CN108193150B - Heat treatment method for improving impact resistance of T6/T651 state 6xxx series aluminum alloy - Google Patents
Heat treatment method for improving impact resistance of T6/T651 state 6xxx series aluminum alloy Download PDFInfo
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- CN108193150B CN108193150B CN201810092132.XA CN201810092132A CN108193150B CN 108193150 B CN108193150 B CN 108193150B CN 201810092132 A CN201810092132 A CN 201810092132A CN 108193150 B CN108193150 B CN 108193150B
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
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Abstract
The invention discloses a heat treatment method for improving the impact resistance of a T6/T651 state 6xxx series aluminum alloy, which comprises the steps of rolling a cast ingot; determining the minimum temperature X ℃ required by complete recrystallization annealing of the rolled material; annealing the rolled material for 0.5-6 hours at the temperature of X-470 ℃; solution quenching; and (5) artificial aging. According to the invention, on the premise of not changing alloy components, the impact resistance of the T6/T651 state 6xxx material can be remarkably improved through a special heat treatment means.
Description
Technical Field
The invention relates to the field of aluminum alloy smelting, in particular to a heat treatment method for improving the impact resistance of a T6/T651 state 6xxx series aluminum alloy.
Background
The 6xxx belongs to heat-treatable reinforced alloy, the total variety of the 6xxx is 6061, 6013, 6082, 6016 and the like, the 6xxx has the characteristics of low density, high strength, excellent weldability and the like, and the 6xxx can be widely applied to a plurality of fields of traffic, buildings, aerospace and the like. Along with the continuous deepening of the application degree of the 6xxx alloy in various fields, the 6xxx alloy has requirements on the conventional characteristics such as strength, elongation, formability and the like, and also has special requirements on the impact resistance of the 6xxx alloy in more and more industries, particularly the traffic field. If the new energy automobile adopts 6xxx aluminum alloy to make the battery bottom plate, the alloy plate is required to have higher impact resistance, can resist the impact of foreign matters from the road surface and protect the safety of the battery.
According to the prior literature, the adjustment of alloy components and the reduction of impurity crack sources to improve the impact resistance of materials are widely recognized and commonly used methods in materials science. However, in many cases, the use of this method is still very limited, limited by the quality level of the raw materials and the level of the casting technique.
The impact resistance of the T6/T651 state 6xxx series aluminum alloy is further improved on the premise of not changing the alloy components, and at present, the method mainly adopts the method of under-dissolving and under-aging, but the method can also inevitably lose certain mechanical strength of the material while improving the impact resistance of the material; the T6I6 process method is also proposed in the literature, but the process needs three times of artificial aging, wherein the second time of aging takes thousands of hours, the process time is long, the production efficiency is low, and the feasibility of large-scale industrial production is not provided for the moment.
Disclosure of Invention
The invention discloses a heat treatment method for improving the impact resistance of a T6/T651 state 6xxx series aluminum alloy, which can obviously improve the impact resistance of a T6/T651 state 6xxx material by a special heat treatment means on the premise of not changing the alloy components.
In order to achieve the purpose, the technical scheme of the invention is as follows:
a heat treatment method for improving the impact resistance of a T6/T651 temper 6xxx series aluminum alloy, comprises the following steps:
s1, rolling: casting ingots required by 6xxx series aluminum alloy in a T6/T651 state, directly hot rolling the ingots to the thickness of finished products after preheating, controlling the finishing rolling temperature to be 200-280 ℃, or hot rolling the ingots to the thickness of semi-finished products, and then cold rolling a hot rolled coil to the thickness of the finished products by a cold rolling mill;
s2, cutting off the super-thick part of the head of the rolled material obtained in the step S1, sampling the part with qualified thickness for annealing test, and determining the minimum temperature X required by complete recrystallization annealing of the rolled material;
s3, complete recrystallization annealing: annealing the rolled material for 0.5-6 hours at the temperature of X-470 ℃;
s4, solid solution quenching: carrying out solution treatment on the rolled material after annealing treatment, carrying out rapid water quenching after solution treatment, wherein the material transfer time from solution treatment to quenching is less than or equal to 4 seconds, and the material cooling speed is more than or equal to 50 ℃/s;
s5, stretching;
and S6, carrying out artificial aging treatment.
Preferably, in the step S1, when the hot rolling is performed directly to the thickness of the finished product, the finishing temperature is 250 to 280 ℃.
Preferably, in the step S3, the rolled material is annealed at a temperature of X to 470 ℃ for 2 to 3 hours. More preferably, in the step S3, the rolled material is annealed at a temperature of X to 470 ℃ for 2 hours.
Preferably, in the step S4, the material transfer time between the solid solution and the quenching process is less than or equal to 3S, and the material cooling speed is 60-70 ℃/S. More preferably, in the step S4, the material transfer time between the solid solution and quenching processes is less than or equal to 2S, and the material cooling rate is 60 ℃/S.
The invention considers that: the impact fracture of the 6xxx material belongs to the transgranular and intergranular mixed fracture, the transgranular fracture is more caused by hard point crack sources of impurity phases (such as Fe-containing phase) and strengthening phases (such as Mg2Si phase) in the crystal of the material, for primary impurity phases such as Fe-containing phase, the primary impurity phases are difficult to remove by the subsequent process on the premise of fixing the alloy components, and for Mg2The Si strengthening phase can reduce the agglomeration distribution thereof through a certain heat treatment means to weaken the action of a crack source thereof; when the intergranular fracture mainly occurs, cracks are formed by rapidly expanding along the grain boundary with unstable structure, and if the grain boundary in the material can be reduced, the impact resistance of the material can be effectively improved. According to the analysis, the key point of the invention is to improve the impact resistance of the aluminum alloy by reducing the crack source of the material matrix and reducing the crack channel: (1) the process can obviously enlarge the crystal grains after the solid solution quenching and the aging of the material, thereby reducing the crystal boundary crack channel in the material matrix; (2) shorten the material transfer time between solid solution and quenching processes, accelerate the material cooling speed during quenching and reduce Mg as much as possible2The agglomeration of the Si phase separates out and forms a crack source of large particles.
Through the treatment, the invention can obviously improve the shock resistance of the aluminum alloy on the premise of not changing the alloy components and basically not losing the material strength.
Drawings
FIG. 1 is a graph showing the tendency of the yield strength to vary with temperature in the annealing test of the cold rolled coil in example 1.
FIG. 2a is a metallographic structure of a product obtained in comparative example 1, and FIG. 2b is a metallographic structure of a product obtained in example 1.
Fig. 3a is a fracture SEM topography after Charpy impact testing of the finished product obtained in comparative example 1, and fig. 3b is a fracture SEM topography after Charpy impact testing of the finished product obtained in example 1.
FIG. 4 is a graph showing the tendency of the yield strength to vary with temperature in the annealing test of the hot rolled coil in example 2.
Detailed Description
The present invention will be further described with reference to the following specific examples. The scope of the invention is not limited to the following examples.
Comparative example 1
S1.6061 preheating cast ingot at 460 ℃ for 8 hours, hot rolling to 10mm, hot rolling final temperature of 260 ℃, cooling hot rolled coil, and cold rolling to 6mm finished product thickness;
s2, carrying out solid solution heat treatment at 535 ℃ for 40min, carrying out water quenching, wherein the material transfer time from solid solution to quenching is 5 seconds, and the material cooling speed is 40 ℃/s;
s3, stretching the plate: the tensile rate is 2.0 percent;
s4, artificial aging heat treatment; the temperature is 170 ℃, the time is 12 hours, and the finished product is obtained after the aging heat treatment is finished and the natural cooling is carried out.
The method is mainly characterized in that an annealing test and complete recrystallization annealing are not carried out before solid solution of the 6061 plate, the cooling speed of the plate is less than 50 ℃/s during quenching, the complete recrystallization annealing temperature of the 6061 plate needs to be determined and the complete recrystallization annealing needs to be carried out before solid solution, and the cooling speed of the material is ensured to be more than or equal to 50 ℃/s during quenching.
Example 1
S1, rolling: casting a 6061 cast ingot, preheating the cast ingot at 460 ℃ for 8 hours, hot rolling to 10mm, hot rolling final temperature of 260 ℃, cooling a hot rolled coil, and then cold rolling to 6mm finished product thickness;
s2, cutting off the super-thick part of the head of the cold-rolled coil obtained in the step S1, sampling the part with qualified thickness, carrying out an annealing test of keeping the temperature for 2 hours, and determining that the complete recrystallization annealing temperature of the material is more than or equal to 300 ℃ according to the change trend of the material performance along with the annealing temperature shown in figure 1;
s3, complete recrystallization annealing: annealing treatment of keeping the temperature of the cold-rolled coil for 2 hours at 320 ℃;
s4, after the coiled material is cut into plates, solution heat treatment is carried out in a roller hearth furnace at 535 ℃ for 40 minutes, water quenching is carried out quickly after solution, the material transfer time from solution to quenching is 2 seconds, and the material cooling speed is 60 ℃/s;
s5, stretching: the tensile rate is 2.0 percent;
s6, artificial aging treatment: and (3) carrying out artificial aging on the plate at the temperature of 170 ℃ for 12h, and naturally cooling to obtain a finished product.
Table 1 compares the properties of the finished products obtained in comparative example 1 and example 1.
TABLE 1
As can be seen from table 1, the 6061 plate prepared in example 1 has the same mechanical strength as comparative example 1, but the Charpy impact absorption power is significantly improved, and the improvement rate is 33.3%.
Referring to fig. 2, fig. 2a is a metallographic structure diagram of a finished product obtained in comparative example 1, and fig. 2b is a metallographic structure diagram of a finished product obtained in example 1, and as can be seen from comparison of the two diagrams, grain boundaries in the finished product structure of example 1 are obviously reduced, so that crack propagation channels during material fracture are effectively reduced.
Referring to FIG. 3, FIG. 3a is a SEM image of the finished product obtained in comparative example 1 after Charpy impact testing, FIG. 3b is a SEM image of the finished product obtained in example 1 after Charpy impact testing, and EDS shows that the dimple internal particles are mainly Mg2Si-rich particles. As can be seen, Mg is visible in the fracture tough pits of the material of example 12The Si crack source particles are fewer, the diameter of the dimple is larger, and the dimple is deeper, so that the energy absorption characteristic is stronger; in contrast, comparative example 1 materialMg in tough pits of material fracture2The Si-rich particles are significantly more numerous, and the dimple is small in diameter and relatively shallow.
Comparative example 2
Preheating an S1.6082 cast ingot at 460 ℃ for 6 hours, and hot rolling to the thickness of a finished product of 5mm, wherein the final temperature of the hot rolling is 265 ℃;
s2, carrying out solid solution heat treatment at 535 ℃ for 30min, carrying out water quenching, wherein the material transfer time from solid solution to quenching is 5 seconds, and the material cooling speed is 45 ℃/S;
s3, stretching the plate: the tensile rate is 0.5%;
s4, artificial aging heat treatment; the temperature is 170 ℃, the time is 12 hours, and the finished product is obtained after the aging heat treatment is finished and the natural cooling is carried out.
The comparative example 2 is the current conventional 6061-T6 aluminum alloy plate production process, and is mainly different from the invention in that the 6061 plate is not subjected to an annealing test and complete recrystallization annealing before solid solution, the cooling rate of the plate is less than 50 ℃/s during quenching, and the invention needs to determine the complete recrystallization annealing temperature of the 6082 plate and perform complete recrystallization annealing before solid solution through the annealing test and ensure that the cooling rate of the material is more than or equal to 50 ℃/s during quenching.
Example 2
S1, rolling: casting 6082 cast ingots, preheating the cast ingots at 460 ℃ for 6 hours, and hot rolling to the thickness of a finished product of 5mm, wherein the final temperature of the hot rolling is 265 ℃;
s2, cutting off the super-thick part of the head of the hot-rolled coil obtained in the step S1, sampling the part with qualified thickness, carrying out an annealing test of heat preservation for 2 hours, and determining that the complete recrystallization annealing temperature of the material is more than or equal to 360 ℃ according to the change trend of the material performance along with the annealing temperature shown in figure 4;
s3, complete recrystallization annealing: annealing the hot rolled coil for 2 hours at the temperature of 370 ℃;
s4, after the coiled material is cut into plates, solution heat treatment is carried out in a roller hearth furnace at 535 ℃ for 30 minutes, water quenching is carried out quickly after solution, the material transfer time from solution to quenching is 2 seconds, and the material cooling speed is 70 ℃/s;
s5, stretching: the tensile rate is 0.5%;
s6, artificial aging treatment: and (3) carrying out artificial aging on the plate at the temperature of 170 ℃ for 12h, and naturally cooling to obtain a finished product.
Table 2 compares the properties of the finished products obtained in comparative example 2 and example 2.
TABLE 2
As can be seen from table 2, the 6082 plate prepared in example 2 has mechanical strength equivalent to that of comparative example 2, but the Charpy impact absorption power is significantly improved, and the improvement rate is 38.5%.
Claims (6)
1. A heat treatment method for improving the impact resistance of a T6/T651 temper 6xxx series aluminum alloy, is characterized by comprising the following steps of:
s1, rolling: casting ingots required by 6xxx series aluminum alloy in a T6/T651 state, directly hot rolling the ingots to the thickness of finished products after preheating, controlling the finishing rolling temperature to be 200-280 ℃, or hot rolling the ingots to the thickness of semi-finished products, and then cold rolling a hot rolled coil to the thickness of the finished products by a cold rolling mill;
s2, cutting off the super-thick part of the head of the rolled material obtained in the step S1, sampling the part with qualified thickness, performing an annealing test, and determining the minimum temperature X required by complete recrystallization annealing of the rolled material;
s3, complete recrystallization annealing: annealing the rolled material for 0.5-6 hours at the temperature of X-470 ℃;
s4, solid solution quenching: carrying out solution treatment on the rolled material after annealing treatment, carrying out rapid water quenching after solution treatment, wherein the material transfer time from solution treatment to quenching is less than or equal to 4 seconds, and the material cooling speed is more than or equal to 50 ℃/s;
s5, stretching;
s6, artificial aging treatment: and (3) carrying out artificial aging on the plate at the temperature of 170 ℃ for 12h, and naturally cooling to obtain a finished product.
2. The heat treatment process of claim 1, wherein the heat treatment process improves the impact resistance of a T6/T651 temper 6xxx series aluminum alloy, and is characterized by:
in the step S1, when the hot rolling is directly carried out until the thickness of the finished product is reached, the final rolling temperature is 250-280 ℃.
3. The heat treatment process of claim 1, wherein the heat treatment process improves the impact resistance of a T6/T651 temper 6xxx series aluminum alloy, and is characterized by:
in the step S3, annealing treatment is performed on the rolled material for 2-3 hours at the temperature of X-470 ℃.
4. The heat treatment method of claim 3, wherein the heat treatment method is performed by using a heat treatment method for improving the impact resistance of a T6/T651 temper 6xxx series aluminum alloy, and comprises the following steps:
in the step S3, annealing treatment is performed on the rolled material for 2 hours at a temperature of X-470 ℃.
5. The heat treatment process of claim 1, wherein the heat treatment process improves the impact resistance of a T6/T651 temper 6xxx series aluminum alloy, and is characterized by:
in the step S4, the material transfer time between the solid solution and the quenching process is less than or equal to 3S, and the material cooling speed is 60-70 ℃/S.
6. The heat treatment method of claim 5, wherein the heat treatment method is performed by using a heat treatment method to improve the impact resistance of a T6/T651 temper 6xxx series aluminum alloy, and comprises the following steps:
in the step S4, the material transfer time between the solid solution and the quenching process is less than or equal to 2S, and the material cooling speed is 60 ℃/S.
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