CN103725937A - High-performance aluminum alloy for automobile parts - Google Patents
High-performance aluminum alloy for automobile parts Download PDFInfo
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- CN103725937A CN103725937A CN201310612698.8A CN201310612698A CN103725937A CN 103725937 A CN103725937 A CN 103725937A CN 201310612698 A CN201310612698 A CN 201310612698A CN 103725937 A CN103725937 A CN 103725937A
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Abstract
The invention provides a high-performance aluminum alloy for automobile parts. The high-performance aluminum alloy is characterized by comprising the components in percentage by weight (wt.%) as follows: 4.0-4.5wt.% of Mg, 0.6-0.8wt.% of Si, 0.6-1.0wt.% of Cu, 0.05-0.1wt.% of Mn, 0.05-0.1wt.% of Cr, 0.05-0.1wt.% of Zr, 0.05-0.1wt.% of Zn, 0.1-0.2wt.% of Sn, and 0.01-0.05wt.% of Sr. The high-performance aluminum alloy for the automobile parts has an excellent forming property and can meet requirements of baking finish heat treatment hardening and surface attractiveness.
Description
Technical field
The present invention relates to the technical field of trolley part, a kind of trolley part high-performance aluminium alloy is particularly provided.
Background technology
In trolley part field, cold-rolled steel sheet is widely used because of the forming property of its excellent mechanical property, such as vehicle body of automobile etc.Yet along with the enhancing gradually of people's environmental protection consciousness and the continuous rising of energy-saving and emission-reduction cry in recent years; requirement for running car oil consumption is also harsh all the more, and this just requires the weight that reduces on the whole automobile to obtain the oil consumption performance of more economy, environmental protection.
Aluminium alloy has the intensity that cold-rolled steel sheet does not compare favourably, and its proportion only has 1/3 of cold-rolled steel sheet, therefore be used as the substitute products of cold-rolled steel sheet and obtain increasingly extensive application at auto industry field, as vehicle body, chassis, chair framework and framework etc., much all progressively start to adopt aluminium alloy to prepare.
At present, in trolley part manufacture, using is that 5000 of non-thermal treatment type is that 6000 of (Al-Mg) aluminium alloy and thermal treatment type is (Al-Mg-Si) magnesium alloy comparatively widely.Wherein, 5000 is that (Al-Mg) aluminium alloy has very excellent forming property, but in the process of press forming, easily produce tension strain trace and affect the aesthetic property of parts surface, also can in baking vanish process, there is obvious baking vanish ruckbildung simultaneously, thereby cause intensity to be difficult to meet the requirement of using.And 6000 be (Al-Mg-Si) although magnesium alloy there will be hardly stretcher strain markings in the process of compacting, and can be by baking vanish thermal treatment process flexibly to improve yield strength, yet than 5000 being (Al-Mg) aluminium alloy, its forming property is inferior a lot.
How can obtain economically a kind of excellent forming property that both had, meet again the new automobile parts high-performance aluminium alloy of baking vanish thermal treatment sclerosis needs, for improving Integral automobile performance, mean a great.
Summary of the invention
Object of the present invention is to provide a kind of excellent forming property that both had, and meets again the new automobile parts high-performance aluminium alloy of baking vanish thermal treatment sclerosis and surface aesthetic needs.
Aluminium alloy of the present invention has following composition: in hundred parts of ratios of weight (wt.%), Mg4.0-4.5, Si0.6-0.8, Cu0.6-1.0, Mn0.05-0.1, Cr0.05-0.1, Zr0.05-0.1, Zn0.05-0.1, Sn0.1-0.2, Sr0.01-0.05.
Further preferred, Mg4.2, Si0.7, Cu0.8, Mn0.07, Cr0.06, Zr0.06, Zn0.08, Sn0.15, Sr0.03;
Further preferred, Mg+Cu+Si≤6.0.
Aluminium alloy of the present invention is to prepare by following method:
First according to the stoichiometric preparation raw material of aluminium alloy, the method by semicontinuous casting after raw materials melt is obtained to aluminum alloy slab;
Aluminum alloy slab is implemented to homogenize under the condition of 520-550 ℃ processing, treatment time 3-4h;
Subsequently aluminium alloy is implemented to hot roughing, it is 520-550 ℃ that roughing starts temperature, and finishing temperature is 450-480 ℃, and draft is more than 90%;
Subsequently aluminium alloy is implemented to hot finishing, the temperature of hot finishing is 400-430 ℃, and draft is 70-80%, strain rate 15-20/s;
Through cold rolling, aluminium alloy is pressed into required thickness subsequently;
Subsequently aluminium alloy is heated to 480-530 ℃ and implements solution treatment 30-60s, with the speed of cooling of 20-30 ℃/s, be cooled to after 280-320 ℃, with the speed of 150-200 ℃/s, be chilled to room temperature, natural aging 24-30h;
Again aluminium alloy is heated to subsequently to 50-70 ℃ of insulation 30-36h, obtains the present invention and both there is excellent forming property, meet again the new automobile parts high-performance aluminium alloy of baking vanish thermal treatment sclerosis and surface aesthetic needs.
Advantage of the present invention is, the aluminium alloy stock proportioning that silicon, magnesium, copper are main alloy element is take in redesign, by cooperatively interacting of each material composition, and corresponding rolling, thermal treatment process, obtained and both there is excellent forming property, met again the new automobile parts high-performance aluminium alloy of baking vanish thermal treatment sclerosis needs.
Embodiment
Below by specific embodiment, describe content of the present invention in detail.
According to the al alloy component proportioning described in table 1, preparation starting material, obtain aluminum alloy slab by the method by semicontinuous casting after raw materials melt; Aluminum alloy slab is implemented to homogenize under the condition of 520 ℃ processing, treatment time 3h; Subsequently aluminium alloy is implemented to hot roughing, it is 520 ℃ that roughing starts temperature, and finishing temperature is 450 ℃, and draft is 90%; Subsequently aluminium alloy is implemented to hot finishing, the temperature of hot finishing is 400 ℃, and draft is 70%, strain rate 15/s; Through cold rolling, aluminium alloy is pressed into required thickness subsequently; Subsequently aluminium alloy is heated to 480 ℃ and implements solution treatment 30s, with the speed of cooling of 20 ℃/s, be cooled to after 280 ℃, with the speed of 150 ℃/s, be chilled to room temperature, natural aging 24; Again aluminium alloy is heated to subsequently to 50 ℃ of insulation 30h, obtains aluminium alloy of the present invention.
Table 1
| ? | 1 | 2 | 3 | 1# | 2# | 3# | 4# | 5# | 6# |
| Mg | 4.0 | 4.2 | 4.5 | 3.0 | 5.5 | 4.5 | 4.2 | 4.1 | 4.2 |
| Si | 0.8 | 0.7 | 0.6 | 0.4 | 0.6 | 0.8 | 0.7 | 0.8 | 0.7 |
| Cu | 1.0 | 0.8 | 0.6 | 0.5 | 0.8 | 1.0 | 0.8 | 0.9 | 0.7 |
| Mn | 0.05 | 0.07 | 0.08 | 0.06 | 0.05 | 0.1 | 0.04 | 0.2 | 0.07 |
| Cr | 0.1 | 0.06 | 0.07 | 0.08 | 0.09 | 0.1 | 0.02 | 0.1 | 0.08 |
| Zr | 0.05 | 0.07 | 0.09 | 0.07 | 0.08 | 0.08 | - | 0.1 | 0.07 |
| Zn | 0.05 | 0.08 | 0.1 | 0.07 | 0.08 | 0.06 | 0.02 | 0.15 | 0.05 |
| Sn | 0.1 | 0.15 | 0.2 | 0.15 | 0.1 | 0.15 | 0.2 | 0.2 | - |
| Sr | 0.01 | 0.03 | 0.05 | 0.04 | 0.02 | 0.05 | 0.03 | 0.04 | - |
| TS | 282 | 294 | 275 | 211 | 298 | 312 | 256 | 308 | 284 |
| YS-1 | 115 | 120 | 110 | 102 | 154 | 165 | 104 | 157 | 117 |
| YS-2 | 183 | 192 | 178 | 143 | 185 | 201 | 155 | 190 | 152 |
| LDR | 2.21 | 2.28 | 2.28 | 1.95 | 1.86 | 1.88 | 2.07 | 1.94 | 2.13 |
| SS | ○ | ○ | ○ | ○ | × | ○ | ○ | ○ | × |
In table 1, TS is tensile strength, units MPa; YS-1 is the yield strength without paint baking, units MPa; YS-2 is the yield strength after 170 ℃, 30min paint baking, units MPa; LDR is limit stretching ratio; SS is the surface quality evaluation after being shaped, and zero is without obvious stretcher strain markings, * for there being obvious stretcher strain markings.
Result by table 1 can be found out, Mg is as main alloying element, intensity and plasticity for aluminum-system have material impact, the content of Mg alloying element is too low, is difficult to realize grain refining, and the effect of strengthening phase strengthening, thereby cannot meet system for the requirement of intensity and plasticity, if but the too high levels of Mg easily intercrystalline failure occurs when being shaped and cause brittle rupture, invent obvious plasticity and worsen.Mg too high levels also has adverse influence for the surface quality of aluminium alloy after being shaped simultaneously.In the present invention, preferably the content of Mg is 4.0-4.5, more preferably 4.2.
Si alloying element is significant for forming intermetallic compound strengthening phase, and in order to form enough strengthening phases to meet the needs of intensity, the content of Si can not be too low, at least should reach 0.6.But too much Si addition may cause excessive the separating out of strengthening phase, thereby make forming process easily brittle rupture occur and affect processability, therefore should control its content is less than 0.8.Preferably, the Si in the present invention is 0.7.
Mg is not the same with Si for precipitation strength, has mutually determinative for Cu alloying element, in order to obtain excellent intensity and processability, the content of Cu should guarantee more than 0.6, but thereby too much Cu content not only can cause the excessive plasticity variation that makes of precipitated phase, intergranular corrosion resistance performance that also can severe exacerbation system, therefore should control its content is less than 1.0.Preferably, the Cu in the present invention is 0.8.
Meanwhile, consider that tensile strength improves saturability and avoids the too high consideration of yield strength, preferably Mg+Cu+Si≤6.0.
Mn, Cr, Zr, Zn are as micro-alloying element, it has mainly played grain refining, appropriate interpolation has beneficial effect for intensity and the forming property of system, for guaranteeing its effectiveness of performance, the addition of each composition at least reaches Mn0.05, Cr0.05, Zr0.05, Zn0.05, but its interpolation should be inexcessive yet, otherwise can generate coarse grain and severe exacerbation plasticity on the contrary, and reduce the corrosion resistance nature of system, specifically should control its content and be no more than Mn0.1, Cr0.1, Zr0.1, Zn0.1.And the complex intensifying of Mn, Cr, Zr is comparatively effective, preferably its content is Mn0.07, Cr0.06, Zr0.06.
Sn alloying element can play the effect that improves surface quality in system, and for bringing into play its effect, the addition of Sn at least should reach 0.1.But too much Sn addition may cause the corrosion resistance nature of other degradation, particularly aluminium alloy of system, therefore preferably below 0.2, more preferably 0.15.
The Main Function of Sr alloying element is to play inhibiting grain growth, the particularly generation of the coarse grains in solution treatment process, for bringing into play above-mentioned effect, the addition of Sr at least should be 0.01, but too much interpolation can make the mechanical property of system worsen, therefore should control its addition and be less than 0.05, more preferably 0.03.
For further investigating subsequent heat treatment technique for the impact of aluminium alloy capability, the chemical composition of embodiment 2 is not identical to have adopted embodiment 2(comparative example) chemical composition and processing parameter as according to object, changed heat treatment parameter and tested results of property, specifically referring to table 2.
Table 2
In order to obtain sufficient homogenizing effect, all heat treated temperature should be at least 520 ℃, but also should be not too high, to avoid the local melting of alloy.Meanwhile, for fear of the coarsening of the alloying element precipitates such as Mn, Cr, should avoid the heat treated of process time or heating repeatedly, in the present invention, controlling soaking temperature is 520-550 ℃, and the treatment time is 3-4h.
The preferred uneven materialization treatment temp of beginning temperature of hot roughing is consistent, if the temperature of hot roughing is lower than 520 ℃, recrystallize fully in the process of rolling, the tendency of coarsening in a organized way, and the beginning excess Temperature of roughing, easily cause the series of problems such as local melting, surface oxidation, thereby affect surface quality and plasticity.
The preferred 450-480 ℃ of finishing temperature of hot roughing, finishing temperature is too low, can make hot finishing after recrystallize insufficient, finishing temperature is too high can make the crystal grain of hot finishing subsequently have coarsening tendency.
The processing temperature of hot finishing is preferably 400-430 ℃, the temperature of hot finishing is too low, can make finish rolling after recrystallize can not fully carry out, the ductility of alloy and processing characteristics are not enough, and the excess Temperature of hot finishing, be difficult to effectively to control grain fineness number evenly with the performance of guarantee system.Meanwhile, too low strain rate, also can cause the inhomogeneous of grain fineness number, should control strain rate at 15-20/s.
Solid solution temperature should guarantee at 480 ℃, because too low temperature can not make the precipitation strength elements such as Mg, Cu, Si obtain sufficient solid solution, thereby be difficult to obtain enough plasticities and bake hardening, but also should do not surpass 530 ℃, otherwise have local melting, surface oxidation equivalent risk.And in order to obtain enough solid solution effects, solution time should be at least more than 30s, but also unsuitable long efficiency of producing with impact.
One section of cooling slow cooling is mainly that separating out of strengthening phase is now not remarkable, therefore slow cooling can't cause the obvious rising of yield strength, thereby can not worsen the forming property of system, preferably control its cooling rate at 20-30 ℃/s, further reduce speed of cooling likely in crystal boundary generation precipitation-hardening, thus impact plasticity and bake hardening subsequently.
The chilling of two-step cooling can suppress the generation of precipitation-hardening effectively, thereby can effectively suppress the increase of yield strength, reaches the object that improves forming property.To achieve these goals, speed of cooling at least should reach 150 ℃/s, but should be not too high, otherwise has the risk that quenching strain occurs.
Again aluminium alloy is heated to 50-70 ℃ of insulation, can impels the abundant diffusion of solute atoms, to form low-temperature reinforcement phase, thereby reach, improve plasticity, put forward high-intensity object.But too high aging temp may cause separating out of high-temperature-phase, thus the plasticity of deterioration system.
Claims (4)
1. a trolley part high-performance aluminium alloy, it is characterized in that described aluminium alloy has following composition: in hundred parts of ratios of weight (wt.%), Mg4.0-4.5, Si0.6-0.8, Cu0.6-1.0, Mn0.05-0.1, Cr0.05-0.1, Zr0.05-0.1, Zn0.05-0.1, Sn0.1-0.2, Sr0.01-0.05.
2. a kind of aluminium alloy according to claim 1, is characterized in that described aluminium alloy has following composition: Mg4.2, Si0.7, Cu0.8, Mn0.07, Cr0.06, Zr0.06, Zn0.08, Sn0.15, Sr0.03.
3. a kind of aluminium alloy according to claim 1, is characterized in that: wherein, and Mg+Cu+Si≤6.0.
4. a kind of aluminium alloy according to claim 1, is characterized in that: it prepares by the following method,
First according to the composition preparation raw material of described aluminium alloy, the method by semicontinuous casting after raw materials melt is obtained to aluminum alloy slab;
Aluminum alloy slab is implemented to homogenize under the condition of 520-550 ℃ processing, treatment time 3-4h;
Subsequently aluminium alloy is implemented to hot roughing, it is 520-550 ℃ that roughing starts temperature, and finishing temperature is 450-480 ℃, and draft is more than 90%;
Subsequently aluminium alloy is implemented to hot finishing, the temperature of hot finishing is 400-430 ℃, and draft is 70-80%, strain rate 15-20/s;
Through cold rolling, aluminium alloy is pressed into required thickness subsequently;
Subsequently aluminium alloy is heated to 480-530 ℃ and implements solution treatment 30-60s, with the speed of cooling of 20-30 ℃/s, be cooled to after 280-320 ℃, with the speed of 150-200 ℃/s, be chilled to room temperature, natural aging 24-30h; Again aluminium alloy is heated to subsequently to 50-70 ℃ of insulation 30-36h, obtains the present invention and both there is excellent forming property, meet again the new automobile parts high-performance aluminium alloy of baking vanish thermal treatment sclerosis needs.
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| CN201310612698.8A CN103725937B (en) | 2013-11-27 | 2013-11-27 | A kind of trolley part high-performance aluminium alloy |
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| CN201310612698.8A CN103725937B (en) | 2013-11-27 | 2013-11-27 | A kind of trolley part high-performance aluminium alloy |
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| CN103725937A true CN103725937A (en) | 2014-04-16 |
| CN103725937B CN103725937B (en) | 2016-04-13 |
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH04297539A (en) * | 1991-03-26 | 1992-10-21 | Ndc Co Ltd | Alambda-sn-si-pb bearing material |
| JP2004084060A (en) * | 2002-06-24 | 2004-03-18 | Denso Corp | Aluminum alloy fin material for heat exchanger and heat exchanger including the fin material |
| CN1753740A (en) * | 2003-02-26 | 2006-03-29 | 皮奇尼何纳吕公司 | Method for warm swaging al-mg alloy parts. |
| JP2008511756A (en) * | 2004-08-27 | 2008-04-17 | コモンウェルス インダストリーズ，インコーポレーテッド | Aluminum automotive structural members |
| CN103119184A (en) * | 2010-09-08 | 2013-05-22 | 美铝公司 | Improved 6xxx aluminum alloys, and methods for producing the same |
-
2013
- 2013-11-27 CN CN201310612698.8A patent/CN103725937B/en not_active Expired - Fee Related
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH04297539A (en) * | 1991-03-26 | 1992-10-21 | Ndc Co Ltd | Alambda-sn-si-pb bearing material |
| JP2004084060A (en) * | 2002-06-24 | 2004-03-18 | Denso Corp | Aluminum alloy fin material for heat exchanger and heat exchanger including the fin material |
| CN1753740A (en) * | 2003-02-26 | 2006-03-29 | 皮奇尼何纳吕公司 | Method for warm swaging al-mg alloy parts. |
| JP2008511756A (en) * | 2004-08-27 | 2008-04-17 | コモンウェルス インダストリーズ，インコーポレーテッド | Aluminum automotive structural members |
| CN103119184A (en) * | 2010-09-08 | 2013-05-22 | 美铝公司 | Improved 6xxx aluminum alloys, and methods for producing the same |
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Inventor after: Tu Ping Inventor before: Mao Yangqun |
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Effective date of registration: 20170517 Address after: 528414 Guangdong Province, Zhongshan City Dongsheng town of Chi motorcycle factory side Patentee after: ZHONGSHAN JIANPING ALUMINUM PRODUCTS CO., LTD. Address before: Yuyao City, Zhejiang province 315400 Ningbo City Yangming streets Liang Yan Cun Patentee before: YUYAO WUXING COPPER INDUSTRY CO., LTD. |
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