CN111471945B - Hot forming method for improving comprehensive performance and surface quality of aluminum alloy component - Google Patents
Hot forming method for improving comprehensive performance and surface quality of aluminum alloy component Download PDFInfo
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- CN111471945B CN111471945B CN202010494381.9A CN202010494381A CN111471945B CN 111471945 B CN111471945 B CN 111471945B CN 202010494381 A CN202010494381 A CN 202010494381A CN 111471945 B CN111471945 B CN 111471945B
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/34—Methods of heating
- C21D1/42—Induction heating
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
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Abstract
The invention provides a hot forming manufacturing method for improving comprehensive performance and surface quality of an aluminum alloy member. Compared with the aluminum alloy member formed by the traditional method, the member produced by the hot forming process has better surface quality and corrosion resistance, faster production speed, shorter production period, obviously improved production efficiency and is beneficial to saving energy.
Description
Technical Field
The invention relates to the technical field of nonferrous metal material processing engineering, in particular to a hot forming method for improving the comprehensive performance and the surface quality of an aluminum alloy member.
Background
The aluminum alloy has the advantages of small density, high specific strength, good corrosion resistance, good electrical and thermal conductivity and the like, and is widely applied to the fields of aerospace, rail transit, automobiles and the like. In recent years, members used in airplanes and automobiles have been developed in a direction of weight reduction, integration, and complication. Cold forming can enable the aluminum alloy to obtain high enough strength through work hardening and subsequent artificial aging strengthening, but the cold forming has insufficient plasticity in the forming process, is easy to have the defects of cracking and the like, and is difficult to process complex components with large deformation; although the plasticity of the aluminum alloy in the forming process can be improved by the traditional hot forming, the formability of the component is improved, the dynamic recovery effect can be continuously generated in the hot processing process, dislocation annihilation can be generated in the dislocation introduced in the forming process, and sufficient dislocation density is difficult to be reserved in the component, so that a good dislocation strengthening effect cannot be realized, and the development of the strength of the component is limited. Therefore, the member produced by a simple hot forming process is difficult to break through in mechanical properties only by precipitation strengthening, and cannot meet the requirement of further lightening the member. Therefore, when processing aluminum alloy, the joint action and mutual influence of a plurality of strengthening mechanisms must be considered, so as to further improve the formability and mechanical property of the aluminum alloy.
Meanwhile, with the development of various industries, people pursue surface quality more and more, good surface quality can not only improve the overall macroscopic impression of the components, but also is beneficial to effective matching (assembly of pins, keys and bearings) and transmission (gears, worms and the like) among the components, and the paint spraying effect of the aluminum alloy for the automobile is closely related to the surface quality. In order to pursue better overall impression and paint spraying effect, when the aluminum alloy plate is processed, tiny and regular textures are processed on the surface of the automobile body plate, and the paint spraying effect is improved while the surface quality is guaranteed. This means that industry now places higher demands on the overall performance, forming accuracy, and surface quality of aluminum alloy components.
Therefore, it is important to comprehensively consider dislocation strengthening and precipitation strengthening, and the mutual relationship between the dislocation strengthening and the precipitation strengthening, and to develop a forming manufacturing method capable of improving the comprehensive performance and the surface quality of the aluminum alloy member.
Disclosure of Invention
The invention provides a hot forming method for improving the comprehensive performance and the surface quality of an aluminum alloy member, and aims to improve the comprehensive performance and strengthen the surface quality of the aluminum alloy member.
In order to achieve the purpose, the invention provides a hot forming method for improving the comprehensive performance and the surface quality of an aluminum alloy member.
Preferably, the method comprises the following specific steps:
firstly, carrying out solution treatment on an aluminum alloy plate in an air circulation resistance furnace and then carrying out water quenching;
step two, carrying out cold deformation pretreatment on the plate treated in the step one;
step three, transferring the plate processed in the step two to a forming device for rapid forming manufacturing after heating;
and step four, carrying out artificial aging treatment on the plate treated in the step three.
Preferably, the cold deformation pretreatment in the second step is cold rolling treatment, and the deformation amount of the cold rolling treatment is 10-95%.
Preferably, the cold deformation pretreatment in the second step is performed at room temperature.
Preferably, the heating of the plate in the third step is specifically electromagnetic induction rapid heating, the heating rate is more than 50 ℃/s, and the target temperature range after heating is 150-300 ℃, wherein the temperature is preferably 280-300 ℃.
Preferably, the strain rate in the rapid prototyping process in the third step is more than 0.1/s.
Preferably, the artificial aging in the fourth step is specifically performed by: and (4) heating the plate treated in the step three to 120-160 ℃, and preserving heat for 5-10 hours.
According to the invention, a large amount of dislocation is introduced through cold deformation treatment before hot forming, so that the effect of work hardening is improved; through rapid heating and rapid forming, the aluminum alloy with the work hardening effect undergoes the heating process and the heat preservation process which are as short as possible, thereby limiting the occurrence of dislocation annihilation and retaining enough work hardening effect; by heating and heat preservation, dynamic recovery is induced to occur, so that dislocation movement is easily activated, a large amount of movable dislocations are generated, deformation resistance is reduced, elongation is improved, and therefore formability of the aluminum alloy is improved. By introducing high dislocation density, a large number of nucleation sites which are beneficial to precipitation are provided, the precipitation of a main strengthening phase is promoted, the density of the precipitation phase is increased, the size of the precipitation phase is refined, and the precipitation strengthening effect is improved. In the subsequent artificial aging process, a large amount of dislocation is still reserved in the organization after hot forming, so that the artificial aging temperature is favorably reduced, the artificial aging time is shortened, and the overall efficiency of the process is improved.
The scheme of the invention has the following beneficial effects:
1. compared with the traditional T4-state component, the component produced by the hot forming process provided by the invention has the strengthening effects of precipitation strengthening and dislocation strengthening, and meanwhile, the dislocations introduced by cold deformation pretreatment provide a plurality of precipitation phase nucleation sites, so that the precipitation phases are refined and uniformly distributed, the precipitation strengthening effect of the aluminum alloy can be improved, and the final component with higher mechanical property after hot forming can be obtained.
2. Compared with cold forming, the hot forming process provided by the invention has low deformation resistance and high plasticity, so that the integral formability is better, and the hot forming process is beneficial to producing complex components with larger deformation.
3. According to the artificial aging in the hot forming process, a large amount of dislocation is introduced before hot forming, so that nucleation and evolution of a precipitated phase are facilitated, the subsequent artificial aging process is accelerated, and the artificial aging temperature is reduced. Therefore, the production process has the advantages of faster production rhythm, shorter production period, obviously improved production efficiency and contribution to energy conservation.
4. The member produced by the hot forming process provided by the invention has better surface quality and corrosion resistance compared with the aluminum alloy member formed by the traditional method.
Drawings
FIG. 1 is an overall temperature-time flow diagram of the present invention;
FIG. 2 is a graph of hardness versus time for an artificial aging process and a 2219 aluminum alloy T6 temper treatment according to the method of the present invention;
FIG. 3 is a surface quality observation of a final component produced using the method of the present invention and a conventionally formed 2219 aluminum alloy;
FIG. 4 is a graph of the results of an intercrystalline corrosion experiment for a final part produced using the method of the present invention and a conventional process for forming 2219 aluminum alloy.
Detailed Description
In order to make the technical problems, technical solutions and advantages of the present invention more apparent, the following detailed description is given with reference to the accompanying drawings and specific embodiments.
Aiming at the existing problems, the invention provides a hot forming method for improving the comprehensive performance and the surface quality of an aluminum alloy member, and a sample used in the embodiment is commercial 2219 aluminum alloy; the alloy hardness test is carried out on a Vickers hardness tester, the test load is 4.9N, and the duration is 15 s; the hot stretching experiment is carried out on a self-built hot stretching experiment device; a universal tensile testing machine produced by the Saint Seiki company is matched with an induction heating device for use; the temperature control precision of the device is +/-10 ℃, and the load precision is +/-3N.
Comparative example 1
After solid solution treatment and water quenching are carried out on 2219 aluminum alloy in an air circulation resistance furnace, deformation treatment of cold rolling 80% is carried out at room temperature, a tensile sample is taken along the rolling direction, then a room temperature tensile test is carried out on a universal tensile testing machine, and the strain rate is selected to be 0.1/s.
Comparative example 2
After the 2219 aluminum alloy is subjected to solution treatment and water quenching in an air circulation resistance furnace, the aluminum alloy is subjected to artificial aging treatment at 165 ℃ (simulating an industrial T6 state), and then is subjected to a tensile test. And recording the hardness change process of the alloy in the artificial aging process by using a Vickers hardness tester.
Comparative example 3
After the 2219 aluminum alloy is subjected to solution treatment and water quenching in an air circulation resistance furnace, the pre-stretching deformation is carried out for 5% at room temperature, then the artificial aging is carried out for 8h at 165 ℃ (simulating the industrial T8 state), and then the tensile test is carried out. And observing the surface quality by using a metallographic microscope. And (3) according to a GB/T7998-1987 aluminum alloy intercrystalline corrosion determination method, determining the corrosion resistance of the sample.
Example 1
After solid solution treatment and water quenching are carried out on 2219 aluminum alloy in an air circulation resistance furnace, cold rolling 80% of deformation treatment is carried out at room temperature, a tensile sample is taken along the rolling direction, then a hot tensile test is carried out, the temperature is selected to be 150 ℃, the strain rate is selected to be 0.1/s, and the sample is air-cooled.
Example 2
After solid solution treatment and water quenching are carried out on 2219 aluminum alloy in an air circulation resistance furnace, cold rolling 80% of deformation treatment is carried out at room temperature, a tensile sample is taken along the rolling direction, then a hot tensile test is carried out, the temperature is 200 ℃, the strain rate is 0.1/s, and the sample is air-cooled. Samples were taken in the deformation zone, artificially aged at 120 ℃ and 160 ℃ and subjected to hardness tracking tests. And observing the surface quality by using a metallographic microscope. And (3) according to a GB/T7998-1987 aluminum alloy intercrystalline corrosion determination method, determining the corrosion resistance of the sample.
Example 3
After solid solution treatment and water quenching are carried out on 2219 aluminum alloy in an air circulation resistance furnace, cold rolling 80% deformation treatment is carried out at room temperature, a tensile sample is taken along the rolling direction, then a hot tensile test is carried out, the temperature is 250 ℃, the strain rate is 0.1/s, and the sample is air-cooled.
Example 4
After solid solution treatment and water quenching are carried out on 2219 aluminum alloy in an air circulation resistance furnace, cold rolling 80% of deformation treatment is carried out at room temperature, a tensile sample is taken along the rolling direction, then a hot tensile test is carried out, the temperature is 300 ℃, the strain rate is 0.1/s, and the sample is air-cooled.
Example 5
After solid solution treatment and water quenching are carried out on 2219 aluminum alloy in an air circulation resistance furnace, deformation treatment of cold rolling 80% is carried out at room temperature, a tensile sample is taken along the rolling direction, then simulated forming processing of thermal tensile deformation 5% is carried out, the temperature is selected to be 150 ℃, the strain rate is selected to be 0.1/s, and the sample is air-cooled. Then, the artificial aging is carried out at 160 ℃ until the hardness reaches the peak value, and finally, the tensile test is carried out.
Example 6
After solid solution treatment and water quenching are carried out on 2219 aluminum alloy in an air circulation resistance furnace, deformation treatment of cold rolling 80% is carried out at room temperature, a tensile sample is taken along the rolling direction, then simulated forming processing of hot tensile deformation 5% is carried out, the temperature is 200 ℃, the strain rate is 0.1/s, and the sample is air-cooled. Then, the artificial aging is carried out at 160 ℃ until the hardness reaches the peak value, and finally, the tensile test is carried out.
Example 7
After solid solution treatment and water quenching are carried out on 2219 aluminum alloy in an air circulation resistance furnace, deformation treatment of cold rolling 80% is carried out at room temperature, a tensile sample is taken along the rolling direction, then simulated forming processing of hot tensile deformation 5% is carried out, the temperature is 250 ℃, the strain rate is 0.1/s, and the sample is air-cooled. Then, the artificial aging is carried out at 160 ℃ until the hardness reaches the peak value, and finally, the tensile test is carried out.
Example 8
After solid solution treatment and water quenching are carried out on 2219 aluminum alloy in an air circulation resistance furnace, deformation treatment of cold rolling 80% is carried out at room temperature, a tensile sample is taken along the rolling direction, then simulated forming processing of hot tensile deformation 5% is carried out, the temperature is 300 ℃, the strain rate is 0.1/s, and the sample is air-cooled. Then, the artificial aging is carried out at 160 ℃ until the hardness reaches the peak value, and finally, the tensile test is carried out.
TABLE 1 tensile test data (strength unit: MPa) corresponding to comparative example 1 and examples 1 to 4
| Comparative example 1 | Example 1 | Example 2 | Example 3 | Example 4 | |
| Yield strength | 430 | 328 | 188 | 105 | 66 |
| Tensile strength | 488 | 389 | 281 | 203 | 109 |
| Elongation percentage | 6％ | 10％ | 17％ | 23％ | 26％ |
Table 1 shows tensile test data (yield strength, tensile strength, elongation) of comparative example 1 and examples 1 to 4. It is known that after cold pre-deformation treatment, the strength of the aluminum alloy is significantly improved, the elongation is very low, and this state is not suitable for forming. As the thermoforming temperature increased, the yield strength of the example decreased to 76% -15% (150 ℃ -300 ℃) of the room temperature yield strength and the elongation increased to 167% -433% (150 ℃ -300 ℃) of the room temperature elongation. Therefore, with the increase of the forming temperature, the forming force of the cold pre-deformation aluminum alloy is greatly reduced, the plasticity is greatly improved, and the formability is greatly improved.
TABLE 2 mechanical properties (strength units: MPa) after treatment of comparative examples 2 and 3 and examples 5 to 8 according to the relevant procedures
| Comparative example 2 | Comparative example 3 | Example 5 | Example 6 | Example 7 | Example 8 | |
| Yield strength | 280 | 383 | 507 | 488 | 442 | 405 |
| Tensile strength | 341 | 445 | 567 | 423 | 483 | 460 |
| Elongation percentage | 12％ | 8％ | 9％ | 10％ | 10％ | 11％ |
Table 2 shows the mechanical properties of the samples treated by the corresponding processes of comparative examples 2 to 3 and examples 5 to 8. It can be seen that the final structural member obtained by the process provided by the invention has obviously improved strength without loss of elongation compared with the conventional T6 and T8 states. The yield strength can be improved by 127MPa at most, and the tensile strength can be improved by 126MPa at most.
Therefore, by combining table 1 and table 2, it can be seen that the method of the present invention can simultaneously and effectively improve the formability and mechanical properties of the aluminum alloy, so that the aluminum alloy can obtain more excellent comprehensive properties, as shown in fig. 1 and 2, it can be seen that by using the hot forming process provided by the present invention, the final mechanical properties of the component can be improved, the temperature of the artificial aging can be reduced, and the time of the artificial aging can be shortened, thereby saving energy and improving the production efficiency. FIG. 3 is a surface quality observation of the final part (part a) and T8 temper 2219 aluminum alloy (part b) produced using the method of the present invention. As shown in FIG. 3, the surface of the T8 sample has a significant orange peel effect, and the surface of the sample prepared by the method of the present invention has only a fine and regular slip band, so that the member produced by the hot forming process of the present invention has better surface quality. FIG. 4 shows the results of an intergranular corrosion test on the final part (part a) produced by the method of the present invention and on the T8 temper 2219 aluminum alloy (part b), from which it can be seen that the part produced by the hot forming process proposed by the present invention has better corrosion resistance as measured by the depth of corrosion. The experimental results prove that the hot forming process provided by the invention can improve the formability, the mechanical property and the surface quality of the aluminum alloy member, can treat the member by using lower artificial aging temperature and shorter artificial aging time, and reduces the cost while improving the production efficiency. The method provided by the invention is a hot forming manufacturing method capable of improving the comprehensive performance, the surface quality and the production efficiency of the aluminum alloy member.
While the foregoing is directed to the preferred embodiment of the present invention, it will be understood by those skilled in the art that various changes and modifications may be made without departing from the spirit and scope of the invention as defined in the appended claims.
Claims (1)
1. A hot forming method for improving comprehensive performance and surface quality of an aluminum alloy member is characterized by comprising the following specific steps:
firstly, carrying out solution treatment on an aluminum alloy plate in an air circulation resistance furnace and then carrying out water quenching;
step two, carrying out cold deformation pretreatment on the plate treated in the step one;
wherein the cold deformation pretreatment is cold rolling treatment, and the deformation amount of the cold rolling treatment is 10-95%; the cold deformation pretreatment is carried out at room temperature;
step three, transferring the plate processed in the step two to a forming device for rapid forming manufacturing after heating;
wherein the plate heating is specifically electromagnetic induction rapid heating, the heating rate is more than 50 ℃/s, and the target temperature range after heating is 150-300 ℃; the strain rate in the rapid forming process is greater than 0.1/s;
step four, carrying out artificial aging treatment on the plate treated in the step three;
wherein, the artificial aging is specifically operated as follows: and (4) heating the plate treated in the step three to 120-160 ℃, and preserving heat for 5-10 hours.
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