JPH05279780A - Medium-strength aluminum alloy excellent in bendability and its production - Google Patents
Medium-strength aluminum alloy excellent in bendability and its productionInfo
- Publication number
- JPH05279780A JPH05279780A JP10538592A JP10538592A JPH05279780A JP H05279780 A JPH05279780 A JP H05279780A JP 10538592 A JP10538592 A JP 10538592A JP 10538592 A JP10538592 A JP 10538592A JP H05279780 A JPH05279780 A JP H05279780A
- Authority
- JP
- Japan
- Prior art keywords
- aluminum alloy
- alloy
- strength
- less
- medium
- 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.)
- Pending
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 20
- 238000004519 manufacturing process Methods 0.000 title claims description 8
- 230000032683 aging Effects 0.000 claims abstract description 18
- 238000005452 bending Methods 0.000 claims abstract description 16
- 239000002244 precipitate Substances 0.000 claims abstract description 12
- 239000011159 matrix material Substances 0.000 claims abstract description 9
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 239000000203 mixture Substances 0.000 claims abstract description 6
- 229910019018 Mg 2 Si Inorganic materials 0.000 claims description 16
- 239000000956 alloy Substances 0.000 abstract description 7
- 229910045601 alloy Inorganic materials 0.000 abstract description 6
- 229910052804 chromium Inorganic materials 0.000 abstract description 5
- 229910052726 zirconium Inorganic materials 0.000 abstract description 4
- 229910052748 manganese Inorganic materials 0.000 abstract description 3
- 230000001376 precipitating effect Effects 0.000 abstract description 2
- 229910019752 Mg2Si Inorganic materials 0.000 abstract 2
- 230000001105 regulatory effect Effects 0.000 abstract 2
- 238000001556 precipitation Methods 0.000 description 9
- 238000011156 evaluation Methods 0.000 description 8
- 238000001125 extrusion Methods 0.000 description 7
- 230000000694 effects Effects 0.000 description 6
- 238000000265 homogenisation Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 4
- 238000000034 method Methods 0.000 description 4
- 238000010791 quenching Methods 0.000 description 4
- 230000000171 quenching effect Effects 0.000 description 4
- 230000035945 sensitivity Effects 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000002950 deficient Effects 0.000 description 2
- 230000001771 impaired effect Effects 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 229910021365 Al-Mg-Si alloy Inorganic materials 0.000 description 1
- 238000003483 aging Methods 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000007788 roughening Methods 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
Landscapes
- Extrusion Of Metal (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、自動車のシートベルト
等に用いられる中強度の機械的性質を有し、曲げ加工時
のスプリングバック量のバラツキがなく、かつ押出し等
の熱間加工性に優れたアルミニウム合金およびその製造
方法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention has medium-strength mechanical properties used for automobile seat belts, etc., has no variation in the amount of springback during bending, and is excellent in hot workability such as extrusion. The present invention relates to an excellent aluminum alloy and a manufacturing method thereof.
【０００２】[0002]
【従来の技術】最近自動車の車種拡大に伴い、シートベ
ルトにアルミニウム合金を用いることが提案され開発が
進められている。このシートベルトに要求される特性と
しては、優れた中強度の機械的性質を有し、曲げ加工時
のスプリングバック量の大きなバラツキのない成形加工
性と、耐食性の優れていることが求められている。現在
シートベルト材に適したアルミニウム合金として、Ａｌ
−Ｍｇ−Ｓｉ系合金のＪＩＳ６０６１（Ａｌ−0.6wt%
Ｓｉ−0.27wt% Ｃｕ−1.0wt% Ｍｇ−0.2wt% Ｃｒ）
またはＪＩＳ６０６３（Ａｌ−0.4wt% Ｍｇ−0.47wt%
Ｓｉ）が用いられている。しかし前記のアルミニウム
合金は、例えば曲げ加工時のスプリングバック量のバラ
ツキが大きいため問題となっている。すなわち、前記の
アルミニウム合金の製造方法として、通常は押出加工に
より製造されるが、所要強度を得るために押出加工の直
後に水冷（焼入れ）を施すとスプリングバック量のバラ
ツキが大きくなり、スプリングバック量のバラツキを抑
えると所要強度が得られない難点があった。2. Description of the Related Art Recently, with the expansion of vehicle types of automobiles, the use of aluminum alloys for seat belts has been proposed and developed. The characteristics required for this seat belt are that it has excellent medium-strength mechanical properties, moldability without large variations in the amount of springback during bending, and excellent corrosion resistance. There is. As an aluminum alloy currently suitable for seat belt materials, Al
-Mg-Si alloy JIS 6061 (Al-0.6wt%
Si-0.27wt% Cu-1.0wt% Mg-0.2wt% Cr)
Or JIS6063 (Al-0.4wt% Mg-0.47wt%
Si) is used. However, the above-mentioned aluminum alloy has a problem in that the amount of springback during bending is large, for example. That is, as a method for producing the above aluminum alloy, it is usually produced by extrusion, but if water cooling (quenching) is performed immediately after extrusion to obtain the required strength, the variation in the amount of springback increases, and springback There is a problem that the required strength cannot be obtained when the variation in the amount is suppressed.
【０００３】[0003]
【発明が解決しようとする課題】本発明は前記の問題に
ついて検討の結果なされたもので、スプリングバック量
のバラツキがなく、所要の中強度の機械的性質を有し、
かつ成形加工性の良好なアルミニウム合金及びその製造
方法を開発したものである。DISCLOSURE OF THE INVENTION The present invention has been made as a result of studying the above-mentioned problems, and has the required intermediate-strength mechanical properties without variations in the amount of springback.
In addition, an aluminum alloy having good formability and a method for producing the same have been developed.
【０００４】[0004]
【課題を解決するための手段】本発明は、Ｓｉ0.3 〜0.
7wt%、Ｍｇ0.4 〜0.8wt%、Ｃｕ0.01〜0.3wt%、Ｚｒ0.05
wt% 未満、Ｍｎ0.05wt% 未満、Ｃｒ0.05〜0.25wt% を含
有し、残部Ａｌと不可避的不純物とからなり、マトリッ
クス中に微細分散析出するＭｇ2 Ｓｉが0.8 〜1.5wt%
で、かつＭｇ2 Ｓｉ析出物の数密度が50〜300 個/ μｍ
3 であることを特徴とする曲げ加工性に優れた中強度ア
ルミニウム合金を請求項１とし、Ｓｉ0.3 〜0.7wt%、Ｍ
ｇ0.4 〜0.8wt%、Ｃｕ0.01〜0.3wt%、Ｚｒ0.05wt% 未
満、Ｍｎ0.05wt% 未満、Ｃｒ0.05〜0.25wt% を含有し、
残部Ａｌと不可避的不純物とからなるＡｌ合金鋳塊を、
500 〜580 ℃の温度で2 〜24時間の均質化処理を施した
後、400 〜520 ℃の温度で押出し、次いで140 〜210 ℃
で2 〜36時間の時効処理を施して、マトリックス中に微
細分散析出するＭｇ2 Ｓｉが0.8 〜1.5wt%で、かつＭｇ
2 Ｓｉ析出物の数密度が50〜300 個/ μｍ3 であること
を特徴とする曲げ加工性に優れた中強度アルミニウム合
金の製造方法を請求項２とするものである。すなわち本
発明は、前記の組成範囲のＡｌ合金を、前記のような製
造条件下で製造することにより、Ｍｇ2 Ｓｉの金属間化
合物を析出させ、この析出物の存在量を前記の特定の範
囲にマトリックス中に微細に分散析出させることによっ
て、スプリングバック量を安定にし、所要の強度を保持
させると共に成形加工性の良好なＡｌ合金を得たもので
ある。SUMMARY OF THE INVENTION The present invention is based on Si0.3-0.
7wt%, Mg0.4-0.8wt%, Cu0.01-0.3wt%, Zr0.05
It contains less than wt%, less than 0.05 wt% Mn, and 0.05 to 0.25 wt% Cr, and consists of the balance Al and unavoidable impurities, and 0.8 to 1.5 wt% of Mg 2 Si finely dispersed and precipitated in the matrix.
And the number density of Mg 2 Si precipitates is 50 to 300 / μm
3. A medium-strength aluminum alloy having excellent bending workability, characterized in that the content of Si is 0.3 to 0.7 wt%, M
g0.4-0.8wt%, Cu0.01-0.3wt%, Zr0.05wt%, Mn0.05wt%, Cr0.05-0.25wt%,
An Al alloy ingot composed of the balance Al and unavoidable impurities,
After homogenizing treatment at a temperature of 500-580 ° C for 2-24 hours, extruding at a temperature of 400-520 ° C, then 140-210 ° C.
After aging treatment for 2-36 hours, the amount of Mg 2 Si finely dispersed and precipitated in the matrix is 0.8-1.5 wt%, and
A method for producing a medium-strength aluminum alloy having excellent bending workability is characterized in that the number density of 2 Si precipitates is 50 to 300 pieces / μm 3 . That is, the present invention is to produce an Al alloy having the above composition range under the production conditions as described above to precipitate an intermetallic compound of Mg 2 Si, and to adjust the amount of this precipitate to the above specified range. By finely dispersing and precipitating it in the matrix, the amount of springback is stabilized, the required strength is maintained, and an Al alloy having good moldability is obtained.
【０００５】[0005]
【作用】次に本発明の合金組成を前記のように限定した
理由について述べる。Ｍｇは、得られる合金材の強度を
向上させる効果を有する。Ｍｇの含有量が0.4wt%未満で
は、時効処理によりＳｉと結びついた金属間化合物Ｍｇ
2 Ｓｉの均一微細な析出が起こるものの存在量が不十分
で、所定の強度が得られない。また0.8wt%を越えると熱
間加工性が低下して例えば押出加工性が劣り生産性を損
うことになる。したがって0.4 〜0.8wt%が好ましい。Ｓ
ｉはＭｇと同様に合金の強度を向上させる効果を有す
る。しかし0.3wt%未満ではＭｇ2 Ｓｉ生成量との関係か
ら、例えば押出加工後のＴ６処理による強度向上に有効
な過剰Ｓｉ量が十分でなく、また0.7wt%を越えると押出
加工性及び成形性が低下して生産性を損なう。したがっ
て0.3 〜0.7wt%が好ましい。Ｃｕは時効硬化により機械
的性質を向上させる成分であるが、その量が0.01wt% 未
満では効果が少なく、逆に0.3wt%を越えると材料の耐食
性を損なう。したがって0.01〜0.3wt%が適当である。Ｍ
ｎ、Ｚｒ及びＣｒは、それぞれの成分が共存状態でＡｌ
マトリックス中に微細分散し、Ａｌマトリックス全体を
微細再結晶化すると共に、Ｓｉの粒界析出を防止して靱
性を向上させ、さらにこの微細再結晶組織によって、曲
げ加工を施した後の押出材の表面にオレンジピール状の
肌荒が発生することを防止する作用がある。しかしＭｎ
及びＺｒ量が0.05wt% 以上では粗大化合物の生成、焼入
れ感受性の増大、強度及び押出加工性の劣化を招く。ま
たＣｒ量が0.05wt% 未満では前記したＭｎ、Ｚｒと同様
の効果が少なく、0.25wt% を越えると焼入れ感受性の増
大、強度及び押出加工性が低下する。なお、不可避的不
純物としてはＦｅ，Ｚｎ，Ｔｉ，Ｂ等があるが、普通の
Ａｌ地金中に含まれるＦｅ0.7wt%以下, Ｚｎ0.25wt以下
は本発明に影響はない。また、Ｔｉ0.15wt% 以下, Ｂ0.
05wt% 以下も本発明に影響はない。Next, the reason why the alloy composition of the present invention is limited as described above will be described. Mg has the effect of improving the strength of the alloy material obtained. If the Mg content is less than 0.4 wt%, the intermetallic compound Mg combined with Si by aging treatment
Although uniform and fine precipitation of 2 Si occurs, the existing amount is insufficient, and a predetermined strength cannot be obtained. On the other hand, if it exceeds 0.8 wt%, the hot workability is deteriorated and, for example, the extrudability is poor and the productivity is impaired. Therefore, 0.4 to 0.8 wt% is preferable. S
i has the effect of improving the strength of the alloy similarly to Mg. However, if it is less than 0.3 wt%, the amount of excess Si effective for strength improvement by T6 treatment after extrusion is insufficient due to the relationship with the amount of Mg 2 Si produced, and if it exceeds 0.7 wt%, the extrudability and formability are improved. Lowers the productivity. Therefore, 0.3 to 0.7 wt% is preferable. Cu is a component that improves mechanical properties by age hardening, but if its amount is less than 0.01 wt%, it has little effect, and if it exceeds 0.3 wt%, the corrosion resistance of the material is impaired. Therefore, 0.01 to 0.3 wt% is appropriate. M
n, Zr, and Cr are Al when the respective components coexist.
Finely dispersed in the matrix to finely recrystallize the entire Al matrix, prevent grain boundary precipitation of Si to improve toughness, and this fine recrystallized structure allows the extruded material after bending to be processed. It has the effect of preventing orange peel-like roughening of the surface. But Mn
If the Zr content is 0.05 wt% or more, coarse compounds are produced, quenching sensitivity is increased, and strength and extrudability are deteriorated. When the Cr content is less than 0.05 wt%, the same effect as Mn and Zr described above is small, and when it exceeds 0.25 wt%, the quenching sensitivity is increased and the strength and the extrudability are deteriorated. Although unavoidable impurities include Fe, Zn, Ti, B, etc., Fe 0.7 wt% or less and Zn 0.25 wt or less, which are contained in ordinary Al metal, do not affect the present invention. Also, Ti 0.15 wt% or less, B0.
The amount of 05 wt% or less does not affect the present invention.
【０００６】次に、本発明に係るアルミニウム合金の製
造方法について説明する。均質化処理はマトリックスの
溶質濃度を下げ、Ｍｇ2 Ｓｉ等の析出粒子を均一に分散
させるもので、高温で均一化し、低温で析出処理を行う
のが望ましい。均質化処理条件が580 ℃を越えると、Ｆ
ｅやＭｎの析出が大きくなり押出性、焼入れ感受性を敏
感にして性能を劣化させる。また500 ℃未満や、長時間
保持でも析出物の粗大化からの押出性の劣化を伴う。し
たがって均質化処理は500 〜580 ℃、2 〜24時間の条件
範囲内で行うのが適当である。次いで行う熱間加工は、
通常は押出しにより行うが、圧延やスエージングでもよ
く、その温度は400 〜520 ℃が好ましい。400 ℃未満で
は加工性が低く、520℃を越えると割れなどの障害がで
る。時効処理は、時効初期に生じるクラスターを均一分
散させ、これをＧＰゾーンあるいは中間層へと成長させ
強度を向上するもので、好ましくは２段時効で１段目は
140 〜160 ℃でＭｇ2 Ｓｉを微細均一に析出させ、２段
目を200 ℃程度の高温時効で粗大ＧＰゾーン中間層へと
成長させることが望ましい。しかし２段時効は長時間保
持と工程の複雑化により生産性を低下させるので、その
場合は１段時効とし140 〜210 ℃で2 〜36時間処理が可
能である。時効温度が210 ℃を越えるとＭｇ2 Ｓｉの成
長による粗大化と微細析出が不十分であり、140 ℃未満
ではＭｇ2 Ｓｉの析出が不十分となる。また時効時間が
2時間より短いと性能のバラツキを生じ、36時間より長
いと生産性が低下する。従って時効処理は１段時効、２
段時効に拘わらず140 〜210 ℃、2 〜36時間の範囲で適
宜選択して行うことが好ましい。Next, a method for manufacturing an aluminum alloy according to the present invention will be described. The homogenization treatment lowers the solute concentration of the matrix and uniformly disperses precipitated particles such as Mg 2 Si. It is desirable to homogenize at high temperature and perform precipitation treatment at low temperature. If the homogenization condition exceeds 580 ℃, F
Precipitation of e and Mn becomes large and extrudability and quenching sensitivity become sensitive, resulting in deterioration of performance. In addition, extrudability deteriorates due to coarsening of precipitates even if held below 500 ° C or for a long time. Therefore, it is appropriate to carry out the homogenizing treatment within the condition range of 500 to 580 ° C and 2 to 24 hours. The next hot working is
Usually, it is carried out by extrusion, but rolling or swaging may be carried out, and the temperature is preferably 400 to 520 ° C. If it is less than 400 ° C, the workability is low, and if it exceeds 520 ° C, cracks and other problems occur. The aging treatment is to uniformly disperse the clusters generated at the initial stage of aging and grow the clusters in the GP zone or the intermediate layer to improve the strength.
It is desirable to finely and uniformly precipitate Mg 2 Si at 140 to 160 ° C. and to grow the second stage into a coarse GP zone intermediate layer by high temperature aging at about 200 ° C. However, the two-step aging lowers the productivity due to long-term holding and complicated processes, and in that case, the one-step aging can be performed at 140 to 210 ° C for 2 to 36 hours. If the aging temperature exceeds 210 ° C, coarsening and fine precipitation due to the growth of Mg 2 Si are insufficient, and if it is less than 140 ° C, the precipitation of Mg 2 Si is insufficient. Also the aging time
If it is shorter than 2 hours, the performance will vary, and if it is longer than 36 hours, the productivity will decrease. Therefore, the aging treatment is 1 step aging, 2
Regardless of the step aging, it is preferable to select appropriately within the range of 140 to 210 ° C. and 2 to 36 hours.
【０００７】[0007]
【実施例】以下に本発明の一実施例について説明する。
表１に示す各種組成のＡｌ合金を半連続鋳造により345m
m φの押出用鋳塊に鋳造した後、同表に示す種々の温度
と時間により均質化処理を施した。次に420 ℃に再加熱
して、押出機によりシートベルト用形材（平均肉厚2 〜
5mm ）に10m/min の押出速度で押出した。続いてこれら
の押出材について、同表に示すような温度と時間により
時効処理を施した。以上の工程で製造した形材につい
て、引張強さ、耐力、伸び等の機械的性質を、Ｍｇ2 Ｓ
ｉ析出物はＴＥＭ観察により形状と分散形態を観察し、
数密度を算出した。押出性はラム速度から押出速度を算
出し、曲げ性はシートベルト用の曲げ加工性に供されて
いるものと同様に行い、スプリングバック量が規格内で
あるかどうか見極め、さらに肌荒れや割れの発生につい
ても調べ総合評価として、◎印非常に良、○印良、△印
稍不良、×印不良で示した。これらの試験結果を表２に
示す。EXAMPLE An example of the present invention will be described below.
345m of Al alloys with various compositions shown in Table 1 by semi-continuous casting
After casting into a mφ extrusion ingot, homogenization treatment was performed at various temperatures and times shown in the table. Then, reheat to 420 ° C and use an extruder to form seat belt profiles (average wall thickness 2 ~
5 mm) at an extrusion speed of 10 m / min. Subsequently, these extruded materials were subjected to an aging treatment at the temperature and time shown in the same table. For profiles produced in the above process, the tensile strength, yield strength, mechanical properties such as elongation, Mg 2 S
The shape and dispersion morphology of the i precipitate were observed by TEM observation.
The number density was calculated. The extrudability is calculated from the ram speed, and the bendability is the same as that used for bending workability for seat belts. The occurrence was also examined, and as a comprehensive evaluation, ⊚ markedly good, ○ marked good, Δ marked defective, and × marked defective. The results of these tests are shown in Table 2.
【０００８】[0008]
【表１】 [Table 1]
【０００９】[0009]
【表２】 [Table 2]
【００１０】表１及び２から明らかなように、本発明の
合金組成のNo.1〜4 は、機械的性質が従来合金のJIS606
1 相当のNo.11 と、JIS6063 相当のNo.12 と同程度であ
るが、粒内のＭｇ2 Ｓｉ析出物が針状で微細分散してお
り、Ｍｇ2 Ｓｉの数密度も大きく、押出性や曲げ加工
性、及びスプリングバック量等の総合評価が優れてい
る。一方、比較例のNo.5はＭｇが少ないため、No.7はＳ
ｉが少ないため、いずれもＭｇ2 Ｓｉの析出が不十分
で、押出性、曲げ加工性、総合評価が劣る。No.6はＣｕ
が少ないため、機械的性質、曲げ加工性及び総合評価が
劣る。No.8はＺｒ及びＣｒが多いため、機械的性質、曲
げ加工性、総合評価が劣る。またNo.9は均質化温度が低
く、時効処理温度が高いため粗大Ｍｇ2 Ｓｉとなり、押
出性、曲げ加工性、総合評価が劣る。No.10 は時効処理
温度が低いため析出が不十分で押出性、曲げ加工性、総
合評価のいずれかが劣る。さらに従来のNo.11 及び12
は、均質化処理、時効処理を本発明方法の範囲で行った
ものであるが、析出状態が本発明のようにならず、押出
性、曲げ加工性、総合評価が悪い。As is clear from Tables 1 and 2, the alloy compositions Nos. 1 to 4 of the present invention have mechanical properties of JIS 606 which is a conventional alloy.
No.11 equivalent to 1 and No.12 equivalent to JIS6063 are similar, but Mg 2 Si precipitates in the grains are finely dispersed in the shape of needles, and the number density of Mg 2 Si is large and the extrudability is high. Excellent overall evaluation of bending workability and springback amount. On the other hand, since No. 5 of the comparative example has a small amount of Mg, No. 7 has S
Since i is small, precipitation of Mg 2 Si is insufficient in all cases, and extrudability, bending workability, and overall evaluation are poor. No.6 is Cu
Therefore, the mechanical properties, bending workability, and overall evaluation are poor. Since No. 8 contains a large amount of Zr and Cr, mechanical properties, bending workability, and overall evaluation are poor. In addition, No. 9 has a low homogenization temperature and a high aging temperature, resulting in coarse Mg 2 Si, which is poor in extrudability, bending workability, and overall evaluation. No. 10 has a low aging temperature, so that precipitation is insufficient and extrudability, bending workability, and overall evaluation are poor. Furthermore, conventional No. 11 and 12
Shows that the homogenization treatment and the aging treatment were carried out within the range of the method of the present invention, but the precipitation state was not as in the present invention, and the extrudability, bending workability and comprehensive evaluation were poor.
【００１１】[0011]
【発明の効果】以上に説明したように本発明によれば、
強度が安定し、成形加工性に優れ、かつスプリングバッ
ク量の安定したアルミニウム合金を得ることが出来、工
業上顕著な効果を奏するものである。As described above, according to the present invention,
It is possible to obtain an aluminum alloy having stable strength, excellent moldability, and stable springback amount, which is a significant industrial effect.
Claims (2)
Ｃｕ0.01〜0.3wt%、Ｚｒ0.05wt% 未満、Ｍｎ0.05wt% 未
満、Ｃｒ0.05〜0.25wt% を含有し、残部Ａｌと不可避的
不純物とからなり、マトリックス中に微細分散析出する
Ｍｇ2 Ｓｉが0.8 〜1.5wt%で、かつＭｇ2 Ｓｉ析出物の
数密度が50〜300 個/ μｍ3 であることを特徴とする曲
げ加工性に優れた中強度アルミニウム合金。1. Si 0.3 to 0.7 wt%, Mg 0.4 to 0.8 wt%,
Cu0.01～0.3Wt%, less than Zr0.05Wt%, less than Mn0.05Wt%, containing Cr0.05～0.25Wt%, consists of a balance being Al and unavoidable impurities, finely dispersed precipitates in a matrix Mg 2 Si is 0.8 to 1.5 wt% and the number density of Mg 2 Si precipitates is 50 to 300 pieces / μm 3, which is a medium strength aluminum alloy excellent in bending workability.
Ｃｕ0.01〜0.3wt%、Ｚｒ0.05wt% 未満、Ｍｎ0.05wt% 未
満、Ｃｒ0.05〜0.25wt% を含有し、残部Ａｌと不可避的
不純物とからなるＡｌ合金鋳塊を、500 〜580 ℃の温度
で2 〜24時間の均質化処理を施した後、400 〜520 ℃の
温度で押出し、次いで140 〜210 ℃で2 〜36時間の時効
処理を施して、マトリックス中に微細分散析出するＭｇ
2 Ｓｉが0.8 〜1.5wt%で、かつＭｇ2 Ｓｉ析出物の数密
度が50〜300 個/ μｍ3 であることを特徴とする曲げ加
工性に優れた中強度アルミニウム合金の製造方法。2. Si0.3-0.7wt%, Mg0.4-0.8wt%,
An Al alloy ingot containing 0.01 to 0.3% by weight of Cu, less than 0.05% by weight of Zr, less than 0.05% by weight of Mn, and 0.05 to 0.25% by weight of Cr, and the balance of Al and unavoidable impurities was prepared at 500 to 580 ° C. After the homogenizing treatment at a temperature of 2 to 24 hours, the mixture is extruded at a temperature of 400 to 520 ° C, and then an aging treatment at 140 to 210 ° C for 2 to 36 hours to form a finely dispersed Mg precipitate in the matrix.
A method for producing a medium-strength aluminum alloy having excellent bendability, characterized in that 2 Si is 0.8 to 1.5 wt% and the number density of Mg 2 Si precipitates is 50 to 300 pieces / μm 3 .
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10538592A JPH05279780A (en) | 1992-03-31 | 1992-03-31 | Medium-strength aluminum alloy excellent in bendability and its production |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10538592A JPH05279780A (en) | 1992-03-31 | 1992-03-31 | Medium-strength aluminum alloy excellent in bendability and its production |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH05279780A true JPH05279780A (en) | 1993-10-26 |
Family
ID=14406202
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP10538592A Pending JPH05279780A (en) | 1992-03-31 | 1992-03-31 | Medium-strength aluminum alloy excellent in bendability and its production |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH05279780A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0714993A1 (en) * | 1994-11-29 | 1996-06-05 | Alusuisse-Lonza Services AG | Deep drawable and weldable AlMgSi type aluminium alloy |
| WO1997011203A1 (en) * | 1995-09-19 | 1997-03-27 | Alcan International Limited | Precipitation-hardened aluminum alloys for automotive structural applications |
| AU746249B2 (en) * | 1998-03-20 | 2002-04-18 | Alcan International Limited | Extrudable aluminum alloys |
-
1992
- 1992-03-31 JP JP10538592A patent/JPH05279780A/en active Pending
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0714993A1 (en) * | 1994-11-29 | 1996-06-05 | Alusuisse-Lonza Services AG | Deep drawable and weldable AlMgSi type aluminium alloy |
| CH688379A5 (en) * | 1994-11-29 | 1997-08-29 | Alusuisse Lonza Services Ag | Thermaformed and weldable aluminum alloy of the AlMgSi type |
| WO1997011203A1 (en) * | 1995-09-19 | 1997-03-27 | Alcan International Limited | Precipitation-hardened aluminum alloys for automotive structural applications |
| AU746249B2 (en) * | 1998-03-20 | 2002-04-18 | Alcan International Limited | Extrudable aluminum alloys |
| US6565679B1 (en) * | 1998-03-20 | 2003-05-20 | Alcan International Limited | Extrudable aluminum alloys |
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