CN105385971A - Aging process for AI-Mg-Si based alloy after bent deformation - Google Patents
Aging process for AI-Mg-Si based alloy after bent deformation Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
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Abstract
The invention discloses an aging process for AI-Mg-Si based alloy after bent deformation, comprising the procedure of carrying out aging treatment on the AI-Mg-Si based alloy in conditions of 160 DEG C for 9 hours and 180 DEG C for 2 hours. The invention provides the aging process which can promote performance of the AI-Mg-Si based alloy after bent deformation, so as to meet the high performance requirement of products.
Description
Technical field
The invention belongs to alloy field, be specifically related to the aging technique after the alloy bending distortion of a kind of Al-Mg-Si system.
Background technology
Rapidly, aluminium alloy has moderate strength, quality is light, the features such as easy-formation, is applicable to automotive light weight technology design in automotive light weight technology development.
The natural aging of 6082 trade mark alloys is relatively strong, and hardness promotes very fast; Under T4 state, it is bending that alloy needs larger external force just can complete when bending, around the hard phase that this process is separated out in natural aging, produces the dislocation of greater density, form dislocation enrichment region.Al-Mg-Si system alloy aging strengthening principle is mainly α (Al base supersaturated solid solution) → GP district → β " → β ' → β, but the dislocation that bending produces affects the intensity after the follow-up timeliness of alloy.
At present, comprise for the existing standard of 6082 alloy designations: (1) GMW15665 standard: T6 performance, tension >=300Mpa, surrender >=270Mpa, unit elongation >=8%; (2) EN755 standard of performance: T6 performance, tension >=290Mpa, surrender >=250Mpa, unit elongation >=8%; (3) GB/T6892 standard of performance: T6 performance, tension >=310Mpa, surrender >=260Mpa, unit elongation >=10%.
But the requirement of vehicle beam performance is tending towards personalized, requires that the high-performance standard of 6082 trade mark alloys after bending is as follows further: T6 performance, tension >=320Mpa, surrender >=290Mpa, unit elongation >=8%.
Summary of the invention
The performance that alloy after present inventor's research demonstrates aging technique doubling bending deformation finally obtains plays decisive influence effect.The precipitation rate of aluminum alloy hard phase depends on the temperature of timeliness; Ag(e)ing process, while reply dislocation structure, the precipitation ratio reducing hard item is the key of this time invention, thus provides the aging technique of the rear improving performance of a kind of 6082 alloy bendings distortion, can meet its high performance requirements.
Specifically, as shown in Figure 1, wherein GP I district and the representative of GP II district are in ag(e)ing process, and the order that hard phase precipitation process experiences: the enrichment of hard phase atom forms unordered enrichment region, is called GP I district for intensity and hard phase precipitation state relation; Along with the prolongation of timeliness soaking time, the hard phase atom that these enrichments are got up, lines up in order gradually, forms enrichment region GP II district.As shown in Figure 1, intensity peak is at β, and " end and β ' are just.
Further, first the present invention adopts low temperature aging, replys the dislocation that bending distortion produces, avoids the precipitation that hard phase is a large amount of simultaneously; Then promote aging temp a little, be incubated, maximum capacity ground improves the performance of product.The present invention passes through change aging technique, makes strengthening phase based on β " and β ', reduce β phase, it is main for promoting strengthening phase and matrix to be mainly coherence state, promotes its performance.
Therefore, the object of the present invention is to provide the aging technique after the alloy bending distortion of a kind of Al-Mg-Si system.
For solving the problems of the technologies described above, the technical solution used in the present invention is as follows:
An aging technique after the alloy bending distortion of Al-Mg-Si system, comprises and carries out 160 DEG C ± 3 DEG C/9 hours ± 5 minutes+180 DEG C ± 3 DEG C/2 hours ± 5 minutes ageing treatment to described Al-Mg-Si system alloy.
Further, comprise 160 DEG C/9 hours+180 DEG C/2 hours ageing treatment are carried out to described Al-Mg-Si system alloy.
Further, described Al-Mg-Si system alloy is 6XXX aluminium alloy.
Further, described 6XXX aluminium alloy is 6082 aluminium alloys.
Beneficial effect: the aging technique that the invention provides the rear improving performance of a kind of Al-Mg-Si system alloy bending distortion, can meet the high performance requirements of product.
Accompanying drawing explanation
Fig. 1 is intensity and hard phase precipitation state graph of a relation, and wherein, X-coordinate represents timeliness soaking time, and ordinate zou represents intensity.
Embodiment
Below in conjunction with specific embodiment, the present invention will be further described.Should be understood that following examples only for illustration of the present invention but not for limiting the scope of the invention.
Embodiment 1,
Testing installation: aluminium extruding machine-2200T, finished product sawing machine, pressing and bending machine, timeliness electric furnace, band saw, horizontal milling machine, 20T universal testing machine.
Testing sequence:
1) 6082 alloys are by 2200T extrusion machine, are squeezed into safety lever cross beam sectional bar;
2) length-specific is become by the sawing of finished product sawing machine;
3) on pressing and bending machine, bending and molding is carried out;
4) same timeliness electric furnace is used to carry out former technique (A) the timeliness test condition different with the present invention (B-J) respectively;
5) use band saw and horizontal milling machine, respectively product after timeliness is carried out to the making of tension specimen, in order to Performance Detection; According to GB/T16865 standard, often organize sample preparation 3-10 sheet;
6) use 20T universal testing machine to carry out Performance Detection, measuring method performs GB/T228 standard.
Test-results is as follows:
Illustrate: according to standard of performance (after bending): T6 performance, tension >=320Mpa, surrender >=290Mpa, unit elongation >=8%.
A, 180 DEG C/6 hours (former technique):
| Tension Mpa | Surrender Mpa | Unit elongation % |
| 321.79 | 283.59 | 10.30 |
| 329.79 | 311.11 | 14.07 |
| 327.02 | 311.00 | 14.60 |
| 306.92 | 276.23 | 16.98 |
| 296.94 | 269.57 | 17.63 |
| 319.58 | 303.32 | 16.98 |
| 324.92 | 306.09 | 12.07 |
| 321.79 | 293.59 | 10.30 |
| 301.00 | 270.87 | 15.30 |
| 309.22 | 281.02 | 17.05 |
B, 180 DEG C/7 hours:
| Tension Mpa | Surrender Mpa | Unit elongation % |
| 311.72 | 279.63 | 17.22 |
| 316.83 | 281.57 | 16.85 |
| 320.09 | 291.77 | 13.08 |
C, 180 DEG C/8 hours:
| Tension Mpa | Surrender Mpa | Unit elongation % |
| 307.63 | 281.77 | 14.18 |
| 309.22 | 290.11 | 13.96 |
| 310.57 | 289.63 | 14.23 |
D, 160 DEG C/6 hours+180 DEG C/2 hours:
| Tension Mpa | Surrender Mpa | Unit elongation % |
| 309.22 | 281.02 | 17.05 |
| 306.99 | 279.31 | 16.92 |
| 311.66 | 287.28 | 15.87 |
E, 160 DEG C/7 hours+180 DEG C/2 hours:
| Tension Mpa | Surrender Mpa | Unit elongation % |
| 306.92 | 276.23 | 16.98 |
| 311.22 | 283.96 | 15.28 |
| 309.93 | 281.36 | 16.03 |
F:160 DEG C/8 hours+180 DEG C/2 hours:
G:160 DEG C/9 hours:
| Tension Mpa | Surrender Mpa | Unit elongation % |
| 316.44 | 300.54 | 13.95 |
| 318.00 | 301.88 | 15.25 |
| 315.58 | 298.36 | 15.98 |
H:160 DEG C/10 hours:
| Tension Mpa | Surrender Mpa | Unit elongation % |
| 324.92 | 306.09 | 12.07 |
| 319.89 | 300.11 | 14.03 |
| 321.07 | 296.33 | 15.69 |
I:160 DEG C/11 hours:
| Tension Mpa | Surrender Mpa | Unit elongation % |
| 322.36 | 291.67 | 16.78 |
| 319.88 | 279.68 | 17.21 |
| 326.88 | 299.63 | 15.30 |
J, 160 DEG C/9 hours+180 DEG C/2 hours:
As can be known from the above table, the present invention finds that on a large amount of experiment basis preferred Ageing conditions is 160 DEG C/9 hours+180 DEG C/2 hours, product can realize 100% performance qualified.After present invention process improves, product can meet the high performance requirements special to bumper beam, and crossbeam product can meet the requirement of follow-up car load test.
Claims (4)
1. the aging technique after Al-Mg-Si system alloy bending distortion, is characterized in that, comprise and carry out 160 DEG C ± 3 DEG C/9 hours ± 5 minutes+180 DEG C ± 3 DEG C/2 hours ± 5 minutes ageing treatment to described Al-Mg-Si system alloy.
2. aging technique as claimed in claim 1, is characterized in that, comprise and carry out 160 DEG C/9 hours+180 DEG C/2 hours ageing treatment to described Al-Mg-Si system alloy.
3. aging technique as claimed in claim 1, it is characterized in that, described Al-Mg-Si system alloy is 6XXX aluminium alloy.
4. aging technique as claimed in claim 3, it is characterized in that, described 6XXX aluminium alloy is 6082 aluminium alloys.
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109594027A (en) * | 2019-01-02 | 2019-04-09 | 上海友升铝业有限公司 | A kind of ageing hot processing method improving 6 line aluminium alloy intensity |
| CN112058985A (en) * | 2020-07-28 | 2020-12-11 | 深圳新顿科技有限公司 | Light alloy plate stamping heat treatment process and stamping device |
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| US6350329B1 (en) * | 1998-06-15 | 2002-02-26 | Lillianne P. Troeger | Method of producing superplastic alloys and superplastic alloys produced by the method |
| CN1138868C (en) * | 1999-02-12 | 2004-02-18 | 挪威海德罗公开有限公司 | Aluminium alloy contg. magnesium and silicon |
| CN101798649A (en) * | 2010-03-29 | 2010-08-11 | 江苏大学 | Compound 6013-type aluminum alloy microalloyed by zirconium and strontium and preparation method thereof |
| CN102168213A (en) * | 2011-04-15 | 2011-08-31 | 浙江乐祥铝业有限公司 | High-formability and high-strength aluminum alloy material as well as preparation method and application of the high-formability and high-strength aluminum alloy material |
| CN103225049A (en) * | 2013-04-23 | 2013-07-31 | 天津锐新昌轻合金股份有限公司 | Treatment process for improving electric conductivity of medium strength aluminium alloy |
| JP2014218685A (en) * | 2013-05-01 | 2014-11-20 | 本田技研工業株式会社 | Al-Mg-Si BASED ALLOY MEMBER AND METHOD FOR PRODUCING THE SAME |
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- 2015-12-17 CN CN201510953529.XA patent/CN105385971B/en active Active
Patent Citations (7)
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| US6350329B1 (en) * | 1998-06-15 | 2002-02-26 | Lillianne P. Troeger | Method of producing superplastic alloys and superplastic alloys produced by the method |
| CN1138868C (en) * | 1999-02-12 | 2004-02-18 | 挪威海德罗公开有限公司 | Aluminium alloy contg. magnesium and silicon |
| CN101798649A (en) * | 2010-03-29 | 2010-08-11 | 江苏大学 | Compound 6013-type aluminum alloy microalloyed by zirconium and strontium and preparation method thereof |
| CN102168213A (en) * | 2011-04-15 | 2011-08-31 | 浙江乐祥铝业有限公司 | High-formability and high-strength aluminum alloy material as well as preparation method and application of the high-formability and high-strength aluminum alloy material |
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| CN105018804A (en) * | 2014-04-24 | 2015-11-04 | 贵州理工学院 | Al-Mg-Si as-cast aluminum alloy and aging treatment process thereof |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109594027A (en) * | 2019-01-02 | 2019-04-09 | 上海友升铝业有限公司 | A kind of ageing hot processing method improving 6 line aluminium alloy intensity |
| CN112058985A (en) * | 2020-07-28 | 2020-12-11 | 深圳新顿科技有限公司 | Light alloy plate stamping heat treatment process and stamping device |
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Address after: 201702, Shanghai Qingpu District, Shanghai Qing Ping highway 2058 Patentee after: Shanghai Yousheng Aluminum Co., Ltd Address before: 201702, Shanghai Qingpu District, Shanghai Qing Ping highway 2058 Patentee before: SHANGHAI UNISON ALUMINUM PRODUCTS Co.,Ltd. |
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