CN115874122B - Low-temperature pre-ageing treatment method for improving baking varnish hardening increment of 6451 aluminum alloy - Google Patents
Low-temperature pre-ageing treatment method for improving baking varnish hardening increment of 6451 aluminum alloy Download PDFInfo
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Abstract
The invention discloses a low-temperature pre-ageing treatment method for improving a 6451 aluminum alloy baking varnish hardening increment, which comprises the following steps of: after homogenizing treatment, carrying out hot rolling treatment, cooling and cold rolling treatment on the alloy ingot to obtain a cold-rolled sheet; sequentially carrying out non-isothermal solution treatment and slow quenching treatment on the cold-rolled sheet, wherein the cooling rate is less than 20 ℃/s in the slow quenching treatment process; then carrying out multistage pre-ageing treatment to obtain the 6451 aluminum alloy with high baking varnish hardening increment. The 6451 aluminum alloy treated by the method has excellent baking varnish hardening increment and natural aging resistance stability, 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-ageing treatment method for improving a baking finish hardening increment of 6451 aluminum alloy, which is particularly suitable for improving the baking finish hardening increment of 6xxx aluminum alloy (namely Al-Mg-Si alloy).
Background
With the continuous increase of the number of automobiles, the air pollution and the climate condition are continuously worsened, and the awareness of the world to energy conservation and emission reduction is continuously enhanced. Therefore, how to realize the light weight of the automobile and further achieve the purposes of energy conservation and emission reduction has become a key problem for further development in the automobile field; the aluminum alloy has become a key material for light weight of new generation automobiles due to the advantages of light weight, corrosion resistance, high specific strength, easy processing and the like. In comparison, 6xxx series aluminum alloys (i.e., al-Mg-Si series alloys) among several large series of aluminum alloys have better overall properties and have significant advantages, such as: the alloy has the advantages of heat treatment strengthening, good corrosion resistance, good weldability, easy surface coloring and good formability, and more importantly, the alloy generally has higher baking finish hardening property (namely, the strength of a painted formed part is further greatly improved by baking finish treatment, so that an alloy plate has better dent resistance), and all the advantages make the alloy very suitable for being applied to the processing of automobile body outer plates, and the alloy with a plurality of brands has been widely applied at present, such as AA6016, AA6111, AA6022 and the like.
In order to improve the baking finish hardening increment and the natural aging stability of the 6xxx aluminum alloy, the scientific workers at home and abroad propose the adjustment and control of the pre-aging after solid solution, and the baking finish hardening increment and the natural aging stability of the alloy after adjustment and control are improved to a certain extent, but the effect is still not particularly satisfactory, and further intensive research is still needed. For the 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, which is favorable for better regulating and controlling precipitation phase precipitation, particularly, after the quenching rate is reduced after solid solution, a large amount of Si phase is not precipitated at the grain boundary of the alloy, which is favorable for subsequent better process regulation and control on formation of solute atomic clusters, and the deterioration effect of natural aging can be obviously reduced in the follow-up process due to the reduction of the quenching rate. In addition, in order to reduce the production cost, if the pre-ageing treatment temperature can be sufficiently reduced, or the waste heat of the plate is sufficiently utilized to perform low-temperature pre-ageing treatment, and the solute atomic cluster composition, morphology, 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 finish hardening increment is maintained, and the method has great significance for wide application of the alloy in the automobile light-weight process.
Considering the interaction and influence of the solution quenching process and the pre-ageing process of the alloy, in order to be able to reduce the pre-ageing treatment temperature, the solution and quenching processes, in particular the strict control of the quenching process, must be effectively controlled; 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 in the subsequent pre-ageing treatment process to promote the effective formation and reasonable distribution of the solute atom clusters in the low-temperature pre-ageing process, and simultaneously can effectively reduce the vacancy concentration, so that the alloy can subsequently show excellent natural ageing resistance stability. However, these process influencing factors are complex, and the difficulty of realizing multi-process coupling to regulate and control the formation and distribution of solute atomic clusters is high. Therefore, how to perform the coupling effects of hot working, solid solution, slow quenching and multistage low-temperature pre-ageing, reasonably control the size, shape and distribution of multi-scale and multi-type solute atom clusters, and have important key effects on greatly improving the baking finish hardening increment and the natural ageing resistance stability of the alloy and simultaneously effectively reducing the actual production cost of the alloy.
Currently, the related patents mainly relate to solid solution and pre-aging heat treatment processes, including CN108884524A, CN101885000A, CN101168828A and the like.
The patent number CN108884524A provides a processing method for improving the performance of Al-Mg-Si (Mg+Si > 1.2%) aluminum alloy plates, which adopts high temperature of 100-300 ℃ for 5 seconds-300 seconds, then low temperature of 30-50 ℃ for 5-500 hours, thereby improving the baking varnish hardening strength of the material and finally reaching the maximum baking varnish increment of 92MPa.
The patent number is CN101885000A, after the 6111 aluminum alloy plate is subjected to solid solution heat preservation at 550 ℃ for 7min and water quenching, the heat preservation is carried out for 4-15min in a temperature range of 150-220 ℃, and the purposes that the yield strength is lower before stamping and reaches the normal level after paint baking are achieved.
The patent number CN101168828A provides a method for improving the strength of 6022 aluminum alloy plates after baking varnish, which adopts a pre-ageing treatment process of heat preservation 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 higher yield strength of more than 200MPa after baking varnish.
The prior art adopts the conventional high-temperature short-time or low-temperature long-time pre-ageing technology to carry out heat treatment on the Al-Mg-Si alloy so as to improve the strength of the material after baking, so that the strength increment of the developed plate performance after baking is not ideal, and the requirements of aluminum for automobiles on the high formability and the high baking 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-ageing treatment method for improving the baking varnish hardening increment of 6451 aluminum alloy, which fully utilizes the waste heat in hot rolling, firstly regulates and controls the size and distribution of Mg-Si precipitated phases in an aluminum alloy matrix to be in a proper scale, and the precipitated phases not only can effectively influence the dislocation proliferation condition in the subsequent cold rolling process, but also can increase dislocation to a proper degree, thereby promoting the dissolution of the precipitated phases in a 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 separated out from the alloy matrix while the alloy matrix is in a supersaturated solid solution, and further the 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-ageing process during the subsequent pre-ageing treatment; in addition, the vacancy concentration can be effectively reduced, so that the aluminum alloy can simultaneously have high baking finish hardening increment while the aluminum alloy can subsequently show excellent natural aging stability resistance.
In order to achieve the above purpose, the invention adopts the following technical scheme:
the first aspect of the invention provides a low-temperature pre-ageing treatment method for improving the baking varnish hardening increment of 6451 aluminum alloy, which comprises the following steps of:
(1) After homogenizing treatment, carrying out hot rolling treatment, cooling and cold rolling treatment on the alloy ingot to obtain a cold-rolled sheet;
(2) Sequentially carrying out non-isothermal solution treatment and slow quenching treatment on the cold-rolled sheet, wherein the cooling rate is less than 20 ℃/s in the slow quenching treatment process;
(3) And (3) carrying out multistage pre-ageing treatment on the cold-rolled sheet treated in the step (2) to obtain the 6451 aluminum alloy with high baking varnish hardening increment.
Preferably, in the step (1):
in the hot rolling treatment process, the hot rolling temperature is controlled to be 500-570 ℃, the final rolling temperature is more than 300 ℃, and the total hot rolling deformation is more than 90%; and/or
In the cooling process, controlling the cooling rate to be less than 10 ℃/h; and/or
In the cold rolling treatment process, the rolling reduction of the pass is controlled to be 20-70%, and the total deformation of the cold rolling 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, unidirectional rolling is adopted, the pass reduction is controlled to be 20-40%, and the total cold rolling deformation is 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 within the range of 20-545 ℃, controlling the temperature rising rate to be 5-13 ℃/s; when the temperature of the cold-rolled sheet is within the range of 545-580 ℃, controlling the temperature rising rate to be 1-13 ℃/min; and/or
In the slow quenching treatment process, 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 in the range of 20-545 ℃, the heating rate is 5-10 ℃/s; when the temperature of the cold-rolled sheet is within the range of 545-575 ℃, the heating rate is 1-10 ℃/min.
Preferably, the multistage pre-ageing treatment process comprises a first stage pre-ageing treatment, a second stage pre-ageing treatment and a third stage pre-ageing treatment, wherein the highest temperature of the first stage pre-ageing treatment is 60-120 ℃, and the heating time is 9-20 s; the lowest temperature of the second-stage pre-ageing treatment is 30-60 ℃, and the cooling time is 25-42 h; the lowest temperature of the third-stage pre-ageing treatment is 10-40 ℃, and the cooling time is 7-10 days.
Preferably, in the step (3):
in the first-stage pre-ageing treatment, the highest temperature is 60-112 ℃ and the heating time is 9-16 s; and/or
In the second-stage pre-ageing treatment, the minimum temperature is 30-50 ℃, and the cooling time is 26-41 h.
The invention provides a 6451 aluminum alloy material for an automobile, which is prepared by adopting the low-temperature pre-ageing treatment method for improving the baking varnish hardening increment of the 6451 aluminum alloy.
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 the 6451 aluminum alloy is subjected to 2% pre-stretching and ageing treatment in a simulated baking finish state under the condition of 185 ℃/20min, the yield strength is 200-240 MPa, and the tensile strength is 250-320 MPa.
The low-temperature pre-ageing treatment method for improving the baking varnish hardening increment of the 6451 aluminum alloy has the following beneficial effects:
1. the low-temperature pre-ageing treatment method for improving the baking finish hardening increment of the 6451 aluminum alloy fully utilizes the waste heat of the aluminum alloy matrix to perform low-temperature pre-ageing treatment, reduces the pre-ageing treatment temperature, can effectively control the solute atomic cluster composition, morphology, size and distribution characteristics in the 6451 aluminum alloy matrix, and ensures that the alloy has lower production cost while keeping higher baking finish hardening increment and natural ageing resistance stability;
2. according to the low-temperature pre-ageing treatment method for improving the baking varnish hardening increment of the 6451 aluminum alloy, waste heat during hot rolling is fully utilized, firstly, the size and the distribution of Mg-Si precipitated phases in an aluminum alloy matrix are regulated and controlled to be in proper scales, the precipitated phases not only can effectively influence the dislocation proliferation condition in the subsequent cold rolling process, but also can increase dislocation to proper degrees, and then the redissolution of the precipitated phases in a low-temperature stage is promoted 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 separated out from the alloy matrix while the alloy matrix is in a supersaturated solid solution, and further the 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-ageing process during the subsequent pre-ageing treatment; in addition, the vacancy concentration can be effectively reduced, so that the aluminum alloy can simultaneously have high baking finish hardening increment while the aluminum alloy can subsequently show excellent natural aging stability resistance;
3. the invention not only can lead 6451 aluminum alloy plate to show excellent baking finish hardening increment and natural aging resistance stability after thermal processing, solid solution, slow quenching and multistage low-temperature pre-aging coupling regulation and control, but also fully utilizes waste heat to reduce the actual production cost of the alloy plate;
4. the low-temperature pre-ageing treatment method for improving the baking varnish hardening increment of the 6451 aluminum alloy is very suitable for processing and producing aluminum alloy materials for automobiles and producing other aluminum alloy materials with specific requirements on the distribution state of precipitated phases and solute atomic clusters, and is also suitable for other technical industries with higher requirements on the organization and comprehensive performance of other series of aluminum alloy materials.
Drawings
Other features, objects and advantages of the present invention will become more apparent upon reading of the detailed description of non-limiting embodiments, given with reference to the accompanying drawings in which:
FIG. 1 is a DSC analysis curve of a 6451 aluminum alloy prepared in example 1 of the present invention after non-isothermal solid solution and slow quench;
FIG. 2 is a strain curve simulating the bake hardening behavior of the 6451 aluminum alloy prepared in example 1;
FIG. 3 is a strain curve simulating the bake hardening behavior of the 6451 aluminum alloy prepared in example 4;
fig. 4 is a strain curve simulating bake hardening behavior for the 6451 aluminum alloy prepared in example 7.
Detailed Description
In order to better understand the above technical solution of the present invention, the technical solution of the present invention is further described below with reference to examples.
With the acceleration of automobile weight reduction, higher requirements are put on the production cost and baking finish hardening increment of 6xxx series aluminum alloys for automobile body outer plates. Although some 6xxx aluminum alloys, such as 6016, 6111, 6022, have found widespread use, the manufacturing process is still not reasonable enough, not only is the cost of production higher, but the overall properties still remain to be further improved. Therefore, it is highly necessary to select an alloy of a specific composition for the widely used 6xxx aluminum alloy, and develop process control and optimization studies, so that the baking finish hardening increment and the natural aging stability of the alloy are further improved. It is considered that the bake hardening enhancement and the natural aging resistance are mainly related to the formation and growth of a precipitated phase, and the process is closely related to the prior hot working process, the solid solution and quenching modes, and the like besides the subsequent pre-aging process. Therefore, if the homogenized alloy ingot can be directly hot rolled, and then the waste heat is utilized to carry out annealing treatment, on one hand, the dislocation density of the alloy is effectively regulated and controlled, the subsequent cold rolling deformation is facilitated, and on the other hand, the size of a precipitated 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 dissolved back when being subjected to non-isothermal solution treatment, and can also preferentially stimulate recrystallization nucleation around the precipitated phase, so that the alloy structure is optimized. After solution treatment, the concentration of vacancies in the alloy matrix is further reduced by controlling the cooling rate, and then multistage low-temperature pre-ageing regulation is adopted, so that multi-scale solute atom clusters with reasonable constitution, size, morphology 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 ageing process is reduced. Therefore, if multi-scale solute atom clusters can be formed in the alloy matrix through the process, the alloy matrix can show excellent baking finish hardening increment after being subjected to stamping forming and baking finish hardening treatment, and meanwhile, the baking finish hardening increment of the alloy plate subjected to the multi-stage low-temperature pre-ageing treatment is not obviously reduced even if the alloy plate is naturally placed for a long time, and the alloy plate shows excellent natural ageing stability resistance.
The invention provides a low-temperature pre-ageing treatment method for improving the baking varnish hardening increment of 6451 aluminum alloy, which comprises the following steps of:
(1) After homogenizing treatment, carrying out hot rolling treatment, cooling and cold rolling treatment on the 6451 aluminum alloy cast ingot 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; smelting and casting to obtain 6451 aluminum alloy cast ingot, homogenizing the 6451 aluminum alloy cast ingot, and then carrying out hot rolling treatment to obtain a hot rolled plate, wherein the rolling temperature is 500-570 ℃, the final rolling temperature is more than 300 ℃, the total deformation of hot rolling 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 performing cold rolling treatment, wherein the pass reduction is 20-70%, the total cold rolling deformation is 70-90%, and 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) Sequentially carrying out non-isothermal solution treatment and slow quenching treatment on the cold-rolled sheet;
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 20-545 ℃, and the heating rate is controlled to be 1-13 ℃/min when the temperature of the cold-rolled sheet is 545-580 ℃; in a further preferred embodiment, the maximum temperature of the cold-rolled sheet is 550 to 575 ℃ during the non-isothermal solution treatment, the heating rate is 5 to 10 ℃/s when the temperature of the cold-rolled sheet is 20 to 545 ℃, and the heating rate is 1 to 10 ℃/min when the temperature of the cold-rolled sheet is 545 to 575 ℃. 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) carrying out multistage pre-ageing treatment on the cold-rolled sheet treated in the step (2) to obtain the 6451 aluminum alloy with high baking varnish hardening increment.
The specific process is as follows: directly carrying out multistage low-temperature pre-ageing treatment on the cold-rolled sheet subjected to slow quenching treatment to obtain 6451 aluminum alloy with high baking varnish hardening increment, wherein in the specific treatment process, the multistage pre-ageing treatment process comprises a first-stage pre-ageing treatment, a second-stage pre-ageing treatment and a third-stage pre-ageing treatment, wherein the first-stage pre-ageing 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-ageing 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-ageing 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-ageing treatment process 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-ageing treatment is a cooling process, the minimum 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.
The alloy plate developed through the multi-process comprehensive regulation and control, especially the slow quenching after non-isothermal solution treatment and the low-temperature multistage pre-ageing cooperative regulation and control, can be ensured to have excellent baking finish hardening increment and natural ageing resistance stability. The high baking varnish hardening increment 6451 aluminum alloy prepared by the treatment has the hardness of 65-90 HV and the baking varnish hardening increment of 10-30 HV. The elongation percentage of the 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 the 6451 aluminum alloy with high baking varnish hardening increment is subjected to 2% pre-stretching and ageing treatment in a baking varnish simulation state at 185 ℃/20min, the yield strength is 200-240 MPa, and the tensile strength is 250-320 MPa.
The low temperature pre-ageing treatment method for improving the baking varnish hardening increment of the 6451 aluminum alloy is further described below with specific examples; in the following examples, the 6451 aluminum alloy comprises the following components 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 smelting, casting and homogenizing treatment, the 6451 aluminum alloy is subjected to hot rolling deformation, the hot rolling temperature is 500-570 ℃, the total hot rolling deformation is more than 90%, the final rolling temperature is more than 320 ℃, and the hot rolled plate is cooled by controlling the cooling rate: the cooling rate is less than 10 ℃/h, and then cold rolling deformation is directly carried out: the total deformation of cold rolling is 70-80%, and the pass reduction is 20-40%; then non-isothermal solution treatment is carried out on the mixture: the temperature rising rate of 20-545 ℃ is 5-10 ℃/s, 545-575 ℃, the temperature rising 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; finally, directly carrying out multistage pre-ageing treatment on the quenched alloy plate: first-stage pre-ageing treatment: the highest temperature is 120 ℃, the heating time is 9-16 s, and the heating rate is 8 ℃/s; and (3) second-stage pre-ageing treatment: the initial 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-ageing treatment: minimum temperature: the temperature is 10 ℃ for 7 to 10 days, and the cooling rate is 4 ℃/d. The alloy solid solution and slow quenching state alloy is then subjected to DSC characterization analysis to analyze the precipitation behavior (shown in figure 1). Meanwhile, the hardness change conditions of the multistage pre-ageing state and the multistage pre-ageing state +185 ℃/20min state, and the tensile properties of the pre-ageing state and the 2% pre-stretching +185 ℃/20min simulation baking finish state were measured (as shown in tables 1, 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, the hot rolling temperature is 560 ℃, the total deformation of hot rolling is more than 90%, the final rolling temperature is more than 320 ℃, and the cooling rate is controlled to cool the hot rolled plate: the cooling rate is less than 10 ℃/h, and then cold rolling deformation is directly carried out: cold rolling total deformation amount is 75%, pass reduction amount is 20% -40%; then non-isothermal solution treatment is carried out on the mixture: the temperature rising rate of 20-545 ℃ is 5-10 ℃/s, 545-575 ℃, the temperature rising 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; finally, directly carrying out multistage pre-ageing treatment on the quenched alloy plate: first-stage pre-ageing treatment: the highest temperature is 112 ℃, the heating time is 9-16 s, the heating rate is 8 ℃/s, and the second-stage pre-ageing treatment is carried out: the initial 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-ageing treatment is carried out: minimum temperature: the temperature is 20 ℃ for 7-10 days, and the cooling rate is 3.5 ℃/d. The hardness change in the multi-stage pre-ageing state and the multi-stage pre-ageing state +185 ℃/20min state, and the tensile properties of the pre-ageing state and the 2% pre-stretching +185 ℃/20min simulated stoving varnish state were then measured (as shown in tables 1, 2).
Example 3
In the implementation, after smelting, casting and homogenizing treatment, the 6451 aluminum alloy is subjected to hot rolling deformation, the hot rolling temperature is 500-570 ℃, the total hot rolling deformation is more than 90%, the final rolling temperature is more than 320 ℃, and the hot rolled plate is cooled by controlling the cooling rate: the cooling rate is less than 10 ℃/h, and then cold rolling deformation is directly carried out: the total deformation of cold rolling is 70-80%, and the pass reduction is 20-40%; then non-isothermal solution treatment is carried out on the mixture: 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; finally, directly carrying out multistage pre-ageing treatment on the quenched alloy plate: first-stage pre-ageing treatment: the highest temperature is 110 ℃, the heating time is 9-16 s, the heating rate is 6 ℃/s, and the second-stage pre-ageing treatment is carried out: the initial temperature of cooling is 110 ℃, the final temperature is 60 ℃, the cooling time is 25-33 h, the cooling rate is 1.3 ℃/h, and the third-stage pre-ageing treatment is carried out: minimum temperature: the temperature is 30 ℃ for 7-10 days, and the cooling rate is 3 ℃/d. The hardness change in the multi-stage pre-ageing state and the multi-stage pre-ageing state +185 ℃/20min state, and the tensile properties of the pre-ageing state and the 2% pre-stretching +185 ℃/20min simulated stoving varnish state were then measured (as shown in tables 1, 2).
Example 4
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, the hot rolling temperature is 560 ℃, the total deformation of hot rolling is more than 90%, the final rolling temperature is more than 320 ℃, and the cooling rate is controlled to cool the hot rolled plate: the cooling rate is less than 10 ℃/h, and then cold rolling deformation is directly carried out: cold rolling total deformation amount is 75%, pass reduction amount is 35%; then non-isothermal solution treatment is carried out on the mixture: 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; finally, directly carrying out multistage pre-ageing treatment on the quenched alloy plate: first-stage pre-ageing treatment: the highest temperature is 100 ℃, the heating time is 9-16 s, the heating rate is 5 ℃/s, and the second-stage pre-ageing treatment is carried out: the initial 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-ageing treatment is carried out: temperature: the temperature is 10 ℃ and the time is 7-10 days, and the cooling rate is 4 ℃/d. The hardness change in the multi-stage pre-ageing state and the multi-stage pre-ageing state +185 c/20 min state, and the tensile properties of the pre-ageing state and 2% pre-stretching +185 c/20 min simulated stoving varnish state were then measured (as shown in table 1, table 2 and figure 3).
Example 5
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, the hot rolling temperature is 560 ℃, the total deformation of hot rolling is more than 90%, the final rolling temperature is more than 320 ℃, and the cooling rate is controlled to cool the hot rolled plate: the cooling rate is less than 10 ℃/h, and then cold rolling deformation is directly carried out: cold rolling total deformation amount is 75%, pass reduction amount is 35%; then non-isothermal solution treatment is carried out on the mixture: 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; finally, directly carrying out multistage pre-ageing treatment on the quenched alloy plate: first-stage pre-ageing treatment: the highest temperature is 90 ℃, the heating time is 9-16 s, the heating rate is 4 ℃/s, and the second-stage pre-ageing treatment is carried out: the initial temperature of cooling is 90 ℃, the final temperature is 50 ℃, the cooling time is 37-41 h, the cooling rate is 0.8 ℃/h, and the third-stage pre-ageing treatment is carried out: minimum temperature: the temperature is 20 ℃ for 7-10 days, and the cooling rate is 3.5 ℃/d. The hardness change in the multi-stage pre-ageing state and the multi-stage pre-ageing state +185 ℃/20min state, and the tensile properties of the pre-ageing state and the 2% pre-stretching +185 ℃/20min simulated stoving varnish state were then measured (as shown in tables 1, 2).
Example 6
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, the hot rolling temperature is 560 ℃, the total deformation of hot rolling is more than 90%, the final rolling temperature is more than 320 ℃, and the cooling rate is controlled to cool the hot rolled plate: the cooling rate is less than 10 ℃/h, and then cold rolling deformation is directly carried out: cold rolling total deformation amount is 75%, pass reduction amount is 35%; then non-isothermal solution treatment is carried out on the mixture: 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; finally, directly carrying out multistage pre-ageing treatment on the quenched alloy plate: first-stage pre-ageing treatment: the highest temperature is 75 ℃, the heating time is 9-16 s, the heating rate is 3.5 ℃/s, and the second-stage pre-ageing treatment is carried out: the initial temperature of cooling is 75 ℃, the final temperature is 50 ℃, the cooling time is 33-36 h, the cooling rate is 0.55 ℃/h, and the third-stage pre-ageing treatment is carried out: minimum temperature: the temperature is 10 ℃ and the time is 7-10 days, and the cooling rate is 4 ℃/d. The hardness change in the multi-stage pre-ageing state and the multi-stage pre-ageing state +185 ℃/20min state, and the tensile properties of the pre-ageing state and the 2% pre-stretching +185 ℃/20min simulated stoving varnish state were then measured (as shown in tables 1, 2).
Example 7
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, the hot rolling temperature is 560 ℃, the total deformation of hot rolling is more than 90%, the final rolling temperature is more than 320 ℃, and the cooling rate is controlled to cool the hot rolled plate: the cooling rate is less than 10 ℃/h, and then cold rolling deformation is directly carried out: cold rolling total deformation amount is 75%, pass reduction amount is 35%; then non-isothermal solution treatment is carried out on the mixture: 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; finally, directly carrying out multistage pre-ageing treatment on the quenched alloy plate: first-stage pre-ageing treatment: the highest temperature is 60 ℃, the heating time is 9-16 s, the heating rate is 3 ℃/s, and the second-stage pre-ageing treatment is carried out: the initial 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-ageing treatment is carried out: minimum temperature: the temperature is 10 ℃ and the time is 7-10 days, and the cooling rate is 4 ℃/d. The alloy solid solution and slow quenching state alloy is then subjected to DSC characterization analysis to analyze the precipitation behavior (shown in figure 1). Meanwhile, the hardness change conditions of the multistage pre-ageing state and the multistage pre-ageing state +185 ℃/20min state, and the tensile properties of the pre-ageing state and the 2% pre-stretching +185 ℃/20min simulation baking finish state were measured (as shown in tables 1, 2 and fig. 4).
Table 1 6451 hardness and conductivity of aluminum alloy after multistage pre-ageing treatment and after simulation of the paint state
Comparative example 1
The present comparative example (CN 108884524 a) provides a processing method for improving the performance of Al-Mg-Si (mg+si > 1.2%) aluminum alloy sheet, which uses high temperature of 100 ℃ to 300 ℃ for 5 seconds to 300 seconds, then low temperature of 30 ℃ to 50 ℃ for 5 hours to 500 hours, and the increment of yield strength after baking paint corresponding to 6451 alloy composition is shown in table 2.
Comparative example 2
The comparative example (CN 101885000A) provides a processing method for improving the performance of 6111 aluminum alloy plates, which adopts 550 ℃ solution heat preservation for 7min and water quenching, and then keeps the temperature in a temperature range of 150-220 ℃ for 4-15min, so that the aluminum alloy plates have lower yield strength before stamping and reach the purpose of normal level of yield strength after baking, and the yield strength increment after baking is shown in Table 2.
Table 2 mechanical Properties of the 6451 aluminum alloy after Multi-stage Pre-aging treatment and after simulation of the paint baking State
From 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 performed on the 6451 aluminum alloy, it can be seen that solute atom cluster precipitation peaks do not appear in a low-temperature zone of the alloy, which proves that the vacancy concentration is effectively controlled, and the deterioration effect of the increase of hardening increment of Jin Kaoqi due to natural aging of the alloy is effectively inhibited. In addition, if the temperatures of the first stage and the second stage in the multistage low-temperature pre-ageing process are higher, the pre-ageing state alloy has higher strength, and the alloy has better natural ageing resistance stability at the moment, but the baking varnish hardening increment corresponding to the alloy plate is obviously reduced. As contemplated by the present invention, the 6451 alloy, which exhibited the best bake hardening gain after controlled by the process of example 7, was higher than the bake hardening gain corresponding to the other temperatures by synergistically controlling solute clusters through slow quenching and low temperature pre-aging. Therefore, the 6451 aluminum alloy needs to comprehensively design and regulate a plurality of non-isothermal processes to obtain reasonable regulation and control of solute atom clusters, and the formed multi-scale solute atom clusters can be kept stable in a natural placing process and can grow quickly in a baking varnish process so that the alloy shows excellent high baking varnish hardening characteristics.
In conclusion, the invention comprehensively regulates and controls the precipitation phase dissolution and solute atomic cluster formation and distribution in a multi-process of 6451 aluminum alloy hot working, solid solution, slow quenching and multistage low-temperature preaging, so that the alloy has excellent baking finish hardening increment and natural aging resistance stability. This is very beneficial to reduce the production cost of the alloy, and has positive effect on accelerating the wide application of the alloy. Therefore, the treatment process is not only suitable for being widely applied to the manufacture of Al-Mg-Si alloy plates for automobiles, thereby accelerating the process of aluminum alloy for automobile weight reduction, but also has certain guiding significance for the development, processing and application of aluminum alloy with special requirements on natural stability and for other fields, and is worth of paying attention to the invention 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 will be appreciated by persons skilled in the art that the above embodiments are provided for illustration only and not for limitation of the invention, and that variations and modifications of the above described embodiments are intended to fall within the scope of the claims of the invention as long as they fall within the true spirit of the invention.
Claims (6)
1. The low-temperature pre-ageing treatment method for improving the baking varnish hardening increment of the 6451 aluminum alloy is characterized by comprising the following steps of:
(1) After homogenizing treatment, carrying out hot rolling treatment, cooling and cold rolling treatment on the alloy ingot to obtain a cold-rolled sheet; wherein:
in the hot rolling treatment process, the hot rolling temperature is controlled to be 500-570 ℃, the final rolling temperature is more than 300 ℃, and the total hot rolling deformation is more than 90%;
in the cooling process, controlling the cooling rate to be less than 10 ℃/h;
in the cold rolling treatment process, the rolling reduction of the pass is controlled to be 20-70%, and the total deformation of the cold rolling is controlled to be 70-90%;
(2) Sequentially carrying out non-isothermal solution treatment and slow quenching treatment on the cold-rolled sheet, wherein:
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 ℃, controlling the temperature rising rate to be 5-13 ℃/s; when the temperature of the cold-rolled sheet is within the range of 545-575 ℃, controlling the temperature rising rate to be 1-13 ℃/min;
in the slow quenching treatment process, the cooling rate is less than 20 ℃/s;
(3) Carrying out multistage pre-ageing treatment on the cold-rolled sheet treated in the step (2) to obtain 6451 aluminum alloy with high baking varnish hardening increment, wherein:
the multistage pre-ageing treatment process comprises a first stage pre-ageing treatment, a second stage pre-ageing treatment and a third stage pre-ageing treatment, wherein the highest temperature of the first stage pre-ageing treatment is 60-120 ℃, and the heating time is 9-20 s; the lowest temperature of the second-stage pre-ageing treatment is 30-60 ℃, and the cooling time is 25-42 h; the lowest temperature of the third-stage pre-ageing treatment is 10-30 ℃, the cooling time is 7-10 days,
the hardness of the 6451 aluminum alloy material is 65-90 HV, and the baking varnish hardening increment is 10-30 HV.
2. The low temperature pre-aging treatment method for improving the baking varnish hardening increment of the 6451 aluminum alloy according to claim 1, wherein 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 the 6451 aluminum alloy is subjected to 2% pre-stretching and ageing treatment in a simulated baking finish state under the condition of 185 ℃/20min, the yield strength is 200-240 MPa, and the tensile strength is 250-320 MPa.
3. The method for low temperature pre-aging treatment for increasing the baking finish hardening increment of 6451 aluminum alloy according to claim 1, wherein said step (1):
in the hot rolling treatment process, the finishing temperature is more than 320 ℃; and/or
In the cold rolling treatment process, unidirectional rolling is adopted, the pass reduction is controlled to be 20-40%, and the total cold rolling deformation is 70-80%.
4. The method for low temperature pre-aging treatment for increasing the bake hardening increment of 6451 aluminum alloy according to claim 1, wherein said cooling rate is less than 15 ℃/s during said slow quench treatment.
5. The method for low temperature pre-aging treatment for increasing the baking finish hardening increment of 6451 aluminum alloy according to claim 1, wherein said step (3):
in the first-stage pre-ageing treatment, the highest temperature is 60-112 ℃ and the heating time is 9-16 s; and/or
In the second-stage pre-ageing treatment, the minimum temperature is 30-50 ℃, and the cooling time is 26-41 h.
6. A6451 aluminum alloy material for automobiles is characterized in that the 6451 aluminum alloy material for automobiles is prepared by the low-temperature pre-ageing treatment method for improving the baking varnish hardening increment of the 6451 aluminum alloy according to any one of claims 1 to 5,
the hardness of the 6451 aluminum alloy material is 65-90 HV, and the baking varnish hardening increment is 10-30 HV.
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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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