JPH0711368A - Al-mg-si series alloy extruded material excellent in bendability - Google Patents
Al-mg-si series alloy extruded material excellent in bendabilityInfo
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- JPH0711368A JPH0711368A JP11339894A JP11339894A JPH0711368A JP H0711368 A JPH0711368 A JP H0711368A JP 11339894 A JP11339894 A JP 11339894A JP 11339894 A JP11339894 A JP 11339894A JP H0711368 A JPH0711368 A JP H0711368A
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- bendability
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は自動車のサイドメンバー
及びバンパー等のように高強度であると共に曲げ加工性
が要求される用途に好適の曲げ性が優れたＡｌ−Ｍｇ−
Ｓｉ系合金押出材に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention is Al-Mg- which has excellent bendability and is suitable for applications requiring high bending strength such as side members and bumpers of automobiles.
The present invention relates to a Si-based alloy extruded material.
【０００２】[0002]
【従来の技術】アルミニウム合金は鉄に比して軽量であ
ると共に錆びにくいという長所があり、近年、自動車、
各種車輌、船舶及び建築等の分野に広く使用されてい
る。2. Description of the Related Art Aluminum alloys have the advantages of being lighter in weight and less rusty than iron.
Widely used in various fields such as vehicles, ships and construction.
【０００３】ところで、自動車のサイドメンバー及びバ
ンパー等の部品に使用される材料には、高強度であると
共に曲げ加工性が優れていることが要求される。このた
め、従来、これらの部品には、ＮＰ１１４及びＳＰＣＣ
等の鋼板が使用されている。By the way, materials used for parts such as automobile side members and bumpers are required to have high strength and excellent bending workability. For this reason, conventionally, these parts have been NP114 and SPCC.
Etc. are used.
【０００４】しかし、近年、これらの部品に対しても軽
量化の要求が強く、自動車メーカーにおいては、これら
の部品にもアルミニウム押出材を使用することが検討さ
れている。この場合に、強度等の機械的特性、耐食性及
び加工性が比較的優れていることから、Ａｌ−Ｍｇ−Ｓ
ｉ系（６０００系）合金が注目されている。代表的なＡ
ｌ−Ｍｇ−Ｓｉ系合金としては、Ａ６０６３及びＡ６０
６１合金がある。Ａ６０６３合金は、押出性が優れてい
るため建築用サッシ等に使用されている。また、Ａ６０
６１合金は、中強度材であり、構造用組立材として使用
されている。更に、自動車用バンパー材として、Ａ７０
０３合金が使用されている。However, in recent years, there is a strong demand for reducing the weight of these parts as well, and automobile manufacturers are considering using aluminum extruded materials for these parts as well. In this case, Al-Mg-S is relatively excellent in mechanical properties such as strength, corrosion resistance and workability.
Attention is paid to i-based (6000 series) alloys. Representative A
As the 1-Mg-Si alloy, A6063 and A60
There is 61 alloy. A6063 alloy is used for building sashes and the like because of its excellent extrudability. Also, A60
61 alloy is a medium strength material and is used as a structural assembly material. Furthermore, as a bumper material for automobiles, A70
03 alloy is used.
【０００５】[0005]
【発明が解決しようとする課題】しかしながら、自動車
用サイドメンバー及びバンパーとして使用する場合に、
Ａ６０６３合金には強度が十分でないという欠点があ
り、Ａ６０６１合金には曲げ加工性が劣るという欠点が
ある。また、Ａ７００３合金には、応力腐食割れを生じ
る虞れがあるという問題点がある。However, when used as side members and bumpers for automobiles,
The A6063 alloy has a defect that the strength is not sufficient, and the A6061 alloy has a defect that the bending workability is poor. Further, the A7003 alloy has a problem that stress corrosion cracking may occur.
【０００６】本発明はかかる問題点に鑑みてなされたも
のであって、強度及び曲げ加工性が優れており、サイド
メンバー及びバンパー等の自動車用部品の材料として好
適の曲げ性が優れたＡｌ−Ｍｇ−Ｓｉ系合金押出材を提
供することを目的とする。The present invention has been made in view of the above problems and is excellent in strength and bending workability, and is excellent in bendability as a material for automobile parts such as side members and bumpers. An object is to provide an extruded material of Mg-Si alloy.
【０００７】[0007]
【課題を解決するための手段】本願の第１発明に係る曲
げ性が優れたＡｌ−Ｍｇ−Ｓｉ系合金押出材は、Ｍｇ2
Ｓｉ；０．７乃至１．４重量％、余剰Ｓｉ；０．２乃至
１．０重量％、Ｃｕ；０．１乃至１．０重量％及びＴ
ｉ；０．００１乃至０．０５重量％を含有し、残部がＡ
ｌ及び不可避的不純物からなり、Ｍｇ2Ｓｉ析出物の平
均長さが２０ｎｍ以下であり、更に直径１．０ｎｍ以上
のＭｇ2Ｓｉ析出物の密度が２０００個／μｍ2以上であ
ることを特徴とする。The extruded Al-Mg-Si alloy having excellent bendability according to the first invention of the present application is Mg 2
Si; 0.7 to 1.4% by weight, excess Si; 0.2 to 1.0% by weight, Cu; 0.1 to 1.0% by weight and T
i; 0.001 to 0.05% by weight, the balance A
1 and unavoidable impurities, the average length of Mg 2 Si precipitates is 20 nm or less, and the density of Mg 2 Si precipitates with a diameter of 1.0 nm or more is 2000 pieces / μm 2 or more. To do.
【０００８】この場合に、更にＭｎ；０．１乃至０．５
重量％、Ｃｒ；０．０５乃至０．２重量％及びＺｒ；
０．０５乃至０．２重量％からなる群から選択された少
なくとも１種の元素を含有してもよい。In this case, Mn: 0.1 to 0.5
Wt%, Cr; 0.05 to 0.2 wt% and Zr;
It may contain at least one element selected from the group consisting of 0.05 to 0.2% by weight.
【０００９】本願の第２発明に係る曲げ性が優れたＡｌ
−Ｍｇ−Ｓｉ系合金押出材は、Ｍｇ2Ｓｉ；０．７乃至
１．４重量％、余剰Ｓｉ；０．２乃至１．０重量％、Ｃ
ｕ；０．４乃至２．５重量％及びＴｉ；０．００１乃至
０．０５重量％を含有し、残部がＡｌ及び不可避的不純
物からなることを特徴とする。Al having excellent bendability according to the second invention of the present application
-Mg-Si alloy extruded material is Mg 2 Si; 0.7 to 1.4% by weight, excess Si; 0.2 to 1.0% by weight, C
u: 0.4 to 2.5% by weight and Ti: 0.001 to 0.05% by weight, with the balance being Al and inevitable impurities.
【００１０】この場合に、更にＭｎ；０．１乃至０．５
重量％、Ｃｒ；０．０５乃至０．２重量％及びＺｒ；
０．０５乃至０．２重量％からなる群から選択された少
なくとも１種の元素を添加し、断面積の５０％以上の部
分をファイバー組織としてもよい。In this case, Mn: 0.1 to 0.5
Wt%, Cr; 0.05 to 0.2 wt% and Zr;
At least one element selected from the group consisting of 0.05 to 0.2% by weight may be added, and 50% or more of the cross-sectional area may have a fiber structure.
【００１１】[0011]
【作用】次に、本発明に係るＡｌ−Ｍｇ−Ｓｉ系合金押
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。Next, the reason for adding the components and the reason for limiting the composition of the extruded Al-Mg-Si alloy according to the present invention will be described.
【００１２】Ｍｇ2Ｓｉ Ｍｇ2Ｓｉは溶体化処理後、時効処理を行うことによ
り、ＭｇとＳｉとの重量比Ｍｇ：Ｓｉが１．７３：１の
割合で析出する金属間化合物であり、この金属間化合物
の析出によりＡｌ合金の強度が向上するという効果があ
る。 Mg 2 Si Mg 2 Si is an intermetallic compound in which Mg: Si weight ratio Mg: Si is precipitated at a ratio of 1.73: 1 by performing solution treatment and then aging treatment. The precipitation of the intermetallic compound has the effect of improving the strength of the Al alloy.
【００１３】しかし、Ｍｇ2Ｓｉ含有量が０．７重量％
未満では強度が低く、１．４重量％を超えると溶体化処
理時に固溶が不十分となるため、その添加効果が飽和す
ると共に、Ａｌ合金の曲げ性を劣化させる。従って、Ｍ
ｇ2Ｓｉ含有量は０．７乃至１．４重量％とする。However, the Mg 2 Si content is 0.7% by weight.
If it is less than 1.4%, the strength is low, and if it exceeds 1.4% by weight, the solid solution becomes insufficient during the solution treatment, so that the addition effect is saturated and the bendability of the Al alloy is deteriorated. Therefore, M
The g 2 Si content is 0.7 to 1.4% by weight.
【００１４】余剰Ｓｉ 余剰Ｓｉは、添加されるＭｇとＳｉとの重量比（Ｍｇ／
Ｓｉ）が１．７３より小さいときに、このＭｇの重量の
１／１．７３より多い部分のＳｉが金属間化合物を形成
せずに残存したものである。この余剰ＳｉはＭｇ2Ｓｉ
析出物を微細分散させることにより、強度及び曲げ性を
向上させる作用がある。しかし、余剰Ｓｉの含有量が
０．２重量％未満では十分な強度向上効果が得られず、
１．０重量％を超えると曲げ性が劣化する。従って、余
剰Ｓｉ含有量は０．２乃至１．０重量％とする。 Excess Si Excess Si is the weight ratio of added Mg and Si (Mg /
When Si) is less than 1.73, a part of Si that is more than 1 / 1.73 of the weight of Mg remains without forming an intermetallic compound. This surplus Si is Mg 2 Si
Finely dispersing the precipitate has the effect of improving strength and bendability. However, if the content of excess Si is less than 0.2% by weight, a sufficient strength improving effect cannot be obtained,
If it exceeds 1.0% by weight, bendability deteriorates. Therefore, the excess Si content is 0.2 to 1.0% by weight.
【００１５】Ｔｉ ＴｉはＡｌ合金鋳塊中の結晶粒を微細化する効果があ
る。しかし、Ｔｉ含有量が０．００１重量％未満ではそ
の効果が十分でなく、０．０５重量％を超えるとその効
果は飽和する。従って、Ｔｉ含有量は０．００１乃至
０．０５重量％とする。 Ti Ti has the effect of refining the crystal grains in the Al alloy ingot. However, if the Ti content is less than 0.001% by weight, the effect is not sufficient, and if it exceeds 0.05% by weight, the effect is saturated. Therefore, the Ti content is 0.001 to 0.05% by weight.
【００１６】Ｃｕ ＣｕはＭｇ2Ｓｉ析出物を微細分散析出させることによ
り、強度及び曲げ性を向上させる作用がある。本願の第
１発明においては、Ｃｕ含有量を０．１乃至１．０重量
％とする。Ｃｕ含有量が０．１重量％未満では、Ｍｇ2
Ｓｉ析出物の微細分散化効果が不十分で強度が十分に向
上せず、１．０重量％を超えると強度は高くなるもの
の、Ａｌ合金の耐食性が低下する。このため、本願の第
１発明においては、Ｃｕ含有量は０．１乃至１．０重量
％とする。 Cu Cu has an action of improving strength and bendability by finely dispersing and depositing Mg 2 Si precipitates. In the first invention of the present application, the Cu content is 0.1 to 1.0% by weight. When the Cu content is less than 0.1% by weight, Mg 2
The effect of finely dispersing Si precipitates is insufficient and the strength is not sufficiently improved. When it exceeds 1.0% by weight, the strength increases but the corrosion resistance of the Al alloy decreases. Therefore, in the first invention of the present application, the Cu content is 0.1 to 1.0% by weight.
【００１７】また、本願の第２発明においては、Ｃｕ含
有量を０．４乃至２．５重量％とする。Ｃｕ含有量を
０．４重量％以上とすることにより、強度を確実に確保
することができる。また、Ｃｕ含有量が１重量％を超え
ると、耐食性は低下するものの、強度がより一層向上す
る。従って、強度が高いことが必要である場合は、Ｃｕ
を１重量％を超えて添加すればよい。但し、Ｃｕ含有量
が２．５重量％を超えると、従来自動車用バンパー材と
して使用されているＡ７００３合金よりも耐食性が低下
する。このため、本願の第２発明においては、Ｃｕ含有
量を０．４乃至２．５重量％とする。In the second invention of the present application, the Cu content is 0.4 to 2.5% by weight. By setting the Cu content to 0.4% by weight or more, the strength can be reliably ensured. Further, if the Cu content exceeds 1% by weight, the corrosion resistance is lowered, but the strength is further improved. Therefore, if high strength is required, Cu
May be added in an amount of more than 1% by weight. However, if the Cu content exceeds 2.5% by weight, the corrosion resistance is lower than that of the A7003 alloy that has been conventionally used as a bumper material for automobiles. Therefore, in the second invention of the present application, the Cu content is 0.4 to 2.5% by weight.
【００１８】Ｍｎ、Ｃｒ、Ｚｒ Ｍｎ、Ｃｒ及びＺｒはいずれも結晶粒を微細化しファイ
バー組織にすることにより、強度及び曲げ加工性を更に
向上させるという効果がある。これらの元素を添加し、
押出材の断面積の５０％以上の部分をファイバー組織に
することにより、押出材の強度及び曲げ加工性が著しく
向上する。しかし、Ｍｎ含有量が０．１重量％未満の場
合、Ｃｒ含有量が０．０５重量％未満の場合及びＺｒ含
有量が０．０５重量％未満の場合は、いずれもその添加
効果が十分でない。また、Ｍｎ含有量が０．５重量％を
超える場合、Ｃｒ含有量が０．２重量％を超える場合及
びＺｒ含有量が０．２重量％を超える場合は、いずれも
その効果が飽和するだけでなく、曲げ加工性が低下す
る。従って、Ｍｎ含有量は０．１乃至０．５重量％、Ｃ
ｒ含有量は０．０５乃至０．２重量％、Ｚｒ含有量は
０．０５乃至０．２重量％とする。 Mn, Cr, and Zr Mn, Cr, and Zr all have the effect of further improving strength and bending workability by refining the crystal grains into a fiber structure. Add these elements,
By forming a fiber structure in a portion of 50% or more of the cross-sectional area of the extruded material, the strength and bending workability of the extruded material are significantly improved. However, when the Mn content is less than 0.1% by weight, the Cr content is less than 0.05% by weight, and the Zr content is less than 0.05% by weight, the addition effect is not sufficient. . Further, when the Mn content exceeds 0.5% by weight, the Cr content exceeds 0.2% by weight, and the Zr content exceeds 0.2% by weight, the effect is saturated. In addition, bending workability is deteriorated. Therefore, the Mn content is 0.1 to 0.5% by weight, and C
The r content is 0.05 to 0.2% by weight, and the Zr content is 0.05 to 0.2% by weight.
【００１９】なお、上述のＭｎ、Ｃｒ及びＺｒは選択的
添加元素であり、必要に応じてこれらの元素のうちの１
種又は２種以上を添加すればよい。但し、Ｍｎ、Ｃｒ又
はＺｒを添加する場合は、Ｍｎ含有量は０．５重量％以
下、Ｃｒ及びＺｒ含有量はいずれも０．２重量％以下と
することが必要である。The above-mentioned Mn, Cr and Zr are selective addition elements, and if necessary, one of these elements may be added.
One kind or two or more kinds may be added. However, in the case of adding Mn, Cr or Zr, it is necessary that the Mn content is 0.5% by weight or less and the Cr and Zr contents are 0.2% by weight or less.
【００２０】次に、Ｍｇ2Ｓｉ析出物の平均長さ及び密
度の限定理由について説明する。本願の第１発明におい
ては、Ｍｇ2Ｓｉ析出物の平均長さを２０ｎｍ以下、直
径が１．０ｎｍ以上のＭｇ2Ｓｉ析出物密度を２０００
個／μｍ2以上とする。Ａｌ−Ｍｇ−Ｓｉ系押出材の強
度、延性及び曲げ性はＭｇ2Ｓｉ析出物の長さ及び密度
により大きな影響を受ける。Ｍｇ2Ｓｉ析出物の平均長
さを２０ｎｍ以下、直径１．０ｎｍ以上の析出物の密度
を２０００個／μｍ2以上とすることにより、Ａｌ合金
の強度、延性及び曲げ性を向上させることができる。Ｍ
ｇ2Ｓｉ析出物の平均長さが２０ｎｍを超えると、延性
及び曲げ性が著しく低下し、また直径１．０ｎｍ以上の
Ｍｇ2Ｓｉ析出物の密度が２０００個／μｍ2未満である
と強度が低下する。従って、Ｍｇ2Ｓｉ析出物の平均長
さは２０ｎｍ以下、直径１．０ｎｍ以上のＭｇ2Ｓｉ析
出物の密度は２０００個／μｍ2以上であることが必要
である。Next, the reasons for limiting the average length and density of the Mg 2 Si precipitates will be described. In the first invention of the present application, the average length of Mg 2 Si precipitates is 20 nm or less, and the density of Mg 2 Si precipitates having a diameter of 1.0 nm or more is 2000 nm.
No./μm 2 or more. Strength of Al-Mg-Si-based extrudate, ductility and bendability are greatly affected by the length and density of the Mg 2 Si precipitate. By setting the average length of the Mg 2 Si precipitates to 20 nm or less and the density of the precipitates having a diameter of 1.0 nm or more to 2000 pieces / μm 2 or more, the strength, ductility and bendability of the Al alloy can be improved. . M
If the average length of the g 2 Si precipitates exceeds 20 nm, the ductility and bendability are significantly reduced, and if the density of the Mg 2 Si precipitates with a diameter of 1.0 nm or more is less than 2000 pieces / μm 2 , the strength is increased. descend. Therefore, it is necessary that the average length of the Mg 2 Si precipitates is 20 nm or less and the density of the Mg 2 Si precipitates having a diameter of 1.0 nm or more is 2000 pieces / μm 2 or more.
【００２１】[0021]
【実施例】以下、本願の第１発明に係るＡｌ−Ｍｇ−Ｓ
ｉ系合金押出材について、本発明の特許請求の範囲から
外れる比較例と比較して具体的に説明する。EXAMPLES Al-Mg-S according to the first invention of the present application
The i-based alloy extruded material will be specifically described in comparison with a comparative example that is outside the scope of the claims of the present invention.
【００２２】先ず、下記表１に示す組成（重量％）のＡ
ｌ合金鋳塊（直径１５５ｍｍ）を通常の方法により溶製
した。なお、比較材１３は６０６１相当のＡｌ合金であ
る。また、Ｆｅは不可避的不純物である。First, A having the composition (% by weight) shown in Table 1 below.
1 alloy ingot (diameter 155 mm) was melted by a usual method. The comparative material 13 is an Al alloy corresponding to 6061. Further, Fe is an unavoidable impurity.
【００２３】[0023]
【表１】 [Table 1]
【００２４】次に、これらの鋳塊に対して、５４０℃の
温度で４時間均質化処理を施した。その後、押出温度が
５３０℃、押出速度が１０ｍ／分の条件で各鋳塊を押出
加工した後、ファン空冷により幅５４ｍｍ、高さ７０ｍ
ｍ、内厚が２ｍｍの中空押出材を得た。Next, these ingots were homogenized at a temperature of 540 ° C. for 4 hours. After that, each ingot was extruded under the conditions of an extrusion temperature of 530 ° C. and an extrusion speed of 10 m / min, and then 54 mm wide and 70 m high by air cooling with a fan.
A hollow extruded material having an inner diameter of m and an inner thickness of 2 mm was obtained.
【００２５】次に、得られた押出材を所定の長さに切断
した後、５５５℃の温度で１時間保持し、水中に焼入れ
る溶体化処理を行った。次に、これらを１７０℃の温度
で６時間の人工時効処理を施し、供試材とした。Next, the extruded material thus obtained was cut into a predetermined length and then held at a temperature of 555 ° C. for 1 hour to be subjected to solution treatment by quenching in water. Next, these were subjected to artificial aging treatment at a temperature of 170 ° C. for 6 hours to obtain test materials.
【００２６】これらの本実施例材及び比較例材の各供試
材を切断した後、透過型電子顕微鏡で（１００）面のＭ
ｇ2Ｓｉ析出物を観察し、〔１００〕及び〔０１０〕方
向のＭｇ2Ｓｉ析出物の平均長さ及び〔００１〕方向の
直径１．０ｎｍ以上のＭｇ2Ｓｉ析出物密度を測定し
た。その結果を下記表２に示す。また、図１は透過型電
子顕微鏡（ＴＥＭ）により撮影された写真を示す。After cutting each of the test materials of the present Example material and Comparative Example material, M of the (100) plane was observed with a transmission electron microscope.
The g 2 Si precipitates were observed, and the average length of the Mg 2 Si precipitates in the [100] and [010] directions and the density of the Mg 2 Si precipitates having a diameter of 1.0 nm or more in the [001] direction were measured. The results are shown in Table 2 below. Further, FIG. 1 shows a photograph taken by a transmission electron microscope (TEM).
【００２７】次に、これらの本実施例及び比較例の供試
材の引張強さ、耐力及び伸びをＪＩＳ１３号Ｂ試験片に
より測定した。その結果も合わせて表２に示す。次に、
本実施例及び比較例の各供試材について曲げ試験を行っ
た。図２は曲げ試験方法（ドローベンディング）を示す
模式図である。各供試材１０の内側に心金１を押入れ、
クランプ型２、圧力型３、ワイパー（しわ防止当金）４
及び曲げ型５により供試材１０を曲げた。そして、ベン
ダーの曲げ半径を一定として１８０度曲げ試験での割れ
状態を観察して、曲げ加工性を評価した。Next, the tensile strength, proof stress and elongation of the test materials of these Examples and Comparative Examples were measured with JIS No. 13B test pieces. The results are also shown in Table 2. next,
A bending test was performed on each of the test materials of the present example and the comparative example. FIG. 2 is a schematic diagram showing a bending test method (draw bending). Insert the core 1 inside each test material 10,
Clamp type 2, pressure type 3, wiper (wrinkle prevention metal) 4
The test material 10 was bent by the bending die 5. The bending workability was evaluated by observing the cracked state in a 180-degree bending test with the bending radius of the bender kept constant.
【００２８】[0028]
【表２】 [Table 2]
【００２９】その結果を表２に併せて示す。但し、割れ
が発生した場合を×、割れはないが肌あれが発生した場
合を△、割れ及び肌あれのいずれもない場合を○で示し
た。図１からわかるように、余剰Ｓｉを０．６重量％、
Ｃｕを０．５重量％含有する実施例合金No.２は余剰Ｓ
ｉを含有しない比較例合金No.１０及びＣｕを含有しな
い比較例合金No.１２と比較し、Ｍｇ2Ｓｉ析出物が微細
に高密度に析出している。The results are also shown in Table 2. However, the case where cracking occurred is indicated by x, the case where there is no cracking but skin roughness occurs is indicated by Δ, and the case where neither cracking nor skin roughness occurs is indicated by o. As can be seen from FIG. 1, 0.6% by weight of excess Si,
Example alloy No. 2 containing 0.5% by weight of Cu is a surplus of S
Compared with Comparative Example alloy No. 10 containing no i and Comparative Example alloy No. 12 containing no Cu, Mg 2 Si precipitates were finely and densely deposited.
【００３０】また、表２から明かなように、本実施例合
金No.１乃至７は、いずれもＭｇ2Ｓｉ析出物の平均長さ
が２０ｎｍ以下であり、且つ１μｍ2中に２０００個以
上のＭｇ2Ｓｉ析出物が高密度に分散析出しているた
め、強度が高く、延性も優れている。また、これらの合
金は曲げ性も良好である。Further, as is clear from Table 2, in all of the alloys of Examples 1 to 7 of the present invention, the average length of Mg 2 Si precipitates was 20 nm or less, and 2000 or more particles per 1 μm 2 were used. Since Mg 2 Si precipitates are dispersed and deposited at high density, the strength is high and the ductility is also excellent. Moreover, these alloys also have good bendability.
【００３１】一方、比較例合金No.８はＭｇ2Ｓｉ含有量
が０．７重量％未満であり、比較例合金No.１０は余剰
Ｓｉ含有量が０．２重量％未満であるため、Ｍｇ2Ｓｉ
析出物の密度が２０００個／μｍ2未満となり、強度が
低下している。On the other hand, the comparative alloy No. 8 has a Mg 2 Si content of less than 0.7% by weight, and the comparative alloy No. 10 has an excess Si content of less than 0.2% by weight. 2 Si
The density of precipitates is less than 2000 pieces / μm 2 , and the strength is lowered.
【００３２】また、比較例合金No.９はＭｇ2Ｓｉ含有量
が１．４重量％を超えているため、Ｍｇ2Ｓｉ析出物が
２０ｎｍを超えて粗大化し、曲げ性が低下している。Further, Comparative Example Alloy No. 9 has a Mg 2 Si content of more than 1.4% by weight, so that Mg 2 Si precipitates are coarsened to more than 20 nm and bendability is deteriorated.
【００３３】また、比較例合金No.１１は余剰Ｓｉ含有
量が１．０重量％を超えているため、延性の低下と共
に、曲げ性が低下している。Further, since the excess Si content of Comparative Example Alloy No. 11 exceeds 1.0% by weight, the ductility is lowered and the bendability is lowered.
【００３４】また、比較例合金No.１２はＣｕ含有量が
０．１重量％未満であるため、Ｍｇ2Ｓｉ析出物の長さ
が２０ｎｍを超え、曲げ性が低下している。Further, Comparative Example Alloy No. 12 has a Cu content of less than 0.1% by weight, so that the length of the Mg 2 Si precipitate exceeds 20 nm and the bendability is deteriorated.
【００３５】更に、比較例合金No.１３（６０６１相当
材）はＭｇ2Ｓｉ含有量が１．４重量％を超えており、
更に余剰Ｓｉ含有量が０．２重量％未満であるため、Ｍ
ｇ2Ｓｉ析出物の長さが２０ｎｍを超えて粗大化し、曲
げ性が低下している。Further, Comparative Example Alloy No. 13 (6061 equivalent material) has a Mg 2 Si content of more than 1.4% by weight,
Furthermore, since the excess Si content is less than 0.2% by weight, M
The length of the g 2 Si precipitate exceeds 20 nm and becomes coarse, and the bendability is deteriorated.
【００３６】次に、本願の第２発明に係るＡｌ−Ｍｇ−
Ｓｉ系合金押出材について、本発明の特許請求の範囲か
ら外れる比較例と比較して説明する。先ず、下記表３に
示す組成（重量％）のＡｌ合金鋳塊（直径１５５ｍｍ）
を通常の方法により溶製した。なお、Ｆｅは不可避的不
純物である。Next, Al-Mg- according to the second invention of the present application
The Si-based alloy extruded material will be described in comparison with a comparative example outside the scope of the claims of the present invention. First, an Al alloy ingot (diameter 155 mm) having the composition (% by weight) shown in Table 3 below.
Was melted by a usual method. Note that Fe is an unavoidable impurity.
【００３７】[0037]
【表３】 [Table 3]
【００３８】次に、これらの鋳塊に対して、５４０℃の
温度で４時間均質化処理を施した。その後、押出温度が
５３０℃、押出速度が１０ｍ／分の条件で各鋳塊を押出
加工した後、ファン冷却により幅が５４ｍｍ、高さが７
０ｍｍ、肉厚が２ｍｍの中空押出材を得た。Next, these ingots were homogenized at a temperature of 540 ° C. for 4 hours. After that, each ingot was extruded under the conditions of an extrusion temperature of 530 ° C. and an extrusion speed of 10 m / min, and the width was 54 mm and the height was 7 by cooling with a fan.
A hollow extruded material having a thickness of 0 mm and a thickness of 2 mm was obtained.
【００３９】次に、これらの押出材を所定の長さに切断
した後、５５５℃の温度で１時間保持し、水中に焼入れ
る溶体化処理を行った。次いで、これらの押出材を１７
０℃の温度で６時間の人工時効処理を施し、供試材とし
た。Next, these extruded materials were cut into a predetermined length, held at a temperature of 555 ° C. for 1 hour, and subjected to solution treatment by quenching in water. Then, these extruded materials are
An artificial aging treatment was performed at a temperature of 0 ° C. for 6 hours to obtain a test material.
【００４０】これらの本実施例材及び比較例材の各供試
材の結晶粒を光学式顕微鏡により観察した。図３は、実
施例合金No.１５，２１の結晶構造を示す写真である。
この図３からわかるように、Ｍｎ、Ｃｒ及びＺｒを添加
した実施例合金No.２１は断面における殆どの部分がフ
ァイバー組織となっているが、これらの元素が添加され
ていない実施例合金No.１５はファイバー組織にはなっ
ていない。The crystal grains of each of the test materials of the present Example material and Comparative Example material were observed with an optical microscope. FIG. 3 is a photograph showing the crystal structure of Example Alloys Nos. 15 and 21.
As can be seen from FIG. 3, Example alloy No. 21 to which Mn, Cr and Zr were added has a fiber structure in most of the cross section, but Example alloy No. 21 to which these elements are not added. No. 15 does not have a fiber structure.
【００４１】次に、これらの実施例材及び比較例材の供
試材の引張強さ、耐力及び伸びをＪＩＳ１３号Ｂ試験片
により測定した。その結果を、下記表４に示す。また、
本実施例及び比較例の各供試材について、図２に示す方
法により曲げ試験を行った。そして、ベンダーの曲げ半
径を一定にして、１８０度曲げでの割れ状態を観察し
て、曲げ加工性を評価した。その結果も、表４に併せて
示す。但し、割れが発生した場合を×、肌あれが発生し
た場合を△、割れ及び肌あれのいずれもない場合を○で
示した。更に、実施例及び比較例の各供試材に対し、塩
の濃度が５重量％の塩水を５００時間噴霧して耐食性を
調べる塩水噴霧試験を行った。その結果も、表４に併せ
て示した。但し、Ａ７００３合金に比して耐食性が優れ
ている場合を○、劣る場合を×で示した。Next, the tensile strength, yield strength and elongation of the test materials of these Example materials and Comparative Example materials were measured by JIS No. 13B test pieces. The results are shown in Table 4 below. Also,
A bending test was performed on each of the test materials of this example and the comparative example by the method shown in FIG. Then, the bend radius of the bender was kept constant, and the cracking state in 180 degree bending was observed to evaluate the bending workability. The results are also shown in Table 4. However, the case where cracking occurred is indicated by x, the case where skin roughness occurs is indicated by Δ, and the case where neither crack nor skin roughness occurs is indicated by o. Furthermore, a salt water spray test was carried out on each of the test materials of Examples and Comparative Examples to check the corrosion resistance by spraying salt water having a salt concentration of 5% by weight for 500 hours. The results are also shown in Table 4. However, when the corrosion resistance is superior to that of the A7003 alloy, it is indicated by ◯, and when it is inferior, it is indicated by x.
【００４２】[0042]
【表４】 [Table 4]
【００４３】表４から明らかなように、本実施例合金N
o.１４〜２０はいずれも強度が高く、曲げ性及び耐食性
が優れている。また、Ｍｎ、Ｃｒ及びＺｒを添加してフ
ァイバー組織とした本実施例合金No.２１，２２は、再
結晶組織時に比して強度が向上し、曲げ加工性も良好で
ある。As is clear from Table 4, this example alloy N
All of o.14 to 20 have high strength, and are excellent in bendability and corrosion resistance. Further, the alloy Nos. 21 and 22 of this example having a fiber structure by adding Mn, Cr and Zr have improved strength and good bending workability as compared with the recrystallized structure.
【００４４】一方、比較例合金No.２３はＭｇ2Ｓｉ含有
量が０．７重量％未満であり、比較例合金No.２５は余
剰Ｓｉ含有量が０．２重量％未満であるため、いずれも
強度が低下している。On the other hand, Comparative Example Alloy No. 23 has a Mg 2 Si content of less than 0.7% by weight, and Comparative Example Alloy No. 25 has an excess Si content of less than 0.2% by weight. Also the strength is decreasing.
【００４５】また、比較例合金No.２４はＭｇ2Ｓｉ含有
量が１．４重量％を超えており、比較例合金No.２６は
余剰Ｓｉ含有量が１．０重量％を超えているため、曲げ
性が低下している。Further, the comparative alloy No. 24 has a Mg 2 Si content of more than 1.4% by weight, and the comparative alloy No. 26 has a surplus of Si of more than 1.0% by weight. , Bendability is reduced.
【００４６】更に、比較例合金No.２７はＣｕ含有量が
０．４重量％未満であるため、曲げ加工性が低下してい
る。Further, the alloy No. 27 of the comparative example has a Cu content of less than 0.4% by weight, so that the bending workability is deteriorated.
【００４７】更にまた、比較例合金No.２８はＣｕ含有
量が２．５重量％を超えているため、耐食性が低下して
いる。Furthermore, the alloy No. 28 of the comparative example has a Cu content of more than 2.5% by weight, so that the corrosion resistance is lowered.
【００４８】更にまた、比較例合金No.２９〜３１は、
Ｍｎ、Ｃｒ及びＺｒが夫々０．５重量％、０．２重量％
及び０．２重量％を超えているため、曲げ加工性が低下
している。Furthermore, the comparative alloy Nos. 29 to 31 are
Mn, Cr and Zr are 0.5 wt% and 0.2 wt% respectively
And 0.2% by weight, bending workability is deteriorated.
【００４９】[0049]
【発明の効果】以上説明したように本発明に係るＡｌ−
Ｍｇ−Ｓｉ系合金押出材は、所定の組成を有し、Ｍｇ2
Ｓｉ析出物が微細に且つ均一に分散しているので、機械
的強度が高いと共に曲げ性が優れている。このため、本
発明に係るＡｌ−Ｍｇ−Ｓｉ系合金押出材は、自動車の
サイドメンバー及びバンパー等の部品に好適である。As described above, according to the present invention, the Al-
Mg-Si-based alloy extruded material has a predetermined composition, Mg 2
Since the Si precipitates are finely and uniformly dispersed, the mechanical strength is high and the bendability is excellent. Therefore, the Al—Mg—Si alloy extruded material according to the present invention is suitable for parts such as automobile side members and bumpers.
【図１】本実施例合金及び比較例合金の透過型電子顕微
鏡により観察した金属組織写真である。FIG. 1 is a photograph of a metallographic structure of an alloy of this example and an alloy of a comparative example observed by a transmission electron microscope.
【図２】曲げ試験方法（ドローベンディング）を示す模
式図である。FIG. 2 is a schematic diagram showing a bending test method (draw bending).
【図３】本実施例合金の光学顕微鏡により観察した金属
組織写真である。FIG. 3 is a metallographic photograph of the alloy of this example observed by an optical microscope.
１；心金 ２；クランプ型 ３；圧力型 ４；ワイパー ５；曲げ型 １０；供試材 1; Mandrel 2; Clamp type 3; Pressure type 4; Wiper 5; Bending type 10; Specimen
Claims (4)
余剰Ｓｉ；０．２乃至１．０重量％、Ｃｕ；０．１乃至
１．０重量％及びＴｉ；０．００１乃至０．０５重量％
を含有し、残部がＡｌ及び不可避的不純物からなり、Ｍ
ｇ2Ｓｉ析出物の平均長さが２０ｎｍ以下であり、更に
直径１．０ｎｍ以上のＭｇ2Ｓｉ析出物の密度が２００
０個／μｍ2以上であることを特徴とする曲げ性が優れ
たＡｌ−Ｍｇ−Ｓｉ系合金押出材。1. Mg 2 Si; 0.7 to 1.4% by weight,
Excess Si: 0.2 to 1.0% by weight, Cu: 0.1 to 1.0% by weight and Ti: 0.001 to 0.05% by weight
With the balance consisting of Al and unavoidable impurities, M
The average length of the g 2 Si precipitates is 20 nm or less, and the density of the Mg 2 Si precipitates having a diameter of 1.0 nm or more is 200 nm or less.
An Al-Mg-Si alloy extruded material having excellent bendability, which is characterized in that the number is 0 pieces / μm 2 or more.
余剰Ｓｉ；０．２乃至１．０重量％、Ｃｕ；０．１乃至
１．０重量％及びＴｉ；０．００１乃至０．０５重量％
を含有し、更にＭｎ；０．１乃至０．５重量％、Ｃｒ；
０．０５乃至０．２重量％及びＺｒ；０．０５乃至０．
２重量％からなる群から選択された少なくとも１種の元
素を含有し、残部がＡｌ及び不可避的不純物からなり、
Ｍｇ2Ｓｉ析出物の平均長さが２０ｎｍ以下であり、更
に直径１．０ｎｍ以上のＭｇ2Ｓｉ析出物の密度が２０
００個／μｍ2以上であることを特徴とする曲げ性が優
れたＡｌ−Ｍｇ−Ｓｉ系合金押出材。2. Mg 2 Si; 0.7 to 1.4% by weight,
Excess Si: 0.2 to 1.0% by weight, Cu: 0.1 to 1.0% by weight and Ti: 0.001 to 0.05% by weight
0.1% to 0.5% by weight, Cr;
0.05 to 0.2% by weight and Zr; 0.05 to 0.
Containing at least one element selected from the group consisting of 2% by weight, the balance being Al and inevitable impurities,
The average length of Mg 2 Si precipitates is 20 nm or less, and the density of Mg 2 Si precipitates having a diameter of 1.0 nm or more is 20 nm.
An Al-Mg-Si based alloy extruded material having excellent bendability, which is characterized in that the number is 00 / μm 2 or more.
余剰Ｓｉ；０．２乃至１．０重量％、Ｃｕ；０．４乃至
２．５重量％及びＴｉ；０．００１乃至０．０５重量％
を含有し、残部がＡｌ及び不可避的不純物からなること
を特徴とする曲げ性が優れたＡｌ−Ｍｇ−Ｓｉ系合金押
出材。3. Mg 2 Si; 0.7 to 1.4% by weight,
Excess Si: 0.2 to 1.0% by weight, Cu: 0.4 to 2.5% by weight and Ti: 0.001 to 0.05% by weight
An Al-Mg-Si alloy extruded material having excellent bendability, characterized in that the remainder is composed of Al and inevitable impurities.
余剰Ｓｉ；０．２乃至１．０重量％、Ｃｕ；０．４乃至
２．５重量％及びＴｉ；０．００１乃至０．０５重量％
を含有し、更にＭｎ；０．１乃至０．５重量％、Ｃｒ；
０．０５乃至０．２重量％及びＺｒ；０．０５乃至０．
２重量％からなる群から選択された少なくとも１種の元
素を含有し、残部がＡｌ及び不可避的不純物からなり、
断面積の５０％以上の部分がファイバー組織であること
を特徴とする曲げ性が優れたＡｌ−Ｍｇ−Ｓｉ系合金押
出材。4. Mg 2 Si; 0.7 to 1.4% by weight,
Excess Si: 0.2 to 1.0% by weight, Cu: 0.4 to 2.5% by weight and Ti: 0.001 to 0.05% by weight
0.1% to 0.5% by weight, Cr;
0.05 to 0.2% by weight and Zr; 0.05 to 0.
Containing at least one element selected from the group consisting of 2% by weight, the balance being Al and inevitable impurities,
An Al-Mg-Si based alloy extruded material having excellent bendability, characterized in that 50% or more of the cross-sectional area has a fiber structure.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11339894A JP2873165B2 (en) | 1993-04-30 | 1994-05-02 | Extruded Al-Mg-Si alloy with excellent bendability |
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5-128037 | 1993-04-30 | ||
| JP12803793 | 1993-04-30 | ||
| JP11339894A JP2873165B2 (en) | 1993-04-30 | 1994-05-02 | Extruded Al-Mg-Si alloy with excellent bendability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0711368A true JPH0711368A (en) | 1995-01-13 |
| JP2873165B2 JP2873165B2 (en) | 1999-03-24 |
Family
ID=26452387
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|---|---|---|---|
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| Country | Link |
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6419265A (en) * | 1987-07-10 | 1989-01-23 | Sanyo Electric Co | Generator |
| EP0997547A1 (en) * | 1998-10-27 | 2000-05-03 | Kabushiki Kaisha Kobe Seiko Sho | Al-Mg-Si based aluminum alloy extrusion |
| JP2002275567A (en) * | 2001-03-19 | 2002-09-25 | Asahi Tec Corp | Precipitation hardening type Al alloy and heat treatment method of precipitation hardening type alloy |
| JP2008019483A (en) * | 2006-07-13 | 2008-01-31 | Kobe Steel Ltd | Aluminum alloy sheet for warm-forming and warm-forming method |
-
1994
- 1994-05-02 JP JP11339894A patent/JP2873165B2/en not_active Expired - Lifetime
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6419265A (en) * | 1987-07-10 | 1989-01-23 | Sanyo Electric Co | Generator |
| EP0997547A1 (en) * | 1998-10-27 | 2000-05-03 | Kabushiki Kaisha Kobe Seiko Sho | Al-Mg-Si based aluminum alloy extrusion |
| JP2002275567A (en) * | 2001-03-19 | 2002-09-25 | Asahi Tec Corp | Precipitation hardening type Al alloy and heat treatment method of precipitation hardening type alloy |
| JP2008019483A (en) * | 2006-07-13 | 2008-01-31 | Kobe Steel Ltd | Aluminum alloy sheet for warm-forming and warm-forming method |
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| JP2873165B2 (en) | 1999-03-24 |
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