CN117626148A - Aluminum alloy and heat treatment method and application thereof - Google Patents
Aluminum alloy and heat treatment method and application thereof Download PDFInfo
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- CN117626148A CN117626148A CN202311216355.XA CN202311216355A CN117626148A CN 117626148 A CN117626148 A CN 117626148A CN 202311216355 A CN202311216355 A CN 202311216355A CN 117626148 A CN117626148 A CN 117626148A
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 105
- 238000000034 method Methods 0.000 title claims abstract description 54
- 238000010438 heat treatment Methods 0.000 title claims abstract description 52
- 238000011282 treatment Methods 0.000 claims abstract description 80
- 230000032683 aging Effects 0.000 claims abstract description 51
- 238000005097 cold rolling Methods 0.000 claims abstract description 31
- 238000010791 quenching Methods 0.000 claims abstract description 18
- 230000000171 quenching effect Effects 0.000 claims abstract description 18
- 239000000463 material Substances 0.000 claims abstract description 11
- 229910045601 alloy Inorganic materials 0.000 claims description 23
- 239000000956 alloy Substances 0.000 claims description 23
- 229910018594 Si-Cu Inorganic materials 0.000 claims description 14
- 229910008465 Si—Cu Inorganic materials 0.000 claims description 14
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 6
- 229910021365 Al-Mg-Si alloy Inorganic materials 0.000 claims description 2
- 238000001816 cooling Methods 0.000 claims description 2
- 239000007769 metal material Substances 0.000 abstract description 3
- 238000000926 separation method Methods 0.000 abstract description 3
- 239000000243 solution Substances 0.000 description 20
- 230000008569 process Effects 0.000 description 18
- 238000012360 testing method Methods 0.000 description 11
- 230000000052 comparative effect Effects 0.000 description 8
- 238000010276 construction Methods 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 229910052802 copper Inorganic materials 0.000 description 3
- 230000005662 electromechanics Effects 0.000 description 3
- 238000005265 energy consumption Methods 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 230000009286 beneficial effect Effects 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 230000008859 change Effects 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000001035 drying Methods 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 239000002245 particle Substances 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 238000012546 transfer Methods 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 229910000978 Pb alloy Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 230000006978 adaptation Effects 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 239000003153 chemical reaction reagent Substances 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000007858 starting material Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 230000035882 stress Effects 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 230000001550 time effect Effects 0.000 description 1
Abstract
The invention discloses an aluminum alloy and a heat treatment method and application thereof, and belongs to the technical field of metal materials. The heat treatment method of the aluminum alloy provided by the invention comprises the following steps: sequentially carrying out solution treatment, quenching treatment, cold rolling treatment and aging treatment on the aluminum alloy to obtain the heat-treated aluminum alloy; the total deformation of the cold rolling treatment is 5-20%. According to the invention, the aluminum alloy is subjected to small deformation cold rolling pretreatment at room temperature, the total deformation is 2-20%, dislocation is introduced, partial solute atoms are separated out along dislocation lines, the microstructure continuity is improved, the aging separation efficiency can be effectively improved, the time required by aging treatment is greatly shortened, the time required by the aluminum alloy to reach a peak aging state is shortened, the elongation of the aluminum alloy in a T6 state can be greatly improved, the strength and the hardness are kept high, and the obtained aluminum alloy has wide application in being used as a structural material.
Description
Technical Field
The invention belongs to the technical field of metal materials, and particularly relates to an aluminum alloy and a heat treatment method and application thereof.
Background
The aluminum alloy is an alloy with aluminum as a base and added with a certain amount of other alloy elements, is one of light metal materials, has higher strength, has specific strength close to that of high alloy steel, has specific rigidity exceeding that of steel, has good casting performance and plastic processing performance, good electric conduction, heat conduction and corrosion resistance and weldability, can be used as a structural material, and has wide application in aerospace, aviation, transportation, construction, electromechanics, lightening and daily necessities. Al-Mg-Si-Cu series alloys (such as 6xxx series) are an important series in aluminum alloys, and have the characteristics of small density, high specific strength, excellent corrosion resistance, excellent casting performance, good weldability, thermal expansibility and the like, and are increasingly focused on in the fields of aerospace, automobiles, machinery and the like in recent years, and the use amount is rapidly increased. The series of alloy is heat-treatable aluminum alloy, the mechanical property of the alloy is required to be improved through ageing treatment, and the alloy is normally subjected to ageing treatment at 180 ℃ in the industry at present so as to separate out fine needle-shaped beta' (Mg) 5 Si 6 ) The time for the strengthening phase to reach the peak time effect state (T6 state) generally needs more than 4 hours, and the production cost is greatly increased.
Meanwhile, the elongation of Al-Mg-Si-Cu (such as 6xxx series) alloy in the T6 state is only 7% conventionally, and the alloy is difficult to use as a structural material. A large amount of nano-scale beta' precipitated phases are dispersed in an Al matrix in a T6 state, dislocation cuts through the motion of the precipitated phases, and on one hand, the yield strength of the alloy is greatly improved; on the other hand, the hard second phase particles cause stress concentration, microcracks are easy to generate, and the elongation of the alloy is correspondingly reduced along with the increase of the density of the second phase particles. Therefore, a novel heat treatment process is developed, the elongation of the alloy is improved while the T6 state strength is not reduced, and the application range of the Al-Mg-Si-Cu (such as 6xxx series) alloy is greatly expanded.
Disclosure of Invention
In order to overcome the problems in the prior art, one of the purposes of the invention is to provide a heat treatment method for aluminum alloy, which greatly improves the elongation of the aluminum alloy in the T6 state, and has short treatment process period, high efficiency and low energy consumption.
The second object of the present invention is to provide a heat-treated aluminum alloy obtained by the above heat treatment method.
It is a further object of the present invention to provide a use of the heat treated aluminum alloy as described above as a structural material.
In order to achieve the above purpose, the technical scheme adopted by the invention is as follows:
the first aspect of the present invention provides a heat treatment method of an aluminum alloy, comprising the steps of: sequentially carrying out solution treatment, quenching, cold rolling treatment and aging strengthening on the aluminum alloy to obtain the heat-treated aluminum alloy; the total deformation of the cold rolling treatment is 2-20%.
The cold rolling process is a process of hot-rolled sheet at room temperature, and is called a cold rolling process because the sheet is heated during the process, but no additional heating is required. The aim of the cold rolling treatment is to introduce dislocation, separate out part of solute atoms along dislocation lines, improve microstructure continuity, effectively improve aging separation efficiency by adopting the cold rolling pretreatment of small deformation (total deformation is 2-20%) at room temperature, greatly shorten the time required by aging treatment, shorten the time required by the aluminum alloy to reach a peak aging state (T6 state), and greatly improve the elongation of the aluminum alloy under the T6 state.
The peak aging state, namely the T6 state, refers to aging treatment time required by the aluminum alloy to reach the highest hardness.
The room temperature is 20-30 ℃, namely the temperature of the cold rolling treatment is 20-30 ℃; in a specific embodiment of the present invention, the temperature of the cold rolling treatment is 24 to 26 ℃.
In a specific embodiment of the present invention, the cold rolling process is a multi-pass cold rolling process; in the specific embodiment of the invention, the rolling passes of the multi-pass cold rolling treatment are 1-20 times; more preferably 2 to 10 times.
The multi-pass cold rolling treatment is adopted, so that the aluminum alloy is more uniformly deformed, the possibility of cracking of the aluminum alloy is reduced, and meanwhile, dislocation generated by deformation is more uniformly distributed in the aluminum alloy, thereby being beneficial to the follow-up aging.
In the specific embodiment of the present invention, the reduction per pass of the cold rolling treatment is not particularly required, provided that the aluminum alloy is not cracked.
Preferably, in the heat treatment method, the total deformation amount of the cold rolling treatment is 3-15%; more preferably 4 to 10%; more preferably, the content is 4.5 to 6%.
The invention firstly carries out solid solution treatment on the aluminum alloy, and aims to lead alloy elements (such as Mg, si, cu and the like) in the aluminum alloy to be solid-dissolved into an Al matrix so as to prepare for the subsequent aging treatment precipitation strengthening phase. Wherein, the higher the temperature of the solution treatment, the shorter the time of the solution treatment is required.
Preferably, in the heat treatment method, the temperature of the solution treatment is 520-580 ℃; further preferably from 540 to 560 ℃; even more preferably 540 to 550 ℃.
Preferably, in the heat treatment method, the solution treatment time is 0.3-3 hours; further preferably 0.5 to 2 hours; more preferably 0.8 to 1.5 hours.
After the solution treatment, quenching treatment is performed, so that the solution structure is rapidly cooled and kept at room temperature, and the aluminum alloy containing the supersaturated solid solution is obtained.
Preferably, in the heat treatment method, the quenching treatment mode is selected from water cooling.
In a specific embodiment of the invention, the quenching treatment is quenching in water at 20-30 ℃, wherein the quenching transfer is completed within 10 seconds.
After solution treatment, cold rolling treatment is carried out, dislocation is introduced into the aluminum alloy, then aging treatment is carried out, thermodynamic conditions are provided for precipitation of the strengthening phase through the aging treatment, and the precipitation phase is further grown.
Preferably, in the heat treatment method, the temperature of the aging treatment is 140-220 ℃; further preferably 160 to 200 ℃; more preferably 170 to 190 ℃.
Preferably, in the heat treatment method, the time of aging treatment is 0.3-12 h; further preferably 0.5 to 10 hours; more preferably 1 to 6 hours; more preferably 2 to 3 hours.
Preferably, in the heat treatment method, the alloy element of the aluminum alloy includes at least one of Mg, si, and Cu.
Preferably, in the heat treatment method, the aluminum alloy includes at least one of an Al-Mg-Si-Cu alloy, an Al-Mg-Si alloy; further preferably, in the heat treatment method, the aluminum alloy is selected from al—mg—si—cu alloys.
The heat treatment method is particularly suitable for Al-Mg-Si-Cu alloy. Preferably, the Al-Mg-Si-Cu alloy comprises the following alloy elements in percentage by mass: 0.1 to 0.5 percent of Cu, 0.7 to 1.5 percent of Mg and 0.3 to 1 percent of Si; further preferably, the Al-Mg-Si-Cu alloy comprises the following alloy elements in percentage by mass: 0.15-0.4% Cu, 0.8-1.2% Mg, 0.4-0.8% Si.
In a specific embodiment of the present invention, the Al-Mg-Si-Cu alloy is selected from 6xxx series aluminum alloys; in a specific embodiment of the invention, the 6xxx series aluminum alloy is selected from the group consisting of AA6061 aluminum alloys.
A second aspect of the present invention provides a heat treated aluminum alloy obtained by the heat treatment method according to the first aspect of the present invention.
In a specific embodiment of the invention, the hardness of the aluminum alloy after heat treatment in the peak aging state is 90-150 HV; in a more specific embodiment of the invention, the hardness of the aluminum alloy after heat treatment in the peak aging state is 100-120 HV; in a specific embodiment of the invention, the hardness of the aluminum alloy after heat treatment in the peak aging state is 105-110 HV.
In a specific embodiment of the invention, the yield strength sigma of the heat treated aluminum alloy in the peak aging state 0.2 250-320 MPa; in a more specific embodiment of the invention, the heat treated aluminum alloy has a yield strength sigma at peak aging 0.2 260-310 MPa; in a specific embodiment of the invention, the yield strength sigma of the aluminum alloy after heat treatment in the peak aging state 0.2 280-300 MPa.
In a specific embodiment of the invention, the yield strength sigma of the heat treated aluminum alloy in the peak aging state b 280-350 MPa; in a more specific embodiment of the invention, the heat treated aluminum alloy has a yield strength sigma at peak aging b 300-340 MPa; in a specific embodiment of the invention, the yield strength sigma of the aluminum alloy after heat treatment in the peak aging state b 310-320 MPa.
In the specific embodiment of the invention, the elongation delta of the aluminum alloy after heat treatment in the peak aging state is 10-16%; in a more specific embodiment of the invention, the elongation delta of the aluminum alloy after heat treatment in the peak aging state is 12-15%; in a specific embodiment of the invention, the elongation delta of the aluminum alloy after heat treatment in the peak aging state is 13-14%.
A third aspect of the invention provides the use of the heat treated aluminium alloy according to the second aspect of the invention as a structural material.
In particular embodiments of the present invention, the structural materials include those in the aerospace, aviation, transportation, construction, electromechanical, lightening, or commodity fields.
The beneficial effects of the invention are as follows: according to the invention, the aluminum alloy is subjected to small deformation cold rolling pretreatment at room temperature, the total deformation is 2-20%, dislocation is introduced, partial solute atoms are separated out along dislocation lines, the microstructure continuity is improved, the aging separation efficiency can be effectively improved, the time required by aging treatment is greatly shortened, the time required by the aluminum alloy to reach a peak aging state (T6 state) is shortened, the elongation of the aluminum alloy in the T6 state is greatly improved, and the strength and hardness are kept higher.
Specifically, compared with the prior art, the invention has the following advantages:
1. according to the heat treatment method provided by the invention, the solution treatment, the quenching treatment, the cold rolling treatment and the aging treatment are sequentially carried out on the aluminum alloy, so that compared with the traditional heat treatment process only comprising the solution treatment, the quenching treatment and the aging treatment, the aging treatment time required by the aluminum alloy to reach the T6 state is reduced, the treatment process period is short, the efficiency is high, and the energy consumption is low.
2. Compared with the traditional heat treatment process, the elongation of the aluminum alloy in the T6 state is improved by 70-80%, and the yield strength and the hardness of the aluminum alloy are basically equivalent. The invention improves the elongation percentage of the aluminum alloy without reducing the T6 state strength and the hardness of the aluminum alloy, greatly expands the application range of the aluminum alloy, and has wide application in serving as a structural material, such as the structural material in the fields of aerospace, aviation, transportation, construction, electromechanics, lightening or daily necessities.
Drawings
FIG. 1 is a graph showing temperature versus time for a heat treatment process in accordance with an embodiment of the present invention.
Detailed Description
The present invention will be described in further detail with reference to specific examples. It is also to be understood that the following examples are given solely for the purpose of illustration and are not to be construed as limitations on the scope of the invention, since various modifications and adaptations may be made by those skilled in the art in light of the teachings herein. The specific process parameters and the like described below are also merely examples of suitable ranges, i.e., one skilled in the art can make a selection within the suitable ranges by the description herein and are not intended to be limited to the specific data described below. The starting materials, reagents or apparatus used in the following examples and comparative examples were obtained from conventional commercial sources or by known methods unless otherwise specified.
In a specific embodiment of the present invention, there is provided a heat treatment method of an aluminum alloy, including the steps of:
(1) Solution treatment: carrying out solution treatment on the aluminum alloy for 0.1-4 hours at 520-580 ℃ to obtain the solution treated aluminum alloy;
(2) Quenching: quenching the aluminum alloy subjected to solution treatment in water at 20-30 ℃, wherein quenching transfer is completed within 10 seconds, and the aluminum alloy subjected to quenching treatment is obtained;
(3) Cold rolling: carrying out cold rolling treatment on the aluminum alloy after quenching treatment, wherein the total deformation is 2-20%, and obtaining the aluminum alloy after cold rolling treatment;
(4) Aging treatment: aging the aluminum alloy after cold rolling treatment at 140-220 ℃ for 0.3-12 h to obtain the aluminum alloy after heat treatment.
In the specific embodiment of the invention, the cold rolling treatment in the step (3) adopts multi-pass cold rolling treatment; in the specific embodiment of the invention, the rolling passes of the multi-pass cold rolling treatment are 1-20 times; more preferably 2 to 10 times.
In the specific embodiment of the present invention, the reduction per pass of the cold rolling treatment is not particularly required, provided that the aluminum alloy is not cracked.
In the specific embodiment of the invention, the adopted aluminum alloy is Al-Mg-Si-Cu alloy; in a more specific embodiment of the present invention, the aluminum alloy employed is a 6xxx series aluminum alloy; in an embodiment of the present invention, the aluminum alloy used is AA6061 aluminum alloy.
In a specific embodiment of the present invention, the room temperature is 24-26 ℃.
In a specific embodiment of the present invention, the test results are all average values, wherein the samples for hardness test are: national standard test samples with the thickness of 4mm, the width of 10mm and the gauge length of 35.73mm are tested, and the test result is the average value of seven test points; the tensile test uses a rectangular national standard pattern with a gauge length of 50mm, and the test result is the average value of three samples.
Example 1
The example provides a heat treatment method of aluminum alloy, comprising the following steps:
the Al-Mg-Si-Cu (AA 6061) aluminum alloy sample was solution-treated at 540℃for 1 hour, immediately water-quenched to room temperature, and then cold-rolled to be deformed at room temperature, with a total deformation of 5%. And (3) placing the cold-rolled and deformed sample into an electrothermal constant-temperature blast drying oven, aging for 300min at 180 ℃, recording hardness change every 30min, and carrying out tensile property experiments on the sample in a peak aging state (T6 state). The experimental results are: the hardness of the sample reaches a peak value when being aged for 2 hours at 180 ℃, the hardness is 108+/-5 HV, the yield strength is 287.9+/-2 MPa, and the elongation is 13.6+/-1%.
Comparative example 1
The example provides a heat treatment method of aluminum alloy, comprising the following steps:
Al-Mg-Si-Cu (AA 6061) aluminum alloy samples were solution treated at 540℃for 1 hour, immediately water quenched to room temperature, tested for hardness and tensile properties tested. The test results are: the hardness was 66HV, the yield strength was 84.8MPa, and the elongation was 19.8%.
Comparative example 2
The example provides a heat treatment method of aluminum alloy, comprising the following steps:
the Al-Mg-Si-Cu (AA 6061) aluminum alloy samples were solution treated at 540 ℃ for 1 hour, immediately water quenched to room temperature, then cold rolled deformed at room temperature with a total deformation of 5%, tested for hardness and tensile properties tested. The test results are: the hardness was 86HV, the yield strength was 166.8MPa, and the elongation was 22.2%.
Comparative example 3
The example provides a heat treatment method of aluminum alloy, comprising the following steps:
the Al-Mg-Si-Cu (AA 6061) aluminum alloy sample was solution treated at 540 ℃ for 1 hour, immediately quenched to room temperature, then the sample was put into an electrothermal constant temperature blast drying oven, aged at 180 ℃ for 300min, the hardness change was recorded every 30min, and the tensile property test was performed on the sample in the peak aging state (T6 state). Experimental results: the hardness of the sample reaches a peak value when being aged for 4 hours at 180 ℃, the hardness is 107HV, the yield strength is 287.5MPa, and the elongation is 7.8%.
The test results of example 1 and comparative examples 1 to 3 are shown in table 1.
Table 1 test results of example 1 and comparative examples 1 to 3
As can be seen from Table 1, the samples heat treated in example 1 reached the T6 state at 120min of aging, i.e., the hardness reached the peak, and the aging time required to reach the T6 state was reduced by 50% as compared with the samples of comparative example 3 using the conventional heat treatment process. And the elongation at T6 state of example 1 was 13.6%, the elongation was improved by 74.4% as compared with the sample of comparative example 3 using the conventional heat treatment process.
According to the heat treatment method, the solution treatment, the quenching treatment, the cold rolling treatment and the aging treatment are sequentially carried out on the aluminum alloy, so that compared with the traditional heat treatment process only comprising the solution treatment, the quenching treatment and the aging treatment, the aging treatment time required by the aluminum alloy to reach the T6 state is reduced, the treatment process period is short, the efficiency is high, and the energy consumption is low; in addition, the elongation percentage of the aluminum alloy obtained after heat treatment in the T6 state is greatly improved, compared with the traditional heat treatment process, the elongation percentage of the aluminum alloy obtained in the invention in the T6 state is improved by 70-80%, and the yield strength and the hardness are basically equivalent.
The aluminum alloy obtained by the treatment method disclosed by the invention has the advantages that the T6 state strength and the hardness of the aluminum alloy are not reduced, the elongation rate of the aluminum alloy is improved, the application range of the aluminum alloy is greatly expanded, and the aluminum alloy can be widely applied to structural materials, such as structural materials in the fields of aerospace, aviation, transportation, construction, electromechanics, lightening or daily necessities.
Claims (10)
1. A heat treatment method of an aluminum alloy, comprising the steps of: sequentially carrying out solution treatment, quenching treatment, cold rolling treatment and aging treatment on the aluminum alloy to obtain the heat-treated aluminum alloy; the total deformation of the cold rolling treatment is 2-20%.
2. The heat treatment method according to claim 1, wherein the temperature of the solution treatment is 520 to 580 ℃;
and/or the solution treatment time is 0.1-4 h.
3. The heat treatment method according to claim 1, wherein the quenching treatment is performed by a method selected from the group consisting of water cooling.
4. The heat treatment method according to claim 1, wherein the temperature of the aging treatment is 140 to 220 ℃;
and/or the time of the aging treatment is 0.3-12 h.
5. The heat treatment method according to claim 1, wherein the alloy element of the aluminum alloy includes at least one element of Mg, si, cu.
6. The heat treatment method according to claim 1, wherein the aluminum alloy includes at least one of an Al-Mg-Si-Cu alloy and an Al-Mg-Si alloy.
7. A heat-treated aluminum alloy obtained by the heat treatment method according to any one of claims 1 to 6.
8. The heat treated aluminum alloy according to claim 7, wherein the heat treated aluminum alloy has an elongation δ of 10 to 16% in a peak aging state.
9. The heat treated aluminum alloy as recited in claim 7, wherein said heat treated aluminum alloy has a yield strength σ at peak aging b 280-350 MPa.
10. Use of the heat treated aluminum alloy of any of claims 7-9 as a structural material.
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