CN115341123B - Aluminum alloy and preparation method thereof - Google Patents
Aluminum alloy and preparation method thereof Download PDFInfo
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- CN115341123B CN115341123B CN202211004092.1A CN202211004092A CN115341123B CN 115341123 B CN115341123 B CN 115341123B CN 202211004092 A CN202211004092 A CN 202211004092A CN 115341123 B CN115341123 B CN 115341123B
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- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
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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
- C22F1/053—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 of alloys with zinc as the next major constituent
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Abstract
The invention provides an aluminum alloy and a preparation method thereof, wherein the aluminum alloy comprises the following components: zn:5.4-6.6%, mg:1.5-2.6%, cu:1.0-2.0%, mn:0.08-0.5%, zr:0.06-0.15%, er:0.06-0.15%, si:0.1% or less, fe: less than 0.2%, and the balance of Al and inevitable impurities; the preparation steps of the aluminum alloy comprise a heat treatment process, wherein the heat treatment process comprises the following steps: solid solution, pre-aging, regression treatment, cryogenic treatment and re-aging, wherein: solid solution is carried out for 1 to 3 hours at the temperature of 450 to 480 ℃, and water quenching is carried out to the room temperature; pre-aging at 105-135 deg.C for 20-24h; the regression treatment is that the temperature is kept for 0.5 to 2 hours at the temperature of 170 to 200 ℃; the cryogenic treatment is carried out by keeping the temperature of liquid nitrogen at-196 ℃ for 30-60min; and the re-aging is carried out for 2 to 4 hours at the temperature of between 105 and 135 ℃.
Description
Technical Field
The invention relates to the technical field of new materials, in particular to an aluminum alloy with excellent mechanical property and good corrosion resistance, and the aluminum alloy has short production flow and low cost.
Background
The Al-Zn-Mg-Cu aluminum alloy is widely applied to the fields of aerospace, transportation, marine engineering and the like, has the characteristics of high strength, corrosion resistance and low density, and is an ideal light high-strength structural material. Such aluminum alloys typically require heat treatment to develop their maximum performance potential, and solution + aging is the most common heat treatment process for such alloys.
For Al-Zn-Mg-Cu alloy, the initial heat treatment basically adopts T6 heat treatment, namely a heat treatment process of solid solution and single-stage aging, and the heat treatment process can obtain high strength, but has poor corrosion resistance, so that the application range of the alloy is limited. Then, in order to solve the problem of corrosion resistance, technologists developed a solution treatment and a two-stage aging treatment process, i.e., T73 and T76, and performed low-temperature pre-aging and high-temperature final aging after solution treatment, which treatment process improved corrosion resistance but reduced strength. In order to take the strength and the corrosion resistance into consideration, a solid solution and three-stage aging treatment system, namely solid solution and RRA, is developed, the aging process is firstly carried out low-temperature pre-aging, then high-temperature regression treatment is carried out, and then low-temperature re-aging is carried out, and the aluminum alloy treated by the process has high strength and high corrosion resistance.
However, the RRA process has the defects that the process is long in time consumption, low-temperature pre-aging usually needs about 20-24 hours, regression treatment needs about 1-2 hours, re-aging treatment needs about 20-24 hours, the whole RRA process needs about 45-50 hours after being finished, the whole process needs to be carried out in a heat treatment furnace, and the production period is too long. The process consumes long time in the production process of the aluminum alloy, so that the labor and equipment consumption is high, and the production cost of the alloy is high.
Based on the problems, the invention provides the aluminum alloy which is produced by adopting a short-process, so that the process time consumption is short, the production cost is low, the corrosion resistance of the obtained aluminum alloy is basically equal to that of the aluminum alloy produced by the traditional method, and the strength of the aluminum alloy is improved compared with that of the aluminum alloy produced by the traditional method.
Disclosure of Invention
The inventor of the invention provides the Al-Zn-Mg-Cu aluminum alloy by researching the heat treatment process of the Al-Zn-Mg-Cu aluminum alloy, the heat treatment is carried out through improved solid solution and RRA, the heat treatment time can be greatly shortened while the heat treatment effect is ensured, and the performance of the aluminum alloy after heat treatment reaches the level of conventional solid solution and RRA, namely, the aluminum alloy produced by the new process shortens the time period of the treatment process while the performance is improved, and the cost is greatly reduced.
The technical effect of the invention is realized by the following technical scheme.
The invention provides an aluminum alloy which comprises the following components: zn:5.4-6.6%, mg:1.5-2.6%, cu:1.0-2.0%, mn:0.08-0.5%, zr:0.06-0.15%, er:0.06-0.15%, si:0.1% or less, fe: less than 0.2%, and the balance of Al and inevitable impurities; the preparation steps of the aluminum alloy comprise a heat treatment process, wherein the heat treatment process comprises the following steps: solid solution, pre-aging, regression treatment, cryogenic treatment and re-aging, wherein: solid solution is carried out for 1-3h at 450-480 ℃, and water quenching is carried out to room temperature; pre-aging at 105-135 deg.C for 20-24h; the regression treatment is that the temperature is kept for 0.5 to 2 hours at the temperature of 170 to 200 ℃; the subzero treatment is heat preservation for 30-60min at-196 deg.C in liquid nitrogen; and the secondary aging is carried out for 2-4h at 105-135 ℃.
The principle of the present invention will be described below.
First, the conventional RRA processing principle is described. Pre-aging: the Al-Zn-Mg-Cu alloy is pre-aged, and a strengthening phase G is precipitated in the crystalP zone and η ’ And the phases realize strengthening effect, at the moment, eta phases separated out from the crystal boundary are continuously distributed, and the continuous eta phases are not beneficial to corrosion resistance. And then carrying out regression treatment, wherein the strengthening phase is redissolved and the grain boundary precipitated phase eta phase is in discontinuous distribution. And finally, carrying out re-aging treatment, re-precipitating the strengthening phase and dispersing and distributing the strengthening phase in the crystal, wherein the grain boundary precipitated phase eta phase is discontinuously distributed, so that high strength and corrosion resistance are ensured.
The improvement of the invention is that a process of rapid cooling and cryogenic treatment after regression aging, namely RRCA process, is adopted, and "C" stands for cryogenic treatment. In the RRCA process, the mechanism of preaging and regression treatment is the same as that of the conventional RRA, and the rapid cooling and deep cooling treatment process is added after the regression treatment, so that on one hand, by controlling the proper cooling rate, the deep cooling temperature and time, the strengthening phase which is redissolved in the matrix after the regression treatment can be uniformly, finely and dispersedly separated out into crystal grains in the cooling process, and cannot be combined with each other to grow, thereby ensuring excellent strength and generating overlarge temperature stress deterioration performance; on the other hand, by controlling the cooling rate, the deep cooling temperature, the time and other process parameters, the precipitated phase eta phase at the crystal boundary can be further broken and fractured under the action of the temperature stress in the cooling process, so that the corrosion resistance is ensured. After the cryogenic treatment process is adopted, the effect to be obtained in the traditional reaging process is basically realized, so that the subsequent reaging process does not need long-time heat preservation, and the process time is greatly shortened. The time length of the RRCA procedure of the aluminum alloy is controlled within 30h, even within 25h, compared with the traditional RRA process, the time length of the aging procedure is greatly shortened, the production efficiency is improved, the production cost is reduced, the corrosion resistance of the aluminum alloy obtained by the process treatment is equivalent to that of the traditional RRA, and the strength is more excellent.
It should be noted that, the process time mentioned in this specification, whether it is the conventional RRA process or the RRCA process of the present invention, does not include the time of the temperature rise and temperature fall in the treatment process of each stage, or the time of the temperature rise and temperature fall does not significantly affect the overall treatment process time: on one hand, because the treatment temperature of the aluminum alloy is lower, the pre-aging and the re-aging are about 100 ℃, the regression treatment is about 200 ℃, the time consumption of the heating and cooling process is very short, and compared with the time of tens of hours in the whole process, the time consumption of the two processes can be ignored.
However, although the time of the temperature rise and drop process is short, the optimization of the process can still improve the process efficiency to a certain extent and shorten the process treatment time. For example, as a further optimization direction, the pre-aged aluminum alloy is directly heated from the pre-aging temperature to the regression treatment temperature, so that compared with the traditional process of cooling to room temperature and then heating from the room temperature to the regression temperature after the RRA pre-aging, the scheme directly heats from the pre-aging temperature to the regression temperature, the process time in the temperature raising and lowering process is shortened, and the time can be further saved by about 20-40min through the process optimization.
As a further improvement, after pre-aging, air cooling or water cooling is carried out to room temperature, and then the temperature is raised to the regression treatment temperature at the temperature raising rate of 20-45 ℃/min. The inventors have found that controlling the rate of temperature rise during the regression treatment is effective to obtain finely dispersed GP zones and eta within the crystal ’ The phases and the coarse and discontinuous η phases at the grain boundaries are advantageous, thereby contributing to the most excellent strength and corrosion resistance.
Further, the aluminum alloy of the present invention has a GP zone and eta precipitated in the crystal ’ Coarse and discontinuous eta phases are distributed at grain boundaries.
As mentioned above, the cooling rate during the regression treatment is crucial to obtain the technical effects of the present invention, and the aluminum alloy after the regression treatment is cooled to the cryogenic treatment temperature at a cooling rate of not less than 30 ℃/min, preferably at a cooling rate of 30-60 ℃/min. Too slow of cooling rate, poor thermodynamic driving force, GP zone and eta ’ The precipitation speed in the opposite crystal boundary is slow, the growth trend is obvious, and the eta phase at the crystal boundary can not be fully disintegrated, broken and fractured due to insufficient temperature stress, so that the strength and the corrosion resistance of the aluminum alloy can not be ensured; too high a cooling rate leads to excessive temperature stressMicrocracks are generated at grain boundaries, resulting in a drastic deterioration in strength and corrosion resistance.
The second purpose of the present invention is to provide a preparation method of the foregoing aluminum alloy, including the following steps: s1: smelting, namely, proportioning and smelting according to aluminum alloy components; s2: refining; s3: casting into ingots; s4: carrying out heat treatment on the cast ingot; the heat treatment process of S4 comprises the following steps: solid solution, pre-aging, regression treatment, cryogenic treatment and re-aging, wherein: solid solution is carried out for 1 to 3 hours at the temperature of 450 to 480 ℃, and water quenching is carried out to the room temperature; pre-aging at 105-135 deg.C for 20-24h; the regression treatment is that the temperature is kept for 0.5 to 2 hours at the temperature of 170 to 200 ℃; the cryogenic treatment is carried out by keeping the temperature of liquid nitrogen at-196 ℃ for 30-60min; re-aging at 105-135 deg.C for 2-4h; and cooling the aluminum alloy subjected to the regression treatment to the cryogenic treatment temperature at a cooling rate of not less than 30 ℃/min.
As described above, the preparation process of the aluminum alloy provided by the invention optimizes the heat treatment process, mainly adopts the RRCA process to replace the traditional RRA process, can ensure that the strengthening phase which is redissolved in the matrix after the regression treatment is uniformly, finely and dispersedly separated out into the crystal in the cooling process and is not combined with each other to grow up through the control of the cryogenic speed, the cryogenic temperature and the cryogenic time, ensures the excellent strength, does not generate the excessive temperature stress deterioration performance, and on the other hand, can ensure that the eta phase separated out from the crystal boundary is further broken and cracked and branched under the action of the temperature stress in the cooling process by controlling the process parameters such as the cooling rate, the cryogenic temperature, the cryogenic time and the like, thereby ensuring the corrosion resistance. After the cryogenic treatment process is adopted, the effect to be obtained in the traditional reaging process is basically realized, so that the subsequent reaging process does not need long-time heat preservation, and the process time is greatly shortened. According to the preparation process of the aluminum alloy, the time of the RRCA process is controlled within 30h, even within 25h, compared with the traditional RRA process, the time of the aging process is greatly shortened, the production efficiency is improved, the production cost is reduced, the corrosion resistance of the aluminum alloy obtained by the process is equivalent to that of the traditional RRA, and the strength of the aluminum alloy is more excellent.
Furthermore, in order to prolong the compression process, the pre-aged aluminum alloy is directly heated from the pre-aging temperature to the regression treatment temperature. Compared with the traditional process of cooling to room temperature after RRA pre-aging and then heating from room temperature to regression temperature, the scheme directly heats from the pre-aging temperature to the regression temperature, shortens the process time in the temperature rising and falling process, and can further save the time by about 20-40min through the process optimization.
As a further improved technical scheme, after pre-aging, air cooling or water cooling is carried out to room temperature, and then the temperature is increased to the regression treatment temperature at the temperature increase rate of 20-45 ℃/min. In the preparation process, the temperature rise rate in the regression treatment process is controlled to obtain the GP zones and eta of the fine dispersion in the crystal ’ The phases and the coarse and discontinuous η phases at the grain boundaries are advantageous, thereby contributing to the most excellent strength and corrosion resistance.
As a further optimized scheme, cooling to the cryogenic treatment temperature at a cooling rate of 30-60 ℃/min after the regression treatment. Control of the cooling rate after the regression process is critical to achieving the technical effect of the present invention. Too slow of cooling rate, poor thermodynamic driving force, GP zone and eta ’ The precipitation speed in the opposite crystal boundary is slow, the growth trend is obvious, and the eta phase at the crystal boundary can not be fully disintegrated, broken and fractured due to insufficient temperature stress, so that the strength and the corrosion resistance of the aluminum alloy can not be ensured; too high a cooling rate leads to excessive temperature stress and microcracks at the grain boundaries, resulting in a drastic deterioration in strength and corrosion resistance.
The invention has the following beneficial effects.
The improvement of the invention lies in adopting the rapid cooling and cryogenic treatment process after the regression aging, namely RRCA process, on one hand, by controlling proper cooling rate and cryogenic temperature and time, the strengthening phase redissolved in the matrix after the regression treatment can be evenly, finely and dispersedly precipitated in the crystal in the cooling process, and cannot be combined with each other to grow up, thereby ensuring excellent strength and not generating overlarge temperature stress deterioration performance; on the other hand, by controlling the process parameters such as cooling rate, deep cooling temperature, time and the like, the eta phase precipitated at the crystal boundary can be further broken and decomposed under the action of temperature stress in the cooling process, so that the corrosion resistance is ensured. After the cryogenic treatment process is adopted, the effect to be obtained in the traditional reaging process is basically realized, so that the subsequent reaging process does not need long-time heat preservation, and the process time is greatly shortened. The time length of the RRCA procedure of the aluminum alloy is controlled within 30h, even within 27h, compared with the traditional RRA process, the time length of the aging procedure is greatly shortened, the production efficiency is improved, the production cost is reduced, the corrosion resistance of the aluminum alloy obtained by the process treatment is equivalent to that of the traditional RRA, and the strength is more excellent.
The Al-Zn-Mg-Cu aluminum alloy has the room-temperature tensile strength of more than 700MPa, the room-temperature yield strength of more than 550MPa, the room-temperature elongation of more than 11.0 percent, the exfoliation corrosion resistance grade of more than P grade (including P grade), preferably the room-temperature tensile strength of more than 750MPa, the room-temperature yield strength of more than 620MPa, the room-temperature elongation of more than 13.0 percent and the exfoliation corrosion resistance of N grade.
Detailed Description
In order to make those skilled in the art fully understand the technical solutions and advantages of the present invention, the following description is further provided with reference to specific test examples.
The alloy components A and B are smelted and refined to prepare ingots, heat treatment is carried out according to heat treatment parameters in tables 1 and 2, and the corrosion resistance, tensile strength, yield strength and elongation of the heat-treated aluminum alloy are tested and shown in table 3. Wherein, the corrosion resistance is detected according to GB/T22639-2022 peeling corrosion test method of aluminum alloy products, and the elongation, the tensile strength and the yield strength are determined according to GB/T228.1-2021 part 1 of metal material tensile test: room temperature test method ].
Example A
The aluminum alloy comprises the following components: zn:5.8%, mg:2.1%, cu:1.7%, mn:0.35%, zr:0.09%, er:0.12%, si:0.07%, fe:0.13 percent, the balance being Al and other inevitable impurities, casting 10 samples after smelting and refining, respectively carrying out heat treatment according to the heat treatment process parameters in the table 1, and then detecting the mechanical properties. In table 1, after solid solution, water quenching is performed to room temperature, air cooling is performed to room temperature after pre-aging and re-aging, and in the process duration, the time for heating and cooling in each stage is not counted.
TABLE 1 Heat treatment Process parameters for group A aluminum alloys
Example B
The aluminum alloy comprises the following components: zn:6.2%, mg:2.3%, cu:1.4%, mn:0.29%, zr:0.1%, er:0.13%, si:0.06%, fe:0.15 percent, and the balance of Al and other inevitable impurities, casting 10 samples after smelting and refining, respectively carrying out heat treatment according to the heat treatment process parameters in the table 2, and then detecting the mechanical properties. In table 2, after solid solution, water quenching is performed to room temperature, air cooling is performed to room temperature after pre-aging and re-aging, and in the process duration, the time for heating and cooling in each stage is not counted.
TABLE 2 Heat treatment Process parameters for group B aluminum alloys
The data for each set of performance tests for examples a and B are shown in table 3 below.
TABLE 3 inventive and comparative example Performance data for each set of examples
The effect of the present invention will be further explained and analyzed by combining the 10 tests of example A and the 10 tests of example B.
First, an inventive example of the present invention is analyzed.
The compositions and heat treatment processes of test Nos. A-1 to A-4 and B-1 to B-4 satisfy the requirements of the present invention, and are inventive examples of the present invention. From performance detection, the tensile strength at room temperature of the aluminum alloy of each invention example reaches more than 700MPa, the yield strength at room temperature is more than 550MPa, the elongation at room temperature reaches more than 11.0 percent, and the anti-stripping corrosion grade reaches more than P grade; in particular, for the serial numbers A-1 and A-4 and the test serial numbers B-1 to B-4, on the basis of meeting the heat treatment process requirement of the invention, the temperature rise rate of heating to the regression treatment temperature after pre-aging is within the range of 20-45 ℃/min, which is more favorable for obtaining more excellent tensile strength, yield strength and corrosion resistance, the room temperature tensile strength of the aluminum alloys of the invention examples A-1, A4 and B-1 to B-4 reaches more than 750MPa, the room temperature yield strength reaches more than 620MPa, the room temperature elongation reaches more than 13.0 percent, and the anti-spalling corrosion grade reaches N grade. It is also not difficult to see by comparing invention examples A-2, A-3 and invention example A-1, and more excellent mechanical properties and corrosion resistance can be obtained when the temperature rise rate of heating to the regression treatment temperature after pre-aging is controlled within 20-45 ℃/min.
Meanwhile, the time of the heat treatment process of the embodiment of the invention can be controlled within 30h, even within 27h, so that the period of the heat treatment process is greatly shortened, the production efficiency is improved, and the production cost is reduced.
Next, inventive examples and comparative examples of the present invention were analyzed one by one.
Comparative example A-5 is a comparative example of inventive example A-1, comparative example B-5 is a comparative example of inventive examples B-1 to B4, and both A-5 and B-5 employ a lower cooling rate than required by the present invention. However, it can be readily seen by comparing performance that the lower cooling rate after regression treatment results in a poorer thermodynamic driving force, GP zone and η ’ The precipitation speed in the opposite crystal boundary is slow, the growth trend is obvious, the eta phase at the crystal boundary can not be fully disintegrated, broken and fractured due to insufficient temperature stress, and the tensile strength, the yield strength and the corrosion resistance of the aluminum alloy can not meet the requirements of the invention.
Comparative example A-6 is a comparative example of inventive example A-1, comparative example B-6 is a comparative example of inventive examples B-1 to B4, and both A-6 and B-6 employ higher cooling rates than required by the present invention. However, it is not difficult to find by comparison of performances that the cooling rate after the regression treatment is high, the temperature stress is too large during the cooling process, so that microcracks are generated at grain boundaries, and the tensile strength, the yield strength, the elongation and the corrosion resistance are rapidly deteriorated, which does not meet the requirements of the invention.
Comparative example A-7 is a comparative example of inventive example A-1, comparative example B-7 is a comparative example of inventive example B-1, and both A-7 and B-7 employed a shorter deep cooling time than required by the present invention. However, due to the shorter cryogenic time, GP zone and eta ’ The time window of precipitation in the opposite crystal boundary is narrow, so that sufficient dispersion precipitation cannot be realized, the strengthening effect of the aluminum alloy is insufficient, the eta phase at the crystal boundary cannot be sufficiently disintegrated, broken and broken, and the tensile strength, the yield strength and the corrosion resistance of the aluminum alloy cannot meet the requirements of the invention.
Comparative example A-8 is a comparative example of inventive example A-1, comparative example B-8 is a comparative example of inventive example B-1, and both A-8 and B-8 employ a cryogenic time longer than that required by the present invention. However, the deep cooling time is too long, which results in excessive temperature stress accumulation, and the occurrence of defects such as microcracks at grain boundaries, which causes rapid deterioration in tensile strength, yield strength, elongation, and corrosion resistance, and thus the invention is not satisfactory.
Comparative example A-9 is a comparative example of inventive example A-1, comparative example B-9 is a comparative example of inventive example B-1, neither A-9 nor B-9 was cryogenically cooled after pre-aging, but re-aged by cooling to room temperature and then directly heating at a cooling rate that meets the inventive requirements. However, without cryogenic processes, the thermodynamic driving force is poor and the time for re-aging is too short, the GP zone and η ’ The precipitation speed in the opposite crystal boundary is slow, the precipitation time window is too narrow, the crystal cannot be fully precipitated, and the eta phase at the crystal boundary cannot be fully disintegrated, broken and fractured due to insufficient temperature stress, so that the tensile strength, the yield strength and the corrosion resistance of the aluminum alloy cannot meet the requirements of the invention.
Comparative example A-10 is a comparative example of inventive example A-1, comparative example B-10 is a comparative example of inventive example B-1, A-10 and B-10 were pre-aged, then air-cooled to room temperature and then directly heated for re-aging, both used the conventional RRA process without deep cooling. From the aspect of performance, although the corrosion resistance and the elongation can meet the requirements of the invention, the tensile strength and the yield strength are slightly poor, most importantly, the time of the heat treatment process is more than 45h, even close to 50h, the process period is long, and the technical purpose of obtaining the aluminum alloy with both high strength and high corrosion resistance in a short flow and a short period cannot be met.
It is obvious from the comparison of the above embodiments that the RRCA process of the present invention can realize short-process production of high-strength and high-corrosion-resistance Al-Zn-Mg-Cu alloy, especially the cooling rate and the deep cooling time after the retrogression aging are critical to obtain the corresponding strength and corrosion resistance, and when the temperature rise rate of the retrogression aging is controlled within a certain range, the RRCA process is helpful to obtain the matching of more excellent strength and corrosion resistance.
The above description of the embodiments is only intended to facilitate the understanding of the method of the invention and its core idea. It should be noted that, for those skilled in the art, it is possible to make various improvements and modifications to the present invention without departing from the principle of the present invention, and those improvements and modifications also fall within the scope of the claims of the present invention.
The previous description of the disclosed embodiments is provided to enable any person skilled in the art to make or use the present invention. Various modifications to these embodiments will be readily apparent to those skilled in the art, and the generic principles defined herein may be applied to other embodiments without departing from the spirit or scope of the invention. Thus, the present invention is not intended to be limited to the embodiments shown herein but is to be accorded the widest scope consistent with the principles and novel features disclosed herein.
Claims (7)
1. An aluminum alloy is characterized by comprising the following components: zn:5.4-6.6%, mg:1.5-2.6%, cu:1.0-2.0%, mn:0.08-0.5%, zr:0.06-0.15%, er:0.06-0.15%, si:0.1% or less, fe: less than 0.2%, and the balance of Al and inevitable impurities;
the preparation steps of the aluminum alloy comprise a heat treatment process, wherein the heat treatment process comprises the following steps: solid solution, pre-aging, regression treatment, cryogenic treatment and re-aging, wherein:
solid solution is carried out for 1 to 3 hours at the temperature of 450 to 480 ℃, and water quenching is carried out to the room temperature; pre-aging at 105-135 deg.C for 20-24h; the regression treatment is carried out at 170-200 ℃ for 0.5-2h; the subzero treatment is heat preservation for 30-60min at-196 deg.C in liquid nitrogen; and the secondary aging is carried out for 2-4h at 105-135 ℃, and the temperature is cooled to the cryogenic treatment temperature at the cooling rate of 30-60 ℃/min after the regression treatment.
2. An aluminium alloy according to claim 1, wherein said pre-ageing is followed by a direct increase in temperature from the pre-ageing temperature to the reversion treatment temperature.
3. An aluminium alloy according to claim 1, wherein the aluminium alloy is pre-aged and then air or water cooled to room temperature and then raised to the reversion treatment temperature at a ramp rate of 20-45 ℃/min.
4. The aluminum alloy as recited in claim 1, wherein the aluminum alloy has intracrystalline precipitated GP zones and η ’ And (4) phase.
5. A method of producing an aluminium alloy according to any one of claims 1 to 4, characterised in that the steps comprise:
s1: smelting, namely, proportioning and smelting according to aluminum alloy components; s2: refining; s3: casting into ingots; s4: carrying out heat treatment on the cast ingot;
the heat treatment process of S4 comprises the following steps: solid solution, pre-aging, regression treatment, cryogenic treatment and re-aging, wherein: solid solution is carried out for 1 to 3 hours at the temperature of 450 to 480 ℃, and water quenching is carried out to the room temperature; pre-aging at 105-135 deg.C for 20-24h; the regression treatment is that the temperature is kept for 0.5 to 2 hours at the temperature of 170 to 200 ℃; the cryogenic treatment is carried out by keeping the temperature of liquid nitrogen at-196 ℃ for 30-60min; the reaging is that the temperature is kept for 2 to 4 hours at 105 to 135 ℃; and cooling the aluminum alloy subjected to the regression treatment to the cryogenic treatment temperature at a cooling rate of 30-60 ℃/min.
6. A method for producing an aluminium alloy according to claim 5, wherein the pre-ageing is directly followed by increasing the temperature from the pre-ageing temperature to the reversion treatment temperature.
7. The method of claim 5, wherein the pre-aging is followed by air or water cooling to room temperature and then raising the temperature to the annealing temperature at a rate of 20-45 ℃/min.
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| CN115341123A (en) | 2022-11-15 |
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