CN115874122A - Low-temperature pre-aging treatment method for improving hardening increment of 6451 aluminum alloy baking varnish - Google Patents
Low-temperature pre-aging treatment method for improving hardening increment of 6451 aluminum alloy baking varnish Download PDFInfo
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Abstract
The invention discloses a low-temperature pre-aging treatment method for improving hardening increment of 6451 aluminum alloy baking varnish, which comprises the following steps of: after homogenizing the alloy cast ingot, carrying out hot rolling treatment, cooling and cold rolling treatment to obtain a cold-rolled sheet; carrying out non-isothermal solid solution treatment and slow quenching treatment on the cold-rolled sheet in sequence, wherein in the process of the slow quenching treatment, the cooling rate is less than 20 ℃/s; then, multi-stage pre-aging treatment is carried out to obtain 6451 aluminum alloy with high baking finish hardening increment. The 6451 aluminum alloy treated by the method has excellent baking finish hardening increment and natural aging resistance stability, and the method also fully utilizes waste heat and reduces the actual production cost of the alloy plate.
Description
Technical Field
The invention belongs to the technical field of aluminum alloy, and particularly relates to a low-temperature pre-aging treatment method for improving hardening increment of 6451 aluminum alloy baking finish, which is particularly suitable for improving hardening increment of 6xxx series aluminum alloy (namely Al-Mg-Si series alloy) baking finish.
Background
With the increasing number of automobiles, air pollution and climate conditions deteriorate continuously, and the awareness of energy conservation and emission reduction of countries in the world is strengthened continuously. Therefore, how to realize the light weight of the automobile and further achieve the purposes of energy conservation and emission reduction becomes a key problem for further development of the automobile field; aluminum alloy has become a key material for lightweight automobiles of a new generation due to the advantages of light weight, corrosion resistance, high specific strength, easy processing and the like. In contrast, the 6xxx series aluminum alloys (i.e., al-Mg-Si series alloys) in several large series aluminum alloys have better overall properties and have significant advantages, such as: but the heat treatment is reinforceed, the corrosion resistance is good, the weldability is good, it is easy to the surface coloration and formability is good, and more importantly this series of alloy generally has higher baking finish hardening characteristic (i.e. the formed part after painting is processed by baking finish, its intensity can obtain further greater promotion, and then make the alloy sheet material have better dent-resisting ability), all these advantages make this series of alloys very suitable for applying to the processing of the car body planking, and there are several brands of alloys that have been used at present to obtain the wide application, such as AA6016, AA6111 and AA6022, etc..
In order to improve the baking varnish hardening increment and the natural aging resistance stability of 6xxx series aluminum alloy, domestic and foreign technologists propose the regulation and control of pre-aging after solid solution, the regulated and controlled alloy obtains certain improvement on both the baking varnish hardening increment and the natural aging resistance stability, but the effect is not particularly satisfactory, and further intensive research is still needed. For 6451 aluminum alloy, although the Si content of the aluminum alloy is higher than that of Mg, the Mg/Si ratio is obviously higher than that of the traditional 6xxx aluminum alloy, such as 6016 aluminum alloy, so that the precipitation of a precipitated phase can be better regulated and controlled, particularly, after the quenching rate is reduced after solid solution, the alloy can not separate a large amount of Si phase at a grain boundary, the subsequent process regulation of the formation of solute atom clusters can be better facilitated, and the deterioration effect of natural aging can be obviously reduced due to the reduction of the quenching rate. In addition, in order to reduce the production cost, if the pre-aging treatment temperature can be fully reduced, or the residual heat of the plate can be fully utilized to carry out low-temperature pre-aging treatment, and the solute atom cluster composition, form, size and distribution characteristics in the alloy matrix can be effectively controlled, the actual production cost of the alloy can be effectively reduced while the higher baking varnish hardening increment is kept, and the method has great significance for the wide application of the alloy in the automobile light weight process.
In consideration of the interaction and influence of the solid solution quenching process and the pre-aging process of the alloy, in order to reduce the pre-aging treatment temperature, the solid solution and quenching process must be effectively controlled, especially the strict control of the quenching process; the alloy can properly form solute atom clusters with certain scale or multi-scale characteristics while keeping supersaturated solid solution, and further can be used as nucleation points to promote the effective formation and reasonable distribution of the solute atom clusters in the low-temperature pre-aging process in the subsequent pre-aging treatment process, and simultaneously can effectively reduce the vacancy concentration, so that the alloy can show excellent natural aging resistant stability in the subsequent process. However, the process influencing factors are complex, and the difficulty in realizing multi-process coupling regulation and control of the formation and distribution of solute atom clusters is high. Therefore, how to couple the hot working, solid solution, slow quenching and multi-stage low-temperature pre-aging and reasonably control the size, shape and distribution of multi-scale and multi-type solute atom clusters is very critical to greatly improve the baking varnish hardening increment and the natural aging resistance stability of the alloy system, and has an important effect on effectively reducing the actual production cost of the alloy system.
At present, the prior patents are mainly in the aspects of solution and pre-aging heat treatment processes, including CN108884524A, CN101885000A, CN101168828A and the like.
The patent No. CN108884524A provides a processing method for improving the performance of an Al-Mg-Si (Mg + Si > 1.2%) aluminum alloy plate, which adopts a high temperature of 100-300 ℃ for short time of 5-300 seconds, and then keeps for long time of 5-500 hours at a low temperature of 30-50 ℃, thereby improving the hardening strength of the material baking finish and finally achieving the maximum baking finish increment of 92MPa.
The method is characterized in that a6111 aluminum alloy plate is subjected to solid solution heat preservation for 7min at 550 ℃ and water quenching, and then is subjected to heat preservation for 4-15min at a temperature range of 150-220 ℃, so that the purposes of low yield strength before stamping and normal yield strength after baking finish are achieved.
The patent number CN101168828A provides a method for improving the strength of 6022 aluminum alloy plates after baking finish, which adopts a pre-aging treatment process of preserving heat for 2-30 min at 60-200 ℃ after solution treatment, so as to achieve the purposes of lower yield strength and higher plasticity before stamping and yield strength greater than 200MPa after baking finish.
The above patents all adopt the conventional high-temperature short-time or low-temperature long-time pre-aging process to carry out heat treatment on the Al-Mg-Si alloy so as to improve the strength of the material after baking finish, therefore, the strength increment of the developed plate after baking is not ideal, and the requirements of automobile aluminum on high formability and high baking finish strength of the material cannot be met.
Disclosure of Invention
Aiming at the defects in the prior art, the invention aims to provide a low-temperature pre-aging treatment method for improving the hardening increment of 6451 aluminum alloy baking varnish, which fully utilizes the waste heat in hot rolling, firstly regulates and controls the size and distribution of Mg-Si precipitation phases in an aluminum alloy matrix to enable the precipitation phases to be in a proper size, and the precipitation phases not only can effectively influence the dislocation multiplication condition in the subsequent cold rolling process and increase the dislocation to a proper degree, but also can promote the redissolution of the precipitation phases in the low-temperature stage in the subsequent non-isothermal solid solution process; on the basis, the quenching cooling rate after solid solution is further reduced, so that a certain number of multi-scale solute atom clusters can be precipitated in the alloy matrix while the alloy matrix is in a supersaturated solid solution, and further the multi-scale solute atom clusters can be used as nucleation points to promote the effective formation and reasonable distribution of the solute atom clusters in the low-temperature pre-aging process during the subsequent pre-aging treatment; in addition, the vacancy concentration can be effectively reduced, so that the aluminum alloy can show excellent natural aging resistance stability and simultaneously has high baking varnish hardening increment.
In order to achieve the purpose, the invention adopts the following technical scheme:
the invention provides a low-temperature pre-aging treatment method for improving hardening increment of 6451 aluminum alloy baking varnish, which comprises the following steps:
(1) After homogenizing the alloy cast ingot, carrying out hot rolling treatment, cooling and cold rolling treatment to obtain a cold-rolled sheet;
(2) Carrying out non-isothermal solution treatment and slow quenching treatment on the cold-rolled sheet in sequence, wherein in the process of the slow quenching treatment, the cooling rate is less than 20 ℃/s;
(3) And (3) performing multistage pre-aging treatment on the cold-rolled sheet treated in the step (2) to obtain the 6451 aluminum alloy with high baking finish hardening increment.
Preferably, in the step (1):
in the hot rolling treatment process, the hot rolling temperature is controlled to be 500-570 ℃, the finishing temperature is more than 300 ℃, and the total deformation of the hot rolling is more than 90%; and/or
In the cooling process, the cooling rate is controlled to be less than 10 ℃/h; and/or
In the cold rolling treatment process, the pass reduction is controlled to be 20-70%, and the total cold rolling deformation is controlled to be 70-90%.
Preferably, in the step (1):
in the hot rolling treatment process, the finishing temperature is more than 320 ℃; and/or
In the cold rolling treatment process, one-way rolling is adopted, the pass reduction is controlled to be 20-40%, and the total cold rolling deformation is controlled to be 70-80%.
Preferably, in the step (2): in the non-isothermal solution treatment process, the highest temperature of the cold-rolled sheet is 550-580 ℃; when the temperature of the cold-rolled sheet is in the range of 20-545 ℃, controlling the heating rate to be 5-13 ℃/s; when the temperature of the cold-rolled sheet is in the range of 545-580 ℃, controlling the heating rate to be 1-13 ℃/min; and/or
In the process of the slow quenching treatment, the cooling rate is less than 15 ℃/s.
Preferably, in the step (2): in the non-isothermal solution treatment process, the highest temperature of the cold-rolled sheet is 550-575 ℃; when the temperature of the cold-rolled sheet is within the range of 20-545 ℃, the heating rate is 5-10 ℃/s; when the temperature of the cold-rolled sheet is in the range of 545-575 ℃, the heating rate is 1-10 ℃/min.
Preferably, the multistage pre-aging treatment process comprises a first stage pre-aging treatment, a second stage pre-aging treatment and a third stage pre-aging treatment, wherein the maximum temperature of the first stage pre-aging treatment is 60-120 ℃, and the temperature rise time is 9-20 s; the lowest temperature of the second-stage pre-aging treatment is 30-60 ℃, and the cooling time is 25-42 h; the minimum temperature of the third-stage pre-aging treatment is 10-40 ℃, and the cooling time is 7-10 days.
Preferably, in the step (3):
in the first-stage pre-aging treatment, the highest temperature is 60-112 ℃, and the temperature rise time is 9-16 s; and/or
In the second-stage pre-aging treatment, the minimum temperature is 30-50 ℃, and the cooling time is 26-41 h.
The invention provides 6451 aluminum alloy material for an automobile, and the 6451 aluminum alloy material for the automobile is prepared by adopting the low-temperature pre-aging treatment method for improving the hardening increment of 6451 aluminum alloy baking varnish.
Preferably, the hardness of the 6451 aluminum alloy material is 65-90 HV, and the baking varnish hardening increment is 10-30 HV.
Preferably, the elongation of the 6451 aluminum alloy material is 15-25%, the yield strength is 85-160 MPa, and the tensile strength is 175-260 MPa; and/or
After 2 percent of prestretching and aging treatment of simulating a paint baking state under the condition of 185 ℃/20min, the yield strength of the 6451 aluminum alloy is 200-240 MPa, and the tensile strength is 250-320 MPa.
The low-temperature pre-aging treatment method for improving the hardening increment of the 6451 aluminum alloy baking varnish provided by the invention has the following beneficial effects:
1. the low-temperature pre-aging treatment method for improving the hardening increment of the 6451 aluminum alloy baking finish fully utilizes the waste heat of the aluminum alloy matrix to carry out low-temperature pre-aging treatment, reduces the pre-aging treatment temperature, and can effectively control the solute atom cluster composition, form, size and distribution characteristics in the 6451 aluminum alloy matrix, so that the alloy has lower production cost while keeping higher baking finish hardening increment and natural aging resistance stability;
2. according to the low-temperature pre-aging treatment method for improving the baking varnish hardening increment of the 6451 aluminum alloy, the waste heat in hot rolling is fully utilized, the size and distribution of Mg-Si precipitation phases in an aluminum alloy matrix are regulated and controlled to be in a proper size, the precipitation phases can not only effectively influence the dislocation multiplication condition in the subsequent cold rolling process, but also increase the dislocation to a proper degree, and further promote the redissolution of the precipitation phases in the low-temperature stage in the subsequent non-isothermal solid solution process; on the basis, the quenching cooling rate after solid solution is further reduced, so that a certain number of multi-scale solute atom clusters can be precipitated in the alloy matrix while the alloy matrix is in a supersaturated solid solution, and further the multi-scale solute atom clusters can be used as nucleation points to promote the effective formation and reasonable distribution of the solute atom clusters in the low-temperature pre-aging process during the subsequent pre-aging treatment; in addition, the vacancy concentration can be effectively reduced, so that the aluminum alloy can show excellent natural aging resistance stability and simultaneously has high baking varnish hardening increment;
3. the invention not only can lead the 6451 aluminum alloy plate to show excellent baking finish hardening increment and natural aging resistance stability after hot working, solid solution, slow quenching and multi-stage low-temperature pre-aging coupling regulation, but also fully utilizes the waste heat to reduce the actual production cost of the alloy plate;
4. the low-temperature pre-aging treatment method for improving the hardening increment of the 6451 aluminum alloy baking varnish is very suitable for processing and producing aluminum alloy materials for automobiles, producing and using other aluminum alloy materials with specific requirements on distribution states of precipitated phases and solute atom clusters, and certainly being also suitable for being applied to other technical industries with higher requirements on tissues and comprehensive properties of other series of aluminum alloy materials.
Drawings
Other features, objects and advantages of the invention will become more apparent upon reading of the detailed description of non-limiting embodiments with reference to the following drawings:
FIG. 1 is a DSC analysis curve of 6451 aluminum alloy prepared in example 1 of the present invention after non-isothermal solution and slow quenching;
FIG. 2 is a strain curve simulating the bake hardening behavior for the 6451 aluminum alloy prepared in example 1;
FIG. 3 is a strain curve simulating the bake hardening behavior for 6451 aluminum alloy prepared in example 4;
FIG. 4 is a strain curve simulating the bake hardening behavior for 6451 aluminum alloy prepared in example 7.
Detailed Description
In order to better understand the technical scheme of the invention, the technical scheme of the invention is further explained by combining the embodiment.
With the increase in weight reduction of automobiles, higher demands have been made on the production cost and the baking varnish hardening increment of 6 xxx-series aluminum alloys for outer panels of automobile bodies. Although some 6xxx aluminum alloys, such as 6016, 6111 and 6022, have been widely used, the preparation process is still unreasonable, the production cost is high, and the overall performance is still to be further improved. Therefore, it is necessary to select specific alloy components for the widely-used 6xxx aluminum alloy, and develop process regulation and optimization research, so as to further improve the hardening increment and the natural aging resistance stability of the alloy baking varnish. Considering that the enhancement of baking finish hardening and the stability against natural aging are mainly related to the formation and growth of precipitation phase, the process is closely related to the previous hot working process, the solid solution and quenching mode and the like besides the subsequent pre-aging process. Therefore, if the alloy ingot after homogenization treatment can be directly hot-rolled and then annealed by using waste heat, on one hand, the dislocation density of the alloy is effectively regulated and controlled, so that the subsequent cold rolling deformation is facilitated, and on the other hand, the size of the precipitation phase can be effectively controlled by controlling the cooling rate. If the size of the precipitated phase is reasonable, dislocation lines with proper concentration can be distributed around the precipitated phase in the subsequent direct cold rolling process, and the precipitated phase can be well redissolved and can preferentially stimulate recrystallization nucleation around the precipitated phase to optimize the alloy structure when being subjected to non-isothermal solution treatment. After the solution treatment, the concentration of vacancies in the alloy matrix is reduced by further controlling the cooling rate, and then multi-stage low-temperature pre-aging regulation is adopted, so that multi-scale solute atom clusters with reasonable composition, size, form and distribution can be formed in the corresponding aluminum alloy matrix, the alloy matrix is relatively stable, and the formation of unstable solute atom clusters in the natural aging process is reduced. Therefore, if the multi-scale solute atom clusters can be formed in the alloy matrix through the process, the alloy matrix can show excellent baking varnish hardening increment after stamping forming and baking varnish hardening treatment, and the alloy plate subjected to the multi-stage low-temperature pre-aging treatment has the advantages that the baking varnish hardening increment is not obviously reduced even if the alloy plate is naturally placed for a long time, and the alloy plate shows excellent natural aging stability resistance.
The invention provides a low-temperature pre-aging treatment method for improving hardening increment of 6451 aluminum alloy baking varnish, which comprises the following steps of:
(1) 6451 homogenizing the aluminum alloy cast ingot, and then carrying out hot rolling treatment, cooling and cold rolling treatment to obtain a cold-rolled sheet;
the specific process is as follows: according to the composition proportion of the 6451 aluminum alloy, the 6451 aluminum alloy comprises the following components in percentage by mass: 0.6 to 1.0 percent of Si, less than or equal to 0.4 percent of Fe, less than or equal to 0.4 percent of Cu, 0.05 to 0.40 percent of Mn, 0.40 to 0.80 percent of Mg, less than or equal to 0.1 percent of Cr, less than or equal to 0.15 percent of Zn, less than or equal to 0.1 percent of V, and the balance of Al; obtaining 6451 aluminum alloy cast ingots through smelting and casting, carrying out homogenization treatment on the 6451 aluminum alloy cast ingots, and then carrying out hot rolling treatment to obtain hot rolled plates, wherein the rolling temperature is 500-570 ℃, the final rolling temperature is more than 300 ℃, the total hot rolling deformation is more than 90%, and in a further preferred scheme, the final rolling temperature is more than 320 ℃; then cooling the hot rolled plate, wherein the cooling rate is less than 10 ℃/h; and then directly carrying out cold rolling treatment, wherein the pass reduction is 20-70%, and the total cold rolling deformation is 70-90%, in a further preferred scheme, the cold rolling adopts unidirectional rolling, the pass reduction is controlled to be 20-40%, and the total cold rolling deformation is 70-80%.
(2) Carrying out non-isothermal solution treatment and slow quenching treatment on the cold-rolled sheet in sequence;
the specific process is as follows: carrying out non-isothermal solution treatment on the cold-rolled sheet treated in the step (1), wherein the highest temperature of the cold-rolled sheet is 550-580 ℃, the heating rate is controlled to be 5-13 ℃/s when the temperature of the cold-rolled sheet is in the range of 20-545 ℃, and the heating rate is controlled to be 1-13 ℃/min when the temperature of the cold-rolled sheet is in the range of 545-580 ℃; in a further preferable scheme, in the non-isothermal solution treatment process, the maximum temperature of the cold-rolled sheet is 550-575 ℃, when the temperature of the cold-rolled sheet is in the range of 20-545 ℃, the heating rate is 5-10 ℃/s, and when the temperature of the cold-rolled sheet is in the range of 545-575 ℃, the heating rate is 1-10 ℃/min. And then directly carrying out slow quenching treatment on the cold-rolled sheet subjected to non-isothermal solution treatment, wherein the cooling rate is controlled to be less than 20 ℃/s, and in a further preferred scheme, the cooling rate is controlled to be less than 15 ℃/s in the slow quenching treatment process.
(3) And (3) performing multistage pre-aging treatment on the cold-rolled sheet treated in the step (2) to obtain 6451 aluminum alloy with high baking finish hardening increment.
The specific process is as follows: directly carrying out multistage low-temperature pre-aging treatment on the cold-rolled sheet after the slow quenching treatment to obtain 6451 aluminum alloy with high baking finish hardening increment, wherein in the specific treatment process, the multistage pre-aging treatment process comprises first-stage pre-aging treatment, second-stage pre-aging treatment and third-stage pre-aging treatment, wherein the first-stage pre-aging treatment is a heating process, the highest temperature in the whole process is 60-120 ℃, the heating time is 9-20 s, in a further preferred scheme, the temperature of the first-stage pre-aging treatment is 60-112 ℃, the heating time is 9-16 s, and the heating rate is controlled to be more than 2.5 ℃/s; the second-stage pre-aging treatment is a cooling process, the lowest temperature in the whole process is 30-60 ℃, the cooling time is 25-42 h, in a further preferred scheme, the lowest temperature in the second-stage pre-aging treatment is 30-50 ℃, the cooling time is 26-41 h, and the cooling rate is controlled to be less than 3 ℃/h; the third-stage pre-aging treatment is a cooling process, the lowest temperature in the whole process is 10-30 ℃, the cooling time is 7-10 days, and the cooling rate is controlled to be less than 5 ℃/d.
Through the comprehensive regulation and control of the multiple processes, particularly the cooperative regulation and control of the slow quenching and the low-temperature multi-stage pre-aging after the non-isothermal solution treatment, the developed alloy plate can be ensured to have excellent baking finish hardening increment and natural aging resistance stability. The hardness of the 6451 aluminum alloy with high baking varnish hardening increment prepared by the treatment is 65-90 HV, and the baking varnish hardening increment is 10-30 HV. The elongation of 6451 aluminum alloy with high baking varnish hardening increment is 15-25%, the yield strength is 85-160 MPa, and the tensile strength is 175-260 MPa; after 2 percent of pre-stretching and aging treatment of simulating a baking varnish state at 185 ℃/20min, the yield strength of the 6451 aluminum alloy with high baking varnish hardening increment is 200-240 MPa, and the tensile strength is 250-320 MPa.
The low temperature pre-aging treatment method for increasing the hardening increment of 6451 aluminum alloy baking varnish according to the present invention will be further described with reference to the following specific examples; in the following examples, 6451 aluminium alloy comprises the following composition in mass percent: 0.6 to 1.0 percent of Si, less than or equal to 0.4 percent of Fe, less than or equal to 0.4 percent of Cu, 0.05 to 0.40 percent of Mn, 0.40 to 0.80 percent of Mg, less than or equal to 0.1 percent of Cr, less than or equal to 0.15 percent of Zn, less than or equal to 0.1 percent of V, and the balance of Al;
example 1
In the implementation, after the 6451 aluminum alloy is smelted, cast and homogenized, the aluminum alloy is subjected to hot rolling deformation, the hot rolling temperature is 500-570 ℃, the total hot rolling deformation is more than 90%, and the finish rolling temperature is more than 320 ℃, and the cooling rate is controlled to cool: the cooling rate is less than 10 ℃/h, and then cold rolling deformation is directly carried out: the total cold rolling deformation is 70-80%, and the pass reduction is 20-40%; then carrying out non-isothermal solution treatment: the temperature rise rate is 5-10 ℃/s at 20-545 ℃, the temperature rise rate is 1-10 ℃/min at 545-575 ℃, and the highest temperature is controlled at 550-575 ℃; directly carrying out slow quenching treatment after non-isothermal solution treatment: the cooling rate is less than 15 ℃/s; and finally, directly carrying out multistage pre-aging treatment on the quenched alloy plate: the first-stage pre-aging treatment: the highest temperature is 120 ℃, the temperature rise time is 9-16 s, and the temperature rise rate is 8 ℃/s; and (3) secondary pre-aging treatment: the initial maximum temperature of cooling is 120 ℃, the final temperature is 50 ℃, the cooling time is 37-41 h, and the cooling rate is 1.8 ℃/h; third-stage pre-aging treatment: minimum temperature: the temperature is 10 ℃, the time is 7-10 days, and the cooling rate is 4 ℃/d. The alloy in the solid solution and slow quenching state is subjected to DSC characterization to analyze the precipitation behavior (shown in figure 1). At the same time, the hardness changes in the multi-stage pre-aged state and the multi-stage pre-aged state +185 ℃/20min state were measured, as well as the tensile properties in the pre-aged state and the 2% pre-stretch +185 ℃/20min simulated paint-bake state (as shown in table 1, table 2 and fig. 2).
Example 2
In the implementation, after the 6451 aluminum alloy is subjected to smelting casting and homogenization treatment, hot rolling deformation is carried out on the aluminum alloy, wherein the hot rolling temperature is 560 ℃, the total hot rolling deformation is more than 90%, and the finish rolling temperature is more than 320 ℃, and the cooling rate is controlled to cool: the cooling rate is less than 10 ℃/h, and then cold rolling deformation is directly carried out: the total cold rolling deformation is 75 percent, and the pass reduction is 20 to 40 percent; then carrying out non-isothermal solution treatment on the steel: the temperature rise rate is 5-10 ℃/s at 20-545 ℃, the temperature rise rate is 1-10 ℃/min at 545-575 ℃, and the highest temperature is controlled at 550-575 ℃; directly carrying out slow quenching treatment after non-isothermal solution treatment: the cooling rate is less than 15 ℃/s; and finally, directly carrying out multistage pre-aging treatment on the quenched alloy plate: the first-stage pre-aging treatment: the highest temperature is 112 ℃, the temperature rise time is 9-16 s, the temperature rise rate is 8 ℃/s, and the second-stage pre-aging treatment comprises the following steps: the initial maximum temperature of cooling is 112 ℃, the final temperature is 50 ℃, the cooling time is 33-36 h, the cooling rate is 1.7 ℃/h, and the third-stage pre-aging treatment: minimum temperature: at 20 ℃ for 7-10 days, and the cooling rate is 3.5 ℃/d. Then, the hardness changes in the multi-stage pre-aged state and the multi-stage pre-aged state +185 ℃/20min state, and the tensile properties in the pre-aged state and the 2% pre-stretched state +185 ℃/20min simulated paint-baked state were measured (as shown in tables 1 and 2).
Example 3
In the implementation, after the 6451 aluminum alloy is smelted, cast and homogenized, the aluminum alloy is subjected to hot rolling deformation, the hot rolling temperature is 500-570 ℃, the total hot rolling deformation is more than 90%, and the finish rolling temperature is more than 320 ℃, and the cooling rate is controlled to cool: the cooling rate is less than 10 ℃/h, and then cold rolling deformation is directly carried out: the total cold rolling deformation is 70-80%, and the pass reduction is 20-40%; then carrying out non-isothermal solution treatment on the steel: 20-545 ℃, the heating rate is 5-10 ℃/s, 545-575 ℃, the heating rate is 1-10 ℃/min, and the highest temperature is controlled at 550-575 ℃; directly carrying out slow quenching treatment after non-isothermal solution treatment: the cooling rate is less than 15 ℃/s; and finally, directly carrying out multistage pre-aging treatment on the quenched alloy plate: the first-stage pre-aging treatment: the maximum temperature is 110 ℃, the temperature rise time is 9-16 s, the temperature rise rate is 6 ℃/s, and the second-stage pre-aging treatment comprises the following steps: the initial maximum temperature of temperature reduction is 110 ℃, the final temperature is 60 ℃, the temperature reduction time is 25-33 h, the temperature reduction rate is 1.3 ℃/h, and the third-stage pre-aging treatment: minimum temperature: at 30 ℃ for 7-10 days, and the cooling rate is 3 ℃/d. Then, the hardness changes in the multi-stage pre-aged state and the multi-stage pre-aged state +185 ℃/20min state, and the tensile properties in the pre-aged state and the 2% pre-stretched state +185 ℃/20min simulated paint-baked state were measured (as shown in tables 1 and 2).
Example 4
In the implementation, 6451 aluminum alloy is subjected to hot rolling deformation after smelting, casting and homogenizing treatment, wherein the hot rolling temperature is 560 ℃, the total hot rolling deformation is more than 90%, and the finish rolling temperature is more than 320 ℃, and the cooling rate is controlled to cool: the cooling rate is less than 10 ℃/h, and then cold rolling deformation is directly carried out: the total deformation of cold rolling is 75 percent, and the pass reduction is 35 percent; then carrying out non-isothermal solution treatment: 20-545 ℃, the heating rate is 5-10 ℃/s, 545-575 ℃, the heating rate is 1-10 ℃/min, and the highest temperature is controlled at 550-575 ℃; directly carrying out slow quenching treatment after non-isothermal solution treatment: the cooling rate is less than 15 ℃/s; and finally, directly carrying out multistage pre-aging treatment on the quenched alloy plate: the first-stage pre-aging treatment: the highest temperature is 100 ℃, the temperature rise time is 9-16 s, the temperature rise rate is 5 ℃/s, and the secondary pre-aging treatment: the initial maximum temperature of cooling is 100 ℃, the final temperature is 30 ℃, the cooling time is 25-33 h, the cooling rate is 2 ℃/h, and the third-stage pre-aging treatment: temperature: the temperature is 10 ℃, the time is 7 to 10 days, and the cooling rate is 4 ℃/d. The hardness change was then measured in the multi-stage pre-aged state and in the multi-stage pre-aged state +185 ℃/20min state, as well as the tensile properties in the pre-aged state and in the 2% pre-stretched state +185 ℃/20min simulated paint-bake state (as shown in table 1, table 2 and figure 3).
Example 5
In the implementation, 6451 aluminum alloy is subjected to hot rolling deformation after smelting, casting and homogenizing treatment, wherein the hot rolling temperature is 560 ℃, the total hot rolling deformation is more than 90%, and the finish rolling temperature is more than 320 ℃, and the cooling rate is controlled to cool: the cooling rate is less than 10 ℃/h, and then cold rolling deformation is directly carried out: the total deformation of cold rolling is 75 percent, and the pass reduction is 35 percent; then carrying out non-isothermal solution treatment on the steel: 20-545 ℃, the heating rate is 5-10 ℃/s, 545-575 ℃, the heating rate is 1-10 ℃/min, and the highest temperature is controlled at 550-575 ℃; directly carrying out slow quenching treatment after non-isothermal solution treatment: the cooling rate is less than 15 ℃/s; and finally, directly carrying out multistage pre-aging treatment on the quenched alloy plate: the first-stage pre-aging treatment: the highest temperature is 90 ℃, the temperature rise time is 9-16 s, the temperature rise rate is 4 ℃/s, and the second-stage pre-aging treatment comprises the following steps: the initial maximum temperature of temperature reduction is 90 ℃, the final temperature is 50 ℃, the temperature reduction time is 37-41 h, the temperature reduction rate is 0.8 ℃/h, and the third-stage pre-aging treatment: minimum temperature: the temperature is controlled at 20 ℃ for 7-10 days, and the cooling rate is 3.5 ℃/d. The hardness changes in the multi-stage pre-aged state and the multi-stage pre-aged state +185 ℃/20min were then measured, as well as the tensile properties in the pre-aged state and the 2% pre-stretch +185 ℃/20min simulated paint-bake state (as shown in tables 1, 2).
Example 6
In the implementation, 6451 aluminum alloy is subjected to hot rolling deformation after smelting, casting and homogenizing treatment, wherein the hot rolling temperature is 560 ℃, the total hot rolling deformation is more than 90%, and the finish rolling temperature is more than 320 ℃, and the cooling rate is controlled to cool: the cooling rate is less than 10 ℃/h, and then cold rolling deformation is directly carried out: the total deformation of cold rolling is 75 percent, and the pass reduction is 35 percent; then carrying out non-isothermal solution treatment: 20-545 ℃, the heating rate is 5-10 ℃/s, 545-575 ℃, the heating rate is 1-10 ℃/min, and the highest temperature is controlled at 550-575 ℃; directly carrying out slow quenching treatment after non-isothermal solution treatment: the cooling rate is less than 15 ℃/s; and finally, directly carrying out multistage pre-aging treatment on the quenched alloy plate: the first-stage pre-aging treatment: the maximum temperature is 75 ℃, the temperature rise time is 9-16 s, the temperature rise rate is 3.5 ℃/s, and the secondary pre-aging treatment: the initial temperature of temperature reduction is 75 ℃, the final temperature is 50 ℃, the temperature reduction time is 33-36 h, the temperature reduction rate is 0.55 ℃/h, and the third-stage pre-aging treatment: minimum temperature: the temperature is 10 ℃, the time is 7 to 10 days, and the cooling rate is 4 ℃/d. The hardness changes in the multi-stage pre-aged state and the multi-stage pre-aged state +185 ℃/20min were then measured, as well as the tensile properties in the pre-aged state and the 2% pre-stretch +185 ℃/20min simulated paint-bake state (as shown in tables 1, 2).
Example 7
In the implementation, 6451 aluminum alloy is subjected to hot rolling deformation after smelting, casting and homogenizing treatment, wherein the hot rolling temperature is 560 ℃, the total hot rolling deformation is more than 90%, and the finish rolling temperature is more than 320 ℃, and the cooling rate is controlled to cool: the cooling rate is less than 10 ℃/h, and then cold rolling deformation is directly carried out: the total deformation of cold rolling is 75 percent, and the pass reduction is 35 percent; then carrying out non-isothermal solution treatment on the steel: 20-545 ℃, the heating rate is 5-10 ℃/s, 545-575 ℃, the heating rate is 1-10 ℃/min, and the highest temperature is controlled at 550-575 ℃; directly carrying out slow quenching treatment after non-isothermal solution treatment: the cooling rate is less than 15 ℃/s; and finally, directly carrying out multistage pre-aging treatment on the quenched alloy plate: first-stage pre-aging treatment: the maximum temperature is 60 ℃, the temperature rise time is 9-16 s, the temperature rise rate is 3 ℃/s, and the second-stage pre-aging treatment comprises the following steps: the initial maximum temperature of cooling is 60 ℃, the final temperature is 50 ℃, the cooling time is 25-33 h, the cooling rate is 0.34 ℃/h, and the third-stage pre-aging treatment: minimum temperature: the temperature is 10 ℃, the time is 7 to 10 days, and the cooling rate is 4 ℃/d. Then, DSC characterization is carried out on the alloy in a solid solution state and a slow quenching state to analyze the precipitation behavior (shown in figure 1). Meanwhile, the hardness change conditions of the multi-stage pre-aged state and the multi-stage pre-aged state +185 ℃/20min state are measured, and the tensile properties of the pre-aged state and the 2% pre-stretching +185 ℃/20min simulated paint-baking state are measured (as shown in table 1, table 2 and figure 4).
TABLE 1 hardness and conductivity of 6451 aluminum alloy after multistage Pre-aging treatment and after simulated paint bake condition
Comparative example 1
The comparative example (CN 108884524A) provides a processing method for improving the performance of an Al-Mg-Si (Mg + Si > 1.2%) aluminum alloy plate, which adopts a high temperature of 100-300 ℃ for short time of 5-300 seconds, then at a low temperature of 30-50 ℃ for long time of 5-500 hours, and the yield strength increment after baking finish corresponding to 6451 alloy components is shown in Table 2.
Comparative example 2
The comparative example (CN 101885000A) provides a processing method for improving the performance of a6111 aluminum alloy plate, solid solution at 550 ℃ is adopted for heat preservation for 7min, water quenching is adopted, heat preservation is carried out for 4-15min in a temperature range of 150-220 ℃, the purposes that the yield strength is low before stamping and the yield strength reaches a normal level after paint baking are achieved, and the yield strength increment after paint baking is shown in a table 2.
TABLE 2 mechanical properties of 6451 aluminium alloy after multistage pre-ageing treatment and after simulated paint-baking
According to the results of examples 1-7, it can be found that, after the 6451 aluminum alloy is subjected to non-isothermal solution treatment and slow quenching treatment, if DSC analysis is carried out on the alloy, a solute atom cluster precipitation peak does not appear in the low-temperature region of the alloy, which indicates that the vacancy concentration is effectively controlled, and the method is very beneficial to effectively inhibiting the deteriorating effect of natural aging of the alloy on the improvement of the hardening increment of the alloy baking varnish. In addition, if the first-stage and second-stage temperatures in the multi-stage low-temperature pre-aging process are higher, the strength of the alloy in a pre-aging state is higher, although the alloy has better natural aging stability, the corresponding baking varnish hardening increment of the alloy plate is obviously reduced. As the coordinated control of solute atom clusters by slow rate quenching and low temperature pre-aging as contemplated by the present invention, the 6451 alloy, as controlled by the process of example 7, exhibited the best bake hardening increments, all higher than the bake hardening increments corresponding to other temperatures. Therefore, the 6451 aluminum alloy can obtain reasonable regulation and control of solute atom clusters only by comprehensively designing and regulating a plurality of non-isothermal processes, and the formed multi-scale solute atom clusters can be kept stable in the natural placing process and can also grow rapidly in the baking finish process to enable the alloy to show excellent high baking finish hardening characteristics.
In conclusion, the invention comprehensively regulates and controls precipitation phase redissolution, solute atom cluster formation and distribution by integrating multiple processes of hot working, solid solution, slow quenching and multi-stage low-temperature pre-aging of the 6451 aluminum alloy, so that the alloy shows excellent baking finish hardening increment and natural aging resistance stability. This is very beneficial to reduce the production cost of the series of alloys, and has a positive effect on accelerating the wide application of the series of alloys. Therefore, the treatment process is not only suitable for being widely applied to manufacturing of Al-Mg-Si series alloy plates for automobiles, so that the process of aluminum alloy for light weight of automobiles is accelerated, but also has certain guiding significance on development, processing and application of aluminum alloy with quick aging response and special requirements on natural stability in other fields, and is worthy of being emphasized by automobile manufacturers and aluminum alloy processing enterprises, so that the aluminum alloy can be popularized and applied in the field as soon as possible.
It should be understood by those skilled in the art that the above embodiments are only for illustrating the present invention and are not to be used as a limitation of the present invention, and that changes and modifications to the above described embodiments are within the scope of the claims of the present invention as long as they are within the spirit and scope of the present invention.
Claims (10)
1. A low-temperature pre-aging treatment method for improving hardening increment of 6451 aluminum alloy baking varnish is characterized by comprising the following steps of:
(1) After homogenizing the alloy cast ingot, carrying out hot rolling treatment, cooling and cold rolling treatment to obtain a cold-rolled sheet;
(2) Carrying out non-isothermal solid solution treatment and slow quenching treatment on the cold-rolled sheet in sequence, wherein in the process of the slow quenching treatment, the cooling rate is less than 20 ℃/s;
(3) And (3) performing multistage pre-aging treatment on the cold-rolled sheet treated in the step (2) to obtain 6451 aluminum alloy with high baking finish hardening increment.
2. A low temperature pre-ageing treatment process for increasing the hardening increment of 6451 aluminium alloy stoving varnish according to claim 1, wherein in step (1):
in the hot rolling treatment process, the hot rolling temperature is controlled to be 500-570 ℃, the finishing temperature is more than 300 ℃, and the total deformation of hot rolling is more than 90%; and/or
In the cooling process, the cooling rate is controlled to be less than 10 ℃/h; and/or
In the cold rolling treatment process, the pass reduction is controlled to be 20-70%, and the total cold rolling deformation is controlled to be 70-90%.
3. A low temperature pre-ageing treatment process for increasing the hardening increment of 6451 aluminium alloy stoving varnish according to claim 2, wherein in step (1):
in the hot rolling treatment process, the finishing temperature is more than 320 ℃; and/or
In the cold rolling treatment process, one-way rolling is adopted, the pass reduction is controlled to be 20-40%, and the total cold rolling deformation is controlled to be 70-80%.
4. The low temperature pre-aging treatment method for increasing hardening increment of 6451 aluminum alloy baking varnish according to claim 1, wherein in the step (2): in the non-isothermal solution treatment process, the highest temperature of the cold-rolled sheet is 550-575 ℃; when the temperature of the cold-rolled sheet is in the range of 20-545 ℃, controlling the heating rate to be 5-13 ℃/s; when the temperature of the cold-rolled sheet is in the range of 545-575 ℃, controlling the heating rate to be 1-13 ℃/min; and/or
In the process of the slow quenching treatment, the cooling rate is less than 15 ℃/s.
5. The low temperature pre-aging treatment method for increasing the hardening increment of 6451 aluminum alloy baking varnish according to claim 4, wherein in the step (2): in the non-isothermal solution treatment process, the highest temperature of the cold-rolled sheet is 550-575 ℃; when the temperature of the cold-rolled sheet is within the range of 20-545 ℃, the heating rate is 5-10 ℃/s; when the temperature of the cold-rolled sheet is in the range of 545-575 ℃, the heating rate is 1-10 ℃/min.
6. The low-temperature pre-aging treatment method for increasing the hardening increment of 6451 aluminum alloy baking varnish according to claim 1, wherein in the step (3), the multi-stage pre-aging treatment process comprises a first-stage pre-aging treatment, a second-stage pre-aging treatment and a third-stage pre-aging treatment, the maximum temperature of the first-stage pre-aging treatment is 60-120 ℃, and the temperature rise time is 9-20 s; the lowest temperature of the second-stage pre-aging treatment is 30-60 ℃, and the cooling time is 25-42 h; the minimum temperature of the third-stage pre-aging treatment is 10-30 ℃, and the cooling time is 7-10 days.
7. The low temperature pre-aging treatment method for increasing hardening increment of 6451 aluminum alloy baking varnish according to claim 6, wherein in the step (3):
in the first-stage pre-aging treatment, the highest temperature is 60-112 ℃, and the temperature rise time is 9-16 s; and/or
In the second-stage pre-aging treatment, the minimum temperature is 30-50 ℃, and the cooling time is 26-41 h.
8. An 6451 aluminum alloy material for an automobile, which is characterized in that the 6451 aluminum alloy material for an automobile is prepared by the low-temperature pre-aging treatment method for improving the hardening increment of 6451 aluminum alloy baking varnish according to any one of claims 1 to 7.
9. An 6451 aluminium alloy material for automobile according to claim 8, wherein the hardness of the 6451 aluminium alloy material is 65 to 90HV, and the baking varnish hardening increment is 10 to 30HV.
10. The 6451 aluminum alloy material for automobile according to claim 8, wherein the elongation of the 6451 aluminum alloy material is 15 to 25%, the yield strength is 85 to 160MPa, and the tensile strength is 175 to 260MPa; and/or
After 2 percent of prestretching and aging treatment of simulating a paint baking state under the condition of 185 ℃/20min, the yield strength of the 6451 aluminum alloy is 200-240 MPa, and the tensile strength is 250-320 MPa.
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| JP2007262484A (en) * | 2006-03-28 | 2007-10-11 | Kobe Steel Ltd | Method for producing 6000 series aluminum alloy sheet for automobile panel excellent in hem bendability and bake hardenability |
| CN103757507A (en) * | 2014-02-25 | 2014-04-30 | 北京科技大学 | High baking varnish hardening aluminum alloy material for external car body plate and preparation method thereof |
| CN104018040A (en) * | 2014-06-23 | 2014-09-03 | 北京科技大学 | Automotive high-formability aluminum alloy material and preparation method thereof |
| CN108251712A (en) * | 2018-03-06 | 2018-07-06 | 东北大学 | A kind of preparation method of 6111 aluminum alloy plate materials of body of a motor car |
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