JPH09202933A - High strength aluminum alloy excellent in hardenability - Google Patents
High strength aluminum alloy excellent in hardenabilityInfo
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- JPH09202933A JPH09202933A JP1054796A JP1054796A JPH09202933A JP H09202933 A JPH09202933 A JP H09202933A JP 1054796 A JP1054796 A JP 1054796A JP 1054796 A JP1054796 A JP 1054796A JP H09202933 A JPH09202933 A JP H09202933A
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- hardenability
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- aluminum alloy
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、焼入性に優れ、自
動車の構造材をはじめ、車両，電気機器，建築用等の材
料に適した高強度を有するアルミニウム合金に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to an aluminum alloy which is excellent in hardenability and has high strength suitable for materials such as automobile structural materials, vehicles, electric equipment, and construction.
【０００２】[0002]
【従来の技術】従来より、Ａｌ−Ｍｇ−Ｓｉ系合金は押
出性に優れる上に、熱処理によって高強度が得られるた
め、車両，船舶，建築等の用途に広く使用されている。
近年、自動車の軽量化の観点から、アルミニウム合金の
押出型材が自動車の構造部材に適用されるようになり、
その材料として、上記のＡｌ−Ｍｇ−Ｓｉ系合金が注目
されている。本系合金は熱処理型合金であるため、通常
は溶体化・焼入れ後、時効処理を行って使用されるが、
ＪＩＳＡ６０６３合金やＪＩＳＡ６ＮＯ１合金など、一
部の合金は焼入性に優れているため、この溶体化・焼入
れ処理を省略し、押出加工後そのまま時効処理を行える
ので製造コストを節約できるという利点を有している。
しかしながら、これらの焼入性に優れた合金はいずれも
時効処理後の強度が低く、構造材としては強度不足であ
った。2. Description of the Related Art Conventionally, Al-Mg-Si alloys have been widely used in applications such as vehicles, ships, and constructions because they have excellent extrudability and high strength by heat treatment.
In recent years, from the viewpoint of reducing the weight of automobiles, extruded aluminum alloy materials have come to be applied to structural members of automobiles,
As the material thereof, the Al-Mg-Si based alloy described above is drawing attention. Since this alloy is a heat treatment type alloy, it is usually used after aging treatment after solution heat treatment.
Since some alloys such as JISA6063 alloy and JISA6NO1 alloy have excellent hardenability, this solution treatment / hardening treatment can be omitted, and aging treatment can be performed as it is after extrusion processing, which has the advantage of saving manufacturing costs. ing.
However, all of these alloys having excellent hardenability had low strength after aging treatment and were insufficient in strength as structural materials.
【０００３】[0003]
【発明が解決しようとする課題】そこで、焼入性に優
れ、溶体化・焼入れ処理を省略して、押出加工後そのま
ま時効処理を行うだけで、構造材として十分な強度が得
られるアルミニウム合金が望まれている。本発明は以上
の事情を背景としてなされたもので、焼入性に優れると
ともに、Ｔ６処理によって３００ＭＰａ以上の引張強さ
が得られる高強度アルミニウム合金を提供することを目
的としたものである。Therefore, an aluminum alloy which has excellent hardenability and which has sufficient strength as a structural material can be obtained by omitting the solution heat treatment and the aging treatment after extrusion. Is desired. The present invention has been made in view of the above circumstances, and an object thereof is to provide a high-strength aluminum alloy which is excellent in hardenability and which can obtain a tensile strength of 300 MPa or more by T6 treatment.
【０００４】[0004]
【課題を解決するための手段】従来、Ａｌ−Ｍｇ−Ｓｉ
系合金の焼入性はＭｇ2 Ｓｉ量および過剰Ｓｉ量の増大
とともに低下するとされていた（たとえば、軽金属学会
編「アルミニウムの組織と性質」（１９９１））。しか
しながら、本発明者は、Ａｌ−Ｍｇ−Ｓｉ系合金の焼入
性および時効硬化能に及ぼす合金成分の影響について種
々検討した結果、本系合金の成分組成を適切に選択する
とともに、Ｍｇ2 Ｓｉ量と過剰Ｓｉ量の関係を特定する
ことによって上記目的を達成できることを見い出し、本
発明をなすに至ったものである。すなわち、本発明は、 （１）重量％で、 Ｍｇ：０．４〜１．０％ Ｓｉ：０．６〜１．６％ を含有し、かつＭｇ2 Ｓｉ量（重量％）とＭｇ2 Ｓｉバ
ランス組成よりも過剰なＳｉ量（重量％）が、 １．２−０．１５×（過剰Ｓｉ量）≧（Ｍｇ2 Ｓｉ量）
≧１．４−１．４×（過剰Ｓｉ量） ここで、（過剰Ｓｉ量）＝（全Ｓｉ量）−（Ｍｇ2 Ｓｉ
としてのＳｉ量）なる関係式を満足し、残部がＡｌおよ
び不可避的不純物よりなることを特徴とする焼入性に優
れた高強度アルミニウム合金。Conventionally, Al--Mg--Si is conventionally used.
It has been said that the hardenability of a system alloy decreases as the amount of Mg 2 Si and the amount of excess Si increase (for example, “Structure and Properties of Aluminum” (1991) edited by Japan Institute of Light Metals). However, as a result of various studies on the influence of alloy components on the hardenability and age-hardening ability of the Al-Mg-Si alloy, the present inventor appropriately selected the component composition of the alloy of the present system and Mg 2 Si. The inventors have found that the above object can be achieved by specifying the relationship between the amount and the amount of excess Si, and have completed the present invention. That is, the present invention includes (1) wt%, containing Mg: 0.4 to 1.0% Si: 0.6 to 1.6%, and Mg 2 Si amount (wt%) and Mg 2 Si. The amount of Si (wt%) in excess of the balance composition is 1.2-0.15 x (excess Si amount) ≥ (Mg 2 Si amount)
≧ 1.4−1.4 × (amount of excess Si) where (amount of excess Si) = (total amount of Si) − (Mg 2 Si
A high-strength aluminum alloy having excellent hardenability, characterized in that the balance of Al and unavoidable impurities is satisfied.
【０００５】（２）上記（１）記載のアルミニウム合金
において、さらに、重量％で、 Ｃｕ：０．０５〜１．０％ Ｚｎ：０．０３〜１．５％ Ｍｎ：０．０３〜０．１％ Ｃｒ：０．０３〜０．１％ Ｚｒ：０．０３〜０．１％ Ｖ ：０．０３〜０．１％ Ｆｅ：０．０３〜０．６％ Ｔｉ：０．００５〜０．２％ のうちの１種または２種以上を含有する焼入性に優れた
高強度アルミニウム合金にある。(2) In the aluminum alloy described in (1) above, further, in weight%, Cu: 0.05 to 1.0% Zn: 0.03 to 1.5% Mn: 0.03 to 0. 1% Cr: 0.03 to 0.1% Zr: 0.03 to 0.1% V: 0.03 to 0.1% Fe: 0.03 to 0.6% Ti: 0.005 to 0. It is a high-strength aluminum alloy containing 1% or more of 2% and having excellent hardenability.
【０００６】[0006]
【発明の実施の形態】以下に本発明を詳細に説明する。
まず、成分組成の限定理由を述べる。なお、以下の％は
重量％を意味する。 Ｍｇ：Ｍｇは本発明で対象としている系の合金で基本と
なる合金元素であり、Ｓｉとともに化合物を形成して強
度の上昇に寄与する。Ｍｇ量が０．４％未満では、析出
硬化によって強度の向上に寄与するＭｇ2 Ｓｉの生成量
が少なくなるため、十分な強度が得られず、一方、１．
０％を越えれば焼入性が低下する上に、押出加工性も低
下することから、Ｍｇ量は０．４〜１．０％の範囲内と
した。DESCRIPTION OF THE PREFERRED EMBODIMENTS The present invention will be described below in detail.
First, the reasons for limiting the component composition will be described. In addition, the following% means weight%. Mg: Mg is a basic alloy element in the alloy of the system targeted in the present invention, and forms a compound with Si to contribute to an increase in strength. If the amount of Mg is less than 0.4%, the amount of Mg 2 Si that contributes to the improvement of strength due to precipitation hardening decreases, so sufficient strength cannot be obtained.
If it exceeds 0%, the hardenability is lowered and the extrusion processability is also lowered. Therefore, the Mg content is set within the range of 0.4 to 1.0%.
【０００７】Ｓｉ：Ｓｉも本発明の系の合金で基本とな
る合金元素であって、Ｍｇとともに化合物を形成して強
度の向上に寄与する。Ｓｉが０．６％未満では硬化に寄
与するＭｇ2 Ｓｉの生成量が少なくなるため、十分な強
度が得られない上に、焼入性が低下する。一方、１．６
％を越えると、凝固の際に粗大Ｓｉ相が晶出して押出加
工性や曲げ加工性を低下させる。従って、Ｓｉ量は０．
６〜１．６％の範囲とした。焼入性と強度のバランスか
らは０．７〜１．５％が好ましい。Si: Si is also an alloying element which is a basic component of the alloy of the present invention, and forms a compound with Mg to contribute to the improvement of strength. If Si is less than 0.6%, the amount of Mg 2 Si that contributes to hardening is reduced, so that sufficient strength cannot be obtained and hardenability deteriorates. On the other hand, 1.6
If it exceeds 0.1%, a coarse Si phase is crystallized during solidification to deteriorate the extrudability and bendability. Therefore, the Si content is 0.
The range is 6 to 1.6%. From the viewpoint of balance between hardenability and strength, 0.7 to 1.5% is preferable.
【０００８】上記の基本組成以外に、Ｃｕ，Ｚｎ，Ｃ
ｒ，Ｚｒ，Ｖ，Ｆｅ，Ｔｉの中から１種以上を含有させ
ることも有効である。 Ｃｕ：Ｃｕは時効硬化を促進し、合金の強度を高める元
素である。０．０５％未満ではその効果が十分に得られ
ず、一方、１．０％を越えると耐食性が低下する。従っ
て、Ｃｕの添加量は０．０５〜１．０％の範囲内とし
た。 Ｚｎ：Ｚｎは合金の時効硬化性の向上を通じて強度の向
上に寄与する元素であり、その含有量が０．０３％未満
では上記の効果が不十分であり、一方、１．５％を越え
ると曲げ加工性および耐食性が低下する。そのため、Ｚ
ｎを添加する場合のＺｎ量は０．０３〜１．５％の範囲
内とした。In addition to the above basic composition, Cu, Zn, C
It is also effective to contain one or more of r, Zr, V, Fe and Ti. Cu: Cu is an element that promotes age hardening and enhances the strength of the alloy. If it is less than 0.05%, the effect cannot be sufficiently obtained, while if it exceeds 1.0%, the corrosion resistance is lowered. Therefore, the addition amount of Cu is set within the range of 0.05 to 1.0%. Zn: Zn is an element that contributes to the improvement of strength through the improvement of age hardening of the alloy, and if the content thereof is less than 0.03%, the above effect is insufficient, while if it exceeds 1.5%. Bending workability and corrosion resistance decrease. Therefore, Z
When adding n, the amount of Zn was made into the range of 0.03 to 1.5%.
【０００９】Ｍｎ，Ｃｒ，Ｚｒ，Ｖ：これらの元素は強
度の向上と結晶粒の微細化に有効な元素であるが、いず
れも含有量が０．０３％未満では上記の効果が十分に得
られず、一方、０．１％を越えると焼入性が低下する。
従って、Ｍｎ，Ｃｒ，ＺｒおよびＶの含有量はいずれも
０．０３〜０．１％の範囲内とした。 Ｆｅ：Ｆｅは本来、不可避的不純物として、アルミニウ
ム合金中に含まれる元素であるが、やはり強度の向上と
結晶粒の微細化に有効であり、０．０３〜０．６％の範
囲内で添加しても良い。この場合、０．０３％未満では
上記の効果が十分に得られず、一方、０．６％を越える
と上記効果は飽和するばかりでなく、巨大金属間化合物
が生成されて押出加工性、曲げ加工性等に悪影響を及ぼ
す恐れがある。従って、Ｆｅの含有量は０．０３〜０．
６％の範囲内とした。Mn, Cr, Zr, V: These elements are effective for improving the strength and refining the crystal grains, but if the content is less than 0.03%, the above effect is sufficiently obtained. However, if it exceeds 0.1%, the hardenability deteriorates.
Therefore, the contents of Mn, Cr, Zr and V are all within the range of 0.03 to 0.1%. Fe: Fe is an element that is originally contained in an aluminum alloy as an unavoidable impurity, but it is also effective in improving strength and refining crystal grains, and is added within the range of 0.03 to 0.6%. You may. In this case, if it is less than 0.03%, the above effect is not sufficiently obtained, while if it exceeds 0.6%, the above effect is not only saturated, but also a giant intermetallic compound is formed to cause extrusion processability and bending. It may adversely affect workability. Therefore, the Fe content is 0.03 to 0.
It was within the range of 6%.
【００１０】また、Ｔｉは一般に鋳塊の結晶粒微細化の
ため、単独あるいは微量のＢと組み合わせて添加する。
この場合、Ｔｉの含有量が０．００５％未満では上記の
効果は得られず、０．２％を越えるとその効果は飽和す
る。従って、Ｔｉの含有量は０．００５〜０．２％の範
囲内とする。Ｂの添加量は０．０００５〜０．０３％が
有利である。つぎに、Ｍｇ2 Ｓｉ量と過剰Ｓｉ量の関係
について説明する。ここで、過剰Ｓｉ量とは全Ｓｉ量か
らＭｇ2 ＳｉとしてのＳｉ量を差し引いた量である。Further, Ti is generally added alone or in combination with a slight amount of B in order to refine the crystal grains of the ingot.
In this case, if the Ti content is less than 0.005%, the above effect cannot be obtained, and if it exceeds 0.2%, the effect is saturated. Therefore, the Ti content is set within the range of 0.005 to 0.2%. The amount of B added is preferably 0.0005 to 0.03%. Next, the relationship between the amount of Mg 2 Si and the amount of excess Si will be described. Here, the excess Si amount is an amount obtained by subtracting the Si amount as Mg 2 Si from the total Si amount.
【００１１】Ａｌ−Ｍｇ−Ｓｉ系合金においては、Ｍｇ
2 Ｓｉ量および過剰Ｓｉ量の増加に伴い、強度は上昇す
る。本発明者がＴ６処理後の引張強さに及ぼすＭｇ2 Ｓ
ｉ量および過剰Ｓｉ量の影響を調査した結果、Ｍｇ2 Ｓ
ｉ量と過剰Ｓｉ量が次式（１）を満足する時にＴ６処理
後の引張強さが３００ＭＰａを越えることが明らかにな
った。 （Ｍｇ2 Ｓｉ量）≧１．４−１．４×（過剰Ｓｉ量） ・・・・・（１）In the Al--Mg--Si system alloy, Mg
2 Strength increases as the amount of Si and excess Si increases. The present inventor has an effect on the tensile strength after T6 treatment Mg 2 S
As a result of investigating the effects of the i content and the excess Si content, Mg 2 S
It was revealed that the tensile strength after T6 treatment exceeds 300 MPa when the i amount and the excess Si amount satisfy the following expression (1). (Amount of Mg 2 Si) ≧ 1.4−1.4 × (Amount of excess Si) (1)
【００１２】一方、Ｍｇ2 Ｓｉ量および過剰Ｓｉ量の増
加に伴い、Ａｌ−Ｍｇ−Ｓｉ系合金の焼入性は低下す
る。今、焼入性の指標として、水冷後１８０℃×８時間
の時効処理を行った場合の引張強さに対する、空冷後同
処理を行った場合の引張強さの比を取り、この値が０．
８以上を示すものを焼入性が良好であるとする。この焼
入性指標とＭｇ2 Ｓｉ量および過剰Ｓｉ量の関係を調査
した結果、Ｍｇ2 Ｓｉ量と過剰Ｓｉ量が次式（２）を満
足する時に焼入性指標が０．８以上になることを見いだ
した。 １．２−０．１５×（過剰Ｓｉ量）≧（Ｍｇ2 Ｓｉ量）・・・・・（２）On the other hand, as the amount of Mg 2 Si and the amount of excess Si increase, the hardenability of the Al-Mg-Si alloy decreases. Now, as an index of hardenability, take the ratio of the tensile strength when the same treatment is performed after air cooling to the tensile strength when the aging treatment is performed at 180 ° C. for 8 hours after water cooling, and this value is 0. ．
Those having a hardness of 8 or more are considered to have good hardenability. As a result of investigating the relationship between the hardenability index, the Mg 2 Si amount and the excess Si amount, the hardenability index becomes 0.8 or more when the Mg 2 Si amount and the excess Si amount satisfy the following equation (2). I found a thing. 1.2-0.15 × (excess Si amount) ≧ (Mg 2 Si amount) (2)
【００１３】従って、Ｍｇ2 Ｓｉ量と過剰Ｓｉ量の関係
を次式（３）のように規定した。 １．２−０．１５×（過剰Ｓｉ量）≧（Ｍｇ2 Ｓｉ量）≧１．４−１．４ ×（過剰Ｓｉ量） ・・・・・・・・・・・・・（３） 以上のように、本発明では合金の成分組成を適切に調整
するとともに、Ｍｇ2Ｓｉ量と過剰Ｓｉ量の関係を特定
することによって、焼入性に優れるとともに、Ｔ６処理
によって３００ＭＰａ以上の引張強さを示す高強度アル
ミニウム合金が得られる。Therefore, the relationship between the amount of Mg 2 Si and the amount of excess Si is defined by the following equation (3). 1.2-0.15 x (excess Si amount) ≥ (Mg 2 Si amount) ≥ 1.4-1.4 x (excess Si amount) ... (3) As described above, in the present invention, by appropriately adjusting the component composition of the alloy and identifying the relationship between the amount of Mg 2 Si and the amount of excess Si, the hardenability is excellent and the tensile strength of 300 MPa or more is obtained by the T6 treatment. A high-strength aluminum alloy having the following characteristics is obtained.
【００１４】[0014]
【実施例】次に、本発明を実施例で説明する。表１に示
す化学成分を有する各合金を常法により、溶解，鋳造
し，面削，均質化処理を行って熱間押出用素材とした。
これらの素材を５００℃で５分間予備加熱後、２０ｍ／
分の押出速度で熱間押出成形を行い、押出型材を作製し
た。型材の形状は板厚２ｍｍ、一辺４０ｍｍのロ型であ
る。押出後、５０ｍｍ長さの試験片を切り出し、５４０
℃×３０分の溶体化処理を施し、その温度から水冷およ
び空冷した後、１８０℃×８時間の時効処理を行った。
このようにして得られた各合金について、引張試験を実
施し、引張特性と焼入性を評価した。EXAMPLES Next, the present invention will be described with reference to Examples. Each alloy having the chemical composition shown in Table 1 was melted, cast, chamfered and homogenized by a conventional method to obtain a material for hot extrusion.
After preheating these materials at 500 ° C for 5 minutes,
Hot extrusion molding was performed at an extrusion speed of minutes to produce an extrusion mold material. The shape of the mold material is a square shape having a plate thickness of 2 mm and a side of 40 mm. After extrusion, cut out a test piece of 50 mm in length, 540
After solution treatment at 30 ° C. for 30 minutes, water cooling and air cooling from that temperature, aging treatment at 180 ° C. for 8 hours was performed.
A tensile test was performed on each of the alloys thus obtained, and the tensile properties and hardenability were evaluated.
【００１５】[0015]
【表１】 [Table 1]
【００１６】焼入性は溶体化後空冷した場合と水冷した
場合の１８０℃×８時間時効後の引張強さの比で評価し
た。さらに、耐食性，押出性および曲げ加工性について
も評価した。耐食性は５００時間の塩水噴霧後の錆発生
状況から〇：錆無し，△：錆小，×：錆大の三段階に評
価した。押出性は押出型材の作製の際の押出成形の容易
さを、比較材のＪＩＳＡ６０６３合金を１００として相
対評価した。また、曲げ加工性はパンチ半径２００ｍｍ
でプレス曲げ試験によって行い、〇：良好，△：しわ有
り，×：割れ、の３段階で評価した。それらの結果を表
２に示す。The hardenability was evaluated by the ratio of tensile strength after aging for 8 hours at 180 ° C. when air-cooled after solution heat treatment and water-cooled. Furthermore, the corrosion resistance, extrudability and bending workability were also evaluated. Corrosion resistance was evaluated on the basis of the rust generation state after 500 hours of salt spraying, in three grades of ◯: no rust, △: small rust, ×: large rust. The extrudability was evaluated relative to the ease of extrusion molding when producing an extruded mold material by setting JIS A6063 alloy as a comparative material to 100. The bending radius is 200 mm for punches.
A press bending test was carried out, and the evaluation was made in three grades: ◯: good, Δ: wrinkled, ×: cracked. Table 2 shows the results.
【００１７】[0017]
【表２】 [Table 2]
【００１８】Ｎｏ．１〜２８はいずれも合金の成分組成
が本発明で規定する範囲内で、かつＭｇ2 Ｓｉ量と過剰
Ｓｉ量の関係が本発明で規定する条件を満たした例であ
る。これらの場合は、いずれも焼入性が良好（空冷材と
水冷材の引張強さの比が０．８以上）で、引張強さが３
００ＭＰａ以上の高強度が得られ、その他の特性も良好
である。No. Nos. 1 to 28 are examples in which the composition of the alloy is within the range specified by the present invention and the relationship between the amount of Mg 2 Si and the excess Si satisfies the conditions specified by the present invention. In all of these cases, the hardenability is good (the ratio of the tensile strength of the air-cooled material to the water-cooled material is 0.8 or more), and the tensile strength is 3
A high strength of 00 MPa or more is obtained, and other properties are also good.
【００１９】これに対して、Ｎｏ．２９〜３８は合金の
成分範囲が本発明で規定する条件を満たさなかったた
め、全ての特性を同時に満足することはできなかった。
すなわち、Ｎｏ．２９は焼入性は良好であるがＴ６処理
後の強度が低く、Ｎｏ．３０は焼入性および強度には優
れているが、押出性および曲げ加工性に劣り、Ｎｏ．３
１は耐食性および押出性に劣り、Ｎｏ．３２，３３，３
５，３６，３７および３８は焼入性，押出性および曲げ
加工性に劣る。また、Ｎｏ．３４は耐食性および曲げ加
工性に劣っている。Ｎｏ．３９および４０は合金の成分
組成は本発明で規定する範囲内であるが、Ｍｇ2 Ｓｉ量
と過剰Ｓｉ量の関係が本発明で規定する関係式を満たさ
ないため、Ｎｏ．３９は焼入性に劣り、Ｎｏ．４０はＴ
６処理後の強度が３００ＭＰａに満たなかった。On the other hand, in No. In Nos. 29 to 38, the composition range of the alloy did not satisfy the conditions specified in the present invention, so that all the properties could not be satisfied at the same time.
That is, No. No. 29 has good hardenability, but the strength after T6 treatment is low. No. 30 is excellent in hardenability and strength, but inferior in extrudability and bending workability. 3
No. 1 was inferior in corrosion resistance and extrudability, and No. 1 32, 33, 3
5, 36, 37 and 38 are inferior in hardenability, extrudability and bending workability. In addition, No. 34 is inferior in corrosion resistance and bending workability. No. Nos. 39 and 40 are alloy compositions within the range specified by the present invention, but the relationship between the amount of Mg 2 Si and the excess Si does not satisfy the relational expression specified by the present invention. No. 39 is inferior in hardenability, and No. 40 is T
6 The strength after treatment was less than 300 MPa.
【００２０】[0020]
【発明の効果】以上の説明で明らかなように、本発明に
よるとＭｇ2 Ｓｉ量と過剰Ｓｉの量的関係を特定するこ
とによって、焼入性が良好で、耐食性，押出性，曲げ加
工性にも優れ、かつＴ６処理後の引張強さが３００ＭＰ
ａ以上の高強度アルミニウム合金を得ることができる。As is clear from the above description, according to the present invention, by specifying the quantitative relationship between the amount of Mg 2 Si and the excess Si, the hardenability is good, the corrosion resistance, the extrudability and the bendability are good. Also excellent, and the tensile strength after T6 treatment is 300MP
It is possible to obtain a high-strength aluminum alloy of a or more.
Claims (2)
ランス組成よりも過剰なＳｉ量（重量％）が、 １．２−０．１５×（過剰Ｓｉ量）≧（Ｍｇ2 Ｓｉ量）
≧１．４−１．４×（過剰Ｓｉ量） ここで、（過剰Ｓｉ量）＝（全Ｓｉ量）−（Ｍｇ2 Ｓｉ
としてのＳｉ量）なる関係式を満足し、残部がＡｌおよ
び不可避的不純物よりなることを特徴とする焼入性に優
れた高強度アルミニウム合金。1. By weight%, Mg: 0.4-1.0% Si: 0.6-1.6% is contained, and the amount of Mg 2 Si (% by weight) and the Mg 2 Si balance composition are higher than the balance composition. Excessive Si amount (% by weight) is 1.2-0.15 × (excess Si amount) ≧ (Mg 2 Si amount)
≧ 1.4−1.4 × (amount of excess Si) where (amount of excess Si) = (total amount of Si) − (Mg 2 Si
A high-strength aluminum alloy having excellent hardenability, characterized in that the balance of Al and unavoidable impurities is satisfied.
て、さらに、重量％で、 Ｃｕ：０．０５〜１．０％ Ｚｎ：０．０３〜１．５％ Ｍｎ：０．０３〜０．１％ Ｃｒ：０．０３〜０．１％ Ｚｒ：０．０３〜０．１％ Ｖ ：０．０３〜０．１％ Ｆｅ：０．０３〜０．６％ Ｔｉ：０．００５〜０．２％ のうちの１種または２種以上を含有する焼入性に優れた
高強度アルミニウム合金。2. The aluminum alloy according to claim 1, further comprising Cu: 0.05 to 1.0% Zn: 0.03 to 1.5% Mn: 0.03 to 0.1% by weight. Cr: 0.03-0.1% Zr: 0.03-0.1% V: 0.03-0.1% Fe: 0.03-0.6% Ti: 0.005-0.2% A high-strength aluminum alloy having excellent hardenability, which contains one or more of the above.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1054796A JPH09202933A (en) | 1996-01-25 | 1996-01-25 | High strength aluminum alloy excellent in hardenability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1054796A JPH09202933A (en) | 1996-01-25 | 1996-01-25 | High strength aluminum alloy excellent in hardenability |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH09202933A true JPH09202933A (en) | 1997-08-05 |
Family
ID=11753294
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1054796A Withdrawn JPH09202933A (en) | 1996-01-25 | 1996-01-25 | High strength aluminum alloy excellent in hardenability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH09202933A (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6461454B2 (en) | 2000-04-20 | 2002-10-08 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Aluminum alloy plate for automobile and manufacturing method thereof |
| JP2007177308A (en) * | 2005-12-28 | 2007-07-12 | Sumitomo Light Metal Ind Ltd | High strength and high toughness aluminum alloy extruded material and forged material having excellent corrosion resistance, and methods for producing the extruded material and forged material |
| JP2007254809A (en) * | 2006-03-23 | 2007-10-04 | Aisin Keikinzoku Co Ltd | Aluminum alloy extruded shape material having excellent impact absorbing property and satisfactory hardenability, and its production method |
| WO2013115227A1 (en) * | 2012-01-31 | 2013-08-08 | アイシン軽金属株式会社 | High-strength aluminum alloy extrudate with excellent corrosion resistance, ductility, and hardenability and process for producing same |
| JP2015166480A (en) * | 2014-03-03 | 2015-09-24 | 住友電気工業株式会社 | Aluminum alloy, aluminum alloy wire material, method for producing aluminum alloy wire material, method for producing aluminum alloy member and aluminum alloy member |
| WO2019083969A1 (en) * | 2017-10-23 | 2019-05-02 | Novelis Inc. | High-strength, highly formable aluminum alloys and methods of making the same |
-
1996
- 1996-01-25 JP JP1054796A patent/JPH09202933A/en not_active Withdrawn
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6461454B2 (en) | 2000-04-20 | 2002-10-08 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Aluminum alloy plate for automobile and manufacturing method thereof |
| JP2007177308A (en) * | 2005-12-28 | 2007-07-12 | Sumitomo Light Metal Ind Ltd | High strength and high toughness aluminum alloy extruded material and forged material having excellent corrosion resistance, and methods for producing the extruded material and forged material |
| JP2007254809A (en) * | 2006-03-23 | 2007-10-04 | Aisin Keikinzoku Co Ltd | Aluminum alloy extruded shape material having excellent impact absorbing property and satisfactory hardenability, and its production method |
| WO2013115227A1 (en) * | 2012-01-31 | 2013-08-08 | アイシン軽金属株式会社 | High-strength aluminum alloy extrudate with excellent corrosion resistance, ductility, and hardenability and process for producing same |
| JPWO2013115227A1 (en) * | 2012-01-31 | 2015-05-11 | アイシン軽金属株式会社 | High strength aluminum alloy extruded material excellent in corrosion resistance, ductility and hardenability and method for producing the same |
| JP2015166480A (en) * | 2014-03-03 | 2015-09-24 | 住友電気工業株式会社 | Aluminum alloy, aluminum alloy wire material, method for producing aluminum alloy wire material, method for producing aluminum alloy member and aluminum alloy member |
| WO2019083969A1 (en) * | 2017-10-23 | 2019-05-02 | Novelis Inc. | High-strength, highly formable aluminum alloys and methods of making the same |
| JP2020537039A (en) * | 2017-10-23 | 2020-12-17 | ノベリス・インコーポレイテッドＮｏｖｅｌｉｓ Ｉｎｃ． | High-strength and highly moldable aluminum alloy and its manufacturing method |
| JP2022172234A (en) * | 2017-10-23 | 2022-11-15 | ノベリス・インコーポレイテッド | High-strength, highly formable aluminum alloys and methods of making the same |
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