JP2016141880A - Aluminum alloy and material, and manufacturing method of extrusion material - Google Patents
Aluminum alloy and material, and manufacturing method of extrusion material Download PDFInfo
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Abstract
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本発明は高強度でありながら高い伸びを有するアルミニウム合金、それを用いたアルミニウム合金材料及び押出材の製造方法に関する。 The present invention relates to an aluminum alloy having high strength and high elongation, an aluminum alloy material using the aluminum alloy, and a method for producing an extruded material.
従来のＡｌ−Ｚｎ−Ｍｇ−Ｃｕ系合金は高強度が得られるものの、伸び特性が不充分で構造材に適用するのが困難であった。
特許文献１には、Ｍｇ：１．５〜２．０質量％（以下単に％と称する），Ｚｎ：７．０〜９．０％，Ｃｕ：０．２〜０．４％等からなり、溶体化処理後に冷却速度１０００℃／ｍｉｎ以上で急冷する高強度アルミニウム合金押出材を開示する。
本材料は引張強さ５００〜６００ＭＰａ級の高強度材料としては優れているが、さらなる高強度材料が要求されている。
特許文献２は、Ｍｇ：０．９％〜１．３％，Ｚｎ：８．０〜１０．０％，Ｃｕ：０．４５〜０．５５％，Ｚｒ：０．１〜０．２％のアルミニウム合金からなる押出材を室温に保持後に２段階に加熱処理する製造方法を開示する。
この材料はＣｕ成分量が比較的少なく、強度が５００ＭＰａ以下で不充分である。
特許文献３は、Ｍｇ：１．９〜２．６％，Ｚｎ：５．７〜６．７％，Ｃｕ：２．０〜２．６％，Ｚｒ：０．０８〜０．１５％を含有し、２段階の均質化処理後に、熱間加工、溶体化焼入れ、冷間加工、時効処理を順に行うことでＡｌ３Ｚｒの析出を制御する技術を開示する。
同公報に開示する材料は、破壊靭性の改善効果は認められるものの、所定の圧延材に限定される。
特許文献４は、Ｍｇ：１．０〜１．５％，Ｚｎ：５．０〜７．０％，Ｃｕ：０．１〜０．３％，Ｚｒ：０．０５〜０．２％等を含有し、表面再結晶層を制御したアルミニウム合金押出材を開示する。
しかし、同公報に開示する材料は引張強度が５００ＭＰａ以下と不充分である。
Although conventional Al-Zn-Mg-Cu-based alloys can provide high strength, they have insufficient elongation characteristics and are difficult to apply to structural materials.
Patent Document 1 includes Mg: 1.5 to 2.0% by mass (hereinafter simply referred to as%), Zn: 7.0 to 9.0%, Cu: 0.2 to 0.4%, and the like. Disclosed is a high-strength aluminum alloy extruded material that is rapidly cooled at a cooling rate of 1000 ° C./min or higher after solution treatment.
Although this material is excellent as a high-strength material having a tensile strength of 500 to 600 MPa, a further high-strength material is required.
In Patent Document 2, Mg: 0.9% to 1.3%, Zn: 8.0 to 10.0%, Cu: 0.45 to 0.55%, Zr: 0.1 to 0.2% A manufacturing method is disclosed in which an extruded material made of an aluminum alloy is heat-treated in two stages after being kept at room temperature.
This material has a relatively small amount of Cu component and is insufficient with a strength of 500 MPa or less.
Patent Document 3 contains Mg: 1.9 to 2.6%, Zn: 5.7 to 6.7%, Cu: 2.0 to 2.6%, Zr: 0.08 to 0.15% and, after homogenization in two stages, hot working, solution heat hardening, cold working, discloses a technique for controlling the precipitation of Al 3 Zr by performing aging treatment in order.
The material disclosed in the publication is limited to a predetermined rolled material although an effect of improving fracture toughness is recognized.
Patent Document 4 describes Mg: 1.0 to 1.5%, Zn: 5.0 to 7.0%, Cu: 0.1 to 0.3%, Zr: 0.05 to 0.2%, and the like. An aluminum alloy extruded material containing a controlled surface recrystallized layer is disclosed.
However, the material disclosed in the publication has an insufficient tensile strength of 500 MPa or less.
本発明は、高強度でありながら伸び特性に優れるアルミニウム合金、それを用いた材料と押出材の製造方法の提供を目的とする。 An object of this invention is to provide the manufacturing method of the aluminum alloy which is excellent in the elongation characteristic while being high strength, and the material and extrusion material using the same.
本発明に係るアルミニウム合金は、以下質量％にて、Ｍｇ：１．５〜２．０％，Ｚｎ：９．０〜１１．０％，Ｃｕ：２．０〜２．５％，Ｚｒ：０．１５〜０．２５％であり、残部がＡｌ及び不純物であることを特徴とする。
このようなアルミニウム合金の組成は、特許文献１〜４のいずれとも相違し、それらに比較して高強度が得られる。
The aluminum alloy according to the present invention has the following mass%: Mg: 1.5 to 2.0%, Zn: 9.0 to 11.0%, Cu: 2.0 to 2.5%, Zr: 0 15 to 0.25%, and the balance is Al and impurities.
The composition of such an aluminum alloy is different from any of Patent Documents 1 to 4, and high strength is obtained as compared with them.
本発明は金属組織の母相中に準安定相η’（ＭｇＺｎ２）の折出形態及びその前駆構造であるＧＰ（１）ゾーン，ＧＰ（２）ゾーンを制御したことにより高強度とそれに相反する高い伸び特性との両立を図ることができた点に特徴がある。
その態様として本発明に係るアルミニウム合金材料は、請求項１に記載のアルミニウム合金を４５０〜５５０℃の温度にて溶体化処理後に焼入れ処理し、次に圧延率５０％以上の冷間圧延及び１００〜１５０℃の温度で人工時効処理することで、金属の折出組織にＧＰ（１）ゾーン又は／及びＧＰ（２）ゾーンを有することを特徴とする。
また、前記金属の折出組織に、さらに母相の結晶格子に対して２層周期のη’相又は／及びη１相と、母相中にＡｌ３Ｚｒを有することを特徴とする。
従来のＡｌ−Ｚｎ−Ｍｇ−Ｃｕ系の合金においては 母相の結晶格子に対して３層周期にη’相、η１相が析出していたのに対して、本発明では上記のように２層周期のη’、η１相となっている。
ここで前駆構造であるＧＰゾーンのうち、ＧＰ（１）ゾーンは、母相の結晶格子に整合した配列を持って析出する溶質の、極めて微細な板状の相である。
その長さは数ｎｍと微細である。
ＧＰ（２）ゾーンは母相の結晶格子に対して３次元的に規則的配列を有する。
また、Ａｌ３Ｚｒは微細な析出物である。
The present invention controls the strength of the metastable phase η ′ (MgZn 2 ) in the matrix of the metallographic structure and the GP (1) zone and GP (2) zone, which are the precursor structures thereof, and thereby provides high strength. It is characterized in that it was possible to achieve both high elongation characteristics.
As an aspect thereof, an aluminum alloy material according to the present invention is obtained by subjecting the aluminum alloy according to claim 1 to a quenching treatment after a solution treatment at a temperature of 450 to 550 ° C., followed by cold rolling with a rolling rate of 50% or more and 100 It is characterized by having a GP (1) zone and / or a GP (2) zone in a metal folding structure by performing an artificial aging treatment at a temperature of ˜150 ° C.
Further, the metal folding structure further includes a η ′ phase or / and η 1 phase having a two-layer period with respect to the crystal lattice of the parent phase, and Al 3 Zr in the parent phase.
In the conventional Al—Zn—Mg—Cu alloy, the η ′ phase and η 1 phase were precipitated in a three-layer cycle with respect to the crystal lattice of the parent phase, whereas in the present invention, as described above, It has η ′ and η 1 phases with a two-layer period.
The GP (1) zone in the GP zone which is a precursor structure is a very fine plate-like phase of a solute that precipitates with an alignment matched with the crystal lattice of the parent phase.
Its length is as fine as several nm.
The GP (2) zone has a three-dimensional regular arrangement with respect to the crystal lattice of the parent phase.
Al 3 Zr is a fine precipitate.
本発明の具体的な態様としては、請求項１に記載のアルミニウム合金を用いてビレットを鋳造し、前記ビレットを用いて押出加工及びその直後に急冷又は、押出加工後に温度４５０〜５００℃にて溶体化処理及び焼入れ処理をし、次に圧延率５０％以上の冷間圧延及び１００〜１５０℃の温度で人工時効処理することで、引張強さ７００ＭＰａ以上、耐力値６００ＭＰａ以上であって、伸びが８％以上有することを特徴とするアルミニウム合金押出材の製造方法が例として挙げられる。 As a specific aspect of the present invention, a billet is cast using the aluminum alloy according to claim 1 and the billet is extruded and immediately cooled immediately thereafter, or at a temperature of 450 to 500 ° C. after the extrusion. Solution treatment and quenching treatment, followed by cold rolling with a rolling rate of 50% or more and artificial aging treatment at a temperature of 100 to 150 ° C., have a tensile strength of 700 MPa or more, a proof stress value of 600 MPa or more, and elongation As an example, a method for producing an aluminum alloy extruded material characterized by having a content of 8% or more is mentioned.
本発明に係る合金組成はＭｇ，Ｚｎ，Ｃｕの成分量をＭｇ：１．５〜２．０％，Ｚｎ：９．０〜１１．０％，Ｃｕ：２．０〜２．５％と従来のＡｌ−Ｚｎ−Ｍｇ−Ｃｕ系合金よりも比較的高濃度に設定するとともに、Ｚｒを０．１５〜０．２５％添加することで析出組織を制御し、高強度及び高い伸び特性を実現したものである。
従って、本発明において他の成分は次のように取り扱う。
Ｔｉ成分は合金鋳造時の微細化に寄与することから必要に応じて添加してもよく、添加する場合はＴｉ：０．０１〜０．０５％の範囲が好ましく、この範囲でＴｉを添加した合金も本発明に含まれる。
その他の成分は不純物として取り扱い金属組織に影響を与えない範囲にて含有することが許容される。
Ｆｅ，Ｓｉ成分は製造工程にて不可避的に混入する成分であり、いずれも０．２％程度までは許容される。
In the alloy composition according to the present invention, the Mg, Zn and Cu component amounts are conventionally Mg: 1.5 to 2.0%, Zn: 9.0 to 11.0%, Cu: 2.0 to 2.5%. In addition to the relatively high concentration of the Al-Zn-Mg-Cu alloy, 0.15 to 0.25% Zr was added to control the precipitation structure, realizing high strength and high elongation characteristics. Is.
Therefore, in the present invention, the other components are handled as follows.
The Ti component contributes to miniaturization at the time of casting the alloy, so it may be added as necessary. When added, Ti is preferably in the range of 0.01 to 0.05%, and Ti is added in this range. Alloys are also included in the present invention.
The other components are allowed to be contained as impurities in a range that does not affect the metal structure handled.
Fe and Si components are components that are inevitably mixed in the manufacturing process, and both are allowed up to about 0.2%.
本発明においては合金成分範囲の調整により、好ましくは金属組織の制御により、引張強さが７００ＭＰａ以上の高強度でありながら、伸び８％以上を有することから従来、適用できないとされていた構造部材に適用でき、軽量化に寄与できる。 In the present invention, a structural member that has been conventionally considered to be inapplicable because it has an elongation of 8% or more while having a high strength of 700 MPa or more by adjusting the alloy composition range, preferably by controlling the metal structure. Can contribute to weight reduction.
本発明に係るアルミニウム合金材料を比較評価したので以下説明する。
図１の表に示す各組成のアルミニウム合金を調整及び鋳造し、評価サンプルを押出加工した。
次に図２の表に示す条件で溶体化処理し、水焼入れ（ＷＱ）した後に圧延率約５３％の冷間圧延をした。
次に図２の表に基づいて焼戻し（人工時効処理）をした。
このようにして得られた材料の評価結果を図３に示す。
表中に記載の物性値は本発明における目標値を示す。
また、実施例１にて得られた材料の金属組織写真を図４及び図５に示す。
機械的性質はＪＩＳ Ｚ２２４１に基づいて実施した。
結晶粒径は押出方向に沿って鏡面研磨し、測定した。
本発明においては結晶粒径が小さい方が好ましく、平均結晶粒径を５０μｍ以下と設定し、評価した。
その結果、実施例１，２は、合金組成が設定範囲内にあり、図４，図５に示すようにＧＰ（１）ゾーン，ＧＰ（２）ゾーン，Ａｌ３Ｚｒが析出し、母相の結晶格子に対して２層間毎にη’相が現れているので機械的性質における全ての目標値をクリアしている。
比較例１は、Ｍｇ、Ｚｎ、Ｃｕ、Ｚｒが設定より少ないためＧＰ（１），ＧＰ（２），２層のη、Ａｌ３Ｚｒの析出がなく、機械的性質の目標を満足しない
比較例２〜７、９、１１〜１７は、Ｚｎ、Ｃｕ、Ｚｒが設定より少ないためＧＰ（１），ＧＰ（２），２層のη’，Ａｌ３Ｚｒの析出がなく、機械的性質の目標を満足しない。
比較例８、１０は、Ｍｇ、Ｃｕ、Ｚｒが設定より少ないためＧＰ（１），ＧＰ（２），２層のη’，Ａｌ３Ｚｒの析出がなく、機械的性質の目標を満足しない。
比較例１８は、Ｃｕ、Ｚｒが設定より少ないためＧＰ（１），ＧＰ（２），Ａｌ３Ｚｒの析出がなく、機械的性質の目標を満足しない。
The aluminum alloy material according to the present invention was comparatively evaluated and will be described below.
An aluminum alloy having each composition shown in the table of FIG. 1 was prepared and cast, and an evaluation sample was extruded.
Next, solution treatment was performed under the conditions shown in the table of FIG. 2, water quenching (WQ) was performed, and then cold rolling was performed at a rolling rate of about 53%.
Next, tempering (artificial aging treatment) was performed based on the table of FIG.
The evaluation result of the material thus obtained is shown in FIG.
The physical property values described in the table indicate target values in the present invention.
Moreover, the metal structure photograph of the material obtained in Example 1 is shown in FIGS.
The mechanical properties were implemented based on JIS Z2241.
The crystal grain size was measured by mirror polishing along the extrusion direction.
In the present invention, a smaller crystal grain size is preferable, and the average crystal grain size was set to 50 μm or less for evaluation.
As a result, in Examples 1 and 2, the alloy composition is within the set range, and GP (1) zone, GP (2) zone, and Al 3 Zr are precipitated as shown in FIGS. Since the η ′ phase appears every two layers with respect to the crystal lattice, all target values in the mechanical properties are cleared.
Comparative Example 1 has no Mg, Zn, Cu, and Zr than set, so GP (1), GP (2), η of two layers, Al 3 Zr does not precipitate, and does not satisfy the target of mechanical properties 2-7, 9, 11-17 have less Zn, Cu, and Zr than set, so there is no precipitation of GP (1), GP (2), two-layer η ', Al 3 Zr, and the target of mechanical properties Not satisfied.
In Comparative Examples 8 and 10, since Mg, Cu, and Zr are less than the set values, GP (1), GP (2), η ′ in two layers, and Al 3 Zr do not precipitate, and the mechanical properties target is not satisfied.
In Comparative Example 18, since Cu and Zr are less than the set values, GP (1), GP (2), and Al 3 Zr do not precipitate, and the mechanical property target is not satisfied.
Claims (4)
次に圧延率５０％以上の冷間圧延及び１００〜１５０℃の温度で人工時効処理することで、金属の折出組織にＧＰ（１）ゾーン又は／及びＧＰ（２）ゾーンを有することを特徴とするアルミニウム合金材料。 The aluminum alloy according to claim 1 is hardened after solution treatment at a temperature of 450 to 550 ° C,
Next, it has a GP (1) zone and / or a GP (2) zone in the metal folding structure by cold rolling with a rolling rate of 50% or more and artificial aging treatment at a temperature of 100 to 150 ° C. Aluminum alloy material.
前記ビレットを用いて押出加工及びその直後に急冷又は、押出加工後に温度４５０〜５００℃にて溶体化処理及び焼入れ処理をし、
次に圧延率５０％以上の冷間圧延及び１００〜１５０℃の温度で人工時効処理することで、引張強さ７００ＭＰａ以上、耐力値６００ＭＰａ以上であって、伸びが８％以上有することを特徴とするアルミニウム合金押出材の製造方法。 A billet is cast using the aluminum alloy according to claim 1,
Extrusion using the billet and quenching immediately after that, or solution treatment and quenching at a temperature of 450-500 ° C. after extrusion,
Next, it is characterized by having a tensile strength of 700 MPa or more, a proof stress value of 600 MPa or more, and an elongation of 8% or more by performing cold rolling with a rolling rate of 50% or more and artificial aging treatment at a temperature of 100 to 150 ° C. A method for producing an extruded aluminum alloy material.
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