JP3481064B2 - Slow acting aluminum alloy extruded material for bending - Google Patents
Slow acting aluminum alloy extruded material for bendingInfo
- Publication number
- JP3481064B2 JP3481064B2 JP35274896A JP35274896A JP3481064B2 JP 3481064 B2 JP3481064 B2 JP 3481064B2 JP 35274896 A JP35274896 A JP 35274896A JP 35274896 A JP35274896 A JP 35274896A JP 3481064 B2 JP3481064 B2 JP 3481064B2
- Authority
- JP
- Japan
- Prior art keywords
- weight
- aluminum alloy
- extruded material
- bending
- strength
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
Landscapes
- Extrusion Of Metal (AREA)
Description
【０００１】[0001]
【発明の属する技術分野】本発明は自動車用フレーム等
の曲げ加工を施される部材又は構造部材に使用される高
強度の遅効性アルミニウム合金押出材とその製造方法に
関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high-strength slow-acting aluminum alloy extruded material used for a member to be bent or a structural member such as an automobile frame, and a method for producing the same.
【０００２】[0002]
【従来の技術】アルミニウム合金は、鉄に比べ比重が約
１／３と軽量であるため、鉄からアルミニウム合金に材
料を置換し軽量化を計る例が数多くある。一方、電気自
動車をはじめとして、近年の自動車においては、燃費の
向上が強く求められており、そのため従来鉄のプレス品
で製作されていた自動車フレームをアルミニウム合金押
出材で製作することが試みられ、現在、市場にもアルミ
ニウム合金押出材フレームを採用した自動車が出始めて
いる。自動車フレームには衝撃吸収性も要求されるが、
アルミ合金押出材は衝撃吸収性も鉄に比べ優れている。
そのため自動車部材におけるアルミニウム押出材の需要
は非常に高い。2. Description of the Related Art Aluminum alloys have a specific gravity of about 1/3 that of iron and are lighter in weight. Therefore, there are many examples in which iron is replaced with aluminum alloys to reduce the weight. On the other hand, in recent automobiles including electric automobiles, there is a strong demand for improvement in fuel consumption, and therefore, it has been attempted to produce an automobile alloy frame extruded from an aluminum alloy, which was conventionally produced from a pressed iron product, Currently, automobiles using aluminum alloy extruded material frames are beginning to appear on the market. Shock absorption is also required for automobile frames,
The aluminum alloy extruded material is also superior in shock absorption compared to iron.
Therefore, the demand for aluminum extruded materials in automobile parts is very high.
【０００３】[0003]
【発明が解決しようとする課題】しかしながら、従来の
アルミニウム合金は鉄のプレス品に比べ小Ｒ曲げ加工性
が劣るという問題があった。そのため、アルミニウム合
金押出材に曲げ加工を行う場合、時効処理を行わない状
態（Ｔ１又はＴ４状態）で曲げ加工を行うという方法が
用いられていた。However, the conventional aluminum alloy has a problem that the small R bending workability is inferior to that of the iron pressed product. Therefore, when bending an aluminum alloy extruded material, a method of bending the aluminum alloy extruded material in a state where the aging treatment is not performed (T1 or T4 state) has been used.
【０００４】しかし、Ｔ１又はＴ４状態では室温状態で
の放置によっても室温時効が進み耐力の変化が起きる。
曲げ加工は材料の耐力によってスプリングバック量が変
化し、Ｔ１又はＴ４状態で室温時効が進行する場合は曲
げ加工の精度が安定しない。安定した精度を得る手段と
して、押出直後室温時効が未だ進行しないうちに曲げ加
工及び人工時効処理を施すことが考えられるが、実操業
上の観点からは現実的でない。これに類似の例として例
えば特開平８−６０２８５号公報に自然時効時間の規制
が記載されている。そこで、押出後長期間経過しても、
その間安定した曲げ加工精度を得るため、室温放置によ
っても機械的性質の変化しない遅効性合金が求められて
いた。このような遅効性アルミニウム合金にはＳｎを添
加することが有効であることは知られていたが、シュレ
ッダーダストによる環境破壊等の問題から、Ｓｎを添加
することは容認されなくなった。However, in the T1 or T4 state, the aging proceeds at room temperature and changes in proof stress occur even if it is left at room temperature.
In the bending process, the springback amount changes depending on the proof stress of the material, and when room temperature aging progresses in the T1 or T4 state, the accuracy of the bending process is not stable. As a means for obtaining stable accuracy, it is conceivable to perform bending and artificial aging treatment immediately after extrusion at room temperature before the aging has progressed, but this is not practical from the viewpoint of actual operation. As a similar example, for example, Japanese Patent Application Laid-Open No. 8-60285 discloses regulation of natural aging time. Therefore, even if a long time has passed after extrusion,
In the meantime, in order to obtain stable bending accuracy, a slow-acting alloy that does not change its mechanical properties even when left at room temperature has been required. It has been known that it is effective to add Sn to such a slow-acting aluminum alloy, but due to problems such as environmental destruction due to shredder dust, addition of Sn has become unacceptable.
【０００５】一方、自動車フレームは構造材であるため
熱処理後の強度が高いことも要求される。また、厳しい
寸法精度が要求される自動車部品においては、プレス焼
入れの際ひずみの生じる水冷によらず、ファン空冷によ
って十分な強度が得られるプレス焼入れ性も要求され
る。On the other hand, since the automobile frame is a structural material, it is required to have high strength after heat treatment. Further, in automobile parts that require strict dimensional accuracy, press hardenability capable of obtaining sufficient strength by air cooling of a fan is also required, not by water cooling that causes strain during press hardening.
【０００６】本発明はかかる問題点に鑑みてなされたも
のであり、遅効性アルミニウム合金に従来から添加され
てきたＳｎを用いることなく、熱処理により高強度化が
可能であり、かつ熱処理前には機械的性質の変化しない
遅効性アルミニウム合金押出材を提供することを目的と
する。The present invention has been made in view of the above problems, and it is possible to increase the strength by heat treatment without using Sn which has been conventionally added to a slow-acting aluminum alloy, and before heat treatment. It is an object of the present invention to provide a slow-acting aluminum alloy extruded material whose mechanical properties do not change.
【０００７】[0007]
【課題を解決するための手段】本発明者らは、自動車フ
レーム用等に好適な遅効性アルミニウム合金押出材を開
発すべく種々の研究を行い、その結果、Ａｌ−Ｍｇ−Ｓ
ｉ系合金において、Ｍｇ／Ｓｉ比が遅効性に大きく影響
すること、そしてＭｇ2Ｓｉの化学量論比よりＳｉリッ
チ側の特定の組成領域で室温時効の進行が抑制されるこ
とを見い出した。また、Ｃｕの添加が熱処理後の析出物
（Ｍｇ2Ｓｉ）の分布を均一微細にして強度を向上させ
ることを見い出し、本発明を完成した。DISCLOSURE OF THE INVENTION The inventors of the present invention conducted various researches to develop a delayed-acting aluminum alloy extruded material suitable for automobile frames, etc., and as a result, Al-Mg-S
It has been found that in the i-based alloy, the Mg / Si ratio has a great influence on the retardation effect, and that the progress of room temperature aging is suppressed in a specific composition region on the Si-rich side relative to the stoichiometric ratio of Mg 2 Si. Further, they have found that the addition of Cu makes the distribution of precipitates (Mg 2 Si) after heat treatment uniform and fine and improves the strength, and completed the present invention.
【０００８】本発明に係る遅効性アルミニウム合金押出
材は、Ｍｇ０．４〜０．８重量％、Ｓｉ０．４〜１．０
重量％、Ｃｕ０．１５〜０．５重量％、Ｔｉ０．００５
〜０．２重量％を含有し、残部Ａｌ及び不可避不純物か
らなり、さらに、Ｍｇ含有重量％をＸ、Ｓｉ含有重量％
をＹとしたとき、Ｙ≧（１／１．７３）Ｘ＋０．１５の
関係を満たすことを特徴とする。この押出材は、Ｍｇ
０．４〜０．６５重量％、Ｓｉ０．４〜１．０重量％の
範囲内でより優れた遅効性を示し、さらに、Ｍｇ０．４
〜０．６重量％、Ｓｉ０．５〜０．７重量％の範囲内が
より好ましい。また、この遅効性アルミニウム合金押出
材は、強度及び延性の向上のため必要に応じて、Ｍｎ
０．０５〜０．６重量％、Ｃｒ０．０５〜０．３重量
％、Ｚｒ０．０５〜０．３重量％の内１種以上を合計で
０．９重量％以下含有することができる。The slow-acting aluminum alloy extruded material according to the present invention contains 0.4 to 0.8% by weight of Mg and 0.4 to 1.0 of Si.
% By weight, Cu 0.15 to 0.5% by weight, Ti 0.005
.About.0.2 wt%, the balance is Al and unavoidable impurities, and further Mg content wt% is X and Si content wt%.
Is defined as Y, the relationship of Y ≧ (1 / 1.73) X + 0.15 is satisfied. This extruded material is Mg
In the range of 0.4 to 0.65% by weight and Si 0.4 to 1.0% by weight, more excellent slow-acting effect is exhibited, and further, Mg0.4
Is more preferably in the range of .about.0.6 wt%, Si 0.5 to 0.7 wt%. In addition, this delayed-acting aluminum alloy extruded material may contain Mn, if necessary, in order to improve strength and ductility.
One or more of 0.05 to 0.6% by weight, Cr of 0.05 to 0.3% by weight, and Zr of 0.05 to 0.3% by weight can be contained in a total amount of 0.9% by weight or less.
【０００９】本発明に係る遅効性アルミニウム合金押出
材は、上記の組成のアルミニウム合金鋳塊を、５００〜
６００℃で２〜１０ｈｒ均質化処理を行い、ついで４４
０〜５６０℃に再加熱した鋳塊を押出加工し、押出直後
にファン空冷によるプレス焼入れすることにより製造す
る。The slow-acting aluminum alloy extruded material according to the present invention comprises an aluminum alloy ingot having the above-mentioned composition,
Perform homogenization treatment at 600 ° C for 2 to 10 hours, then 44
The ingot that has been reheated to 0 to 560 ° C. is extruded, and immediately after extrusion, it is manufactured by press quenching by air cooling with a fan.
【００１０】[0010]
【発明の実施の形態】以下、本発明に係る遅効性アルミ
ニウム合金押出材の成分添加理由及び組成限定理由につ
いて説明する。BEST MODE FOR CARRYING OUT THE INVENTION The reasons for adding the components and the reasons for limiting the composition of the extruded aluminum alloy of the present invention will be explained below.
【００１１】Ｍｇ、Ｓｉ
先に述べたように、Ｍｇ2Ｓｉの化学量論比に対してＳ
ｉを相当量過剰に添加したとき、室温時効が抑制され遅
効性が発現する。そのＭｇ、Ｓｉの割合は、Ｍｇ含有重
％をＸ、Ｓｉ含有重量％をＹとしたときＹ≧（１／１．
７３）Ｘ＋０．１５を満たす範囲である。これよりＭｇ
リッチ側、すなわちＹ＜（１／１．７３）Ｘ＋０．１５
の範囲では、Ｓｉによる室温時効の抑制効果が不十分で
あり、室温時効が進行してしまう。Mg, Si As described above, S relative to the stoichiometric ratio of Mg 2 Si
When i is added in an excessive amount, the room temperature aging is suppressed and the delayed effect is exhibited. When the Mg content weight% is X and the Si content weight% is Y, the ratio of Mg and Si is Y ≧ (1/1.
73) A range satisfying X + 0.15. Than Mg
Rich side, that is, Y <(1 / 1.73) X + 0.15
In the range, the effect of suppressing the room temperature aging by Si is insufficient, and the room temperature aging will proceed.
【００１２】一方、ＭｇはＳｉと結合し、Ｍｇ2Ｓｉを
形成することにより合金強度を向上させる。この効果を
発揮するには、Ｍｇの添加量は０．４重量％以上とする
必要がある。しかし、Ｍｇの含有量が０．８重量％を越
えると、上記の範囲を満たしていても、Ｍｇの拡散によ
り室温時効が進行してしまい、また、押出性も劣るよう
になる。従って、Ｍｇの含有量は０．４重量％以上、
０．８重量％以下とする。また、Ｓｉは、上述したよう
にＭｇ2Ｓｉを形成して合金強度を向上させるととも
に、材料の延性を向上させる効果がある。しかし、Ｓｉ
の添加量が０．４重量％未満では材料の強度を向上させ
ることができず、１．０重量％以上では材料の延性が阻
害される。さらに、ＳｉはＭｇ2Ｓｉ析出の核となる
が、その添加量が多くなると析出の核が多くなる結果、
析出が進行しやすくなり、遅効性が失われる。以上の理
由から、Ｓｉの含有量は０．４重量％以上、１．０重量
％以下とする。On the other hand, Mg combines with Si to form Mg 2 Si, thereby improving the alloy strength. In order to exert this effect, the addition amount of Mg needs to be 0.4% by weight or more. However, if the Mg content exceeds 0.8% by weight, even if the Mg content is within the above range, room temperature aging is promoted due to the diffusion of Mg, and the extrudability becomes poor. Therefore, the content of Mg is 0.4% by weight or more,
It is 0.8% by weight or less. Further, Si has the effects of forming Mg 2 Si to improve the alloy strength and improve the ductility of the material as described above. But Si
If the addition amount of is less than 0.4% by weight, the strength of the material cannot be improved, and if it is 1.0% by weight or more, the ductility of the material is hindered. Furthermore, Si becomes nuclei for precipitation of Mg 2 Si, but as the addition amount increases, more nuclei for precipitation result.
Precipitation is more likely to proceed and the delayed action is lost. For the above reasons, the Si content is 0.4% by weight or more and 1.0% by weight or less.
【００１３】なお、上記範囲内では、Ｍｇが少ない領域
の方が優れた遅効性が得られ、また、押出性もよくなり
複雑な形状の押出が可能で、例えば自動車用部材として
の適用範囲が増す。従って、Ｍｇ含有量は好ましくは
０．６５重量％以下であり、この範囲内で際だって優れ
た遅効性を示す。より好ましくはＭｇ含有量は０．６重
量％以下であり、同時にＳｉを０．５〜０．７重量％の
範囲とすることにより、優れた強度と伸び、及び遅効性
を示す押出材を得ることができる。図１に本発明のＭｇ
及びＳｉの組成範囲を図示する。なお、Ｙ＝（１／１．
７３）Ｘのラインは、Ｍｇ2Ｓｉの化学量論比のライン
である。Within the above range, the Mg-reduced region has a better delayed-acting property, and the extrudability is also improved so that a complicated shape can be extruded. Increase. Therefore, the Mg content is preferably 0.65% by weight or less, and within this range, a markedly superior slow-release effect is exhibited. More preferably, the Mg content is 0.6% by weight or less, and at the same time, by setting Si in the range of 0.5 to 0.7% by weight, an extruded material exhibiting excellent strength, elongation, and delayed action is obtained. be able to. FIG. 1 shows the Mg of the present invention.
And the composition range of Si is illustrated. Note that Y = (1/1.
73) The X line is the line of the stoichiometric ratio of Mg 2 Si.
【００１４】Ｃｕ
Ｃｕは析出硬化により合金強度を向上させるとともに材
料の延性を向上させる。また、Ｃｕを添加することによ
り、Ｍｇ、Ｓｉによって生成される析出物Ｍｇ2Ｓｉを
均一微細に分布させる効果がある。しかし、Ｃｕの添加
量が０．１５重量％未満では前記効果を発揮することが
できない。一方、０．５重量％を超えるとプレス焼き入
れ性を低下させる。従って、Ｃｕの含有量は０．１５重
量％以上、０．５重量％以下とする。Cu Cu improves the alloy strength and the ductility of the material by precipitation hardening. In addition, the addition of Cu has the effect of uniformly and finely distributing the precipitate Mg 2 Si produced by Mg and Si. However, if the added amount of Cu is less than 0.15% by weight, the above effect cannot be exhibited. On the other hand, if it exceeds 0.5% by weight, press hardenability is deteriorated. Therefore, the Cu content is set to 0.15% by weight or more and 0.5% by weight or less.
【００１５】Ｍｎ、Ｃｒ、Ｚｒ
Ｍｎ、Ｃｒ、Ｚｒはビレットの均質化処理時において微
細な金属間化合物として析出し、結晶粒を微細化させる
ことにより、強度、延性を向上させる。しかし、これら
の元素は添加量が増えるとともに焼き入れ感受性を鋭く
し、プレス焼き入れ性を低下させる作用がある。Ｍｎ、
Ｃｒ、Ｚｒの添加量がそれぞれ０．０５重量％未満では
前記効果を発揮し得ない。一方、Ｍｎ、Ｃｒ、Ｚｒの添
加量がそれぞれ０．６重量％、０．３重量％、０．３重
量％を超えるか、これらの合計が０．９重量％を超える
と、粗大な金属間化合物が晶出してしまうとともに焼き
入れ感受性を鋭くし、所定の合金強度の向上が計れな
い。従って、Ｍｎ、Ｃｒ、Ｚｒを添加する場合は、Ｍｎ
０．０５〜０．６重量％、Ｃｒ０．０５〜０．３重量
％、Ｚｒ０．０５〜０．３重量％の内１種以上を合計で
０．９重量％以下とする。Mn, Cr, and Zr Mn, Cr, and Zr are precipitated as fine intermetallic compounds during homogenization of the billet, and crystal grains are refined to improve strength and ductility. However, these elements have the effect of sharpening the quenching sensitivity and decreasing the press hardenability as the added amount increases. Mn,
If the addition amounts of Cr and Zr are each less than 0.05% by weight, the above effect cannot be exhibited. On the other hand, if the addition amounts of Mn, Cr, and Zr exceed 0.6% by weight, 0.3% by weight, and 0.3% by weight, respectively, or if the total amount of these exceeds 0.9% by weight, coarse intermetallic compounds are present. As the compound crystallizes out, the quenching sensitivity becomes sharp, and the predetermined alloy strength cannot be improved. Therefore, when adding Mn, Cr and Zr, Mn
One or more of 0.05 to 0.6% by weight, Cr 0.05 to 0.3% by weight, and Zr 0.05 to 0.3% by weight are set to 0.9% by weight or less in total.
【００１６】Ｔｉ
Ｔｉは鋳造時における結晶粒を微細化することにより合
金強度を向上させる。この効果を発揮させるにはＴｉ添
加量は０．００５重量％以上とすることが必要である。
一方、Ｔｉ添加量が０．２重量％を超えると前記効果が
飽和してしまい、また粗大な金属間化合物が晶出し所定
の合金強度が得られない。従って、Ｔｉの含有量は０．
００５〜０．２重量％とする。Ti Ti improves the alloy strength by refining the crystal grains during casting. In order to exert this effect, the Ti addition amount must be 0.005% by weight or more.
On the other hand, if the amount of addition of Ti exceeds 0.2% by weight, the above effect is saturated, and coarse intermetallic compounds are crystallized, so that a predetermined alloy strength cannot be obtained. Therefore, the Ti content is 0.
It is 005 to 0.2% by weight.
【００１７】そのほか、不可避不純物としては少ない方
が好ましいが、Ｆｅは０．３５重量％以下、その他の不
純物は０．０５重量％以下であれば許容される。In addition, although it is preferable that the amount of unavoidable impurities is small, Fe is allowed to be 0.35% by weight or less and other impurities to be 0.05% by weight or less.
【００１８】上記の組成のアルミニウム合金鋳塊を、５
００〜６００℃で２〜１０ｈｒ均質化処理を行い、つい
で４４０〜５６０℃に再加熱した鋳塊を押出加工し、押
出直後にファン空冷によるプレス焼入れすることによ
り、遅効性アルミニウム合金押出材を得ることができ
る。なお、均質化処理条件を上記のように設定するの
は、５００℃未満では鋳造時に生じた偏析をマトリック
ス中に拡散させるには不十分であり、６００℃を超える
と局部溶解が発生し、押出時に欠陥となるためである。
また、押出加工に際して上記温度に再加熱するのは、４
４０℃未満では均質化処理後の冷却過程で生じた析出物
を分解させ固溶体状態とするには不十分であり、５６０
℃を超えると押出時の加工発熱により局部溶解が生じる
ためである。プレス焼入れをファン空冷によるのは焼入
れ時のひずみの発生を防止するためである。The aluminum alloy ingot having the above composition was added to 5
A slow-acting aluminum alloy extruded material is obtained by performing homogenization treatment at 00 to 600 ° C. for 2 to 10 hours, then extruding an ingot reheated to 440 to 560 ° C., and press quenching by fan air cooling immediately after extrusion. be able to. The homogenization treatment conditions set as described above are insufficient for diffusing segregation generated during casting into the matrix if the temperature is lower than 500 ° C, and local melting occurs if the temperature exceeds 600 ° C. This is because it sometimes becomes a defect.
In addition, when reheating to the above temperature during extrusion,
If the temperature is lower than 40 ° C, it is insufficient to decompose the precipitate generated in the cooling process after the homogenization treatment into a solid solution state.
This is because if the temperature exceeds ℃, local heat will be generated due to heat generated during processing during extrusion. Press quenching is performed by air cooling with a fan in order to prevent strain from occurring during quenching.
【００１９】[0019]
【実施例】以下、本発明の実施例について、本発明に規
定する条件から外れる比較例と比較して説明する。EXAMPLES Examples of the present invention will be described below in comparison with comparative examples that deviate from the conditions specified in the present invention.
【００２０】まず、表１に示す組成の１６０φ×１５０
ｈのアルミニウム合金ビレットに５８０℃×２ｈｒの均
質化処理を行った。そのビレットを再加熱しビレット温
度５００℃、押出速度５ｍ／ｍｉｎで押し出した。この
とき、プレス焼き入れをＮｏ．１８（ＪＩＳ６０６１）
のみ水冷を用い、その他についてはファン空冷にて行っ
た。押出材の断面形状は４０×４０×２ｔの角パイプに
て押し出した。First, 160 φ × 150 of the composition shown in Table 1
The aluminum alloy billet of h was homogenized at 580 ° C. for 2 hours. The billet was reheated and extruded at a billet temperature of 500 ° C. and an extrusion speed of 5 m / min. At this time, press quenching was performed using No. 18 (JIS6061)
Only water cooling was used, and others were air cooled with a fan. The cross-sectional shape of the extruded material was extruded with a square pipe of 40 × 40 × 2t.
【００２１】[0021]
【表１】 [Table 1]
【００２２】押出材からＪＩＳ５号引張試験片を採取
し、押出直後（３日以内）及び室温放置１２０日後に引
っ張り試験を行い、供試材の機械的性質を調査した。そ
の結果を表２に示す。また、表３には押出直後の押出材
に対し１９０℃×３ｈｒの人工時効を施した後（Ｔ５調
質）、同様にＪＩＳ５号引張試験片により機械的性質を
調査した結果を示す。A JIS No. 5 tensile test piece was sampled from the extruded material, and a tensile test was conducted immediately after extrusion (within 3 days) and after 120 days of standing at room temperature to investigate the mechanical properties of the test material. The results are shown in Table 2. Further, Table 3 shows the results of similarly examining mechanical properties by JIS No. 5 tensile test pieces after artificial aging (T5 tempering) was performed on the extruded material immediately after extrusion at 190 ° C. for 3 hours.
【００２３】[0023]
【表２】 [Table 2]
【００２４】[0024]
【表３】 [Table 3]
【００２５】Ｎｏ．１〜７は、従来品Ｎｏ．１８に比べ
長期の室温放置によっても機械的性質の変化が小さく、
Ｍｎ等を含まないＮｏ．７を除いてＴ５状態での強度は
従来品と同等となっている。比較例Ｎｏ．８、９の結果
をみると、Ｔｉの含有量が０．００５重量％未満のＮ
ｏ．９はＴ５状態での強度が低く、逆に０．２０重量％
を超えるＮｏ．８は粗大な金属間化合物のために強度、
伸び共に低い。 No. 1 to 7 are conventional product Nos. Compared with 18, the change in mechanical properties is small even when left at room temperature for a long time,
No. containing no Mn, etc. Except for 7, the strength in the T5 state is the same as the conventional product. Comparative Example No. The results of Nos. 8 and 9 show that the content of Ti is less than 0.005% by weight of N.
o. No. 9 has low strength in the T5 state, and conversely 0.20% by weight.
No. 8 is strength due to the coarse intermetallic compound,
Both growth is low.
【００２６】Ｍｎ、Ｃｒ、Ｚｒの含有量が０．９０重量
％を超える比較例Ｎｏ．１０の結果をみると、粗大な金
属間化合物とプレス焼き入れ性の低下のために、Ｔ５状
態での強度、伸びは共に低い。比較例Ｎｏ．１１、１２
の結果をみると、Ｍｇの含有量が０．４０重量％未満の
Ｎｏ．１２はＴ５状態での強度が低く、逆に０．８０重
量％を超えるＮｏ．１１は１２０日経過後の機械的性質
の変化が大きく、室温時効が進行していることが分か
る。Comparative Example No. 3 in which the contents of Mn, Cr and Zr exceeded 0.90% by weight. Looking at the result of No. 10, both strength and elongation in the T5 state are low due to the coarse intermetallic compound and the deterioration of press hardenability. Comparative Example No. 11, 12
Looking at the results of No. 3, the content of Mg is less than 0.40% by weight. No. 12 has a low strength in the T5 state, and conversely exceeds 0.80% by weight. It can be seen that No. 11 has a large change in mechanical properties after 120 days, and that aging at room temperature is progressing.
【００２７】比較例Ｎｏ．１３、１４の結果をみると、
Ｃｕの含有量が０．１５重量％未満のＮｏ．１４はＴ５
状態での強度が低く、逆に０．５０重量％を超えるＮ
ｏ．１３は強度、伸びが共に低く、室温時効も進行して
いる。比較例Ｎｏ．１５、１６の結果をみると、Ｓｉの
含有量が０．４０重量％未満であるＮｏ．１６はＴ５状
態での強度が低く、逆に０．８０重量％を超えるＮｏ．
１５は伸びが低い。Comparative Example No. Looking at the results of 13 and 14,
No. with a Cu content of less than 0.15% by weight. 14 is T5
Strength is low and conversely N exceeds 0.50% by weight
o. In No. 13, both strength and elongation are low, and room temperature aging is progressing. Comparative Example No. Looking at the results of Nos. 15 and 16, No. 1 having a Si content of less than 0.40% by weight. No. 16 has a low strength in the T5 state, and conversely exceeds 0.80% by weight.
No. 15 has low elongation.
【００２８】比較例Ｎｏ．１７は、Ｙ≧（１／１．７
３）Ｘ＋０．１５の範囲内になく、１２０日経過後の機
械的性質の変化が大きく、Ｓｉによる室温時効の抑制効
果が不十分で室温時効が進行していることが分かる。Comparative Example No. 17 is Y ≧ (1 / 1.7
3) It is not within the range of X + 0.15, the change in mechanical properties after 120 days is large, and it can be seen that the effect of suppressing room temperature aging by Si is insufficient and room temperature aging is progressing.
【００２９】[0029]
【発明の効果】本発明によれば、所定の組成を有するア
ルミニウム合金を押出してファン空冷によるプレス焼き
入れを与えることにより、高強度の遅効性アルミニウム
合金押出材を得ることができる。また、前記アルミニウ
ム合金押出材を自動車用フレーム等に用いることによ
り、軽量で曲げ加工精度の優れるアルミニウム合金製自
動車フレームを組み立てることができる。According to the present invention, a high-strength delayed-acting aluminum alloy extruded material can be obtained by extruding an aluminum alloy having a predetermined composition and subjecting it to press quenching by air cooling with a fan. Further, by using the aluminum alloy extruded material for an automobile frame or the like, it is possible to assemble an aluminum alloy automobile frame which is lightweight and has excellent bending accuracy.
【図１】本発明のＭｇ、Ｓｉ範囲を示す図である。FIG. 1 is a diagram showing Mg and Si ranges of the present invention.
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 平６−25783（ＪＰ，Ａ) 特開 平５−247575（ＪＰ，Ａ) 特開 平５−279780（ＪＰ，Ａ) 特開 昭60−221544（ＪＰ，Ａ) 特開 昭57−82450（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C22C 21/00 - 21/18 B21C 23/00 C22F 1/04 - 1/057 ─────────────────────────────────────────────────── --- Continuation of front page (56) References JP-A-6-25783 (JP, A) JP-A-5-247575 (JP, A) JP-A-5-279780 (JP, A) JP-A-60- 221544 (JP, A) JP-A-57-82450 (JP, A) (58) Fields investigated (Int.Cl. 7 , DB name) C22C 21/00-21/18 B21C 23/00 C22F 1/04- 1/057
Claims (3)
５〜０．７重量％、Ｃｕ０．１５〜０．５重量％、Ｔｉ
０．００５〜０．２重量％を含有し、残部Ａｌ及び不可
避不純物からなり、さらに、Ｍｇ含有重量％をＸ、Ｓｉ
含有重量％をＹとしたとき、Ｙ≧（１／１．７３）Ｘ＋
０．１５の関係を満たし、かつＴ１状態であることを特
徴とする曲げ加工用遅効性アルミニウム合金押出材。1. Mg 0.4 to 0.65% by weight, Si0.
5 to 0.7% by weight, Cu 0.15 to 0.5% by weight, Ti
0.005 to 0.2% by weight, the balance Al and unavoidable impurities, and further Mg content by weight% X, Si
When the content weight% is Y, Y ≧ (1 / 1.73) X +
A delayed-acting aluminum alloy extruded material for bending, which satisfies the relationship of 0.15 and is in a T1 state.
０５〜０．３重量％、Ｚｒ０．０５〜０．３重量％の内
１種以上を合計で０．９重量％以下含有することを特徴
とする請求項１に記載された曲げ加工用遅効性アルミニ
ウム合金押出材。2. Mn 0.05 to 0.6% by weight, Cr 0.
05-0.3% by weight, Zr 0.05-0.3% by weight, and one or more kinds in total of 0.9% by weight or less is contained, and the delayed effect for bending according to claim 1 . Aluminum alloy extruded material.
る請求項１又は２に記載された曲げ加工用遅効性アルミ
ニウム合金押出材。3. The slow-acting aluminum alloy extruded material for bending according to claim 1 or 2 , which is used for an automobile frame.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP35274896A JP3481064B2 (en) | 1996-12-12 | 1996-12-12 | Slow acting aluminum alloy extruded material for bending |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP35274896A JP3481064B2 (en) | 1996-12-12 | 1996-12-12 | Slow acting aluminum alloy extruded material for bending |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH10168535A JPH10168535A (en) | 1998-06-23 |
| JP3481064B2 true JP3481064B2 (en) | 2003-12-22 |
Family
ID=18426178
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP35274896A Expired - Fee Related JP3481064B2 (en) | 1996-12-12 | 1996-12-12 | Slow acting aluminum alloy extruded material for bending |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3481064B2 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103643092B (en) * | 2013-12-24 | 2016-01-06 | 北京科技大学 | Large strain intensified index AlMgSi sheet alloy and preparation method thereof |
-
1996
- 1996-12-12 JP JP35274896A patent/JP3481064B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH10168535A (en) | 1998-06-23 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US5389165A (en) | Low density, high strength Al-Li alloy having high toughness at elevated temperatures | |
| EP0480402B1 (en) | Process for manufacturing aluminium alloy material with excellent formability, shape fixability and bake hardenability | |
| JPH07109536A (en) | Aluminum alloy for forging and heat treatment therefor | |
| JP2997145B2 (en) | Method for producing aluminum alloy sheet having delayed aging at room temperature | |
| JP7318274B2 (en) | Al-Mg-Si-based aluminum alloy cold-rolled sheet and its manufacturing method, and Al-Mg-Si-based aluminum alloy cold-rolled sheet for forming and its manufacturing method | |
| JPH07252574A (en) | Al-cu-mg alloy excellent in toughness and its production | |
| JP3516566B2 (en) | Aluminum alloy for cold forging and its manufacturing method | |
| JPH04341546A (en) | Production of high strength aluminum alloy-extruded shape material | |
| JP5166702B2 (en) | 6000 series aluminum extrudate excellent in paint bake hardenability and method for producing the same | |
| JP2663078B2 (en) | Aluminum alloy for T6 treatment with stable artificial aging | |
| JPH07145440A (en) | Aluminum alloy forging stock | |
| JP3481064B2 (en) | Slow acting aluminum alloy extruded material for bending | |
| JPH08232035A (en) | High strength aluminum alloy material for bumper, excellent in bendability, and its production | |
| JPH07150312A (en) | Manufacture of aluminum alloy forged base stock | |
| JPH08232053A (en) | Production of high strength aluminum alloy extruded material | |
| JPH0543974A (en) | Aluminum alloy sheet excellent in baking hardenability of coating material and press formability and its production | |
| JP3504917B2 (en) | Aluminum-beryllium-silicon alloy for automotive engine moving parts and casing members | |
| JP2000160272A (en) | Al ALLOY SHEET EXCELLENT IN PRESS FORMABILITY | |
| JPH09202933A (en) | High strength aluminum alloy excellent in hardenability | |
| JPH06145918A (en) | Production of al-li alloy extruded material excellent in toughness | |
| JPH06212336A (en) | Al alloy extruded material excellent in strength and bendability | |
| JP3248263B2 (en) | Al-Mn alloy for cryogenic forming | |
| JPH09176805A (en) | Production of aluminum fin material | |
| JPH04160131A (en) | Al-mg-si alloy plate excellent in strength and formability, and its manufacture | |
| JP3208234B2 (en) | Aluminum alloy sheet for forming process excellent in formability and method for producing the same |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20081010 Year of fee payment: 5 |
|
| LAPS | Cancellation because of no payment of annual fees |