held by the central excitation method is the center of the sample, and this position is 80 mm from the tip of the bat (striking portion).
[0033]
The aluminum alloy bats of Invention Examples 1 to 8 in Table 1 satisfying the composition of the present invention were subjected to the composite artificial aging treatment of Invention T76 or Invention T77 under the conditions of the present invention as shown in Table 2, and the tensile strength as shown in Table 3. Has tensile properties of 540 MPa or more, elongation of 10% or more, compressive properties of proof stress of 540 MPa or more, longitudinal elastic modulus of 70000 MPa or more, SCC stress resistance of 180 MPa or more, exfoliation corrosion resistance is EB in EXCO rank It has the above-mentioned corrosion resistance, and also has a hit feeling that the loss factor is 0.017 or less in the primary mode with a frequency of 700 Hz and 0.010 or more in the tertiary mode with a frequency of 3800 Hz.
[0034]
On the other hand, in Comparative Example, as shown in Table 1, Comparative Example 9 in which the content of Mn and Zr is too high, Comparative Example 10 in which the content of Si and Fe is too high, Comparative Example 12 in which the content of Zn is too high, and Mg In Comparative Example 14 in which the content is too high, as shown in Table 2, the composite artificial aging treatment T77 or T76 under the conditions of the present invention was applied, as shown in Table 3. SCC stress and exfoliation corrosion are significantly inferior to those of the inventive examples. In addition, the tensile characteristics, compression characteristics, and impact feeling are low.
[0035]
Comparative Example 11 in which the Zr content is too low, Comparative Example 13 in which the Zn content is too low, Comparative Example 15 in which the Mg content is too low, and Comparative Example 16 in which the Cu content is too low are shown in Table 2. Although the composite artificial aging treatment was performed under the conditions of the present invention, as shown in Table 3, the tensile properties, the compression properties, the impact feeling, etc. were significantly lower than those of the inventive examples. Further, in Comparative Example 17 where the conventional T77 artificial aging treatment deviating from the conditions of the present invention was used, although the alloy 8 within the scope of the present invention was used, the restoration treatment temperature at T77 was too high, and it was made of an aluminum alloy. SCC stress and exfoliation corrosion resistance as a bat are remarkably inferior to those of the invention examples. Further, the tensile properties, compression properties, impact feeling and the like are inferior to those of the invention examples.
[0036]
Therefore, the above results show the critical significance of the requirements of the present invention.
[0037]
[Table 1]

[0038]
[Table 2]

[0039]
[Table 3]

[0040]
【The invention's effect】
According to the present invention, an aluminum alloy comprising a heat treatment type 7000 series aluminum alloy extrudate having excellent corrosion resistance, excellent tensile properties and compressive properties necessary for a bat, and excellent impact feeling expressed by a loss factor. A bat made can be provided. Therefore, it has a great industrial value in that the application of the heat treatment type 7000 series aluminum alloy extruded material can be expanded.

Claims

Heat treatment type 7000 series aluminum alloy extruded material bat, 7000 series aluminum alloy extruded material, Zn: 5.7-8.5%, Mg: 1.2-2.6%, Cu: 1.9-2.6%, Zr: 0.08-0.15% Si: 0.12% or less, Fe: 0.15% or less, Mn: 0.30% or less, Cr: 0.20% or less, V: 0.05% or less, Ti: 0.10% or less, and the balance is Al and unavoidable impurities. In addition, this 7000 series aluminum alloy extruded material is subjected to a two-stage aging treatment in which a re-artificial aging treatment is carried out at 160-190 ° C. for 6-12 hours after an artificial aging treatment at 115-145 ° C. for 12-48 hours. It has been applied after heat treatment and quenching, has tensile strength of 540 MPa or more, elongation of 10% or more, compressive property of proof stress of 540 MPa or more and longitudinal elastic modulus of 70000 MPa or more, and SCC resistance Stress is 180MPa or more, exfoliation corrosion resistance is EXCO rank, EB or more corrosion resistance, and loss factor is 0.017 or less in the primary mode with frequency 700Hz. Aluminum alloy steel vat having a striking feeling is 0.010 or more third mode frequency 3800Hz.

Heat treatment type 7000 series aluminum alloy extruded material bat, 7000 series aluminum alloy extruded material, Zn: 5.7-8.5%, Mg: 1.2-2.6%, Cu: 1.9-2.6%, Zr: 0.08-0.15% Si: 0.12% or less, Fe: 0.15% or less, Mn: 0.30% or less, Cr: 0.20% or less, V: 0.05% or less, Ti: 0.10% or less, and the balance is Al and unavoidable impurities. At the same time, this 7000 series aluminum alloy extruded material was restored at 170-190 ° C. for 1-4 hours after artificial aging treatment at 115-145 ° C. for 12-48 hours, and further at 115-145 ° C. for 12-48 hours. 3 stages of re-artificial aging treatment are applied after solution treatment and quenching, tensile strength of 540 MPa or more, elongation of 10% or more, proof stress of 540 MPa or more, longitudinal elastic modulus Has a compression characteristic of 70000 MPa or more, SCC stress resistance of 180 MPa or more, exfoliation corrosion resistance of EXCO rank, EB or more, and loss Aluminum alloy steel vat but having a striking feeling is 0.010 or more third mode of 0.017 or less and the frequency 3800Hz in the primary mode frequency 700 Hz.