CN110238229B - Manufacturing method of aluminum alloy plate - Google Patents
Manufacturing method of aluminum alloy plate Download PDFInfo
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- CN110238229B CN110238229B CN201910607163.9A CN201910607163A CN110238229B CN 110238229 B CN110238229 B CN 110238229B CN 201910607163 A CN201910607163 A CN 201910607163A CN 110238229 B CN110238229 B CN 110238229B
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
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Abstract
The invention provides an aluminum alloy plate based on Al-Mg-Si alloy and a manufacturing method thereof. Compared with the existing preparation method of the Al-Mg-Si series aluminum alloy plate, the plate prepared by the preparation method of the Al-Mg-Si series aluminum alloy plate has excellent strength and formability, and also has excellent room temperature aging inhibition performance.
Description
Technical Field
The invention relates to the technical field of alloys, in particular to an aluminum alloy plate and a manufacturing method thereof, and particularly relates to an aluminum alloy plate based on Al-Mg-Si alloy and a manufacturing method thereof.
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 and a manufacturing method thereof, thereby overcoming the defects and shortcomings of the prior art.
In order to achieve the above object, the present invention provides a method for producing an Al-Mg-Si-based aluminum alloy sheet, characterized by comprising the steps of:
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) carrying out solution treatment on the finally cold-rolled plate and then carrying out heat treatment;
9) and (4) stretching and straightening the heat-treated plate.
Preferably, the heating and melting means that the raw materials are heated to the liquidus temperature of 30-50 ℃; the double rollers are hollow copper rollers; during casting, the two rolls are rotated in opposite directions at a peripheral speed of 50-100 m/min while applying a pressure of 1.5-2.0kN/mm to the rolls.
Preferably, the homogenization treatment is to heat the cast plate to 480-520 ℃ and then preserve the heat for 10-20 hours, and then cool the plate to below 320 ℃ at a cooling rate of 100-150 ℃/hour.
Preferably, the hot rolling is performed at a start rolling temperature of 400-450 ℃.
Preferably, the annealing refers to furnace cooling after heating the plate after the initial cold rolling to 450-500 ℃ and preserving the heat for 1-3 hours.
Preferably, the solution treatment is to heat the plate after the final cold rolling to the solution treatment temperature of 520-550 ℃ and then keep the temperature for 4-6 hours; then the plate is quenched to 165-180 ℃, then is insulated for 1-2 hours, and is cooled to room temperature by air. The heat treatment refers to heating the plate to 100-120 ℃, preserving the heat for 5-10 hours, and then cooling the plate to room temperature.
Preferably, the stretch straightening is performed by applying the sheet in a stretch straightening device to produce a tensile strain of 0.2-0.5% followed by holding at a temperature of 150 ℃ and 160 ℃ for 0.5-1 hour.
Preferably, the Al-Mg-Si-based aluminum alloy contains, in mass%, 1 to 1.5% of Mg, 3.5 to 4% of Si, 0.3 to 0.5% of Cu, 0.4 to 1.0% of Fe, 0.05 to 0.2% of Mn, 0.2 to 0.3% of Li, and the balance of Al and inevitable impurities.
Compared with the existing preparation method of the Al-Mg-Si series aluminum alloy plate, the plate prepared by the preparation method of the Al-Mg-Si series aluminum alloy plate has excellent strength and formability, and also has excellent room temperature aging inhibition performance.
Detailed Description
Example 1
The Al-Mg-Si series aluminum alloy plate with excellent comprehensive performance is prepared by the following method:
firstly, according to the mass percentage, weighing raw materials of 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 inevitable impurities, and heating the raw materials to 40 ℃ higher than the liquidus temperature to obtain molten metal.
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.
Finally, the plate after the time-lapse heat treatment was subjected to a tensile strain of 0.3% in a stretch-straightening apparatus, and then heat-preserved at a temperature of 150 ℃ for 0.8 hour. The tensile strain is generated, and the forming performance of the plate can be effectively improved by resisting the increase of yield strength caused by subsequent natural aging, but the tensile strain is not suitable to be too large, otherwise, the forming performance of the plate is adversely affected due to the increase of strength caused by the tensile strain.
In the example 2, the rotation peripheral speed of the copper roller is adjusted to 200 m/min, the opposite pressure applied to the copper roller is adjusted to 1.0kN/mm, and the conditions of the rest process steps, parameters and the like are the same as those of the example 1; in example 3, the cooling rate of the molten metal was adjusted to 100 ℃/s, and the conditions of the remaining process steps, parameters, and the like were the same as those of example 1.
In example 4, the homogenization temperature was 480 ℃ and the holding time was 20 hours, and the other process steps, parameters, and other conditions were the same as in example 1; in example 5, the homogenization treatment was followed by cooling to 320 ℃ or lower at a cooling rate of 80 ℃/hr, and the conditions of the remaining process steps, parameters, and the like were the same as those in example 1.
In the embodiment 6, the initial rolling temperature is adjusted to 400 ℃, and the conditions of the rest process steps, parameters and the like are the same as those in the embodiment 1; in example 7, the hot rolling reduction was 70%, and the conditions of the remaining process steps, parameters, and the like were the same as those in example 1.
In example 8, the annealing temperature was set to 530 ℃, and the remaining process steps, parameters, and the like were the same as in example 1.
In example 9, the total reduction of cold rolling was adjusted to 75%, and the conditions of the remaining process steps, parameters, and the like were the same as those in example 1.
In example 10, the plate after the solution treatment and heat preservation was directly air-cooled to room temperature without being subjected to salt bath quenching and heat preservation treatment, and the conditions of the rest of the process steps, parameters and the like were the same as those in example 1. In example 11, the temperature of the aging heat treatment was set to 90 ℃, and the other process steps, parameters, and the like were the same as in example 1.
In example 12, the tensile strain produced by the stretch straightening was set to 0.7%, and the conditions such as the remaining process steps and parameters were the same as in example 1.
TABLE 1 Properties of Al-Mg-Si series aluminum alloy sheet of the present invention
The aluminum alloy sheets of examples 1-12 were tested for room temperature tensile strength, elongation, press formability, and room temperature aging. Wherein, the room temperature tensile strength and the elongation are measured according to the national standard; the forming performance adopts a plate with the thickness of 1mm and the square of 200mm, a cylindrical needle with the diameter of 100mm is used for stamping under the pressure of 450kN, the height of the plate which is stretched out when the plate is broken is used as judgment, and the larger the numerical value is, the better the forming performance is; the room temperature aging performance is judged by taking the difference between the 0.2% yield strength measured after being placed at room temperature for 180 days and the 0.2% yield strength directly measured after preparation as a judgment, and the smaller the numerical value is, the smaller the increase value of the yield strength is after room temperature natural aging for a sufficient period of time is, so that the better the performance of inhibiting room temperature natural aging is. The performance parameters obtained from the tests are specifically shown in table 1.
The Al-Mg-Si series aluminum alloy adopted by the aluminum alloy plate mainly comprises Si, Mg, Cu, Fe, Mn, Li and other alloy elements.
Wherein the alloying elements Si and Mg are the main alloying elements of the Al-Mg-Si series aluminum alloy, and can form a beta-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, so that enough beta phase cannot be precipitated, the subsequent baking hardening performance is obviously reduced, the extension is also poor, and the melt fluidity can be increased by a proper amount of Si, so that the casting performance of the alloy melt is improved; however, the content of Si is not so high that grain boundary segregation and coarsening of grain precipitation are caused to deteriorate ductility and formability, and too high Si content makes it difficult to realize uniformity of distribution of the melt alloy.
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 the precipitation of a beta' phase 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.
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 (1)
1. A manufacturing method of an Al-Mg-Si series aluminum alloy plate is characterized by comprising 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 metal raw materials through double-roller casting equipment, wherein the double rollers are hollow copper rollers; during casting, the two rollers rotate oppositely, the rotating speed is 50-100 m/min, and meanwhile, the pressure of 1.5-2.0KN/mm is applied to the two rollers; the heating and melting means that the metal raw material is heated to 30-50 ℃ above the liquidus temperature;
3) homogenizing the cast plate; the homogenization treatment is that the cast plate is heated to 480-520 ℃ and then is kept warm for 10-20 hours, and then is cooled to below 320 ℃ at the cooling speed of 100-150 ℃/hour;
4) hot rolling the homogenized plate with the reduction rate not less than 80%; the hot rolling is performed at the initial rolling temperature of 400-450 ℃;
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; the annealing is that the plate after the initial cold rolling is heated to the temperature of 450-500 ℃, and then is cooled along with the furnace after heat preservation for 1-3 hours;
7) performing final cold rolling on the annealed sheet material to ensure that the total reduction rate after the two cold rolling is more than or equal to 60 percent and less than 70 percent;
8) carrying out solution treatment on the finally cold-rolled plate and then carrying out heat treatment; the solution treatment is that the plate after the final cold rolling is heated to the solution treatment temperature of 520-550 ℃, and then the heat is preserved for 4-6 hours; then, the plate is cooled down to 165-180 ℃, then is insulated for 1-2 hours, and is cooled to room temperature; the heat treatment is that the plate is heated to the temperature of 100-120 ℃, and then is cooled to the room temperature after heat preservation for 5-10 hours;
9) performing stretching straightening on the plate subjected to heat treatment, wherein the stretching straightening refers to that the plate generates 0.2-0.5% of stretching strain in stretching straightening equipment and then is subjected to heat preservation for 0.5-1 hour at the temperature of 150-160 ℃;
the Al-Mg-Si series aluminum alloy comprises, by mass, 1-1.5% of Mg, 3.5-4% of Si, 0.3-0.5% of Cu, 0.4-1% of Fe, 0.05-0.2% of Mn, 0.2-0.3% of Li, and the balance of Al and inevitable impurities.
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