CN103725937B - A kind of trolley part high-performance aluminium alloy - Google Patents
A kind of trolley part high-performance aluminium alloy Download PDFInfo
- Publication number
- CN103725937B CN103725937B CN201310612698.8A CN201310612698A CN103725937B CN 103725937 B CN103725937 B CN 103725937B CN 201310612698 A CN201310612698 A CN 201310612698A CN 103725937 B CN103725937 B CN 103725937B
- Authority
- CN
- China
- Prior art keywords
- aluminium alloy
- subsequently
- temperature
- trolley part
- performance
- 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.)
- Expired - Fee Related
Links
Landscapes
- Forging (AREA)
- Metal Rolling (AREA)
Abstract
The invention provides a kind of trolley part high-performance aluminium alloy.It is characterized in that described aluminium alloy has following composition: in weight hundred parts of ratios (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.New automobile parts high-performance aluminium alloy of the present invention, had both had excellent forming property, had met again baking vanish thermal treatment sclerosis and surface aesthetic needs.
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, the vehicle body etc. of such as automobile because of the forming property of the mechanical property of its excellence.But strengthening gradually and the continuous rising of energy-saving and emission-reduction cry along with people's environmental protection consciousness in recent years; requirement for running car oil consumption is also harsh all the more, and this just requires that the weight reducing automobile is on the whole to obtain the oil consumption performance of more economy, environmental protection.
Aluminium alloy has can not the intensity that compares favourably of cold-rolled steel sheet, and its proportion only has 1/3 of cold-rolled steel sheet, therefore increasingly extensive application is obtained by the substitute products as cold-rolled steel sheet 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, 6000 of (Al-Mg) aluminium alloy that uses in trolley part manufacture that to be 5000 of nonheat-treatable comparatively be widely and thermal treatment type is (Al-Mg-Si) magnesium alloy.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 there is obvious baking vanish ruckbildung in baking vanish process simultaneously, thus cause intensity to be difficult to meet the requirement used.And 6000 is that (Al-Mg-Si) is although magnesium alloy occurs stretcher strain markings hardly in the process of compacting, and can by baking vanish thermal treatment process flexibly to improve yield strength, but be (Al-Mg) aluminium alloy compared to 5000, its forming property is then much inferior.
How can obtain a kind of forming property both with excellence economically, meet again the new automobile parts high-performance aluminium alloy of baking vanish thermal treatment sclerosis needs, mean a great for raising Integral automobile performance.
Summary of the invention
Namely object of the present invention is that providing a kind of had both had excellent forming property, met 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 weight hundred parts of ratios (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.
Preferred further, Mg4.2, Si0.7, Cu0.8, Mn0.07, Cr0.06, Zr0.06, Zn0.08, Sn0.15, Sr0.03;
Preferred further, Mg+Cu+Si≤6.0.
Aluminium alloy of the present invention is prepared 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 aluminum alloy slab;
Aluminum alloy slab is implemented to homogenize process under the condition of 520-550 DEG C, treatment time 3-4h;
Implement hot roughing to aluminium alloy subsequently, it is 520-550 DEG C that roughing starts temperature, and finishing temperature is 450-480 DEG C, and draft is more than 90%;
Implement hot finishing to aluminium alloy subsequently, the temperature of hot finishing is 400-430 DEG C, 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 DEG C and implements solution treatment 30-60s, after being cooled to 280-320 DEG C with the speed of cooling of 20-30 DEG C/s, be chilled to room temperature with the speed of 150-200 DEG C/s, natural aging 24-30h;
Again aluminium alloy is heated to 50-70 DEG C of insulation 30-36h subsequently, 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.
Namely advantage of the present invention is, redesign the aluminium alloy stock proportioning being main alloy element with silicon, magnesium, copper, by cooperatively interacting of each material composition, and corresponding rolling, thermal treatment process, obtain and both there is excellent forming property, meet again the new automobile parts high-performance aluminium alloy of baking vanish thermal treatment sclerosis needs.
Embodiment
Content of the present invention is described in detail below by specific embodiment.
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 process under the condition of 520 DEG C, treatment time 3h; Implement hot roughing to aluminium alloy subsequently, it is 520 DEG C that roughing starts temperature, and finishing temperature is 450 DEG C, and draft is 90%; Implement hot finishing to aluminium alloy subsequently, the temperature of hot finishing is 400 DEG C, 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 DEG C and implements solution treatment 30s, after being cooled to 280 DEG C with the speed of cooling of 20 DEG C/s, be chilled to room temperature with the speed of 150 DEG C/s, natural aging 24; Again aluminium alloy is heated to 50 DEG C of insulation 30h subsequently, 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 through 170 DEG C, yield strength after 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.
As can be seen from the result of table 1, Mg is as main alloying element, for the intensity of aluminum-system and plasticity, there is material impact, the content of Mg alloying element is too low, be then difficult to realize grain refining, and the effect of strengthening phase strengthening, thus the requirement of system for intensity and plasticity cannot be met, if but the too high levels of Mg, then easily there is intercrystalline failure and cause brittle rupture when being shaped, inventing obvious plasticity and worsening.Mg too high levels also has adverse influence for the surface quality of the rear aluminium alloy that is shaped simultaneously.In the present invention, the content of preferred Mg is 4.0-4.5, more preferably 4.2.
Si alloying element is significant for formation 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 the precipitation that too much Si addition may cause strengthening phase excessive, thus make forming process easily brittle rupture occur and affect processability, therefore should control its content and be less than 0.8.Preferably, the Si in the present invention is 0.7.
Mg with Si is not the same has determinative mutually for precipitation strength for Cu alloying element, in order to obtain excellent intensity and processability, the content of Cu should ensure more than 0.6, but too much Cu content not only can cause the excessive of precipitated phase thus make plasticity be deteriorated, also can the intergranular corrosion resistance performance of severe exacerbation system, therefore should control its content and be less than 1.0.Preferably, the Cu in the present invention is 0.8.
Meanwhile, the consideration that tensile strength improves saturability and avoids yield strength too high, preferred Mg+Cu+Si≤6.0 is considered.
Mn, Cr, Zr, Zn are as the alloying element of trace, it mainly serves grain refining, appropriate interpolation has beneficial effect for the intensity of system and forming property, for ensureing to play its effectiveness, the addition of each composition at least reaches Mn0.05, Cr0.05, Zr0.05, Zn0.05, but its interpolation should be inexcessive yet, otherwise coarse grain can be generated on the contrary and severe exacerbation plasticity, 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, and preferably its content is Mn0.07, Cr0.06, Zr0.06.
Sn alloying element can play the effect improving surface quality in system, and for playing 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 preferred below 0.2, more preferably 0.15.
The Main Function of Sr alloying element is to play inhibiting grain growth, the generation of the coarse grains particularly in solution treatment process, for playing 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 investigating the impact of subsequent heat treatment technique for aluminium alloy capability further, the chemical composition that have employed embodiment 2(comparative example not embodiment 2 is identical) chemical composition and processing parameter as according to object, change heat treatment parameter and test results of property, specifically see table 2.
Table 2
In order to obtain sufficient homogenizing effect, all heat treated temperature should be at least 520 DEG C, but also should be not too high, to avoid the local melting of alloy.Meanwhile, in order to avoid the coarsening of the alloying element precipitates such as Mn, Cr, should avoid the heat treated of process time or repeatedly heat, controlling soaking temperature in the present invention is 520-550 DEG C, and the treatment time is 3-4h.
The beginning temperature preferred heterogeneity treatment temp of hot roughing is consistent, if the temperature of hot roughing is lower than 520 DEG C, can not recrystallize fully in the process of rolling, the tendency of coarsening in a organized way, and the beginning temperature of roughing is too high, then easily cause the series of problems such as local melting, surface oxidation, thus affect surface quality and plasticity.
The preferred 450-480 DEG C of finishing temperature of hot roughing, finishing temperature is too low, and after making hot finishing, recrystallize is insufficient, and finishing temperature is too high, and the crystal grain of hot finishing subsequently can be made to have coarsening to be inclined to.
The processing temperature of hot finishing is preferably 400-430 DEG C, the temperature of hot finishing is too low, and after making finish rolling, recrystallize can not fully carry out, the ductility of alloy and processing characteristics deficiency, and the temperature of hot finishing is too high, be then difficult to effectively control the even with the performance of guarantee system of grain fineness number.Meanwhile, too low strain rate, also can cause the uneven of grain fineness number, should controlled strain speed at 15-20/s.
Solid solution temperature should ensure at 480 DEG C, because too low temperature can not make the precipitation strength elements such as Mg, Cu, Si obtain sufficient solid solution, thus be difficult to obtain enough plasticities and bake hardening, but also more than 530 DEG C, otherwise local melting, surface oxidation equivalent risk should do not had.And in order to obtain enough solid solution effects, solution time should at least at more than 30s, but also should not be long to affect the efficiency of producing.
The slow cooling of one-step cooling is mainly that the precipitation of now strengthening phase is not remarkable, therefore slow cooling can't cause the obvious rising of yield strength, thus the forming property of system can not be worsened, its cooling rate of preferred control is at 20-30 DEG C/s, further reduction speed of cooling is then likely in crystal boundary generation precipitation-hardening, thus the plasticity affected subsequently and bake hardening.
The chilling of two-step cooling can suppress the generation of precipitation-hardening effectively, thus effectively can suppress the increase of yield strength, reaches the object improving forming property.To achieve these goals, speed of cooling at least should reach 150 DEG C/s, but should be not too high, otherwise has the risk that quenching strain occurs.
Again aluminium alloy is heated to 50-70 DEG C of insulation, the abundant diffusion of solute atoms can be impelled, to form low-temperature reinforcement phase, thus reach the object improved plasticity, improve intensity.But too high aging temp then may cause the precipitation of high-temperature-phase, thus worsen the plasticity of system.
Claims (4)
1. a trolley part high-performance aluminium alloy, it is characterized in that described aluminium alloy has following composition: in weight hundred parts of ratios (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, 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 aluminum alloy slab; Aluminum alloy slab is implemented to homogenize process under the condition of 520-550 DEG C, treatment time 3-4h;
Implement hot roughing to aluminium alloy subsequently, it is 520-550 DEG C that roughing starts temperature, and finishing temperature is 450-480 DEG C, and draft is more than 90%;
Implement hot finishing to aluminium alloy subsequently, the temperature of hot finishing is 400-430 DEG C, 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 DEG C and implements solution treatment 30-60s, after being cooled to 280-320 DEG C with the speed of cooling of 20-30 DEG C/s, be chilled to room temperature with the speed of 150-200 DEG C/s, natural aging 24-30h; Again aluminium alloy is heated to 50-70 DEG C of insulation 30-36h subsequently, both there is excellent forming property, meet again the trolley part high-performance aluminium alloy of baking vanish thermal treatment sclerosis needs.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201310612698.8A CN103725937B (en) | 2013-11-27 | 2013-11-27 | A kind of trolley part high-performance aluminium alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201310612698.8A CN103725937B (en) | 2013-11-27 | 2013-11-27 | A kind of trolley part high-performance aluminium alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN103725937A CN103725937A (en) | 2014-04-16 |
| CN103725937B true CN103725937B (en) | 2016-04-13 |
Family
ID=50450227
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201310612698.8A Expired - Fee Related CN103725937B (en) | 2013-11-27 | 2013-11-27 | A kind of trolley part high-performance aluminium alloy |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN103725937B (en) |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1753740A (en) * | 2003-02-26 | 2006-03-29 | 皮奇尼何纳吕公司 | Method for warm swaging al-mg alloy parts. |
| CN103119184A (en) * | 2010-09-08 | 2013-05-22 | 美铝公司 | Improved 6xxx aluminum alloys, and methods for producing the same |
Family Cites Families (3)
| 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 |
| JP4166613B2 (en) * | 2002-06-24 | 2008-10-15 | 株式会社デンソー | Aluminum alloy fin material for heat exchanger and heat exchanger formed by assembling the fin material |
| US20060042727A1 (en) * | 2004-08-27 | 2006-03-02 | Zhong Li | Aluminum automotive structural members |
-
2013
- 2013-11-27 CN CN201310612698.8A patent/CN103725937B/en not_active Expired - Fee Related
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1753740A (en) * | 2003-02-26 | 2006-03-29 | 皮奇尼何纳吕公司 | Method for warm swaging al-mg alloy parts. |
| CN103119184A (en) * | 2010-09-08 | 2013-05-22 | 美铝公司 | Improved 6xxx aluminum alloys, and methods for producing the same |
Also Published As
| Publication number | Publication date |
|---|---|
| CN103725937A (en) | 2014-04-16 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN103789583B (en) | Quick aging response type Al-Mg-Si-Cu-Zn system Alloy And Preparation Method | |
| CN104372210B (en) | A kind of automobile using low cost high formability aluminum alloy materials and preparation method thereof | |
| CN100453671C (en) | Al-Mg-Si-Cu alloy for automobile and its production process | |
| CN107779680A (en) | A kind of 6 line aluminium alloy section bars and preparation method thereof | |
| CN110983216A (en) | Process for reducing coarse crystal generation on surface of automotive extrusion forging rod | |
| CN104975209A (en) | 6000 series aluminum alloy material with high natural aging stability, aluminum alloy plate and preparing method of aluminum alloy plate | |
| CN112458344B (en) | High-strength corrosion-resistant aluminum alloy and preparation method and application thereof | |
| CN103243247A (en) | Aluminum alloy and preparation method thereof | |
| CN111014332B (en) | 6-series high alloy component with high long-term thermal stability and preparation method thereof | |
| JP4634249B2 (en) | Aluminum alloy plate for forming and method for producing the same | |
| CN109897995B (en) | High-strength high-plasticity aluminum alloy plate and manufacturing method thereof | |
| CN104975207A (en) | Al-Mg-Si aluminum alloy material, aluminum alloy plate, and preparation methods of Al-Mg-Si aluminum alloy material and aluminum alloy plate | |
| CN103255323B (en) | Al-Mg-Zn-Cu alloy and preparation method thereof | |
| CN113528900A (en) | Short-process high-conductivity 6-series aluminum alloy plate strip and preparation method thereof | |
| CN113106306A (en) | High-strength corrosion-resistant 5xxx series alloy and preparation method thereof | |
| CN104775059A (en) | Al-Mg-Si series aluminum-alloy material with long-time natural aging stability, aluminum-alloy plate and manufacturing method thereof | |
| CN112522552B (en) | Corrosion-resistant aluminum alloy and preparation method and application thereof | |
| JP4602195B2 (en) | Method for producing aluminum alloy sheet for forming | |
| CN112481536B (en) | Magnesium alloy thick plate and preparation method thereof | |
| CN113388764A (en) | High-strength 7-series aluminum alloy for automobile anti-collision beam and automobile anti-collision beam | |
| JP5367250B2 (en) | Aluminum alloy plate for forming and method for producing the same | |
| CN104975208A (en) | 6000-series aluminum alloy material with high strength and elongation, aluminum alloy plate and manufacturing method thereof | |
| CN103725938B (en) | A kind of High-performance aluminum alloy automobile part | |
| CN105734358A (en) | Preparation method for high-strength Al-Mg-Si-Cu-Mn aluminum alloy | |
| CN115747535B (en) | Manufacturing method for improving edge covering performance of 6016 automobile stamping plate |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CB03 | Change of inventor or designer information | ||
| CB03 | Change of inventor or designer information |
Inventor after: Tu Ping Inventor before: Mao Yangqun |
|
| TR01 | Transfer of patent right | ||
| TR01 | Transfer of patent right |
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. |
|
| CF01 | Termination of patent right due to non-payment of annual fee | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20160413 Termination date: 20201127 |