JPH09268342A - High strength aluminum alloy - Google Patents
High strength aluminum alloyInfo
- Publication number
- JPH09268342A JPH09268342A JP10457696A JP10457696A JPH09268342A JP H09268342 A JPH09268342 A JP H09268342A JP 10457696 A JP10457696 A JP 10457696A JP 10457696 A JP10457696 A JP 10457696A JP H09268342 A JPH09268342 A JP H09268342A
- Authority
- JP
- Japan
- Prior art keywords
- aluminum alloy
- toughness
- alloy
- stress corrosion
- corrosion cracking
- 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.)
- Granted
Links
Abstract
Description
【0001】[0001]
【発明の属する技術分野】本発明は構造用部材に用いら
れるアルミニウム合金に関するものである。TECHNICAL FIELD The present invention relates to an aluminum alloy used for structural members.
【0002】[0002]
【従来技術】車両用構造部材として、軽量化の要請の下
に押出加工したアルミニウム合金が使用されている。例
えば、自動車用バンパーリィンホースメントにはJIS
7003合金が、鉄道車両用にはJIS7075合金等
が使用されている。2. Description of the Related Art Extruded aluminum alloys are used as structural members for vehicles under the demand of weight reduction. For example, JIS for automobile bumper reinforcements
7003 alloy and JIS 7075 alloy are used for railway vehicles.
【0003】[0003]
【本発明が解決しようとする課題】しかし、JIS70
03合金では強度不充分であり、一方、JIS7075
合金では高強度は得られるが、靱性が極端に悪くなるば
かりでなく、バンパーリィンホースメント、サイドドア
ビームやサイドメンバー等の車両用部品の分野では耐応
力腐食割れ性や押出加工性が悪く、実用的ではないとい
う課題を抱えていた。これらの車両用部品の分野では、
車両の軽量化が燃費の向上に直接効果を与えるために、
より高強度のアルミ材料の使用による小型化が要求され
る一方で、乗員保護という安全性の観点からは、靱性に
優れたアルミ材料の使用による衝撃吸収性の向上が非常
に重要となってきている。従って、本発明は高強度であ
り、かつ、靱性、耐応力腐食割れ性および押出加工性に
も優れたアルミニウム合金およびその製造方法を提供せ
んとするものである。[Problems to be Solved by the Invention] However, JIS70
03 alloy has insufficient strength, while JIS 7075
Although high strength can be obtained with alloys, not only does toughness deteriorate extremely, but in the field of vehicle parts such as bumper reinforcements, side door beams, side members, etc. I had the problem that it was not the target. In the field of these vehicle parts,
In order for the weight reduction of the vehicle to directly affect the improvement of fuel economy,
While smaller size is required by using higher-strength aluminum material, improvement of shock absorption by using aluminum material with excellent toughness is very important from the viewpoint of safety for passenger protection. There is. Accordingly, the present invention is to provide an aluminum alloy having high strength and excellent in toughness, stress corrosion cracking resistance and extrusion processability, and a method for producing the same.
【0004】[0004]
【課題を解決するための手段】押出成形用アルミニウム
合金においては、Mg、Zn、Cuを添加することで高
強度合金が得られるが、それに反比例して押出加工性お
よび靱性が悪くなることは広く知られているところであ
る。しかし、本発明者はMg、Zn、Cuの成分に加え
て、Mn、Cr、Zr、Fe、Siの成分量を変えて種
々の合金を試作評価した結果、一定の組成範囲にては強
度500MPa(以下、特に示さない限り0.2%耐力
をいう)以上が得られ、かつ、靱性、耐応力腐食割れ性
および押出加工性に優れることが明らかになった。その
内容について以下に述べる。In an aluminum alloy for extrusion molding, a high strength alloy can be obtained by adding Mg, Zn and Cu, but it is widely inversely proportional to deterioration of extrusion processability and toughness. It is known. However, as a result of trial-evaluating various alloys by changing the amounts of components of Mn, Cr, Zr, Fe and Si in addition to the components of Mg, Zn and Cu, the present inventor has found that the strength is 500 MPa within a certain composition range. (Hereinafter, 0.2% proof stress unless otherwise specified) was obtained, and it was revealed that the toughness, stress corrosion cracking resistance and extrusion processability were excellent. The contents will be described below.
【0005】MgおよびZnは金属間化合物成形による
強度向上が期待できる高強度アルミニウム合金の添加主
成分である。Mgは強度向上に対する寄与は大きいが、
押出加工性を著しく害する要因となる。Znは押出加工
性を比較的に低下させずに強度向上に寄与するが、Mg
に対する添加比率を一定以上に高くすると、耐応力腐食
割れ性が著しく低下することになる。従って、後述する
他の添加成分との組み合わせにて、強度約500MPa
を維持しつつ、相反する靱性、耐応力腐食割れ性、押出
加工性に優れた特性を確保するのにZn:7.0〜9.
0wt%(以下、%と略す)、Mg:1.0〜2.0%
が最適である。Cuはアルミニウム合金において固溶硬
化が期待できるとともに、結晶粒界部と結晶粒内との電
位差緩和により、耐応力腐食割れ性を向上させることが
できる。一方、添加量が多すぎると、逆にCuとAlと
の電位差腐食の原因となる。従って、Cu:0.2〜
0.4%に選定した。Mn、Cr、Zrは、一定の範囲
については結晶粒を微細化する効果があり、押出加工性
を低下させることなく、靱性、耐応力腐食割れ性を向上
させることができる。その範囲は、種々試作評価した結
果、Mn:0.1〜0.5%、Cr:0.05〜0.3
%、Zr:0.1〜0.2%であった。FeおよびSi
は、通常、アルミニウムの精練、鋳造過程にて不純物と
して混入される成分であるが、Fe:0.15%以下、
Si:0.1%以下にしないと、いずれも靱性を低下さ
せることも明らかになった。Mg and Zn are added main components of a high-strength aluminum alloy, which can be expected to improve strength by forming an intermetallic compound. Although Mg makes a large contribution to the improvement of strength,
It becomes a factor that significantly impairs the extrusion processability. Zn contributes to the strength improvement without relatively lowering the extrudability, but Mg
If the addition ratio to is higher than a certain level, the stress corrosion cracking resistance is significantly reduced. Therefore, when combined with other additive components described later, the strength is about 500 MPa.
Zn: 7.0 to 9.% in order to secure the characteristics excellent in contradictory toughness, stress corrosion cracking resistance, and extrusion processability while maintaining the above-mentioned values.
0 wt% (hereinafter abbreviated as%), Mg: 1.0 to 2.0%
Is the best. Cu can be expected to undergo solid solution hardening in an aluminum alloy, and can also improve stress corrosion cracking resistance by relaxing the potential difference between the crystal grain boundary portion and the inside of crystal grains. On the other hand, if the addition amount is too large, it causes the potential difference corrosion between Cu and Al. Therefore, Cu: 0.2-
It was selected to be 0.4%. Mn, Cr, and Zr have an effect of refining crystal grains within a certain range, and can improve toughness and stress corrosion cracking resistance without lowering extrusion processability. As a result of various trial evaluations, Mn: 0.1 to 0.5%, Cr: 0.05 to 0.3
%, Zr: 0.1 to 0.2%. Fe and Si
Is a component that is usually mixed as an impurity in the process of refining and casting aluminum, but Fe: 0.15% or less,
It was also clarified that if the content of Si is not more than 0.1%, the toughness is reduced in each case.
【0006】以上の成分範囲にて調整されたアルミニウ
ム合金を用いて、常法されているビレット鋳造し、押出
加工後、所定の熱処理にても充分に高強度アルミニウム
押出形材が得られるが、本発明によるアルミニウム合金
の特性を最も発揮させるには、以下に述べる製造条件が
良い。本発明によるアルミニウム合金を用いて円柱状の
ビレットを鋳造し、その後、440〜480℃にて10
〜20時間均質化処理する。押出加工時のビレット加熱
温度は400〜450℃が良い。400℃以下では押出
加工性が悪く、450℃以上では再結晶が粗大化して耐
応力腐食割れ性が低下する。押出加工後に、そのまま人
工時効処理を実施しても、強度、靱性、耐応力腐食割れ
性、押出加工性に優れたアルミニウム押出形材が得られ
るが、さらに靱性および耐応力腐食割れ性を向上させる
には、押出形材を400〜470℃に再加熱して、その
後、1000℃/分以上の速度で冷却した後に80〜1
60℃にて10〜72時間焼き戻し処理するのが良い。
そのように製造した押出形材は、押出形材の断面にて繊
維状組織部分の面積比率が90%以上で靱性、耐応力腐
食割れ性に優れたアルミニウム押出形材が得られる。Using the aluminum alloy adjusted in the above range of components, it is possible to obtain a sufficiently high-strength aluminum extruded profile even by a conventional heat treatment after billet casting and extrusion processing. In order to maximize the characteristics of the aluminum alloy according to the present invention, the manufacturing conditions described below are good. A cylindrical billet was cast using the aluminum alloy according to the present invention, and then cast at 440 to 480 ° C. for 10 hours.
Homogenize for ~ 20 hours. The billet heating temperature during extrusion is preferably 400 to 450 ° C. Extrusion workability is poor at 400 ° C. or lower, and recrystallization becomes coarse at 450 ° C. or higher to reduce stress corrosion cracking resistance. Even if artificial aging treatment is carried out as it is after extrusion, an aluminum extruded profile excellent in strength, toughness, stress corrosion cracking resistance and extrusion processability can be obtained, but toughness and stress corrosion cracking resistance are further improved. The extruded profile is reheated to 400 to 470 ° C., then cooled at a rate of 1000 ° C./min or more, and then 80 to 1
It is preferable to perform tempering treatment at 60 ° C. for 10 to 72 hours.
The extruded profile produced in this manner can provide an aluminum extruded profile having an area ratio of the fibrous structure of 90% or more in the cross section of the extruded profile and having excellent toughness and stress corrosion cracking resistance.
【0007】[0007]
【発明の実施の形態】本発明におけるアルミニウム合金
例を従来と比較しながら説明する。表1に示す合金A、
Bが本発明による添加成分量の例を示し、比較合金C、
Dは本発明の効果を確認するためのものであり、比較合
金EはJIS7003に相当するアルミニウム合金であ
る。表2に示す押出形材は、図1に示す45mm×45
mm、肉厚2mmの断面形状の角パイプを押出加工した
材料の評価結果を示す。記号の意味は、例えば「A−
(1)」にて説明すると、Aは合金Aを使用したことを
示し、添字(1)は直径204mmの円柱ビレットを鋳
造し、460℃にて12時間均質化処理したビレットを
用いて、押出温度(ビレット加熱温度)440℃にて押
出加工した後に90℃×6時間+150℃×10時間の
人工時効処理したことを示し、添字(2)は押出加工ま
では(1)と同様であり、その後に押出形材を460℃
にて1時間加熱し、速やかに水冷して常温まで冷却した
後に90℃×6時間+150℃×24時間人工時効(焼
き戻し)処理したことを示す。BEST MODE FOR CARRYING OUT THE INVENTION An example of an aluminum alloy according to the present invention will be described in comparison with a conventional one. Alloy A shown in Table 1,
B shows an example of the amount of the additive component according to the present invention, and comparative alloy C,
D is for confirming the effect of the present invention, and comparative alloy E is an aluminum alloy corresponding to JIS7003. The extruded profile shown in Table 2 is 45 mm × 45 shown in FIG.
The evaluation results of a material obtained by extruding a square pipe having a sectional shape of mm and a thickness of 2 mm are shown. The meaning of the symbol is, for example, "A-
(1), A indicates that alloy A was used, and the subscript (1) is a cylindrical billet having a diameter of 204 mm cast and extruded using a billet homogenized at 460 ° C. for 12 hours. It shows that the artificial aging treatment of 90 ° C. × 6 hours + 150 ° C. × 10 hours was performed after extrusion processing at a temperature (billet heating temperature) of 440 ° C., and the subscript (2) was the same as (1) until extrusion processing. After that, extruded profile is 460 ℃
After being heated for 1 hour, rapidly cooled with water and cooled to room temperature, artificial aging (tempering) treatment is performed at 90 ° C. × 6 hours + 150 ° C. × 24 hours.
【0008】次に、材料特性の評価方法を説明する。引
張強度、0.2%耐力、伸びはJISZ2241に基づ
いて測定し、靱性は図2に示すように半円球形状のポン
チにて打ち抜き荷重を負荷し、その際の変位(S)−荷
重(F)曲線をとると、図3に示すグラフになる。
(a)は靱性が悪い場合に途中で材料割れが発生し、荷
重が急激に低下する例を示す。(b)は靱性の良い例で
あり、評価方法としては、(S)−(F)曲線にて得ら
れた積分値を測定し、JIS7003を用いたE−
(1)の値を100として指数評価した。耐応力腐食割
れ性はJISH8711に準じて評価したが、腐食促進
液はCrO3 、K2 Cr2 O7 、NaCl混合水溶液を
用い、液温90℃に浸漬し、割れ発生までの時間を測定
した。繊維状組織面積比率は、押出形材を鏡面研摩した
後にNaOH水溶液にてエッチング処理し、面積比率を
測定した。Next, a method for evaluating material properties will be described. Tensile strength, 0.2% proof stress, and elongation are measured based on JISZ2241, and toughness is punched with a hemispherical punch as shown in FIG. 2, and displacement (S) -load (load) at that time is applied. F) Taking the curve results in the graph shown in FIG.
(A) shows an example in which when the toughness is poor, material cracking occurs on the way and the load sharply decreases. (B) is an example of good toughness. As an evaluation method, the integrated value obtained from the (S)-(F) curve was measured and E-using JIS7003 was used.
The value of (1) was set to 100 and indexed. The resistance to stress corrosion cracking was evaluated according to JIS H8711, but the corrosion accelerator used was a mixed solution of CrO 3 , K 2 Cr 2 O 7 and NaCl, and the solution was immersed at 90 ° C. and the time until cracking was measured. . The fibrous structure area ratio was measured by subjecting the extruded shape member to mirror polishing and then etching with an aqueous NaOH solution to measure the area ratio.
【0009】[0009]
【発明の効果】表2にて示す結果から明らかなように、
本発明による合金A、Bを用いて押出加工し、所定の熱
処理をしたものは高強度でありながら、靱性、耐応力腐
食割れ性に優れた特性を示す。また、押出加工性におい
ても、図1の断面形状のものを3000tonプレスに
て直接押し出した場合に、合金A、Bは10〜12m/
分の押出スピードが得られるが、合金Cは1〜2m/分
であり、合金Dは4〜5m/分であった。As is clear from the results shown in Table 2,
The alloys A and B according to the present invention, which are extruded and subjected to a predetermined heat treatment, have high strength, yet exhibit excellent toughness and stress corrosion cracking resistance. Also in terms of extrusion processability, when the cross-sectional shape of FIG. 1 is directly extruded with a 3000 ton press, alloys A and B are 10 to 12 m /
Minute extrusion rates were obtained, with alloy C at 1-2 m / min and alloy D at 4-5 m / min.
【0010】 [0010]
【0011】 [0011]
【図1】本発明によるアルミニウム合金を用いた押出形
材の断面例を示す。FIG. 1 shows an example of a cross section of an extruded profile using an aluminum alloy according to the present invention.
【図2】靱性評価方法の模式図を示す。FIG. 2 shows a schematic diagram of a toughness evaluation method.
【図3】靱性評価における変位(S)−荷重(F)曲線
を示す。FIG. 3 shows a displacement (S) -load (F) curve in toughness evaluation.
1・・・・・・供試材 2、2´・・・供試材固定上治具 3・・・・・・供試材固定下治具 4・・・・・・供試材に荷重をかけるポンチ (a)・・・・靱性の悪い材料における変位−荷重曲線
例 (b)・・・・靱性の良い材料における変位−荷重曲線
例1 ・ ・ ・ ・ Specimen material 2, 2 '・ ・ ・ Upper jig for fixing specimen material 3 ・ ・ ・ ・ ・ ・ Jig for fixing specimen material 4 ・ ・ ・ ・ Load on specimen material Punch that applies force (a) ...- Example of displacement-load curve for materials with poor toughness (b) ...- Example of displacement-load curve for materials with good toughness
Claims (2)
1.5〜2.0wt%、Cu:0.2〜0.4wt%、
Mn:0.1〜0.5wt%、Cr:0.05〜0.3
wt%、Zr:0.1〜0.2wt%、Ti:0.01
〜0.05wt%を有し、残部がAlおよび不可避的不
純物からなり、不純物Fe:0.15wt%以下、不純
物Si:0.10wt%以下にしたことを特徴とするア
ルミニウム合金。1. Zn: 7.0 to 9.0 wt%, Mg:
1.5-2.0 wt%, Cu: 0.2-0.4 wt%,
Mn: 0.1-0.5 wt%, Cr: 0.05-0.3
wt%, Zr: 0.1 to 0.2 wt%, Ti: 0.01
An aluminum alloy having a content of ˜0.05 wt%, the balance being Al and unavoidable impurities, and Fe: 0.15 wt% or less and Si: 0.10 wt% or less.
し、1000℃/分以上の速度で50℃以下に冷却し、
その後に80〜160℃にて人工時効処理することによ
り、繊維状組織比率90%以上を有することを特徴とす
る、請求項1記載のアルミニウム合金。2. After extrusion, heating to 400 to 470 ° C., cooling to 50 ° C. or less at a rate of 1000 ° C./min or more,
The aluminum alloy according to claim 1, which has a fibrous structure ratio of 90% or more by performing artificial aging treatment at 80 to 160 ° C. thereafter.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP10457696A JP3735407B2 (en) | 1996-04-02 | 1996-04-02 | High strength aluminum alloy |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP10457696A JP3735407B2 (en) | 1996-04-02 | 1996-04-02 | High strength aluminum alloy |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH09268342A true JPH09268342A (en) | 1997-10-14 |
JP3735407B2 JP3735407B2 (en) | 2006-01-18 |
Family
ID=14384272
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP10457696A Expired - Lifetime JP3735407B2 (en) | 1996-04-02 | 1996-04-02 | High strength aluminum alloy |
Country Status (1)
Country | Link |
---|---|
JP (1) | JP3735407B2 (en) |
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JP2006505695A (en) * | 2002-11-06 | 2006-02-16 | ペシネイ レナリュ | Simplified manufacturing method of rolled product made of Al-Zn-Mg alloy, and product obtained by this method |
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-
1996
- 1996-04-02 JP JP10457696A patent/JP3735407B2/en not_active Expired - Lifetime
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US7780802B2 (en) | 2002-11-06 | 2010-08-24 | Alcan Rhenalu | Simplified method for making rolled Al—Zn—Mg alloy products, and resulting products |
JP2006505695A (en) * | 2002-11-06 | 2006-02-16 | ペシネイ レナリュ | Simplified manufacturing method of rolled product made of Al-Zn-Mg alloy, and product obtained by this method |
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CN111566240A (en) * | 2018-03-27 | 2020-08-21 | 古河电气工业株式会社 | Aluminum alloy material, and conductive member, battery member, fastening member, spring member, and structural member using same |
CN111566240B (en) * | 2018-03-27 | 2021-09-07 | 古河电气工业株式会社 | Aluminum alloy material, and conductive member, battery member, fastening member, spring member, and structural member using same |
WO2020195690A1 (en) | 2019-03-28 | 2020-10-01 | 株式会社神戸製鋼所 | Automotive door beam made of aluminum alloy extruded material |
KR20210129137A (en) | 2019-03-28 | 2021-10-27 | 가부시키가이샤 고베 세이코쇼 | Automobile door beams made of aluminum alloy extrusions |
CN113614265A (en) * | 2019-03-28 | 2021-11-05 | 株式会社神户制钢所 | Door impact beam for automobile formed by aluminum alloy extruded material |
EP3929320A4 (en) * | 2019-03-28 | 2022-05-11 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Automotive door beam made of aluminum alloy extruded material |
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