JPS60125346A - High strength aluminum alloy having superior workability - Google Patents
High strength aluminum alloy having superior workabilityInfo
- Publication number
- JPS60125346A JPS60125346A JP23389383A JP23389383A JPS60125346A JP S60125346 A JPS60125346 A JP S60125346A JP 23389383 A JP23389383 A JP 23389383A JP 23389383 A JP23389383 A JP 23389383A JP S60125346 A JPS60125346 A JP S60125346A
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- aluminum alloy
- grain size
- high strength
- 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.)
- Pending
Links
Abstract
Description
【発明の詳細な説明】
* Ia lll! 1+祷罫チ石T畿t−Whす争宜
自フルζニウム合金に関し、さらに詳しくは、優れた機
械的性質と成形性を有し、かつ、ストレッチャストレイ
ンの発生しない成形加工性に優れた高力アルミニウム合
金に関する。[Detailed Description of the Invention] * Ia llll! Regarding the 1+ Stretch Stone T-Wh Stretched Full ζNium alloy, more specifically, it is a high-quality alloy that has excellent mechanical properties and formability, and has excellent formability without stretcher strain. Power related to aluminum alloy.
従来、例えば、自動車用アルミニウム合金として、AA
5182合金が広く使用されているが、この合金は成形
性は優れているものの、強度が低く、さらに、ストレッ
チャストレインが発生し易く、構造部材および表面品質
が問題となるところには使えなかった。Conventionally, for example, AA was used as an aluminum alloy for automobiles.
5182 alloy is widely used, but although this alloy has excellent formability, it has low strength and is prone to stretcher strain, making it unsuitable for use in structural members and where surface quality is a problem.
また、5085合金や2036合金等も使用されてはい
るが、強度については自動車用アルミニウム合金として
は良好であるが、成形性が悪いという問題があった・
本発明は上記に説明したような従来において使用されて
いた、例えば、自動車用のアルミニウム合金の問題点に
鑑みなされたものであり、強度が35 Kg/men2
以上を有し、かつ、成形性に優れ、さらに、ストレッチ
ャストレインの発生がない成形加工性に優れた高力アル
ミニウム合金を提供するものである。In addition, 5085 alloy and 2036 alloy have been used, but although they have good strength as aluminum alloys for automobiles, they have the problem of poor formability. It was created in view of the problems with aluminum alloys used in automobiles, for example, and has a strength of 35 kg/men2.
It is an object of the present invention to provide a high-strength aluminum alloy which has the above properties, has excellent formability, and also has excellent formability without the occurrence of stretcher strain.
本発明に係る成形加工性に優れた高力アルミニウム合金
は、(1)Mg 6.(1−10,Ou+t%、Zn
O,5−2,5wt%、Cu O,05−0,30wt
%を含有し、残部実質的にA1よりなり、平均結晶粒径
が10u以上であることを特徴とする成形加工性に優れ
た高力アルミニウム合金を第1の発明とし、(2)Mg
6.0−10.0wt%、Zn 0.5−2.5+ll
t%、Cu O,05−0、30wt%を含有し、さら
に、Cr 0.05−0.25wt%、Zr O,05
−0,20+ut%、Mn 0.05−0,50wt%
、Vo、05〜0.20wt%のうちから選んだ1種ま
たは2種以上を含有し、残部実質的にA1よりなり、平
均結晶粒径が10u以上であることを特徴とする成形加
工性に優れた高力アルミニウム合金を第2の発明とする
2つの発明よりなるものである。The high-strength aluminum alloy with excellent formability according to the present invention includes (1) Mg6. (1-10, Ou+t%, Zn
O,5-2,5wt%, CuO,05-0,30wt
%, the remainder substantially consists of A1, and the average crystal grain size is 10u or more.
6.0-10.0wt%, Zn 0.5-2.5+ll
t%, Cu O,05-0, 30 wt%, and further contains Cr 0.05-0.25 wt%, Zr O,05
-0,20+ut%, Mn 0.05-0,50wt%
, Vo, and one or more selected from 05 to 0.20 wt%, the remainder substantially consists of A1, and the average crystal grain size is 10 u or more. This invention consists of two inventions, with the second invention being an excellent high-strength aluminum alloy.
本発明に係る成形加工性に優れた高力アルミニウム合金
について以下詳細に説明する。The high-strength aluminum alloy with excellent formability according to the present invention will be described in detail below.
先ず、本発明に係る成形加工性に優れた高力アルミニウ
ム合金の含有成分および成分割合について説明する。First, the components and component ratios of the high-strength aluminum alloy with excellent formability according to the present invention will be explained.
M、は強度と延性を高めるのに有効な元素であり、含有
量が6.0…し%未満では充分な強度が得られず、また
、10. Quit%を越えて含有されると熱間圧延に
際して割れが生じ易くなる。よって、Mg含有量は6.
0〜10.0wt%とする。M is an effective element for increasing strength and ductility, and if the content is less than 6.0%, sufficient strength cannot be obtained; If the content exceeds Quit%, cracks are likely to occur during hot rolling. Therefore, the Mg content is 6.
0 to 10.0 wt%.
Znは成形性を高めると共にストレッチャストレインを
防止する元素であり、含有量が0.5wL%未満ではこ
の効果は少なく、また、2.5@t%を越えて含有され
ると成形性を低下させる。よって、Zn含有量は、0.
5〜2,5u+t%とする。Zn is an element that improves formability and prevents stretcher strain. If the content is less than 0.5wL%, this effect is small, and if the content exceeds 2.5@t%, the formability is reduced. . Therefore, the Zn content is 0.
5 to 2.5u+t%.
Cuは強度を高くする元素であり、0.05iut%未
満ではこの効果は少なく、また、0,30wt%を越え
る含有量では成形性を阻害する。よって、Cu含有量は
0.05−0.30WL%とする。Cu is an element that increases strength, and if the content is less than 0.05 iut%, this effect will be small, and if the content exceeds 0.30 wt%, the formability will be inhibited. Therefore, the Cu content is set to 0.05-0.30WL%.
Cr、Zr、Mn、Vは強度を付与する元素であり、含
有量が夫々0.05wt%未満ではこの効果は少なく、
また、Cr O,25wt%、ZrおよびV O,20
u+t%、Mn 0050u+t%を越える含有量では
成形性を阻害する。よって、Cr含有量0.05〜0.
25wt%、Zr含有量0.05−0.20wt%、M
n含有量0.05−0.50u、t%、■含有量0.0
5−0.20+ut%とする。Cr, Zr, Mn, and V are elements that impart strength, and if their content is less than 0.05 wt%, this effect is small;
In addition, CrO, 25wt%, Zr and VO, 20
If the content exceeds u+t% and Mn 0050u+t%, moldability will be inhibited. Therefore, the Cr content is 0.05 to 0.
25wt%, Zr content 0.05-0.20wt%, M
n content 0.05-0.50u, t%, ■ content 0.0
5-0.20+ut%.
結晶粒度10μ未満ではストレッチャストレインが発生
し、また、あまり結晶粒度が粗大になると成形加工時に
肌荒れを生じるので、20μ以下とするのが適当である
。If the crystal grain size is less than 10 μm, stretcher strain will occur, and if the crystal grain size becomes too coarse, surface roughness will occur during molding, so it is appropriate to set it to 20 μm or less.
また、上記含有成分以外に、鋳塊の結晶粒を微細化する
なめにTi、Nb5BをO,1wt%以下、Mgの酸化
を防止するためBeを0,05u+t%以下含有させる
こともでき、性能上も問題はない。In addition to the above-mentioned components, Ti and Nb5B can be contained in O.1wt% or less to refine the crystal grains of the ingot, and Be can be contained in 0.05u+t% or less to prevent Mg oxidation. There is no problem with the top.
不純物としては、通常工業的に含有される程度であれば
問題はなく、Fe O,5u+t%以下およびS10.
3u+t%以下であれば許容される。There is no problem with impurities as long as they are normally contained in industrial quantities, such as FeO, 5u+t% or less, and S10.
It is permissible if it is 3u+t% or less.
本内に係る成形加工性に優れた高力アルミニウム合金の
実施例を説明し、併せて比較例を説明する。Examples of high-strength aluminum alloys with excellent formability will be described in this book, and comparative examples will also be described.
実施例1
第1表に示す含有成分および成分割合になるように常法
に従って溶製し、鋳造後3.5mm tまで熱間圧延を
行なってか呟さらに、冷間圧延を行なって1.軸−の板
とした。これを500℃の温度で10secの連続焼鈍
を行ってから試験に使用した(連続焼鈍は530〜45
0℃の温度で15sec以下行なうのが望ましい。Example 1 Melting was carried out according to a conventional method so that the ingredients and proportions shown in Table 1 were obtained, and after casting, hot rolling was performed to a thickness of 3.5 mm, followed by cold rolling. It was made into a shaft plate. This was used for the test after being continuously annealed at a temperature of 500°C for 10 seconds (continuous annealing was performed at a temperature of 530 to 45
It is desirable to carry out the process at a temperature of 0° C. for 15 seconds or less.
成形性は応力勾配下における成形性の特性を示す切欠き
伸びにより評価した。Formability was evaluated by notch elongation, which indicates the characteristics of formability under a stress gradient.
その結果を第1表に示すが、本発明に係る成形加工性に
優れた高力アルミニウム合金(第1表では本発明合金)
は強度が高くストレッチャストレインの発生はない。し
カル、比較例ではストレッチャストレインが発生してい
る。The results are shown in Table 1, and the high-strength aluminum alloy according to the present invention with excellent formability (in Table 1, the present invention alloy)
has high strength and does not cause stretcher strain. However, stretcher strain occurs in the comparative example.
実施例2
Mg 8u+t%、Zn 1.2wt%、Cu O,2
u+t%を含有する本発明に係る成形性に優れた高力ア
ルミニウム合金を、410〜530℃の温度で連続焼鈍
を行ない、この時焼鈍温度を変えることにより平均結晶
粒径を変化させて、ストレッチャストレインの有無を調
査した。Example 2 Mg 8u+t%, Zn 1.2wt%, CuO,2
The high-strength aluminum alloy of the present invention containing u+t% and having excellent formability is continuously annealed at a temperature of 410 to 530°C, and the average grain size is changed by changing the annealing temperature. The presence or absence of strain was investigated.
その結果を第2表に示す。この表から平均結晶粒径が1
5μ以上ではストレッチャストレインが発生しないこと
がわかる。The results are shown in Table 2. From this table, the average grain size is 1
It can be seen that stretcher strain does not occur when the thickness is 5μ or more.
第2表
即ち、結晶粒径を10μ以上とするためには、450〜
530℃の高温において短時間の焼鈍を行なうのがよく
、バッチ式では加熱が長時間となり粒径が粗大となり易
いため連続焼鈍を行なうことが好ましいのである。Table 2 shows that in order to make the crystal grain size 10μ or more, 450~
It is preferable to perform short-time annealing at a high temperature of 530° C., and continuous annealing is preferable since batch type heating requires a long time and the grain size tends to become coarse.
以上説明したように、本発明に係る成形加工性に優れた
高力アルミニウム合金は上記の構成を有しているもので
あるから、高い強度および優れた成形性を有し、かつ、
ストレッチャストレインの発生のない自動車用材料とし
て極めて優れた効果を有する。As explained above, the high-strength aluminum alloy with excellent formability according to the present invention has the above structure, so it has high strength and excellent formability, and
It has extremely excellent effects as an automobile material that does not generate stretcher strain.
Claims (2)
−2,5wL%、Cu O,05−0,30wt% を含有し、残部実質的にA1よりなり、平均結晶粒径が
10μ以上であることをW徴とする成形加工性に優れた
高力アルミニウム合金。(1) Mg6.0-10. O@t%, Zn O,5
-2.5 wL%, CuO, 0.5-0.30 wt%, the remainder is substantially A1, and the average crystal grain size is 10 μ or more. Aluminum alloy.
−2.5wt%、Cu O,05−0,30wt% を含有し、さらに、 Cr O,05−0,25@t%、Zr 0.05−0
.20wt%、Mn O,05−0,5Qwt%、V
O,05−Q、20wt%、のうちから選んだ1種また
は2種以上を含有し、残部実質的にA1よりなり、平均
結晶粒径が10μ以上であることを特徴とする成形加工
性に優れた高力アルミニウム合金。(2) Mg 6.0-10.0w1%, Zn 005
-2.5wt%, CuO,05-0,30wt%, and further contains CrO,05-0,25@t%, Zr 0.05-0
.. 20wt%, MnO, 05-0,5Qwt%, V
Containing one or more selected from O, 05-Q, 20 wt%, the remainder being substantially A1, and having an average crystal grain size of 10 μ or more. Superior high strength aluminum alloy.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP23389383A JPS60125346A (en) | 1983-12-12 | 1983-12-12 | High strength aluminum alloy having superior workability |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP23389383A JPS60125346A (en) | 1983-12-12 | 1983-12-12 | High strength aluminum alloy having superior workability |
Publications (1)
Publication Number | Publication Date |
---|---|
JPS60125346A true JPS60125346A (en) | 1985-07-04 |
Family
ID=16962213
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP23389383A Pending JPS60125346A (en) | 1983-12-12 | 1983-12-12 | High strength aluminum alloy having superior workability |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS60125346A (en) |
Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5669345A (en) * | 1979-11-01 | 1981-06-10 | Kobe Steel Ltd | High-toughness high-strength al alloy cast product |
JPS56169745A (en) * | 1980-05-31 | 1981-12-26 | Kobe Steel Ltd | A -mg base alloy |
JPS5861246A (en) * | 1981-10-06 | 1983-04-12 | Mitsuo Sohgoh Kenkyusho Kk | Aluminum alloy |
JPS6050139A (en) * | 1983-08-27 | 1985-03-19 | Kobe Steel Ltd | Aluminum alloy having superior screw characteristic |
-
1983
- 1983-12-12 JP JP23389383A patent/JPS60125346A/en active Pending
Patent Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5669345A (en) * | 1979-11-01 | 1981-06-10 | Kobe Steel Ltd | High-toughness high-strength al alloy cast product |
JPS56169745A (en) * | 1980-05-31 | 1981-12-26 | Kobe Steel Ltd | A -mg base alloy |
JPS5861246A (en) * | 1981-10-06 | 1983-04-12 | Mitsuo Sohgoh Kenkyusho Kk | Aluminum alloy |
JPS6050139A (en) * | 1983-08-27 | 1985-03-19 | Kobe Steel Ltd | Aluminum alloy having superior screw characteristic |
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