CN110184509B - Aluminum alloy with excellent performance and product thereof - Google Patents
Aluminum alloy with excellent performance and product thereof Download PDFInfo
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- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
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- 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
- C22F1/043—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 silicon as the next major constituent
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Abstract
The invention provides an Al-Mg-Si alloy-based aluminum alloy with excellent comprehensive performance and an aluminum alloy plate prepared from the same. The Al-Mg-Si aluminum alloy contains, by mass, 1.0-1.5% of Mg, 3.5-4.0% of Si, 0.3-0.5% of Cu, 0.4-1.0% of Fe, 0.05-0.20% of Mn, 0.20-0.30% of Li, and the balance of Al and inevitable impurities. The Al-Mg-Si series aluminum alloy has excellent mechanical properties, particularly high-temperature strength, and simultaneously has excellent formability and low-temperature baking hardening performance, and the aluminum alloy plate prepared by the Al-Mg-Si series aluminum alloy is particularly suitable for being used as a vehicle body construction material of an automobile.
Description
Technical Field
The invention relates to the technical field of alloys, in particular to an aluminum alloy, and particularly relates to an Al-Mg-Si alloy-based aluminum alloy with excellent comprehensive performance and an aluminum alloy plate prepared from the same.
Background
In recent years, due to increasing importance placed on environmental protection problems such as exhaust emission and the like and increasing demand for reduction of non-renewable energy consumption, there has been an increasing demand for reduction in weight of vehicle bodies of transportation means such as automobiles.
On the other hand, in the structural materials of automobile bodies including hoods, doors, roofs, and the like, the use of aluminum alloy materials having lighter weight (about 1/3 in terms of the density of steel sheet) and excellent formability and bake hardenability has been rapidly increasing, and has gradually replaced steel materials which have been mainly used.
Among the conventional aluminum alloy materials, 6000 series aluminum alloys (i.e., JIS6000 series aluminum alloys, Al-Mg-Si series aluminum alloys) contain magnesium and silicon as essential alloying elements, and Mg is precipitated2Si is used as a main strengthening phase, has the advantages of small density, high specific strength and specific stiffness, good impact resistance, high corrosion resistance, good heat dissipation and the like, and the prepared aluminum alloy plate is particularly suitable for being used as a thin-wall motor vehicle body construction material with high strength requirement, and is the most widely applied aluminum alloy in the field of motor vehicles at present. Meanwhile, in the recycling process of the scrap of the 6000 series aluminum alloy product, the 6000 series aluminum alloy material ingot can be easily obtained again after being melted due to less alloy elements, and the recycling property is also excellent.
Despite the excellent properties and wide application of 6000 series aluminium alloys as described above, there are still some unsatisfactory drawbacks: for example, conventional high-strength 6000 series aluminum alloys have a problem that although they have high tensile strength, they have insufficient ductility and are likely to crack or even break when they are bent or the like; for example, the difference in the sectional shape, thickness, and the like of the aluminum alloy obtained by extrusion causes the cooling rate of each part of the section to vary, and the section becomes deformed, and further, the dimensional accuracy deteriorates and the aluminum alloy becomes difficult to be thinned.
Due to the wide application prospect of the 6000 series aluminum alloy and the problems, a great deal of research is carried out on the 6000 series aluminum alloy so as to develop the Al-Mg-Si series aluminum alloy with more excellent comprehensive performance.
Disclosure of Invention
The invention aims to provide an Al-Mg-Si series aluminum alloy with excellent comprehensive performance, thereby overcoming the defects and shortcomings of the prior art.
To achieve the above object, the present invention provides an Al-Mg-Si-based aluminum alloy having excellent overall properties, characterized in that: the Al-Mg-Si aluminum alloy contains, by mass, 1.0-1.5% of Mg, 3.5-4.0% of Si, 0.3-0.5% of Cu, 0.4-1.0% of Fe, 0.05-0.20% of Mn, 0.20-0.30% of Li, and the balance of Al and inevitable impurities.
More preferably, the content of the above-mentioned component satisfies 2.0. ltoreq. SiRedundancy/(Cu+Fe)≤3.5。
More preferably, the content of the above-mentioned component satisfies 2.2. ltoreq. SiRedundancy/(Cu+Fe)≤3.0。
More preferably, the content of the above-mentioned components satisfies Mn/Fe ≦ 0.25.
More preferably, the Al — Mg — Si-based aluminum alloy contains, in mass%, 1.5% Mg, 4.0% Si, 0.5% Cu, 0.9% Fe, 0.20% Mn, 0.25% Li, and the balance Al and inevitable impurities.
The invention also provides an aluminum alloy plate with excellent performance, which is prepared from the Al-Mg-Si series aluminum alloy.
Further preferably, the aluminum alloy plate is prepared by the following steps:
1) providing a metal raw material of an Al-Mg-Si series aluminum alloy;
2) heating and melting metal raw materials, and pouring the molten raw materials through double-roller casting equipment;
3) homogenizing the cast plate;
4) hot rolling the homogenized plate with the reduction rate not less than 80%;
5) performing primary cold rolling on the hot-rolled plate, wherein the reduction rate is more than or equal to 30%;
6) annealing the plate subjected to the primary cold rolling;
7) performing final cold rolling on the annealed plate to ensure that the total reduction rate after the two cold rolling is more than or equal to 60 percent;
8) and carrying out solution treatment on the finally cold-rolled plate and then carrying out heat treatment.
Preferably, the tensile strength of the aluminum alloy plate at room temperature is more than or equal to 400MPa, the elongation is more than or equal to 15 percent, the tensile strength at high temperature is more than or equal to 120MPa, and the surface hardness after coating, baking and hardening is more than or equal to 135 HV.
Compared with the existing Al-Mg-Si series aluminum alloy, the Al-Mg-Si series aluminum alloy has excellent mechanical properties, particularly high-temperature strength, excellent formability and low-temperature baking hardening performance, and the aluminum alloy plate prepared by the Al-Mg-Si series aluminum alloy is particularly suitable for being used as a structural material of a motor vehicle body.
Detailed Description
Example 1
The Al-Mg-Si series aluminum alloy plate with excellent comprehensive performance is prepared by the following method:
after weighing the raw materials according to the specific proportion in the table 1, heating the raw materials to 40 ℃ higher than the liquidus temperature to obtain molten metal, and fully stirring the molten metal in the heating and melting process to obtain uniformly mixed molten metal because the molten metal contains more light alloy elements such as silicon, magnesium and the like.
Then, the molten metal is poured into a twin-roll casting apparatus, the liquid level of which is 30mm higher than the pouring gate, so as to ensure that sufficient static pressure is generated to stabilize the state of the die-cast melt between the rolls, wherein the twin-roll casting apparatus is a hollow copper roll, and the hollow interior is filled with cooling liquid so as to ensure that the molten metal is quenched from the melting temperature to below 650 ℃ at a speed of above 200 ℃/s, so that the quenching speed is ensured because ultra-fine intermetallic compounds can be obtained, so that the high-temperature strength of the aluminum alloy plate can be effectively improved. Meanwhile, the double rollers are driven to rotate oppositely at the rotation peripheral speed of 70 m/min, and opposite pressure of 1.8kN/mm (kN/mm represents the pressure applied to the copper rollers divided by the thickness of the copper rollers) is respectively applied to the copper rollers, if the roller speed is not required, the increase of load borne by the double rollers and the fluctuation of the thickness of a melt solidification layer in the casting process are easily caused, but the roller speed is not too high, the uneven contact between the melt and the roller surfaces is easily caused, a certain opposite pressure is applied to rotate in coordination with the roller speed so as to keep the shape of the solidification part stable, and the roughening of the roller surfaces is caused by the excessive pressure so as to influence the smoothness of the surfaces of the plate blanks.
Subsequently, the slab is homogenized, specifically, the cast slab is heated to 500 ℃ and then is kept warm for 15 hours, and then is cooled to below 320 ℃ at a cooling rate of 130 ℃/hour. The temperature of the homogenization treatment must be such as to ensure homogeneity of the alloying elements in the cast slab, to eliminate segregation and to allow Mg to form2Si can be sufficiently dissolved in a solid solution. Meanwhile, enough cooling speed must be ensured to prevent the precipitation and aggregation of Mg-Si compounds in the cooling process, thereby influencing the subsequent properties of deep drawing property, low-temperature baking hardening and the like. The homogenization treatment time is also ensured to ensure sufficient solid solution of the second phase particles which causes deterioration of formability, but too long homogenization treatment effects saturate and cause lowering of productivity and increase of cost.
Subsequently, hot rolling treatment was performed at a start rolling temperature of 420 ℃ with a hot rolling reduction of 90%. The low initial rolling temperature leads to high deformation resistance of the plate and difficult effective hot rolling, and can cause precipitation and aggregation of Mg-Si compounds, thereby influencing subsequent properties such as deep tensile property, low-temperature baking hardening and the like. However, the initial rolling temperature should not be too high, which would cause coarsening of the grains during hot rolling. Too low hot rolling reduction results in insufficient Cube orientation generation, which in turn affects formability such as hemming. The hot rolling reduction rate cannot be too high, and the sufficient thickness of the plate after hot rolling needs to be ensured so as to leave enough reduction space for subsequent cold rolling.
Subsequently, the initial cold rolling was performed at a reduction of 40%. Too low initial cold rolling leads to too high final cold rolling reduction after annealing, which leads to excessive Cube orientation generation, and further leads to sheet anisotropy generation, and leads to reduction of deep drawing performance.
And then, carrying out annealing treatment, specifically heating the plate subjected to the primary cold rolling to 480 ℃, preserving the heat for 2 hours, and then cooling along with the furnace. The temperature of the annealing treatment must be sufficient for recrystallization, but not too high to prevent the coarsening of crystal grains during annealing and the deterioration of formability such as hemming.
Subsequently, final cold rolling was performed, and after the final cold rolling, the total reduction of the two cold rolling was 65%. The cold rolling total reduction rate is large enough to ensure the sufficient generation of Cube orientation. However, the total rolling reduction is not so large as to exceed 70%, which leads to anisotropy problems.
After final cold rolling, carrying out solution treatment on the plate, specifically, heating the cold-rolled plate to a solution treatment temperature of 530 ℃, and then carrying out heat preservation for 5 hours, wherein the solution treatment temperature is too low or the heat preservation time is insufficient, so that the solution treatment is insufficient, but if the temperature is too high, problems such as eutectic dissolution and the like can be caused; then placing the plate into salt bath equipment to be quenched to 170 ℃, then preserving heat for 1.5 hours, air-cooling to room temperature, and quenching to a temperature lower than the temperature of solid solution treatment to enable solid solution elements in a parent phase to be in a supersaturated state, thereby promoting the formation of Mg in the subsequent aging heat treatment stage2The formation of Mg-Si intermediate compounds of the beneficial reinforcing phases of the Si type, in contrast, naturally suppresses the formation of other harmful Mg-Si intermetallic compounds. And then carrying out aging heat treatment, specifically heating the plate to 110 ℃, keeping the temperature for 7 hours, then air-cooling to room temperature, wherein if the aging temperature is too low or the time is too short, solid solution elements cannot be fully precipitated to form Mg2Si, which causes a decrease in strength, and an excessively high temperature or an excessively long time results in insufficient elongation properties.
TABLE 1 composition ratio of Al-Mg-Si series aluminum alloy of the present invention
| Serial number | Mg | Si | Cu | Fe | Mn | Li | Al | SiSurplus/(Cu+Fe) | Mn/Fe |
| 1 | 1.2 | 3.7 | 0.4 | 0.5 | 0.10 | 0.25 | Balance of | 3.3 | 0.20 |
| 2 | 1.5 | 4.0 | 0.5 | 0.9 | 0.20 | 0.25 | Balance of | 2.2 | 0.22 |
| 3 | 1.0 | 3.5 | 0.3 | 0.8 | 0.10 | 0.30 | Balance of | 2.6 | 0.13 |
| 1# | 2.0 | 4.0 | 0.4 | 0.8 | 0.15 | 0.25 | Balance of | 2.4 | 0.18 |
| 2# | 1.3 | 4.5 | 0.5 | 0.7 | 0.15 | 0.27 | Balance of | 3.1 | 0.21 |
| 3# | 1.5 | 3.6 | 0.1 | 1.0 | 0.20 | 0.28 | Balance of | 2.5 | 0.20 |
| 4# | 1.4 | 4.0 | 0.3 | 1.3 | 0.20 | 0.25 | Balance of | 2.0 | 0.15 |
| 5# | 1.5 | 4.0 | 0.4 | 0.7 | 0.05 | 0.23 | Balance of | 2.8 | 0.07 |
| 6# | 1.2 | 3.8 | 0.4 | 0.8 | 0.14 | 0.15 | Balance of | 2.6 | 0.17 |
| 7# | 1.1 | 3.8 | 0.3 | 0.4 | 0.10 | 0.24 | Balance of | 4.5 | 0.25 |
| 8# | 1.2 | 3.6 | 0.4 | 0.7 | 0.20 | 0.28 | Balance of | 2.6 | 0.28 |
In examples 2 to 3 and comparative examples 1# -8#, the components of the Al-Mg-Si based aluminum alloy were adjusted, the specific component ratios are shown in table 1, and the conditions of the remaining process steps, parameters, and the like were the same as in example 1.
The plate products of examples 1 to 3 and comparative examples 1# -8# were tested for room temperature tensile strength, elongation, high temperature tensile strength (350 ℃) and paint bake hardenability. Wherein, the room temperature tensile strength, the elongation and the high temperature tensile strength (350 ℃) are measured according to the national standard; the paint bake hardenability was measured by heating the plate to 140 ℃ and then holding for 30 minutes to simulate the paint bake treatment, followed by testing the retained hardness of the plate surface. The performance parameters obtained from the tests are specifically shown in table 2.
TABLE 2 Properties of Al-Mg-Si series aluminum alloy of the present invention
In the present invention, the alloying elements Si and Mg are the main alloying elements of the Al-Mg-Si series aluminum alloy, which are capable of forming β -phase Mg-Si compound Mg2Si, thereby effectively precipitating and strengthening the alloy by heat treatment, and forming Mg in Si and Mg2In order to realize the effects, the content of Si is too small to precipitate enough β phase, the subsequent bake-hardening performance is obviously reduced, the ductility is also poor, the melt fluidity can be increased by a proper amount of Si, the casting performance of the alloy melt is improved, but the content of Si is not too high, grain boundary segregation and grain precipitation coarsening can be caused, the ductility and the formability are further poor, and the uniformity of the melt alloy distribution is difficult to realize by too much Si content.
As described above, the alloying element Mg mainly forms a strengthening phase with Si, and the content of Mg cannot be too low in order to obtain a sufficient strengthening phase; however, if the content of Mg is too high, the additional strengthening effect caused by the excess Si cannot be obtained, and meanwhile, too high content of Mg easily causes component segregation of the alloy melt to affect the casting effect and the product performance.
The alloy element Cu can form a compound with Si in a matching way, so that embrittlement caused by grain boundary segregation of Si is avoided, the strength and the baking hardening performance of the alloy are improved, and the corrosion resistance and the high temperature resistance of the alloy can be improved; however, the content of Cu is not necessarily too high, and deterioration of corrosion resistance and the like is caused.
The alloy element Fe can play a role in solid solution strengthening, and simultaneously Fe can play a role in grain refinement, so that the mechanical properties such as tensile strength of the alloy are improved, and the problems of grain boundary embrittlement and the like caused by segregation of redundant Si in the grain boundary can be effectively inhibited due to the increase of the number of grains caused by grain refinement, and in order to play the roles, the content of Fe cannot be too low; however, since Fe is likely to form an intermetallic compound with Al to lower the plastic workability of the aluminum alloy, the content thereof is not necessarily too high.
The alloy element Mn has a certain solid solution strengthening effect, and can form Al-Mn dispersed particles to play a role in inhibiting the coarsening of crystal grains, thereby achieving the purpose of grain refinement; meanwhile, the spherical precipitation of the Fe-Al compound can be promoted, so that the adverse effect of the Fe-Al compound on processing and shaping is avoided; however, the content of Mn should not be too large, which may cause precipitation of coarse crystals to deteriorate workability, and too large Mn may increase the melt solidus temperature, thereby increasing the casting temperature to increase the production cost and decrease the production efficiency.
The alloy element Li can obviously promote β' phase precipitation in the coating, roasting and hardening treatment process, thereby being converted into stable Mg in the subsequent natural aging process2The addition of Li can significantly reduce the treatment temperature of coating baking hardening and the aging hardening performance, and the addition amount of Li cannot be too low to exert the renting; however, the addition of Li should not be too high, which would result in a reduction in the elongation and formability of the alloy and would cause significant compositional segregation in the melt affecting the properties of the cast product.
In addition, in order to prevent problems such as grain boundary segregation and embrittlement due to excess Si, Si is preferably made to be Si-richRedundancy/(Cu + Fe) ≦ 3.5, and 2.0 or less Si is preferable in order to ensure sufficient strengthening of the excess SiRedundancy/(Cu + Fe), so that the strengthening effect of the excessive Si can be achieved, and various problems possibly caused by the excessive Si can be avoidedRedundancyMeans settlement according to theory and removal of Mg2Si remaining. More preferably, 2.2. ltoreq. SiRedundancy/(Cu+Fe)≤3.0。
In addition, although Mn can play a certain role in promoting the spherical precipitation of Fe-Al compounds, excessive Mn can seriously reduce the amount of Fe dissolved in the solid solution, and affect the effectiveness of Fe, particularly the effect of inhibiting the segregation of Si in grain boundaries, so that Mn/Fe is less than or equal to 0.25.
The foregoing descriptions of specific exemplary embodiments of the present invention have been presented for purposes of illustration and description. It is not intended to limit the invention to the precise form disclosed, and obviously many modifications and variations are possible in light of the above teaching. The exemplary embodiments were chosen and described in order to explain certain principles of the invention and its practical application to enable one skilled in the art to make and use various exemplary embodiments of the invention and various alternatives and modifications as are suited to the particular use contemplated. It is intended that the scope of the invention be defined by the claims and their equivalents.
Claims (7)
1. An Al-Mg-Si series aluminum alloy having excellent comprehensive properties, characterized in that: the Al-Mg-Si series aluminum alloy contains, by mass, 1.0-1.5% of Mg, 3.5-4.0% of Si, 0.3-0.5% of Cu, 0.4-1.0% of Fe, 0.05-0.20% of Mn, 0.20-0.30% of Li, and the balance of Al and inevitable impurities; the content of the above components satisfies 2.0-SiRedundancyV (Cu + Fe) is less than or equal to 3.5, and the Si isRedundancyMeans settlement according to theory and removal of Mg2Si remaining.
2. The Al-Mg-Si-based aluminum alloy according to claim 1, characterized in that: the content of the above components satisfies 2.2-SiRedundancy/（Cu+Fe）≤3.0。
3. The Al-Mg-Si-based aluminum alloy according to claim 1, characterized in that: the content of the components satisfies that Mn/Fe is less than or equal to 0.25.
4. The Al-Mg-Si-based aluminum alloy according to claim 1, characterized in that: the Al-Mg-Si aluminum alloy contains, by mass, 1.5% of Mg, 4.0% of Si, 0.5% of Cu, 0.9% of Fe, 0.20% of Mn, 0.25% of Li, and the balance of Al and unavoidable impurities.
5. An aluminum alloy sheet having excellent properties, which is produced from the Al-Mg-Si series aluminum alloy according to any one of claims 1 to 4.
6. The aluminum alloy sheet according to claim 5, wherein: the aluminum alloy plate is prepared by the following steps:
1) providing a metal raw material of an Al-Mg-Si series aluminum alloy;
2) heating and melting metal raw materials, and pouring the molten raw materials through double-roller casting equipment;
3) homogenizing the cast plate;
4) hot rolling the homogenized plate with the reduction rate not less than 80%;
5) performing primary cold rolling on the hot-rolled plate, wherein the reduction rate is more than or equal to 30%;
6) annealing the plate subjected to the primary cold rolling;
7) performing final cold rolling on the annealed plate to ensure that the total reduction rate after the two cold rolling is more than or equal to 60 percent;
8) and carrying out solution treatment on the finally cold-rolled plate and then carrying out heat treatment.
7. The aluminum alloy sheet according to claim 5 or 6, wherein: the tensile strength of the aluminum alloy plate at room temperature is more than or equal to 400MPa, the elongation is more than or equal to 15 percent, the tensile strength at high temperature is more than or equal to 120MPa, and the surface hardness after coating, baking and hardening is more than or equal to 135 HV.
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Effective date of registration: 20200609 Address after: 528000 workshop 2, No.22, Zone D, Sanshui Industrial Park, Foshan City, Guangdong Province Applicant after: Foshan Gaodun Metal Co.,Ltd. Address before: 518101 23 Xin'an Lake Garden, Xin'an Street, Baoan District, Shenzhen City, Guangdong Province 203 Applicant before: SHENZHEN WANJIA INTERDYNAMIC TECHNOLOGY Co.,Ltd. |
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Denomination of invention: A high-performance aluminum alloy and its products Effective date of registration: 20230718 Granted publication date: 20200703 Pledgee: Bank of China Limited by Share Ltd. Foshan branch Pledgor: Foshan Gaodun Metal Co.,Ltd. Registration number: Y2023980048798 |
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