JP2010189750A - High-strength aluminum alloy wire and rod material excellent in softening resistance and method of manufacturing the same - Google Patents

High-strength aluminum alloy wire and rod material excellent in softening resistance and method of manufacturing the same Download PDF

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JP2010189750A
JP2010189750A JP2009038099A JP2009038099A JP2010189750A JP 2010189750 A JP2010189750 A JP 2010189750A JP 2009038099 A JP2009038099 A JP 2009038099A JP 2009038099 A JP2009038099 A JP 2009038099A JP 2010189750 A JP2010189750 A JP 2010189750A
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aluminum alloy
wire rod
alloy wire
strength
softening resistance
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JP5421613B2 (en
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Manabu Nakai
学 中井
Kentaro Ihara
健太郎 伊原
Kazuhiro Kaita
一浩 貝田
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Kobe Steel Ltd
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Abstract

<P>PROBLEM TO BE SOLVED: To provide a 6000 type high-strength aluminum alloy wire and rod material which is excellent in softening resistance, maintains high mechanical characteristics even when being exposed to a high temperature for a long time and is excellent in both of cold workability and corrosion resistance, and to provide a method of manufacturing the high-strength aluminum alloy wire and rod material. <P>SOLUTION: The wire and rod material is manufactured by subjecting Al-Mg-Si type aluminum alloy of a specified composition to hot rolling in cold strength working, wherein a crystal deposit in a texture of aluminum alloy wire and rod material is made fine, so that the softening resistance is excellent and high mechanical characteristics are maintained even when being exposed to a high temperature for a long time and corrosion resistance is made excellent too. <P>COPYRIGHT: (C)2010,JPO&INPIT

Description

本発明は、耐軟化性に優れた高強度なＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金線棒材に関するものである。本発明の線棒材とは、その製造過程において熱間圧延を施された圧延線棒材であり、径の比較的小さな線材と、径の比較的大きな棒材との総称である。以下、アルミニウムをＡｌ、Ａｌ−Ｍｇ−Ｓｉ系を６０００系とも言う。   The present invention relates to a high-strength Al—Mg—Si-based aluminum alloy wire rod excellent in softening resistance. The wire rod of the present invention is a rolled wire rod that has been hot-rolled in the production process, and is a general term for a wire rod having a relatively small diameter and a rod material having a relatively large diameter. Hereinafter, aluminum is also referred to as Al, and Al—Mg—Si is also referred to as 6000.

従来から、アルミニウム合金やマグネシウム合金などの軽合金を使用して軽量化された自動車のエンジン部品の互いの締結には、通常は鋼製のボルトやネジなどの締結具が用いられる。   Conventionally, fasteners such as steel bolts and screws are usually used for fastening engine parts of automobiles that have been reduced in weight using light alloys such as aluminum alloys and magnesium alloys.

これに対して、近年、自動車車体の軽量化に関連して、自動車エンジン部品の軽量化のために、これらボルトやネジなどの締結具にも、アルミニウム合金の線材や棒材などの線棒材を成形して作製されたアルミニウム合金製締結具を用いたいとの要求がある。   On the other hand, in recent years, in connection with the weight reduction of automobile bodies, in order to reduce the weight of automobile engine parts, these bolts, screws and other fasteners are also used as wire rod materials such as aluminum alloy wires and rods. There is a demand to use a fastener made of an aluminum alloy produced by molding.

従来から、窓用サッシや自動車車体などのアルミニウム合金製構造物の組立てに用いる、高強度な６０００系アルミニウム合金製ねじ（ボルトを含む）が、特許文献１などで提案されている。この特許文献１では、ねじの機械的性質（以下、機械的特性とも言う）として、耐力が３００Ｎ／ｍｍ2 以上、伸びが６％以上、ねじり強さがＪＩＳ−Ｂ−１０５７−１９８９のＡＬ３（Ａ６０６１−Ｔ６）のねじ強さより１０％以上高い値とするために、特定組成の６０００系アルミニウム合金押出材としている。即ち、Ｍｇ：０．５〜１．５wt％、Ｓｉ：０．５〜１．５wt％、Ｃｕ：０．５〜１．５wt％、Ｍｎ：０．２〜０．５wt％、Ｔｉ：０．００５〜０．１wt％、Ｂ：０．００１〜０．０５wt％、Ｚｒ：０．０５〜０．２５wt％を含有し、残部アルミニウムおよび不可避不純物からなるＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金組成としている。 Conventionally, a high-strength 6000 series aluminum alloy screw (including bolts) used for assembling aluminum alloy structures such as window sashes and automobile bodies has been proposed in Patent Document 1 and the like. In this patent document 1, as the mechanical properties of the screw (hereinafter also referred to as mechanical properties), the proof stress is 300 N / mm 2 or more, the elongation is 6% or more, and the torsion strength is AL3 (JIS-B-1057-1989). In order to obtain a value that is 10% or more higher than the screw strength of A6061-T6), a 6000 series aluminum alloy extruded material having a specific composition is used. That is, Mg: 0.5-1.5 wt%, Si: 0.5-1.5 wt%, Cu: 0.5-1.5 wt%, Mn: 0.2-0.5 wt%, Ti: 0. 005 to 0.1 wt%, B: 0.001 to 0.05 wt%, Zr: 0.05 to 0.25 wt%, and an Al-Mg-Si based aluminum alloy composition composed of the balance aluminum and inevitable impurities. .

この特許文献１は、窓用サッシや自動車車体などの締結具用のアルミニウム合金として、６０００系アルミニウム合金を選択したことに意義がある。この６０００系以外のアルミニウム合金では、前記特許文献１に記載されているように、締結具用のアルミニウム合金としての実用化のためには、以下のような問題が各々ある。   This Patent Document 1 is meaningful in that a 6000 series aluminum alloy is selected as an aluminum alloy for fasteners such as window sashes and automobile bodies. This aluminum alloy other than 6000 series has the following problems for practical use as an aluminum alloy for fasteners, as described in Patent Document 1.

５０５２や５０５６などの５０００系アルミニウム合金は、Ｍｇなどの合金量が多く、６０００系に比してリサイクル性に劣り、強度が低い。また、締結具へのヘッダー加工、ねじ転造加工などの成形、加工性も劣る。
７Ｎ０１、７０７５などの７０００系アルミニウム合金は、強度は高いもののＺｎ、Ｃｕなどの合金量が多く、リサイクル性に劣る。また、Ｚｎ、Ｃｕなどの合金量が多いゆえに腐食し易く、信頼性に欠ける。そして、成形、加工性が劣り、ヘッダー加工・ねじ転造加工中に割れ易い。 5000 series aluminum alloys such as 5052 and 5056 have a large amount of alloys such as Mg, are inferior in recyclability and low in strength as compared to 6000 series. In addition, molding and workability such as header processing and screw rolling processing on fasteners are also inferior.
Although 7000 series aluminum alloys such as 7N01 and 7075 have high strength, they have a large amount of alloys such as Zn and Cu and are inferior in recyclability. Moreover, since there are many alloy quantities, such as Zn and Cu, it is easy to corrode and lacks reliability. And, molding and workability are inferior, and it is easy to break during header processing and screw rolling.

２０２４などの２０００系アルミニウム合金は、耐熱性は高いものの、Ｃｕなどの合金量が多い場合には、リサイクル性に劣り、腐食し易い問題もある。また、成形、加工性が劣り、ヘッダー加工・ねじ転造加工中に割れ易い。これは代表的な耐熱性アルミニウム合金であるＡＡ２６１８でも同様である。この合金は、既に数十年に及ぶ使用実績のある合金であり、適用例には、超音速機コンコルドの機体が上げられる。また、耐熱温度は約１２０℃と、実用アルミニウム合金の中では最も高い。但し、耐食性は低く、その使用には、耐食性の対策を施すことが必要となる。このため、使用環境の制限も生じ、決して使い勝手の良い合金ではない。   Although 2000 series aluminum alloys, such as 2024, have high heat resistance, when there are many alloy quantities, such as Cu, there exists a problem which is inferior to recyclability and is easy to corrode. Moreover, it is inferior in molding and workability, and easily breaks during header processing and screw rolling. The same applies to AA2618 which is a typical heat-resistant aluminum alloy. This alloy has already been used for several decades, and examples of applications include the body of a supersonic aircraft Concorde. The heat-resistant temperature is about 120 ° C., which is the highest among practical aluminum alloys. However, the corrosion resistance is low, and it is necessary to take measures against corrosion resistance for its use. For this reason, the usage environment is limited, and the alloy is not easy to use.

ただ、６０００系アルミニウム合金の場合でも、前記締結具として用いられていた既存のＡ６０６１、Ａ６０５６などの合金は、やはり成形、加工性が劣り、ヘッダー加工・ねじ転造加工中に割れ易く、また、人工時効硬化処理を行っても強度自体が低かった。前記特許文献１は、６０００系アルミニウム合金のこれらの問題点を改善しようとしたものでもある。   However, even in the case of a 6000 series aluminum alloy, the existing alloys such as A6061 and A6056 used as the fasteners are still inferior in molding and workability, and are easily broken during header processing and screw rolling, Even after artificial age hardening, the strength was low. Patent Document 1 also attempts to improve these problems of the 6000 series aluminum alloy.

特許第３９３９４１４号公報Japanese Patent No. 3939414

ここで、前記した自動車エンジン部品の締結具に要求される特性は、前記特許文献１が意図する通常の締結具と同じく、締めつけ時の安定軸力の確保や、締めつけ後の使用中の軸力の低下によるゆるみが無いこと、あるいは折損が無いことなどである。そして、自動車エンジン部品の締結具がこれらの特性を発揮するためには、その素材となるアルミニウム合金線棒材は、高強度、高耐力、高破断伸びなどの機械的諸特性と、締結具へのヘッダー加工やねじ転造加工などの冷間加工性、耐食性などを兼備していることが必要である。   Here, the characteristics required for the fasteners of the above-mentioned automobile engine parts are the same as the normal fasteners intended by Patent Document 1, ensuring stable axial force at the time of fastening, and axial force during use after fastening. For example, there is no looseness due to a decrease in the height, or there is no breakage. And in order for the fasteners of automobile engine parts to exhibit these characteristics, the aluminum alloy wire rod material used as the material has various mechanical characteristics such as high strength, high proof stress, high elongation at break, and fasteners. It is necessary to have both cold workability such as header processing and thread rolling processing, and corrosion resistance.

ただ、本発明が意図する、この自動車エンジン部品の締結具には、エンジン部品として、長時間高温に曝された際にも、前記高強度、高耐力、高破断伸びなどの機械的諸特性を維持する耐軟化性が要求される。この点が、前記特許文献１が対象としたような、常温で使用される通常の締結具とは異なる点であり、自動車エンジン部品締結具要求特性のより厳しい点である。   However, the fastener of this automobile engine part intended by the present invention has mechanical characteristics such as high strength, high yield strength and high elongation even when exposed to high temperature for a long time as an engine part. Maintaining softening resistance is required. This is a point different from the normal fastener used at room temperature as the object of Patent Document 1, and is a more strict point of the required characteristics of the automobile engine component fastener.

これに対して、前記特許文献１を含めて、従来の６０００系アルミニウム合金の線棒材では、耐軟化性が劣るという問題がある。即ち、常温では例え高強度であっても、一旦１００℃以上の温度に長時間加熱された（曝された）場合には、特に強度、耐力などの機械的諸特性が著しく低下するという問題がある。近年、自動車車体の軽量化のために、自動車エンジン部品の締結具に要求される耐軟化性は益々厳しくなっている。しかし、前記特許文献１でも、その実施例からして、常温ではこれらの特性を満たすデータもあるものの、一旦、このような１００℃以上の温度に長時間加熱された場合には、特に強度、耐力などが著しく低下して、前記機械的性質を満足できなくなる。   On the other hand, including the said patent document 1, the conventional wire rod material of 6000 series aluminum alloy has a problem that softening resistance is inferior. In other words, even if the strength is high at room temperature, the mechanical properties such as strength and proof stress are remarkably lowered when heated (exposed) to a temperature of 100 ° C. or higher for a long time. is there. In recent years, in order to reduce the weight of automobile bodies, the softening resistance required for fasteners for automobile engine parts has become increasingly severe. However, even in the above-mentioned Patent Document 1, although there are data satisfying these characteristics at room temperature from the examples, when it is heated to such a temperature of 100 ° C. or higher for a long time, the strength, The proof stress is remarkably lowered, and the mechanical properties cannot be satisfied.

しかも、これら６０００系アルミニウム合金の線棒材では、自動車エンジン部品用などのボルトやネジなどの締結具への、ヘッダー加工やねじ転造加工などの冷間加工性も要求される。しかし、前記特許文献１を含めて、従来の６０００系アルミニウム合金の線棒材では、これらの冷間加工性や、あるいは耐食性などを前記耐軟化性を満たした上で、満足させることもできなかった。これは、自動車エンジン部品用などのボルトやネジなどの締結具として、本発明が対象とする、特に断面が円形な線棒材を製造するような場合には、前記特許文献１のような熱間押出による加工方法では、後述する通り、線棒材の特性向上に大きな限界があることにもよる。   Moreover, these 6000 series aluminum alloy wire rod materials are also required to have cold workability such as header processing and screw rolling processing to fasteners such as bolts and screws for automobile engine parts. However, the conventional 6000 series aluminum alloy wire rods including Patent Document 1 cannot satisfy these cold workability and corrosion resistance while satisfying the softening resistance. It was. This is because, as a fastener for bolts and screws for automobile engine parts and the like, particularly when a wire rod having a circular cross section is manufactured, the heat as in Patent Document 1 is used. In the processing method by the inter-extrusion, as will be described later, there is a great limitation in improving the properties of the wire rod material.

本発明は、かかる問題に鑑みなされたもので、耐軟化性や冷間加工性に優れ、耐食性も合わせて優れた、６０００系高強度アルミニウム合金線棒材およびその製造方法を提供することを目的とする。   The present invention has been made in view of such problems, and an object thereof is to provide a 6000 series high-strength aluminum alloy wire rod excellent in softening resistance, cold workability, and corrosion resistance, and a method for producing the same. And

上記目的を達成するための本発明耐軟化性に優れた高強度アルミニウム合金線棒材の要旨は、熱間圧延を施されたＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金線棒材であって、質量％で、Ｍｇ：０．６５〜１．７５％、Ｓｉ：０．７０〜１．３５％、Ｃｕ：０．４０〜１．０５％、Ｆｅ：０．０５〜０．３５％、Ｍｎ：０．０５〜０．９５％、Ｃｒ：０．０５〜０．２５％、Ｔｉ：０．０１〜０．１０％を各々含み、残部Ａｌおよび不可避的不純物からなり、組織中の最大長が２００ｎｍ以上、８００ｎｍ以下の分散粒子の平均密度が５個／μｍ3 以上であるとともに、最大長が１０μｍ以上の晶析出物の平均密度が５００個／ｍｍ2 以下であることとする。 The gist of the high strength aluminum alloy wire rod excellent in softening resistance of the present invention for achieving the above object is an Al-Mg-Si aluminum alloy wire rod that has been hot-rolled, and is mass%. Mg: 0.65 to 1.75%, Si: 0.70 to 1.35%, Cu: 0.40 to 1.05%, Fe: 0.05 to 0.35%, Mn: 0.00. Each containing 05-0.95%, Cr: 0.05-0.25%, Ti: 0.01-0.10%, consisting of the balance Al and inevitable impurities, the maximum length in the structure being 200 nm or more, The average density of dispersed particles of 800 nm or less is 5 particles / μm 3 or more, and the average density of crystal precipitates having a maximum length of 10 μm or more is 500 particles / mm 2 or less.

また、上記目的を達成するための本発明耐軟化性に優れた高強度アルミニウム合金線棒材の製造方法の要旨は、質量％で、Ｍｇ：０．６５〜１．７５％、Ｓｉ：０．７０〜１．３５％、Ｃｕ：０．４０〜１．０５％、Ｆｅ：０．０５〜０．３５％、Ｍｎ：０．０５〜０．９５％、Ｃｒ：０．０５〜０．２５％、Ｔｉ：０．０１〜０．１０％を各々含み、残部Ａｌおよび不可避的不純物からなり、必要により更に、Ｚｒ：０．０１〜０．３０％、Ｖ：０．０１〜０．３０％の内の一種または二種を含有したＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金鋳塊を溶製し、この鋳塊を４７０〜５６５℃の範囲で均質化熱処理後、熱延開始温度が３２０〜５２０℃の範囲で加工率９５％以上の熱間圧延を行い、必要により更に冷間加工して、所定の径のアルミニウム合金線棒材とし、その後、溶体化および急冷処理と１５０〜２００℃での時効処理を記載順に行う調質処理を施した後の組織中の、最大長が２００ｎｍ以上、８００ｎｍ以下の分散粒子の平均密度が５個／μｍ3 以上とするとともに、最大長が１０μｍ以上の晶析出物の平均密度が５００個／ｍｍ2 以下とすることである。 Moreover, the summary of the manufacturing method of the high intensity | strength aluminum alloy wire rod material excellent in the softening resistance of this invention for achieving the said objective is the mass%, Mg: 0.65-1.75%, Si: 0.8. 70 to 1.35%, Cu: 0.40 to 1.05%, Fe: 0.05 to 0.35%, Mn: 0.05 to 0.95%, Cr: 0.05 to 0.25% , Ti: 0.01 to 0.10% each, and the balance consisting of Al and inevitable impurities, and if necessary, Zr: 0.01 to 0.30%, V: 0.01 to 0.30% An Al—Mg—Si-based aluminum alloy ingot containing one or two of them is melted, and this ingot is subjected to homogenization heat treatment in the range of 470 to 565 ° C., and then the hot rolling start temperature is 320 to 520 ° C. Perform hot rolling with a processing rate of 95% or more in the range, and if necessary, further cold work to obtain aluminum with a predetermined diameter. Dispersed particles having a maximum length of 200 nm or more and 800 nm or less in the structure after being subjected to a tempering treatment in which the solution treatment and the rapid cooling treatment and the aging treatment at 150 to 200 ° C. are performed in the order of description. with an average density of the five / [mu] m 3 or more, the average density of the maximum length 10μm or more intermetallic compounds is to a 500 / mm 2 or less.

ここで、本発明で言う、熱間圧延を施されたＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金線棒材とは、前記した通り、その製造過程において熱間圧延を施された線棒材である。したがって、熱間圧延によって所定径や所定形状の線棒材とされ、その後には冷間加工しない線棒材でも良く、熱間圧延後や冷間加工途中に適宜焼鈍しながら、必要により更に冷間圧延、引抜、抽伸、抽芯、鍛造などの所望の冷間加工によって所定径や所定形状とされた線棒材でも良い。また、線棒材を前記選択的な焼鈍も含めて冷間加工した締結具でも良い（本発明では線棒材を冷間加工した締結具も線棒材として範囲に含める）。さらに、本発明が対象とするのは、断面が円形な線棒材であるが、締結具に適用できるものであれば、断面形状が真円だけでなくとも良く、楕円などの他の円形な断面形状も、用途に応じて適宜選択される。   Here, the hot-rolled Al—Mg—Si-based aluminum alloy wire rod material referred to in the present invention is a wire rod material that has been hot-rolled in the manufacturing process as described above. Therefore, it may be a wire rod having a predetermined diameter or shape by hot rolling, and thereafter may be a wire rod that is not cold-worked, and is further cooled if necessary while appropriately annealing after hot rolling or during cold working. It may be a wire rod having a predetermined diameter or a predetermined shape by a desired cold working such as cold rolling, drawing, drawing, drawing, or forging. Moreover, the fastener which cold-worked the wire rod material also including the said selective annealing may be sufficient (In this invention, the fastener which cold-worked the wire rod material is also included as a wire rod material.). Furthermore, the present invention is intended for wire rods having a circular cross section, but the cross sectional shape is not limited to a perfect circle as long as it can be applied to a fastener, and other circular shapes such as an ellipse. The cross-sectional shape is also appropriately selected according to the application.

ここで、前記請求項１に規定の前記組織中の晶析出物の平均密度や分散粒子の平均密度、あるいは前記請求項２に規定の１５０℃で５００時間熱処理した後の室温大気中での機械的性質は、溶体化および急冷処理と１５０〜２００℃での時効処理を記載順に行う調質処理を施した後での、線棒材や冷間加工された締結具の組織や性質とする。言い換えると、前記調質処理を施した後であれば、線棒材の状態だけでなく、冷間加工された締結具の状態で測定された組織や性質でも良い。
線棒材組織中の晶析出物の平均密度は、後述する測定部位の通り、線棒材の中心部（軸中心部）であれば、締結具への冷間加工や前記調質処理によっては殆ど変化せず、元の線棒材の組織を反映したものとなっている。一方、線棒材組織中の分散粒子の平均密度は、後述する測定部位の通り、線棒材の中心部（軸中心）であれば、締結具への冷間加工によっては殆ど変化しないものの、前記調質処理によっては変化する。したがって、再現性良く線棒材の組織や機械的性質を反映した、晶析出物の平均密度や分散粒子の平均密度、あるいは１５０℃で５００時間熱処理した後の室温大気中での機械的性質とするためには、少なくとも前記調質処理を施した後の線棒材や冷間加工された締結具の組織や性質を測定する。 Here, the average density of crystal precipitates and the average density of dispersed particles in the structure defined in claim 1 or the machine in room temperature air after heat treatment at 150 ° C. defined in claim 2 for 500 hours. The physical properties are the structure and properties of the wire rod material and the cold-worked fastener after the tempering treatment in which the solution treatment and the rapid cooling treatment and the aging treatment at 150 to 200 ° C. are performed in the order of description. In other words, as long as the tempering treatment is performed, not only the state of the wire rod material but also the structure and properties measured in the state of the cold-worked fastener may be used.
If the average density of crystal precipitates in the wire rod material structure is the center portion (shaft center portion) of the wire rod material, as will be described later, depending on the cold working to the fastener and the tempering treatment, Almost no change, reflecting the structure of the original wire rod. On the other hand, the average density of the dispersed particles in the wire rod material structure is almost the same as the measurement site to be described later, if it is the central portion (axial center) of the wire rod material, but is hardly changed by cold working on the fastener, It varies depending on the tempering process. Therefore, the average density of crystal precipitates and the average density of dispersed particles, reflecting the structure and mechanical properties of the wire rod material with good reproducibility, or the mechanical properties in room temperature air after heat treatment at 150 ° C. for 500 hours In order to do this, at least the structure and properties of the wire rod material and the cold-worked fastener after the tempering treatment are measured.

本発明で規定する前記晶析出物や前記分散粒子とは、アルミニウム合金線棒材組織のＳＥＭやＴＥＭによる観察で、マトリックス内に存在する、組成を問わない不定形の粒子として確認でき、最大長の測定（判別）ができる、第２相粒子のことを言う。   The crystal precipitates and the dispersed particles defined in the present invention can be confirmed as amorphous particles of any composition existing in the matrix by observation with an SEM or TEM of an aluminum alloy wire rod structure, and have a maximum length. The second phase particles that can be measured (discriminated).

本発明者は、６０００系アルミニウム合金線棒材組織中の前記晶析出物と冷間加工性、前記分散粒子と耐軟化性（１５０℃程度の温度で長時間熱処理された後の機械的性質）などに、深い相関関係があることを知見した。   The present inventor considered that the crystal precipitates in the 6000 series aluminum alloy wire rod structure and cold workability, the dispersed particles and softening resistance (mechanical properties after heat treatment at a temperature of about 150 ° C. for a long time) And so on.

先ず、６０００系アルミニウム合金線棒材組織中の晶析出物を微細化できれば、自動車エンジン部品用などのボルトやネジなどの締結具への、ヘッダー加工やねじ転造加工などの冷間加工性が向上する。粗大な晶析出物が実質量存在する場合には、６０００系アルミニウム合金線棒材の、前記ヘッダー加工やねじ転造加工などの冷間加工性を低下させるからである。したがって、本発明では、冷間加工性向上のために、６０００系アルミニウム合金線棒材組織中の、前記粗大な晶析出物（平均密度）を極力少なくする。   First, if crystal precipitates in the 6000 series aluminum alloy wire rod structure can be refined, cold workability such as header processing and thread rolling processing to fasteners such as bolts and screws for automobile engine parts can be achieved. improves. This is because, when a substantial amount of coarse crystal precipitates is present, the cold workability of the 6000 series aluminum alloy wire rod such as the header processing and screw rolling processing is lowered. Therefore, in the present invention, in order to improve cold workability, the coarse crystal precipitates (average density) in the 6000 series aluminum alloy wire rod structure are reduced as much as possible.

そして、本発明者は、このような線棒材組織の晶析出物の微細化は、特定組成の６０００系アルミニウム合金と、前記低温、強加工の熱間圧延による加工方法との組み合わせによって始めて、製造可能であることも知見した。   And this inventor started the refinement | miniaturization of the crystal precipitate of such a wire rod material structure | tissue only by the combination of the processing method by the 6000 series aluminum alloy of a specific composition, and the said low temperature and strong hot rolling, It was also found that it can be manufactured.

次ぎに、６０００系アルミニウム合金線棒材組織中の特定範囲の微細な分散粒子の密度を高めると、前記高温に長時間加熱された（熱処理された）後でも、室温大気中での機械的性質が低下せず、元の高強度、高耐力、高破断伸びなどの機械的諸特性が保持されることを知見した。また、アルミニウム合金線棒材組織の結晶粒の微細化、繊維組織状化させることが可能となり、耐粒界腐食感受性などの耐食性が向上できることも知見した。そして、このような線棒材組織の特定範囲の微細な分散粒子の密度は、特定組成の６０００系アルミニウム合金と、前記特定範囲の均質化熱処理によって製造可能であることも知見した。   Next, when the density of fine dispersed particles in a specific range in the 6000 series aluminum alloy wire rod structure is increased, the mechanical properties in room temperature atmosphere even after being heated to the high temperature for a long time (heat treated) It was found that the mechanical properties such as the original high strength, high yield strength and high elongation at break were maintained. It was also found that the crystal grain size and fiber structure of the aluminum alloy wire rod structure can be made finer, and the corrosion resistance such as intergranular corrosion resistance can be improved. It was also found that such a density of fine dispersed particles in a specific range of the wire rod material structure can be produced by a 6000 series aluminum alloy having a specific composition and a homogenization heat treatment in the specific range.

また、このアルミニウム合金線棒材組織中の、晶析出物を微細化でき、かつ微細な分散粒子の数を多くすることができれば、このアルミニウム合金線棒材組織の結晶粒径も微細化させることが可能となる。このため、前記高温に長時間熱処理された後でも、室温大気中での機械的性質が低下しない効果が助長され、耐粒界腐食感受性などの耐食性が向上できる。本発明では、これらの組織を、後述する通り、前記特定範囲の均質化熱処理と組み合わせた、前記低温、強加工の熱間圧延によって得る。
この結果、本発明は、耐軟化性が優れて高い機械的諸特性を保持できるとともに、締結具へのヘッダー加工やねじ転造加工などのも合わせて優れ、更に耐食性も兼備した、自動車エンジン部品の締結具として好適な、６０００系高強度アルミニウム合金線棒材およびその製造方法を提供できる。 If the crystal precipitates in this aluminum alloy wire rod structure can be refined and the number of fine dispersed particles can be increased, the crystal grain size of this aluminum alloy wire rod structure can also be refined. Is possible. For this reason, even after the heat treatment at the high temperature for a long time, the effect of not lowering the mechanical properties in the air at room temperature is promoted, and the corrosion resistance such as intergranular corrosion resistance can be improved. In the present invention, as will be described later, these structures are obtained by hot rolling at the low temperature and strong processing combined with the homogenization heat treatment in the specific range.
As a result, the present invention is an automotive engine part that has excellent softening resistance and can maintain high mechanical characteristics, is excellent in header processing and screw rolling processing on fasteners, and also has corrosion resistance. 6000 series high-strength aluminum alloy wire rod suitable for use as a fastener and a method for producing the same can be provided.

以下に、本発明の実施の形態につき、本発明６０００系アルミニウム合金板の組成から、順に要件ごとに具体的に説明する。   Hereinafter, embodiments of the present invention will be specifically described in order from the composition of the present invention 6000 series aluminum alloy sheet.

組成−６０００系：
本発明における６０００系アルミニウム合金線棒材線棒材の化学成分組成について、以下に説明する。本発明が主たる対象とする自動車エンジン部品の締結具には、前記した通り、一旦１００℃以上の温度に長時間加熱された（熱処理された）際にも、締めつけ時の安定軸力の確保、締めつけ後の使用中の軸力の低下によるゆるみが無いこと、あるいは折損が無いことなどの、耐軟化性が求められる。これを締結具の素材であるアルミニウム合金線棒材が保証するためには、１５０℃程度に長時間加熱された（熱処理された）後の室温大気中での機械的性質として、高強度、高耐力、高破断伸びを有することが必要である。また、同時に、優れた耐粒界腐食感受性などの耐食性を兼備していることも必要である。 Composition-6000 series:
The chemical component composition of the 6000 series aluminum alloy wire rod in the present invention will be described below. As described above, the fastener of an automobile engine part as the main object of the present invention is to secure a stable axial force at the time of tightening even when heated to a temperature of 100 ° C. or higher for a long time (heat treated). Softening resistance is required, such as no loosening due to a decrease in axial force during use after tightening, or no breakage. In order to guarantee this, the aluminum alloy wire rod that is the material of the fastener has high strength and high mechanical properties in room temperature air after being heated (heat treated) to about 150 ° C for a long time. It is necessary to have proof stress and high elongation at break. At the same time, it is also necessary to have excellent corrosion resistance such as intergranular corrosion resistance.

このような要求を満足するために、その製造過程において熱間圧延を施された本発明のアルミニウム合金圧延線棒材は、質量％で、Ｍｇ：０．６５〜１．７５％、Ｓｉ：０．７０〜１．３５％、Ｃｕ：０．４０〜１．０５％、Ｆｅ：０．０５〜０．３５％、Ｍｎ：０．０５〜０．９５％、Ｃｒ：０．０５〜０．２５％、Ｔｉ：０．０１〜０．１０％を各々含み、残部Ａｌおよび不可避的不純物からなるＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金組成とする。なお、各元素の含有量の％表示は全て質量％の意味である。   In order to satisfy such a requirement, the aluminum alloy rolled wire rod of the present invention that has been hot-rolled in the production process thereof has a mass% of Mg: 0.65 to 1.75%, Si: 0. 70 to 1.35%, Cu: 0.40 to 1.05%, Fe: 0.05 to 0.35%, Mn: 0.05 to 0.95%, Cr: 0.05 to 0.25 %, Ti: 0.01 to 0.10%, respectively, and an Al—Mg—Si based aluminum alloy composition composed of the balance Al and inevitable impurities. In addition,% display of content of each element means the mass% altogether.

本発明アルミニウム合金圧延線棒材の化学成分組成は、６０００系アルミニウム合金の化学成分組成にしては、前記耐軟化性や高い機械的諸特性を有するために、合金元素の種類や含有量が比較的多い。通常であれば、このように合金元素の種類や含有量が比較的多ければ、鋳塊には、粗大な晶析出物が必然的に形成する。このため、熱間押出などで線棒材を製造した場合には、熱間押出時にダイスとの焼付きが生じ易くなる。このような焼付きを防止するためには、押出速度を小さくする必要が生じ、生産性を低下させる。また、無理に押出速度を大きくすると、押出材の表面に傷が生じ、線加工時の破線、表面割れの原因となり易い。更に、押出加工では、押出材の表層から中心部に向け粗大な晶析出物が残存し易く、高強度な材料であっては、本発明で規定する組織条件（最大長が５μｍ以上の前記晶析出物の平均密度が５００個／ｍｍ2 以下）とは必然的にできず、粗大な晶析出物を無くせない。したがって、冷間加工性は低くなり、線材またねじへの加工性は著しく低下する。 The chemical composition of the aluminum alloy rolled wire rod of the present invention is the same as that of the 6000 series aluminum alloy. Many. Normally, if the kind and content of the alloy elements are relatively large, coarse crystal precipitates are inevitably formed in the ingot. For this reason, when a wire rod material is manufactured by hot extrusion or the like, seizure with a die is likely to occur during hot extrusion. In order to prevent such seizure, it is necessary to reduce the extrusion speed, which reduces productivity. Further, if the extrusion speed is increased excessively, the surface of the extruded material is damaged, which is likely to cause broken lines and surface cracks during wire processing. Furthermore, in the extrusion process, coarse crystal precipitates are likely to remain from the surface layer of the extruded material toward the center, and the high-strength material has a structure condition defined by the present invention (the crystal having a maximum length of 5 μm or more). The average density of precipitates is inevitably not more than 500 pieces / mm 2 ), and coarse crystal precipitates cannot be eliminated. Accordingly, the cold workability is lowered, and the workability to the wire or screw is remarkably lowered.

これに対して、本発明アルミニウム合金圧延線棒材では、合金元素の種類や含有量が比較的多いにも関わらず、前記した化学成分組成のように、選択された合金元素と合金元素量との組み合わせでバランスさせている。そして、その上で、更に、アルミニウム合金線棒材の製造過程における、前記低温、強加工の熱間圧延との組み合わせや相乗効果によって、前記したあるいは後述する組織条件のように、線棒材組織中の晶析出物を微細化させている。また、合金元素と合金元素量、均熱温度との組み合わせまたバランスで、分散粒子を微細高密度化させている。即ち、本発明アルミニウム合金線棒材は、線材ならびにねじ加工時の冷間加工性が高く、前記高温に長時間加熱された（熱処理された）後であっても、前記高強度、高耐力、高破断伸びなどの機械的な諸特性を保持することができる。   On the other hand, in the aluminum alloy rolled wire rod material of the present invention, the selected alloy element and the amount of the alloy element, as in the chemical composition described above, although the type and content of the alloy element are relatively large. Balance with the combination. In addition, in the manufacturing process of the aluminum alloy wire rod material, the wire rod material structure as described above or described later by the combination with the low temperature, strong hot rolling or synergistic effect The crystal precipitate inside is refined. Further, the dispersed particles are finely densified by a combination or balance of alloy elements, alloy element amounts, and soaking temperatures. That is, the aluminum alloy wire rod of the present invention has high cold workability during wire processing and screw processing, and even after being heated to the high temperature for a long time (heat treated), the high strength, high yield strength, Various mechanical properties such as high breaking elongation can be maintained.

また、同時に、前記した化学成分組成のように、選択された合金元素と合金元素量との組み合わせでバランスさせれば、６０００系アルミニウム合金の化学成分組成にしては合金元素の種類や含有量が比較的多いにも関わらず、耐食性も合わせて優れさせることができる。   At the same time, if the balance is made by the combination of the selected alloy element and the amount of the alloy element, as in the chemical component composition described above, the type and content of the alloy element is not enough for the chemical component composition of the 6000 series aluminum alloy. Despite being relatively large, the corrosion resistance can also be improved.

ここで、更に、Ｚｒ：０．０１〜０．３０％、Ｖ：０．０１〜０．３０％の内の一種または二種を含有しても良い。   Here, it may further contain one or two of Zr: 0.01 to 0.30% and V: 0.01 to 0.30%.

これら以外のその他の元素は、基本的には不純物であり、ＡＡ乃至ＪＩＡ規格などに沿った各元素レベルの含有量 (許容量) とする。ただ、リサイクルの観点から、溶解材として、高純度Ａｌ地金だけではなく、６０００系合金やその他のアルミニウム合金スクラップ材、低純度Ａｌ地金などを溶解原料として多量に使用した場合には、これら以外のその他の元素も混入される可能性が高い。そして、これらの不純物元素を低減すること自体が製造コストアップとなり、ある程度の含有を許容することが必要となる。一方、前記した本発明の目的や効果を阻害しない範囲で含有量を規制した方が良い元素もある。   Other elements other than these are basically impurities, and the content (allowable amount) at each element level in accordance with AA to JIA standards and the like. However, from the viewpoint of recycling, not only high-purity Al bullion but also 6000 series alloys, other aluminum alloy scrap materials, low-purity Al bullion, etc. are used as melting materials. There is a high possibility that other elements other than the above will also be mixed. And reducing these impurity elements itself increases the manufacturing cost, and it is necessary to allow the inclusion to some extent. On the other hand, there is an element whose content is better regulated within a range not hindering the object and effect of the present invention described above.

例えば、Ｔｉ添加のための母合金に含まれ、Ｔｉ添加の際に、ほぼ必然的に含まれるＢは、後述する通り、Ｔｉと同様の効果もあり、０．０５％以下の含有を許容する。また、Ａｇは０．２％以下、Ｓｎは０．２％以下の含有を許容する。一方、Ｚｎは、耐食性に対して特に有害であり、０．０５％以下のできるだけ少ない含有量に規制することが好ましい。   For example, B, which is included in the mother alloy for Ti addition, and is inevitably included when Ti is added, has the same effect as Ti, as described later, and allows inclusion of 0.05% or less. . Further, Ag is allowed to be 0.2% or less, and Sn is allowed to be 0.2% or less. On the other hand, Zn is particularly harmful to corrosion resistance, and it is preferable to regulate the content as low as possible to 0.05% or less.

６０００系アルミニウム合金における、各元素の好ましい含有範囲と意義、あるいは許容量について以下に元素毎に説明する。   The preferable content range and significance of each element in the 6000 series aluminum alloy, or the allowable amount will be described below for each element.

Ｓｉ：０．７０〜１．３５％
Ｓｉは、Ｍｇとともに、一部がマトリックスに固溶し、アルミニウム合金線棒材を固溶強化する。また、前記比較的高温での人工時効処理時に強度向上に寄与する時効析出物などを形成する時効硬化能を発揮して、自動車エンジン部品の締結具に要求される特性を満たすのに必要な、前記高強度、高耐力を得るための必須の元素である。なお、前記比較的高温での人工時効処理での優れた時効硬化能を発揮させるためには、Ｍｇ/Ｓｉを質量比１．７３以下とし、Ｍｇに対してＳｉを過剰に含有させた過剰Ｓｉ型の６０００系アルミニウム合金組成とすることが好ましい。 Si: 0.70 to 1.35%
Si, together with Mg, partly dissolves in the matrix and strengthens the aluminum alloy wire rod. Moreover, it is necessary to satisfy the characteristics required for the fasteners of automobile engine parts by demonstrating the age hardening ability to form aging precipitates that contribute to strength improvement during the artificial aging treatment at the relatively high temperature, It is an essential element for obtaining the high strength and high yield strength. In addition, in order to exhibit the excellent age-hardening ability in the artificial aging treatment at the relatively high temperature, excess Si containing Mg / Si at a mass ratio of 1.73 or less and containing Si excessively with respect to Mg. It is preferable to use a type 6000 series aluminum alloy composition.

Ｓｉ含有量が少なすぎると、絶対量が不足するため、前記固溶強化や時効硬化能が不足する。この結果、必要な前記高強度、高耐力を得ることができない。一方、Ｓｉ含有量が多すぎると、粗大な晶出物および析出物が形成されて、却って、必要な前記高強度、高耐力、高破断伸びを得ることができない。また、線棒材への熱間加工性や冷間加工性、締結具への成形性が著しく阻害される。したがって、Ｓｉは０．７０〜１．３５％の範囲とする。   If the Si content is too small, the absolute amount is insufficient, so that the solid solution strengthening and age hardening ability are insufficient. As a result, the required high strength and high yield strength cannot be obtained. On the other hand, if the Si content is too large, coarse crystals and precipitates are formed, and on the contrary, the necessary high strength, high yield strength and high elongation at break cannot be obtained. Moreover, the hot workability and cold workability to a wire rod material, and the moldability to a fastener are remarkably inhibited. Accordingly, Si is set in the range of 0.70 to 1.35%.

Ｍｇ：０．６５〜１．７５％
Ｍｇは、固溶強化と、前記人工時効処理時に、Ｓｉとともに強度向上に寄与する時効析出物を形成して、時効硬化能を発揮し、自動車エンジン部品の締結具に要求される特性を満たすのに必要な、前記高強度、高耐力、高破断伸びを得るための必須の元素である。 Mg: 0.65 to 1.75%
Mg forms an aging precipitate that contributes to strength improvement with Si during solid solution strengthening and artificial aging treatment, exhibits age hardening ability, and satisfies the characteristics required for fasteners of automobile engine parts. It is an essential element for obtaining the high strength, high yield strength, and high elongation at break necessary for the above.

Ｍｇ含有量が少なすぎると、絶対量が不足するため、前記固溶強化や時効硬化能が不足する。この結果、必要な前記高強度、高耐力を得ることができない。一方、Ｍｇ含有量が多すぎると、粗大な晶出物および析出物が形成されて、却って、必要な前記高強度、高耐力、高破断伸びを得ることができない。したがって、Ｍｇの含有量は０．６５〜１．７５％の範囲とする。   If the Mg content is too small, the absolute amount is insufficient, so that the solid solution strengthening and age hardening ability are insufficient. As a result, the required high strength and high yield strength cannot be obtained. On the other hand, if the Mg content is too large, coarse crystals and precipitates are formed, and on the contrary, the necessary high strength, high yield strength and high elongation at break cannot be obtained. Therefore, the Mg content is in the range of 0.65 to 1.75%.

Ｃｕ：０．４０〜１．０５％
Ｃｕは、Ｍｇ、Ｓｉと共に強度、耐力、破断伸びの向上に寄与する。Ｃｕ含有量が少なすぎると、その効果が十分に得られず、自動車エンジン部品の締結具に要求される特性を満たすのに必要な、前記高強度、高耐力、高破断伸びを得ることができない。一方、Ｃｕ含有量が多すぎると、却って、強度、耐力、破断伸びが低下する。また、締結具への成形性や加工性、そして耐蝕性が大きく低下する。したがって、Ｃｕの含有量は０．４０〜１．０５％の範囲とする。 Cu: 0.40 to 1.05%
Cu, together with Mg and Si, contributes to improvement in strength, proof stress, and elongation at break. If the Cu content is too small, the effect cannot be sufficiently obtained, and the high strength, high proof stress, and high elongation at break required for satisfying the characteristics required for a fastener for automobile engine parts cannot be obtained. . On the other hand, when there is too much Cu content, strength, yield strength, and elongation at break decrease. In addition, the formability and workability of the fastener and the corrosion resistance are greatly reduced. Therefore, the Cu content is in the range of 0.40 to 1.05%.

Ｆｅ：０．０５〜０．３５％
Ｆｅも、Ｍｎ，Ｃｒ，ＺｒならびにＶと同様に分散粒子を形成するため、結晶粒を微細化させるなど、破断伸び、耐熱性等の向上に寄与する。Ｆｅ含有量が少なすぎると、結晶粒は粗大化し易く、自動車エンジン部品の締結具に要求される特性を満たすのに必要な高破断伸びを得ることができない。一方、Ｆｅ含有量が多すぎると、粗大な晶出物を形成し却って、破断伸びが低下する。また、締結具への成形性や加工性が大きく低下する。したがって、Ｆｅの含有量は０．０５〜０．３５％の範囲とする。 Fe: 0.05 to 0.35%
Fe also forms dispersed particles in the same manner as Mn, Cr, Zr, and V, and thus contributes to improvement in elongation at break, heat resistance, etc., such as refining of crystal grains. If the Fe content is too small, the crystal grains are likely to be coarsened, and the high elongation at break required to satisfy the characteristics required for fasteners for automobile engine parts cannot be obtained. On the other hand, when there is too much Fe content, a coarse crystallization thing will be formed and rejected, and elongation at break will fall. In addition, the formability and workability of the fastener are greatly reduced. Therefore, the Fe content is in the range of 0.05 to 0.35%.

Ｍｎ：０．０５〜０．９５％
Ｍｎは、一部がマトリックスに固溶し、アルミニウム合金線棒材を固溶強化する。また、均質化熱処理時に、Ａｌ−Ｍｎ系の分散粒子を形成し、前記高温に長時間加熱されても軟化が生じにくく、加熱保持後でも室温大気中での機械的性質が低下せず、元の高強度、高耐力、高破断伸びなどの機械的諸特性が保持される。また、アルミニウム合金線棒材組織の結晶粒の微細化、繊維組織状化させることが可能となり、強度、成形性また耐食性を向上できる。 Mn: 0.05-0.95%
Mn partially dissolves in the matrix and strengthens the aluminum alloy wire rod. Also, during the homogenization heat treatment, Al-Mn-based dispersed particles are formed, and even when heated to the high temperature for a long time, softening does not easily occur. The mechanical properties such as high strength, high yield strength and high elongation at break are maintained. Moreover, it becomes possible to make the crystal grains of the aluminum alloy wire rod material structure finer and to form a fiber structure, thereby improving the strength, formability and corrosion resistance.

Ｍｎ含有量が少なすぎると、その効果が十分に得られず、自動車エンジン部品の締結具に要求される特性を満たすのに必要な、前記高強度、高耐力、高破断伸びを得ることができない。一方、Ｍｎ含有量が多すぎると、却って、強度、耐力、破断伸びが低下する。また、締結具への成形性や加工性が大きく、また耐食性が低下する。したがって、Ｍｎの含有量は０．０５〜０．９５％の範囲とする。   If the Mn content is too small, the effect cannot be sufficiently obtained, and the high strength, high yield strength, and high elongation at break required for satisfying the characteristics required for fasteners for automobile engine parts cannot be obtained. . On the other hand, when there is too much Mn content, strength, yield strength, and elongation at break decrease. Moreover, the moldability and workability to a fastener are large, and corrosion resistance falls. Therefore, the Mn content is in the range of 0.05 to 0.95%.

Ｃｒ：０．０５〜０．２５％、
Ｃｒ、Ｚｒ、Ｖは、Ｍｎ、Ｆｅと同様にそれぞれの元素を含有した分散粒子を形成し、耐軟化性や締結具への加工性の向上に寄与する。また、アルミニウム合金線棒材の熱処理時の結晶粒の粗大化を防止して、結晶粒を微細化させる作用がある。これによって、強度、耐力、破断伸びの向上に寄与し、締結具への加工性も向上する。ただし、熱間押出工程では、ピックアップ（押出材表面の押出方向に生じるむしれ状の不具合）の原因となる金属間化合物を形成し易くなる。このため、押出速度を速くすることが難しく生産性を著しく低下させる。一方、本件では、熱間加工に、熱間圧延を適用するため、ピックアップの発生はなく、Ｃｒを積極的に添加することが出来る。
但し、このＣｒ含有量が少なすぎると、例えＺｒ、Ｖを含有していても、その効果が十分に得られず、自動車エンジン部品の締結具に要求される特性を満たすのに必要な、前記高強度、高耐力、高破断伸びを得ることができない。一方、Ｃｒ含有量が多すぎると、却って、強度、耐力、破断伸びが低下する。また、締結具への加工性が大きく低下する。したがって、Ｃｒの含有量は０．０５〜０．２５％の範囲とする。 Cr: 0.05 to 0.25%,
Cr, Zr, and V form dispersed particles containing the respective elements in the same manner as Mn and Fe, and contribute to improvement in softening resistance and workability to fasteners. Moreover, it has the effect | action which prevents the coarsening of the crystal grain at the time of heat processing of an aluminum alloy wire rod, and refines | miniaturizes a crystal grain. This contributes to improvement in strength, proof stress, and elongation at break, and also improves workability to the fastener. However, in the hot extrusion process, it becomes easy to form an intermetallic compound that causes a pickup (a defective defect that occurs in the extrusion direction of the surface of the extruded material). For this reason, it is difficult to increase the extrusion speed, and the productivity is significantly reduced. On the other hand, in this case, since hot rolling is applied to hot working, there is no pickup and Cr can be positively added.
However, if this Cr content is too small, even if it contains Zr, V, the effect is not sufficiently obtained, and it is necessary to satisfy the characteristics required for fasteners for automobile engine parts, High strength, high yield strength and high elongation at break cannot be obtained. On the other hand, when there is too much Cr content, strength, yield strength, and elongation at break decrease. Moreover, the workability to a fastener falls significantly. Therefore, the Cr content is in the range of 0.05 to 0.25%.

また、Ｚｒ、Ｖは、このＣｒの作用効果を補助する目的で、Ｃｒに加えて、選択的に含有させても良い。Ｚｒ、Ｖを、このように補助的に使う場合には、Ｚｒ：０．０１〜０．３０％、Ｖ：０．０１〜０．３０％の内の一種または二種を含有させる。これらの含有量が少なすぎると効果が十分に得られず、これらの含有量が多すぎると、粗大な晶出物を形成し却って、強度、耐力、破断伸びが低下し、締結具への成形性や加工性も大きく低下する。   Zr and V may be selectively contained in addition to Cr for the purpose of assisting the effect of Cr. When Zr and V are used supplementarily in this way, one or two of Zr: 0.01 to 0.30% and V: 0.01 to 0.30% are contained. If these contents are too small, the effect cannot be obtained sufficiently, and if these contents are too large, coarse crystals are formed and strength, proof stress, elongation at break are lowered, and molding into a fastener is performed. The workability and workability are also greatly reduced.

Ｔｉ：０．０１〜０．１０％
Ｔｉは、Ｔｉ添加のための母合金に含まれるＢとともに、鋳塊の結晶粒を微細化させる作用がある。これによって、アルミニウム合金線棒材の製造過程における鋳造、圧延割れが改善される。Ｔｉ含有量が少なすぎると、その効果が十分に得られず、割れが生じ易くなり、生産性を著しく阻害する。一方、Ｔｉ含有量が多すぎると、粗大な金属間化合物を形成し却って、強度、耐力、破断伸びが低下する。また、締結具への成形性や加工性が大きく低下する。したがって、Ｔｉの含有量は０．０１〜０．１０％の範囲とする。また、ＢはＴｉと同様の理由で０．０５％以下の含有を許容する。 Ti: 0.01-0.10%
Ti has the effect of refining the crystal grains of the ingot together with B contained in the mother alloy for Ti addition. This improves casting and rolling cracks in the production process of the aluminum alloy wire rod. If the Ti content is too small, the effect cannot be obtained sufficiently, cracking is likely to occur, and productivity is significantly inhibited. On the other hand, when there is too much Ti content, a coarse intermetallic compound will be formed and strength, yield strength, and elongation at break will fall. In addition, the formability and workability of the fastener are greatly reduced. Therefore, the Ti content is in the range of 0.01 to 0.10%. Moreover, B permits 0.05% or less of inclusion for the same reason as Ti.

組織−晶析出物の微細化：
前記した通り、本発明では、先ず、６０００系アルミニウム合金線棒材組織中の晶析出物を微細化し、粗大な晶析出物（平均密度）を極力少なくする。これによって、自動車エンジン部品用などのボルトやネジなどの締結具への、ヘッダー加工やねじ転造加工などの冷間加工性を向上させる。 Refinement of structure-crystal precipitates:
As described above, in the present invention, first, crystal precipitates in the 6000 series aluminum alloy wire rod structure are refined to reduce coarse crystal precipitates (average density) as much as possible. This improves cold workability such as header processing and screw rolling processing on fasteners such as bolts and screws for automobile engine parts.

したがって、本発明では、アルミニウム合金線棒材組織中の、最大長が１０μｍ以上の前記晶析出物の平均密度が５００個／ｍｍ2 以下であるように規定し、粗大な晶析出物を無くすとともに、晶析出物を微細化し、前記成分組成との相乗効果で、前記冷間加工性を向上させる。６０００系アルミニウム合金線棒材組織中に、粗大な晶析出物が実質量存在する場合には、最大長が１０μｍ以上の前記晶析出物の平均密度が５００個／ｍｍ2 以下とならず、前記ヘッダー加工やねじ転造加工などの冷間加工性を低下させる。 Therefore, in the present invention, the average density of the crystal precipitates having a maximum length of 10 μm or more in the aluminum alloy wire rod structure is specified to be 500 pieces / mm 2 or less, and the coarse crystal precipitates are eliminated. The crystal precipitates are refined and the cold workability is improved by a synergistic effect with the component composition. When a substantial amount of coarse crystal precipitates is present in the 6000 series aluminum alloy wire rod structure, the average density of the crystal precipitates having a maximum length of 10 μm or more is not 500 pieces / mm 2 or less, Reduces cold workability such as header processing and thread rolling.

ここで、本発明で規定する晶析出物とは、前記した通り、アルミニウム合金線棒材組織の倍率４００倍程度のＳＥＭによる観察で、マトリックス内に存在する、組成を問わない不定形の粒子として確認できる（本発明で規定する最大長が１０μｍ以上か未満かの判別ができる）第２相粒子のことを言う。これら晶析出物は、主として、Ｍｇ、Ｓｉ系化合物、Ｓｉ、Ｆｅ系化合物などである（但し、ＣｕならびにＭｎ，Ｃｒ，Ｚｒ，Ｖなどの遷移元素を多く含有する場合には、前記化合物に、これらの元素を含む場合もある）。これらは、鋳塊鋳造時、鋳塊均熱処理時などに主として生成する晶出物や、熱延時、溶体化・焼入れ処理時、調質処理時などに主として生成する析出物などからなる。但し、本発明では、前記した通り、第２相粒子の組成を問わないゆえに、上記ＳＥＭによる観察の際に、ＥＤＸ（エネルギー分散型分光）などを用いた、各晶析出物の元素分析（元素量分析）を行う必要はない。即ち、ＳＥＭによって、上記の通りに観察できる前記第２相粒子を全て規定する晶析出物として取り扱う。   Here, as described above, the crystal precipitates defined in the present invention are, as described above, as amorphous particles of any composition existing in the matrix by observation with an SEM having a magnification of about 400 times the aluminum alloy wire rod structure. This refers to second phase particles that can be confirmed (can be determined whether the maximum length defined in the present invention is 10 μm or more). These crystal precipitates are mainly Mg, Si-based compounds, Si, Fe-based compounds, etc. (however, when a large amount of transition elements such as Cu and Mn, Cr, Zr, V are contained, These elements may be included). These consist of crystallized substances mainly produced during ingot casting, ingot soaking, and precipitates produced mainly during hot rolling, solution treatment / quenching treatment, tempering treatment, and the like. However, in the present invention, as described above, since the composition of the second phase particles is not limited, elemental analysis (elements) of each crystal precipitate using EDX (energy dispersive spectroscopy) or the like at the time of observation by the SEM (Quantitative analysis) is not necessary. That is, the second phase particles that can be observed as described above by SEM are handled as crystal precipitates that prescribe all.

周知の通り、これらの晶析出物は、アルミニウム合金線棒材ならずとも、均質化熱処理後の冷却中、また熱間加工温度への加熱中・保持中に粗大化しやすい。本発明では、アルミニウム合金線棒材を熱間圧延して製造するとともに、熱間圧延の温度を低くするとともに、加工率を高くすることによって、このような粗大化しやすい晶析出物を、粗大化させずに、微細化させる。即ち、前記した通り、アルミニウム合金線棒材組織中の、最大長が１０μｍ以上の前記晶析出物の平均密度が５００個／ｍｍ2 以下であるように、粗大な晶析出物を無くすとともに、晶析出物を微細化し、前記成分組成との相乗効果で、前記冷間加工性を向上させる。 As is well known, these crystal precipitates are likely to be coarsened during cooling after the homogenization heat treatment, during heating to the hot working temperature, and during holding without being an aluminum alloy wire rod. In the present invention, the aluminum alloy wire rod is manufactured by hot rolling, and the crystal precipitates that are likely to be coarsened are coarsened by lowering the temperature of the hot rolling and increasing the processing rate. Without making it finer. That is, as described above, the coarse crystal precipitates are eliminated so that the average density of the crystal precipitates having a maximum length of 10 μm or more in the aluminum alloy wire rod structure is 500 pieces / mm 2 or less. The precipitate is refined and the cold workability is improved by a synergistic effect with the component composition.

また、晶析出物を微細化すると、このアルミニウム合金線棒材組織の結晶粒も微細化させることが可能となる効果もある。このため、自動車エンジン部品の締結具などとしての、耐粒界腐食感受性などの耐食性が向上できる効果もある。   Further, when the crystal precipitates are refined, there is an effect that the crystal grains of the aluminum alloy wire rod structure can be also refined. For this reason, there exists an effect which can improve corrosion resistance, such as an intergranular corrosion resistance as a fastener of a motor vehicle engine component.

前記した通り、これらの晶析出物は、均質化熱処理後の冷却中、また熱間加工温度への加熱中・保持中に粗大化しやすい。したがって、５２０℃を超える高温での押出加工条件や熱間圧延条件では、本発明の熱延ほどに、線棒材組織の晶析出物の微細化ができず、本発明で規定する最大長が１０μｍ以上の前記晶析出物の平均密度が、必然的に、５００個／ｍｍ2 を超えて粗大化する。このため、前記冷間加工性が必然的に劣ることとなる。 As described above, these crystal precipitates are likely to become coarse during cooling after the homogenization heat treatment and during heating and holding to the hot working temperature. Therefore, under the extrusion processing conditions and hot rolling conditions at a high temperature exceeding 520 ° C., the crystal precipitates of the wire rod material structure cannot be refined as much as the hot rolling of the present invention, and the maximum length specified in the present invention is The average density of the crystal precipitates of 10 μm or more inevitably becomes larger than 500 / mm 2 . For this reason, the cold workability is necessarily inferior.

また、これら晶析出物が粗大化することによって、自動車エンジン部品の締結具としての耐食性も合わせて低下する。これが従来の６０００系アルミニウム合金の線棒材で耐食性が劣る理由である。   Moreover, when these crystal precipitates are coarsened, the corrosion resistance as a fastener for automobile engine parts is also lowered. This is the reason why the conventional 6000 series aluminum alloy wire rod material has poor corrosion resistance.

晶析出物の平均密度の測定：
本発明で規定する晶析出物の平均密度の測定面は、調質処理後のアルミニウム合金線棒材や、これを成形、加工したボルトやネジの締結具などの、長手方向（軸方向）に対する平行な任意の断面の中央部とする。これら平行断面中央部の位置における組織の走査型電子顕微鏡（ＳＥＭ）による倍率１０００倍の観察から、計測、算出される。 Measurement of average density of crystal precipitates:
The measurement surface of the average density of crystal precipitates defined in the present invention is relative to the longitudinal direction (axial direction) of the tempered aluminum alloy wire rod material and the fasteners of bolts and screws formed and processed. The central part of any parallel cross section. Measurement and calculation are performed from observation of the tissue at the central portion of these parallel cross sections at a magnification of 1000 times with a scanning electron microscope (SEM).

即ち、このＳＥＭによる観察視野の画像解析によって、観察視野内の、組成を問わない第２相粒子として観察される、個々の晶析出物の（不定形部分のうちの）最大の長さを測定するとともに、１０μｍ以上の最大長さを有する晶析出物の個数を計測する。そして、この１０μｍ以上の最大長さを有する晶析出物の１ｍｍ2 当たりの密度（個数／ｍｍ2 ）を算出する。測定は各供試線棒材の任意の前記断面５箇所で、各２５視野（計１２５視野）について行い、これらを平均化し、本発明で規定する晶析出物の平均密度とする。 That is, by the image analysis of the observation visual field by this SEM, the maximum length (of the amorphous part) of each crystal precipitate observed in the observation visual field as the second phase particle of any composition is measured. In addition, the number of crystal precipitates having a maximum length of 10 μm or more is measured. Then, the density (number / mm 2 ) per 1 mm 2 of the crystal precipitate having the maximum length of 10 μm or more is calculated. The measurement is carried out at five arbitrary cross sections of each test wire rod for 25 visual fields (total 125 visual fields), and these are averaged to obtain the average density of crystal precipitates defined in the present invention.

組織−分散粒子の密度：
前記した通り、本発明では、６０００系アルミニウム合金線棒材組織中の特定範囲の微細な分散粒子の密度を高めことで、前記高温に長時間加熱されても軟化しにくく、加熱後でも室温大気中での機械的性質が低下は小さく、元の高強度、高耐力、高破断伸びなどの機械的諸特性を保持する。 Tissue-density of dispersed particles:
As described above, in the present invention, by increasing the density of fine dispersed particles in a specific range in the 6000 series aluminum alloy wire rod structure, it is difficult to soften even when heated to the high temperature for a long time, and even after heating to room temperature atmosphere. The mechanical properties in the inside are small and the original mechanical properties such as high strength, high yield strength and high elongation at break are retained.

このため、本発明では、６０００系アルミニウム合金線棒材組織中の最大長が２００ｎｍ以上、８００ｎｍ以下の分散粒子の平均密度を５個／μｍ3 以上とする。この平均密度が５個／μｍ3 未満の場合、最大長が２００ｎｍ未満の分散粒子や最大長が８００ｎｍを越える分散粒子が多くても、前記耐軟化性は向上できない。 Therefore, in the present invention, the average density of dispersed particles having a maximum length in the structure of 6000 series aluminum alloy wire rod material of 200 nm or more and 800 nm or less is 5 particles / μm 3 or more. When the average density is less than 5 particles / μm 3 , the softening resistance cannot be improved even if there are many dispersed particles having a maximum length of less than 200 nm or dispersed particles having a maximum length exceeding 800 nm.

本発明で規定する分散粒子は、主として、Ｃｕ、Ｍｎ、Ｃｒ、Ｚｒ、Ｖなどの遷移元素と、Ａｌや他の合金元素などとの化合物である。これらは、鋳塊鋳造時、鋳塊均熱処理時などに主として生成する。但し、前記晶析出物とは違い、最大長のレベルが大きく異なる（小さい）ために、本発明で規定する分散粒子は、ＴＥＭ（透過型電子顕微鏡）を用いて、倍率５０００倍で観察、測定する。このため、ＥＤＸなどを用いた元素分析（元素量分析）によって識別する必要はない。   The dispersed particles defined in the present invention are mainly compounds of transition elements such as Cu, Mn, Cr, Zr, and V, and Al and other alloy elements. These are mainly generated at the time of ingot casting, at the time of ingot soaking, and the like. However, unlike the crystal precipitates, since the maximum length level is greatly different (small), the dispersed particles defined in the present invention are observed and measured at a magnification of 5000 times using a TEM (transmission electron microscope). To do. For this reason, it is not necessary to identify by elemental analysis (element amount analysis) using EDX or the like.

分散粒子の平均密度の測定
本発明で規定する分散粒子の平均密度の測定面は、前記晶析出物と同様、調質処理後のアルミニウム合金線棒材や、これを成形、加工したボルトやネジの締結具などの、長手方向（軸方向）に対する平行な任意の断面の中央部とする。これら平行断面中央部より、薄膜試料を作製し、成分分析装置付属のＴＥＭ（透過型電子顕微鏡）を用いて、倍率×５０００で、５視野を観察する。前記薄膜試料の厚さは２００〜３００ｎｍである。画像処理で、最大長が２００ｎｍ以上、８００ｎｍ以下の分散粒子の数をカウイントし、１μｍ3 当たりの個数を算出し、これらを平均化し、本発明で規定する分散粒子の平均密度とする。 Measurement of average density of dispersed particles As with the crystal precipitates, the average density measurement surface of the dispersed particles defined in the present invention is an aluminum alloy wire rod after tempering treatment, and bolts and screws formed and processed. The central portion of any cross section parallel to the longitudinal direction (axial direction), such as the fastener of the above. A thin film sample is prepared from the central portion of these parallel cross sections, and five fields of view are observed at a magnification of 5000 using a TEM (transmission electron microscope) attached to the component analyzer. The thin film sample has a thickness of 200 to 300 nm. In image processing, the maximum length is 200nm or more, and Kauinto number of less dispersed particles 800 nm, calculate the number per 1 [mu] m 3, they were averaged, and the average density of the dispersed particles specified in the present invention.

製造方法：
前記したような晶析出物の微細化は、前記特定組成の６０００系アルミニウム合金と、前記低温、強加工の熱間圧延による線棒材への加工との組み合わせあるいは相乗効果によって始めて、製造可能である。即ち、前記特定組成の６０００系アルミニウム合金ビレット（鋳塊）を溶製し、このビレットを均質化熱処理後、加工率９０％以上の熱間圧延を行うによって製造可能である。 Production method:
The refinement of crystal precipitates as described above can be produced only by the combination or synergistic effect of the above-mentioned 6000 series aluminum alloy with the above specific composition and the above-mentioned processing into a wire rod material by high-temperature hot rolling at low temperatures. is there. That is, it can be manufactured by melting a 6000 series aluminum alloy billet (ingot) having the above specific composition and performing hot rolling at a processing rate of 90% or more after homogenizing heat treatment of the billet.

この熱間圧延後は、必要により、更に冷間圧延、引抜、抽伸、抽芯、転造、鍛造などの所望の冷間加工を行なって、所定径や所定形状の線棒材としても良い。また、前記した通り、熱間圧延によって所定径や所定形状の線棒材とされ、その後には冷間加工しない、熱間圧延上がりの線棒材でも良い。これら所定の径のアルミニウム合金線棒材には、その後、溶体化および急冷処理と１５０〜２００℃での時効処理を記載順に行う調質処理を施す。そして、これら線棒材は、例えば、前記自動車エンジン部品の締結具である、ボルトやネジなどの用途の素材として、用途に応じて、必要により、更に所定径や所定形状への成形や加工あるいは表面処理が行われる。   After this hot rolling, if necessary, desired cold working such as cold rolling, drawing, drawing, drawing, rolling, forging, etc. may be performed to obtain a wire rod having a predetermined diameter or shape. Further, as described above, a wire rod having a predetermined diameter or a predetermined shape is formed by hot rolling, and thereafter, a wire rod that has been hot-rolled and is not cold worked may be used. These aluminum alloy wire rods having a predetermined diameter are then subjected to a tempering treatment in which the solution treatment and quenching treatment and the aging treatment at 150 to 200 ° C. are performed in the order described. These wire rods are, for example, materials for applications such as bolts and screws, which are fasteners for the automobile engine parts, and depending on the application, molding or processing to a predetermined diameter or a predetermined shape, if necessary. Surface treatment is performed.

本発明アルミニウム合金圧延線棒材の製造方法について以下に、工程順に説明する。
（溶解、鋳造冷却速度）
先ず、溶解、鋳造工程では、上記６０００系成分組成範囲内に溶解調整されたアルミニウム合金溶湯を、半連続鋳造法（ＤＣ鋳造法）等の通常の溶解鋳造法を適宜選択して鋳造する。 The manufacturing method of the aluminum alloy rolled wire rod of the present invention will be described below in the order of steps.
(Dissolution, casting cooling rate)
First, in the melting and casting process, a molten aluminum alloy melt-adjusted within the above-mentioned 6000 series component composition range is cast by appropriately selecting a normal melting casting method such as a semi-continuous casting method (DC casting method).

（均質化熱処理）
熱間圧延に先立って、鋳造されたアルミニウム合金ビレット（鋳塊）を４７０〜５６５℃の範囲で均質化熱処理（均熱処理）し、組織の均質化（鋳塊組織中の結晶粒内の偏析をなくすなど）を行う。均熱処理温度は、４７０〜５６５℃の範囲、均質化時間は２時間以上の範囲から選択される。 (Homogenization heat treatment)
Prior to hot rolling, the cast aluminum alloy billet (ingot) is subjected to homogenization heat treatment (soaking) in the range of 470 to 565 ° C. to homogenize the structure (segregation within the crystal grains in the ingot structure). Etc.). The soaking temperature is selected from the range of 470 to 565 ° C., and the homogenization time is selected from the range of 2 hours or more.

この均熱処理温度が高すぎると、分散粒子が粗大化して、最大長が８００ｎｍを越える分散粒子が多くなり、最大長が２００ｎｍ以上、８００ｎｍ以下の分散粒子の密度が少なくなる。このため、この分散粒子の平均密度を５個／μｍ3 以上とすることができず、前記耐軟化性を向上できない。一方、この均熱処理温度が低すぎると、分散粒子が微細化して、最大長が２００ｎｍ未満の分散粒子が多くなり、やはり、最大長が２００ｎｍ以上、８００ｎｍ以下の分散粒子の密度が少なくなる。このため、この分散粒子の平均密度を５個／μｍ3 以上とすることができず、前記耐軟化性を向上できない。また、この均熱処理温度が低すぎても６０００系アルミニウム合金線棒材組織中の晶析出物が小さくならず、この均熱処理温度が高すぎても晶析出物が粗大化して、最大長が１０μｍ以上の前記晶析出物の平均密度が５００個／ｍｍ2 以下とならない可能性が高くなる。更に、均熱処理温度が高すぎると、鋳塊のバーニングの危険性が増す。 If the soaking temperature is too high, the dispersed particles are coarsened, the number of dispersed particles having a maximum length exceeding 800 nm increases, and the density of dispersed particles having a maximum length of 200 nm or more and 800 nm or less decreases. For this reason, the average density of the dispersed particles cannot be made 5 particles / μm 3 or more, and the softening resistance cannot be improved. On the other hand, if the soaking temperature is too low, the dispersed particles become finer, the number of dispersed particles having a maximum length of less than 200 nm increases, and the density of dispersed particles having a maximum length of 200 nm to 800 nm also decreases. For this reason, the average density of the dispersed particles cannot be made 5 particles / μm 3 or more, and the softening resistance cannot be improved. Further, even if this soaking temperature is too low, the crystal precipitates in the 6000 series aluminum alloy wire rod structure do not become small, and even if this soaking temperature is too high, the crystal precipitates become coarse and the maximum length is 10 μm. the average density of the intermetallic compounds described above is more likely to not be a 500 / mm 2 or less. Furthermore, if the soaking temperature is too high, the risk of ingot burning increases.

この均熱処理後は、ファンなどによってビレット（鋳塊）を強制的に急冷して、冷却速度を速める方が好ましい。ビレット（鋳塊）を放冷するなど、冷却速度が遅いと、冷却過程でMgSi化合物（晶析物）が粗大化する危険性がある。このような急冷における平均冷却速度の目安は、室温を含む３００℃以下の温度まで、８０℃／ｈｒ以上とすることが好ましい。   After this soaking, it is preferable to forcibly quench the billet (ingot) with a fan or the like to increase the cooling rate. If the cooling rate is slow, such as allowing the billet (ingot) to cool, there is a risk that the MgSi compound (crystallized product) will become coarse during the cooling process. The standard of the average cooling rate in such rapid cooling is preferably 80 ° C./hr or higher up to a temperature of 300 ° C. or lower including room temperature.

（熱間圧延）
線棒材組織の晶析出物の微細化のために、前記均質化処理後のビレットに対して、低温、強加工の熱間圧延を行う。このために、熱延開始温度（熱間圧延開始温度）は、前記アルミニウム合金の成分組成や鋳塊の大きさとの関係で、３２０〜５２０℃の範囲、好ましくは３２０〜４８５℃の範囲、更に好ましくは３２０〜４７０℃の範囲、のできるだけ低い温度から選択する。熱延開始温度が高すぎる場合には、低温での圧延とならず、晶析出物が小さく粉砕されず、粗大な晶析出物が残存して、本発明で規定するようには晶析出物を微細化できない危険性が高い。一方、熱延開始温度が３２０℃未満と低すぎると、強加工での熱間圧延では特に圧延荷重が過大となって、線棒材の圧延自体が困難となる。なお、本発明では、均熱温度よりも熱延開始温度の方が必然的に低くなるので、均熱処理後、均質化熱処理温度から冷却して、前記熱延開始温度として、熱間圧延を開始する。また、均質化熱処理後に、一旦室温まで冷却し、前記熱延開始温度まで再加熱して、この再加熱温度で熱間圧延を開始しても良い。 (Hot rolling)
In order to refine the crystal precipitates of the wire rod material structure, the billet after the homogenization treatment is subjected to hot rolling at low temperature and strong processing. For this reason, the hot rolling start temperature (hot rolling start temperature) is in the range of 320 to 520 ° C., preferably in the range of 320 to 485 ° C., depending on the composition of the aluminum alloy and the size of the ingot. It is preferably selected from the lowest possible temperature in the range of 320 to 470 ° C. When the hot rolling start temperature is too high, rolling at a low temperature is not performed, the crystal precipitates are not pulverized to a small size, and coarse crystal precipitates remain. There is a high risk that it cannot be miniaturized. On the other hand, if the hot rolling start temperature is too low as less than 320 ° C., the rolling load is particularly excessive in the hot rolling in the strong working, and the rolling of the wire rod itself becomes difficult. In the present invention, the hot rolling start temperature is inevitably lower than the soaking temperature. Therefore, after the soaking, cooling is performed from the homogenizing heat treatment temperature, and hot rolling is started as the hot rolling start temperature. To do. Further, after the homogenization heat treatment, it may be once cooled to room temperature, reheated to the hot rolling start temperature, and hot rolling may be started at this reheating temperature.

熱間圧延の加工率も、前記アルミニウム合金の成分組成や、鋳塊の大きさと線棒材径との関係で、９０％以上の、できるだけ高い加工率の範囲から選択する。この加工率が少なすぎると、晶析出物が小さく粉砕されず、粗大な晶析出物が残存して、本発明で規定するようには晶析出物を微細化できない。   The hot rolling processing rate is also selected from the range of 90% or higher processing rate as high as possible depending on the composition of the aluminum alloy and the relationship between the ingot size and the wire rod diameter. If the processing rate is too small, the crystal precipitates are not pulverized small, and coarse crystal precipitates remain, and the crystal precipitates cannot be refined as defined in the present invention.

ここで、熱間圧延は、断面が円形な（丸い）線棒材を、本発明のような組織と特性とに、新たな問題や別の問題が生じることなく製造できる点で、熱間押出に比して格段に優れている。   Here, hot rolling is a hot extrusion method in which a wire rod having a circular cross section (round) can be produced without causing new problems or other problems with the structure and characteristics of the present invention. It is much better than

たとえば、本発明が対象とするような断面形状が丸い線棒材の場合、押出加工では、形状が複雑な形材の場合とは違って、形状が単純である。このため、ダイスの形状も単純となって、ビレット（鋳塊）の中心部は、ダイスによる加工を受けずに、そのまま線棒材の中心部となって押出され、線棒材の中心部はビレットの鋳造組織がそのまま残留しやすくなる。言い換えると、熱間押出加工により製造された線棒材の中心部では、ビレットの鋳造組織中に存在した粗大な晶析物が、小さく粉砕されずに、粗大なまま残存して、本発明で規定するように晶析出物を微細化できない。また、この中心部とは反対に、ビレットの表面ほど強加工となって高温化しやすく、ビレット表面に存在する融点が比較的低い晶析物が局部溶融して、ダイスなどに付着しやすくなる。このため、押出中の線棒材表面がむしれる、ムシレと称される現象発生の原因となり、ピックアップと称される、線棒材の表面不良が発生しやすくなる。このような押出材の不良を防止するためには、前記表面の晶析物を減らすために、均熱処理温度を高するか、遷移元素の量を減らす必要がある。しかし、前記した通り、均熱処理温度を高すると分散粒子が粗大化し、また、遷移元素量を減らすと分散粒子が減って密度が小さくなり、本発明で規定する分散粒子密度とできない。このように、熱間押出加工では、本発明のような組織や特性を有する線棒材を製造することが困難である。これが、自動車エンジン部品用などのボルトやネジなどの締結具として、断面が円形な線棒材を製造する場合、従来の前記特許文献１のような押出加工による製造では、特性向上に大きな限界があった理由である。   For example, in the case of a wire rod having a round cross-section as the object of the present invention, the shape is simple in extrusion, unlike the case of a shape having a complicated shape. For this reason, the shape of the die is also simplified, and the center portion of the billet (ingot) is extruded as it is as the center portion of the wire rod material without being processed by the die, and the center portion of the wire rod material is The cast structure of the billet tends to remain as it is. In other words, in the central portion of the wire rod material manufactured by hot extrusion, the coarse crystallized material existing in the cast structure of the billet is not pulverized to a small size and remains coarse. The crystal precipitate cannot be refined as specified. Contrary to this central portion, the billet surface is more strongly processed and easily heated, and the crystallized material having a relatively low melting point present on the billet surface is locally melted and easily adhered to a die or the like. For this reason, the surface of the wire rod material during extrusion is peeled off, causing a phenomenon called mushy, and the surface failure of the wire rod material called pickup tends to occur. In order to prevent such defects of the extruded material, it is necessary to increase the soaking temperature or reduce the amount of transition elements in order to reduce the crystallized matter on the surface. However, as described above, when the soaking temperature is increased, the dispersed particles become coarse, and when the amount of the transition element is decreased, the dispersed particles are reduced and the density is decreased, and the dispersed particle density specified in the present invention cannot be achieved. Thus, in the hot extrusion process, it is difficult to produce a wire rod having a structure and characteristics as in the present invention. When manufacturing a wire rod material having a circular cross section as a fastener for bolts and screws for automobile engine parts, etc., there is a great limit to the improvement in characteristics in the conventional manufacturing by extrusion as in Patent Document 1. That is why.

（調質処理）
熱間圧延後に冷間圧延などの冷間加工する場合には、熱間圧延後で冷間加工前に、適宜焼鈍しても良く、冷間加工途中に焼鈍を挟んで行っても良い。
熱間圧延後、あるいは冷間圧延などの冷間加工後に、線棒材に対する調質処理として、先ず、溶体化および急冷（焼入れ）処理を行う。この溶体化処理は、前記アルミニウム合金の成分組成との関係や、続く高温での人工時効硬化処理により強度向上に寄与する時効析出物を十分粒内に析出させるために、好ましくは、５００℃〜５７０で所定時間保持する条件で行う。この溶体化処理後、直ちに１０℃／秒以上の冷却速度で急冷処理（焼入れ処理）を行う。この溶体化処理後の急冷処理の冷却速度が遅いと、粒界上にＳｉ、ＭｇＳｉ化合物などが析出しやすくなり、機械的な特性や成形性を低下させる。 (Tempering treatment)
In the case of cold working such as cold rolling after hot rolling, annealing may be performed as appropriate after hot rolling and before cold working, or may be performed by sandwiching annealing during the cold working.
After hot rolling or after cold working such as cold rolling, as a tempering treatment for the wire rod material, first, solution treatment and rapid cooling (quenching) treatment are performed. This solution treatment is preferably performed at 500 ° C. or more in order to sufficiently precipitate aging precipitates that contribute to strength improvement by the relationship with the component composition of the aluminum alloy and the subsequent artificial age hardening treatment at high temperatures. 570 is performed under the condition of holding for a predetermined time. Immediately after the solution treatment, rapid cooling (quenching) is performed at a cooling rate of 10 ° C./second or more. When the cooling rate of the rapid cooling treatment after the solution treatment is slow, Si, MgSi compounds and the like are likely to precipitate on the grain boundaries, and mechanical properties and formability are deteriorated.

次いで、この溶体化急冷処理の後に、線棒材の強度など機械的諸特性を向上させるために、好ましくは直ちに、１５０〜２００℃での高温時効処理を行う。このような高温時効処理を行なわない場合、アルミニウム合金線棒材を常温状態での機械的性質として、引張強さ：４１０ＭＰａ以上、０．２％耐力：３５０ＭＰａ以上、伸び：６％以上とすること自体が難しい。したがって、その後１５０℃で５００時間熱処理した後の室温大気中での機械的性質として、これらの機械的諸特性を満足させることも必然的にできない。   Next, after this solution quenching treatment, a high temperature aging treatment at 150 to 200 ° C. is preferably performed immediately in order to improve mechanical properties such as strength of the wire rod. When such high-temperature aging treatment is not performed, the mechanical properties of the aluminum alloy wire rod at room temperature are set to tensile strength: 410 MPa or more, 0.2% proof stress: 350 MPa or more, and elongation: 6% or more. It is difficult. Therefore, these mechanical properties cannot necessarily be satisfied as the mechanical properties in the air at room temperature after the heat treatment at 150 ° C. for 500 hours.

（成形）
これら線棒材は、前記自動車エンジン部品の締結具など、締結具用途に応じて、更に、所定径や所定形状へのヘッダー加工やねじ転造加工などの冷間加工、成形が行われる。ここで、これら締結具に対して公知の表面処理が適宜行われて良い。
なお、アルミニウム合金線棒材を、自動車エンジン部品のボルトやネジなどの締結具用途などに成形、加工する場合には、前記調質処理をこの成形、加工の前に行っても良く、あるいはボルトやネジなどの締結具用途などに成形、加工した後で、前記調質処理を行っても良い。 (Molding)
These wire rod materials are further subjected to cold working and molding such as header processing and screw rolling processing to a predetermined diameter and shape according to the use of fasteners such as fasteners for automobile engine parts. Here, a known surface treatment may be appropriately performed on these fasteners.
In addition, when the aluminum alloy wire rod is formed and processed for fasteners such as bolts and screws of automobile engine parts, the tempering treatment may be performed before the forming and processing, or the bolt The tempering treatment may be performed after molding and processing for fasteners such as screws and screws.

以下、実施例を挙げて本発明をより具体的に説明するが、本発明はもとより下記実施例によって制限を受けるものではなく、前・後記の趣旨に適合し得る範囲で適当に変更を加えて実施することも可能であり、それらは何れも本発明の技術的範囲に含まれる。   EXAMPLES Hereinafter, the present invention will be described more specifically with reference to examples. However, the present invention is not limited by the following examples, but may be appropriately modified within a range that can meet the purpose described above and below. It is also possible to implement, and they are all included in the technical scope of the present invention.

次に、本発明の実施例を説明する。表１に示す６０００系アルミニウム合金を鋳造後、表２に示す、均熱処理温度、熱延開始温度および熱延加工率の熱間圧延を施して、断面が円形な線棒材を製造し、ボルトへの冷間加工性、耐軟化性や耐食性などの諸特性を評価した。   Next, examples of the present invention will be described. After casting the 6000 series aluminum alloy shown in Table 1, hot rolling at a soaking temperature, a hot rolling start temperature and a hot rolling process rate shown in Table 2 is performed to produce a wire rod with a circular cross section. Various properties such as cold workability, softening resistance and corrosion resistance were evaluated.

アルミニウム合金線棒材のより具体的な製造条件は以下の通りである。表１に示す各組成の６０００系アルミニウム合金を半連続鋳造法によりビレット（鋳塊）に鋳造した。これらビレットは熱延加工率を変えるために径を変え、表２に示す均熱処理温度で共通して４時間（ｈｒ）の均熱処理した。そして、その後一旦室温まで冷却した後に、表２に示す各熱延開始温度まで再加熱し、表２に示す加工率で、熱間圧延し、共通してΦ１３ｍｍの線棒材を製造した。ここで、前記均熱処理後のビレットはファンによって強制的に急冷し、３００℃以下までの平均冷却速度を１５０℃／ｈｒとした。   More specific production conditions for the aluminum alloy wire rod are as follows. A 6000 series aluminum alloy having each composition shown in Table 1 was cast into a billet (ingot) by a semi-continuous casting method. These billets were changed in diameter in order to change the hot rolling rate, and were soaked for 4 hours (hr) in common at the soaking temperature shown in Table 2. And after cooling to room temperature once after that, it reheated to each hot rolling start temperature shown in Table 2, and it hot-rolled with the processing rate shown in Table 2, and manufactured the wire rod material of (phi) 13mm in common. Here, the billet after the soaking was forcibly quenched by a fan, and the average cooling rate up to 300 ° C. or less was set to 150 ° C./hr.

更に、この熱延上がりの線棒材を冷間でΦ３．５ｍｍまで伸線加工した。次にこの細径化させた線棒材を所定に長さに切断し、冷間にてヘッダー加工、ねじ転造加工を行い、多数のＭ４のボルトを作製した。次に、この作製したボルトを、５７０℃で３時間の溶体化処理した後水焼入れし、その後１８０℃で９時間の高温時効処理を行う、調質処理を行った。この際、前記Ｍ４のボルト作製と調質処理との順序について、前記冷間加工にてボルトに作製後に前記調質処理を行う工程をＡ工程、一方、前記調質処理を行った後に前記冷間加工にてボルトに作製する工程をＢ工程とした。   Further, this hot-rolled wire rod was cold drawn to Φ3.5 mm. Next, the wire rod material reduced in diameter was cut into a predetermined length and subjected to header processing and screw rolling processing in a cold state to produce a large number of M4 bolts. Next, the prepared bolt was subjected to a solution treatment at 570 ° C. for 3 hours, followed by water quenching, followed by a high temperature aging treatment at 180 ° C. for 9 hours. At this time, with respect to the order of the M4 bolt preparation and the tempering process, the process of performing the tempering process after the bolt is manufactured in the cold working after the tempering process is performed after the tempering process. A process for producing a bolt by inter-processing was designated as a B process.

加工性:
このボルト加工の際に、ヘッダー加工性と転造加工性（Ｍ４）を評価し、割れなどの不良が生じずに、全量をボルトに加工できた例を○、割れなどの不良が生じて、加工性が悪いと判断された例を×と評価した。 Processability:
In this bolt processing, the header processability and rolling processability (M4) were evaluated, and the example that the entire amount could be processed into bolts without defects such as cracks occurred, defects such as cracks occurred, The example judged that workability was bad was evaluated as x.

これらボルトから供試材を切り出し、下記の通り、アルミニウム合金線棒材の組織や特性として、組織や特性を測定、評価した。これらの結果も合わせて表２に示す。   Sample materials were cut out from these bolts, and the structure and characteristics were measured and evaluated as the structure and characteristics of the aluminum alloy wire rod as described below. These results are also shown in Table 2.

組織：
前記ボルト供試材における、晶析出物と分散粒子の平均密度を前記した方法にて測定した。 Organization:
The average density of crystal precipitates and dispersed particles in the bolt specimen was measured by the method described above.

機械的性質：
前記ボルト供試材よりＦｅｄ．４型の小型引張試験片を作製し、５ｍｍ／分のクロスヘッド速度で、常温中で、破断まで引張試験を行った。応力―歪速度より、引張強さ（ＭＰａ）、０．２％耐力（ＭＰａ）を測定した。伸び（％）は小型引張試験片の平行部の引張試験前後のケガキ線の間隔（引張試験前の間隔１０ｍｍ）より算出した。なお、これらの測定値は、５本のボルト供試材の各測定値の平均値とした。 mechanical nature:
From the bolt specimen, Fed. A 4 type small tensile test piece was prepared, and a tensile test was performed until breakage at room temperature at a crosshead speed of 5 mm / min. From the stress-strain rate, tensile strength (MPa) and 0.2% yield strength (MPa) were measured. The elongation (%) was calculated from the spacing between the marking lines before and after the tensile test of the parallel part of the small tensile test piece (interval 10 mm before the tensile test). In addition, these measured values were made into the average value of each measured value of five bolt test materials.

高温に長時間曝された後の機械的性質：
耐軟化性としての加熱後の引張特性は、ボルトを１５０℃で５００ｈｒ熱処理した後、引張試験片を作製し、前記常温での引張試験と同様に、常温で引張試験を行い、引張強さ、耐力、伸びを測定した。 Mechanical properties after prolonged exposure to high temperatures:
Tensile properties after heating as softening resistance were obtained by heat-treating a bolt at 150 ° C. for 500 hours, then preparing a tensile test piece, and performing a tensile test at normal temperature in the same manner as the normal temperature tensile test, Yield strength and elongation were measured.

耐食性：
耐食性を評価するために、前記各ボルト供試材（高温に長時間曝す前）のＪＩＳ−Ｗ１１０３法の４．４．３項に記載の方法に準じて、腐食試験を行った。即ち、腐食試験条件は、まず、９３℃のエッチング溶液（７０％濃硝酸５０ｍｌ、４８％、ふっ化水素酸５ｍｌ、蒸留水９４５ｍｌの組成）に１分間浸漬後、蒸留水で洗浄し、乾燥させた。その後、３０℃の腐食促進液（ＮａＣｌを５７ｇ、３０％過酸化水素水１０ｍｌを蒸留水で１ｌに希釈したもの) に６時間浸漬した。そして、試験片平行断面を、エッチング溶液（７０％濃硝酸２．５ｍｌ、濃塩酸１．５ｍｌ、４８％ふっ化水素酸１．０ｍｌ、蒸留水９５．０ｍｌの組成) に１０秒間浸漬後、蒸留水で洗浄して乾燥した。この試験片平行断面の腐食状況を２００倍の金属顕微鏡により観察した。腐食の観察は、前記顕微鏡視野内において、他の孔食腐食や全面腐食などと区別して、６０６１−Ｔ６を比較材として、腐食の程度を判断した。これらの結果を、腐食の程度が大きい場合を×、同等もしくは同等以下の程度の○とした。 Corrosion resistance:
In order to evaluate the corrosion resistance, a corrosion test was carried out in accordance with the method described in Section 4.4.3 of the JIS-W1103 method for each of the bolt specimens (before being exposed to a high temperature for a long time). That is, the corrosion test conditions were as follows. First, after immersion in an etching solution at 93 ° C. (composition of 70% concentrated nitric acid 50 ml, 48%, hydrofluoric acid 5 ml, distilled water 945 ml), washed with distilled water and dried. It was. Thereafter, it was immersed in a corrosion accelerating solution at 30 ° C. (57 g of NaCl, 10 ml of 30% hydrogen peroxide solution diluted to 1 liter with distilled water) for 6 hours. Then, the test specimen parallel section was immersed in an etching solution (composition of 70% concentrated nitric acid 2.5 ml, concentrated hydrochloric acid 1.5 ml, 48% hydrofluoric acid 1.0 ml, distilled water 95.0 ml) for 10 seconds, followed by distillation. Washed with water and dried. The corrosion state of this test piece parallel cross section was observed with a 200-fold metal microscope. In the observation of the corrosion, the degree of corrosion was determined using 6061-T6 as a comparative material in the microscope field of view, distinguishing it from other pitting corrosion and overall corrosion. These results were evaluated as “x” when the degree of corrosion was large, and “o” as the same or equivalent.

表１の合金番号１〜９を用いた、表２の各発明例１〜１０は、本発明成分組成範囲内で、かつ、前記した好ましい条件範囲で、低温、強加工の熱間圧延を行なっている。このため、表２に示す通り、本発明で規定する晶析出物と分散粒子の平均密度となっている組織を有している。この結果、前記１５０℃で５００時間、高温長時間熱処理された後の室温大気中での機械的性質として、引張強さ：４１０ＭＰａ以上、０．２％耐力：３５０ＭＰａ以上、伸び：６％以上の耐軟化性を有する。また、耐食性にも優れている。   Inventive Examples 1 to 10 in Table 2 using Alloy Nos. 1 to 9 in Table 1 are subjected to hot rolling at low temperature and strong working within the composition range of the present invention and within the above-described preferable condition range. ing. For this reason, as shown in Table 2, it has the structure | tissue which becomes the average density of the crystal precipitate prescribed | regulated by this invention, and a dispersed particle. As a result, the mechanical properties in the air at room temperature after heat treatment at 150 ° C. for 500 hours for a long time are as follows: tensile strength: 410 MPa or more, 0.2% proof stress: 350 MPa or more, elongation: 6% or more. Has softening resistance. It also has excellent corrosion resistance.

これに対して、表２の比較例１１〜２１は、表１に示す合金番号１０〜２０の合金であり、成分組成が本発明の範囲を外れている。
比較例１０はＭｎ含有量が少な過ぎる（Ｍｎを含有していない）。
比較例１１はＣｕ含有量が少な過ぎる（Ｃｕを含有していない）。
比較例１２はＣｒ含有量が少な過ぎる（Ｃｒを含有していない）。
比較例１３はＭｎ含有量が多すぎる。
比較例１４はＣｕ含有量が多すぎる。
比較例１５はＣｒ含有量が多すぎる
比較例１６はＺｎ含有量が多すぎる。
比較例１７はＳｉ含有量が多すぎる。
比較例１８はＭｇ含有量が多すぎる。
比較例１９はＭｇ含有量が少な過ぎる。
比較例２０はＳｉ含有量が少な過ぎる。 On the other hand, the comparative examples 11-21 of Table 2 are the alloys of the alloy numbers 10-20 shown in Table 1, and a component composition is outside the range of this invention.
The comparative example 10 has too little Mn content (it does not contain Mn).
The comparative example 11 has too little Cu content (it does not contain Cu).
The comparative example 12 has too little Cr content (it does not contain Cr).
The comparative example 13 has too much Mn content.
Comparative Example 14 has too much Cu content.
Comparative Example 15 has too much Cr content and Comparative Example 16 has too much Zn content.
The comparative example 17 has too much Si content.
Comparative Example 18 has too much Mg content.
The comparative example 19 has too little Mg content.
The comparative example 20 has too little Si content.

また、表２の比較例２２〜２５は、表１に示す本発明成分組成範囲内である合金番号１の合金を用いているものの、前記した好ましい条件範囲で、低温、強加工の熱間圧延を行なっていない。
比較例２２は熱延の圧下率は高いものの、均熱温度が高すぎる。
比較例２３は熱延開始温度は低いものの、均熱温度も低すぎる。
比較例２４は熱延の圧下率は高いものの、熱延開始温度が高すぎる。
比較例２５は熱延開始温度は低いものの、熱延の圧下率が低すぎる。 Moreover, although the comparative examples 22-25 of Table 2 use the alloy of the alloy number 1 which is in this invention component composition range shown in Table 1, it is the above-mentioned preferable condition range, and is hot-rolling of low temperature and strong work. Is not done.
Although the comparative example 22 has a high hot rolling reduction, the soaking temperature is too high.
In Comparative Example 23, the hot rolling start temperature is low, but the soaking temperature is too low.
In Comparative Example 24, the hot rolling reduction temperature is high, but the hot rolling start temperature is too high.
In Comparative Example 25, the hot rolling start temperature is low, but the hot rolling reduction is too low.

このため、各比較例は、表２に示す通り、本発明で規定する組織を有していないか、有していても、特に高温に長時間曝された後の機械的性質が劣る。また、耐食性も劣っている。   For this reason, as shown in Table 2, each comparative example does not have or has the structure defined in the present invention, but the mechanical properties after being exposed to a high temperature for a long time are inferior. Moreover, corrosion resistance is also inferior.

したがって、以上の実施例の結果から、本発明における成分や組織の各要件のボルトへの冷間加工性、耐軟化性や耐食性などに対する臨界的な意義乃至効果が裏付けられる。また、好ましい製造条件の本発明組織を得るための臨界的な意義乃至効果が裏付けられる。   Therefore, the results of the above examples support the critical significance or effects on the cold workability, softening resistance, corrosion resistance, and the like of the bolts of the requirements of the components and structures in the present invention. Moreover, the critical significance or effect for obtaining the structure of the present invention under preferable production conditions is supported.

Figure 2010189750
Figure 2010189750

Figure 2010189750
Figure 2010189750

本発明によれば、長時間高温に曝された（長時間加熱された）場合にも、耐軟化性が優れて高い機械的諸特性を保持できるとともに、冷間加工性や耐食性も合わせて優れた、６０００系高強度アルミニウム合金線棒材およびその製造方法を提供することができる。このため、自動車エンジン部品のボルトやネジなどのアルミニウム合金製締結具などに、好適に用いることができる。   According to the present invention, even when exposed to a high temperature for a long time (heated for a long time), it has excellent softening resistance and can maintain high mechanical properties, and also has excellent cold workability and corrosion resistance. In addition, a 6000 series high-strength aluminum alloy wire rod and a method for producing the same can be provided. For this reason, it can be used suitably for aluminum alloy fasteners such as bolts and screws of automobile engine parts.

Claims (6)

熱間圧延を施されたＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金線棒材であって、質量％で、Ｍｇ：０．６５〜１．７５％、Ｓｉ：０．７０〜１．３５％、Ｃｕ：０．４０〜１．０５％、Ｆｅ：０．０５〜０．３５％、Ｍｎ：０．０５〜０．９５％、Ｃｒ：０．０５〜０．２５％、Ｔｉ：０．０１〜０．１０％を各々含み、残部Ａｌおよび不可避的不純物からなり、組織中の最大長が２００ｎｍ以上、８００ｎｍ以下の分散粒子の平均密度が５個／μｍ3 以上であるとともに、最大長が１０μｍ以上の晶析出物の平均密度が５００個／ｍｍ2 以下であることを特徴とする耐軟化性に優れた高強度アルミニウム合金線棒材。 A hot-rolled Al—Mg—Si-based aluminum alloy wire rod in mass%, Mg: 0.65 to 1.75%, Si: 0.70 to 1.35%, Cu: 0.40 to 1.05%, Fe: 0.05 to 0.35%, Mn: 0.05 to 0.95%, Cr: 0.05 to 0.25%, Ti: 0.01 to 0. A crystal comprising 10% each, comprising the balance Al and inevitable impurities, the average length of dispersed particles having a maximum length of 200 nm or more and 800 nm or less in the structure of 5 / μm 3 or more, and a maximum length of 10 μm or more A high-strength aluminum alloy wire rod excellent in softening resistance, wherein the average density of precipitates is 500 pieces / mm 2 or less. 前記アルミニウム合金線棒材を１５０℃で５００時間熱処理した後の室温大気中での機械的性質として、引張強さ：４１０ＭＰａ以上、０．２％耐力：３５０ＭＰａ以上、伸び：６％以上である請求項１に記載の耐軟化性に優れた高強度アルミニウム合金線棒材。   The mechanical properties in air at room temperature after heat-treating the aluminum alloy wire rod at 150 ° C. for 500 hours are tensile strength: 410 MPa or more, 0.2% proof stress: 350 MPa or more, elongation: 6% or more. Item 2. A high-strength aluminum alloy wire rod excellent in softening resistance according to Item 1. 前記アルミニウム合金線棒材が、質量％で、更に、Ｚｒ：０．０１〜０．３０％、Ｖ：０．０１〜０．３０％の内の一種また二種を含有する請求項１または２に記載の耐軟化性に優れた高強度アルミニウム合金線棒材。   3. The aluminum alloy wire rod according to claim 1 or 2, wherein the aluminum alloy wire rod further contains one or two of Zr: 0.01 to 0.30% and V: 0.01 to 0.30% by mass%. A high-strength aluminum alloy wire rod excellent in softening resistance described in 1. 前記アルミニウム合金線棒材の用途が自動車エンジン部品の締結具である請求項１乃至３のいずれか１項に記載の耐軟化性に優れた高強度アルミニウム合金線棒材。   The high-strength aluminum alloy wire rod material excellent in softening resistance according to any one of claims 1 to 3, wherein the aluminum alloy wire rod material is used as a fastener for automobile engine parts. 質量％で、Ｍｇ：０．６５〜１．７５％、Ｓｉ：０．７０〜１．３５％、Ｃｕ：０．４０〜１．０５％、Ｆｅ：０．０５〜０．３５％、Ｍｎ：０．０５〜０．９５％、Ｃｒ：０．０５〜０．２５％、Ｔｉ：０．０１〜０．１０％を各々含み、残部Ａｌおよび不可避的不純物からなり、必要により更に、Ｚｒ：０．０１〜０．３０％、Ｖ：０．０１〜０．３０％の内の一種または二種を含有したＡｌ−Ｍｇ−Ｓｉ系アルミニウム合金鋳塊を溶製し、この鋳塊を４７０〜５６５℃の範囲で均質化熱処理後、熱延開始温度が３２０〜５２０℃の範囲で加工率９５％以上の熱間圧延を行い、必要により更に冷間加工して、所定の径のアルミニウム合金線棒材とし、その後、溶体化および急冷処理と１５０〜２００℃での時効処理を記載順に行う調質処理を施した後の組織中の、最大長が２００ｎｍ以上、８００ｎｍ以下の分散粒子の平均密度が５個／μｍ3 以上とするとともに、最大長が１０μｍ以上の晶析出物の平均密度が５００個／ｍｍ2 以下とすることを特徴とする耐軟化性に優れた高強度アルミニウム合金線棒材の製造方法。 In mass%, Mg: 0.65 to 1.75%, Si: 0.70 to 1.35%, Cu: 0.40 to 1.05%, Fe: 0.05 to 0.35%, Mn: 0.05 to 0.95%, Cr: 0.05 to 0.25%, Ti: 0.01 to 0.10%, respectively, the balance consisting of Al and inevitable impurities, and if necessary, Zr: 0 0.01 to 0.30%, V: 0.01 to 0.30% of Al-Mg-Si-based aluminum alloy ingot containing one or two of them was melted, and this ingot was 470 to 565 After homogenization heat treatment in the range of ℃, hot rolling with a working rate of 95% or more at a hot rolling start temperature in the range of 320 to 520 ℃, further cold working as necessary, aluminum alloy wire rod with a predetermined diameter After that, a tempering treatment is performed in which the solution treatment and quenching treatment and the aging treatment at 150 to 200 ° C. are performed in the order described. The in tissue after applying, the maximum length is 200nm or more, with an average density of less dispersed particles 800nm is 5 pieces / [mu] m 3 or more, the average density of the maximum length 10μm or more intermetallic compounds is 500 / A method for producing a high-strength aluminum alloy wire rod excellent in softening resistance, characterized by being made to be 2 mm 2 or less. 前記アルミニウム合金線棒材を、前記調質処理を行う前か後に、自動車エンジン部品の締結具に加工する請求項５に記載の耐軟化性に優れた高強度アルミニウム合金線棒材の製造方法。   The method for producing a high-strength aluminum alloy wire rod excellent in softening resistance according to claim 5, wherein the aluminum alloy wire rod is processed into a fastener for an automobile engine part before or after the tempering treatment.
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WO2021153412A1 (en) * 2020-01-30 2021-08-05 住友電気工業株式会社 Aluminum alloy, aluminum alloy wire, aluminum alloy member, and bolt
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CN112746199A (en) * 2020-12-16 2021-05-04 银邦金属复合材料股份有限公司 Aluminum alloy for shutter and preparation method thereof
CN114892050A (en) * 2022-05-23 2022-08-12 江苏亚太航空科技有限公司 High-strength Al-Mg-Si aluminum alloy and preparation process and application thereof
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