CN112626384A - Aluminum alloy with medium strength and high plasticity as well as preparation method and application thereof - Google Patents
Aluminum alloy with medium strength and high plasticity as well as preparation method and application thereof Download PDFInfo
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- 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
- C22F1/05—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 of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
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Abstract
The invention belongs to the technical field of metal material preparation, and discloses a medium-strength high-plasticity aluminum alloy, and a preparation method and application thereof, wherein the medium-strength high-plasticity aluminum alloy comprises, by weight, 0.6-1.0% of Mg, 0.75-1.1% of Si, 0.1-0.3% of Cu, 0.2-0.4% of Mn, 0.05-0.2% of Ge, 0.1-0.3% of Er, 0.1-0.25% of Zr, and less than or equal to 0.5% of Fe. By adding trace Ge element and improving alloyThe solid solubility of Er element in ingot casting matrix is reduced, and primary Al is reduced3Er phase content is increased, and secondary Al formation is realized3Content of (Er, Zr) phase. The content and the proportion of Mg, Si and Cu elements are optimized, aging Cu-Si-Ge early clusters are formed with vacancies, the dispersion precipitation of a strengthening phase is promoted, and the alloy strength is improved; meanwhile, the formation of a Q phase is avoided, and good plasticity and corrosion resistance are maintained; through the multi-scale microstructure design, the obtained aluminum alloy with medium strength and high plasticity is suitable for being used as the aluminum alloy for the automobile structural part or applied to the section bar of the automobile structural part.
Description
Technical Field
The invention belongs to the technical field of metal material preparation, and particularly relates to a medium-strength high-plasticity aluminum alloy, and a preparation method and application thereof.
Background
With the increasing awareness of energy conservation and emission reduction in various countries in the world, the light weight of automobiles is an important measure for energy conservation and emission reduction. On the other hand, 6xxx series aluminum alloys (i.e., Al — Mg — Si series alloys) are the first choice for the weight reduction of the new generation of automobiles due to their moderate strength and high formability. At present, AA6016, AA6111, AA6022 and other aluminum alloys generally have higher plasticity and baking varnish hardening characteristics, so that the alloy plate has better anti-sinking capability), and is suitable for processing of automobile body outer plates.
The strength of Al-Mg-Si series aluminum alloy is generally contradictory to the plasticity and corrosion resistance. The content of Mg and Si elements is improved, but the plasticity and corrosion resistance of the alloy are reduced, and the processing performance is greatly reduced. The content of Mg and Si elements is generally required to be controlled to obtain high formability of the alloy. The addition of Cu element significantly increases the strength and the fast response capability, such as 6111 alloy, but reduces the corrosion resistance of the material. Mn element can form Al (Mn, Fe) Si and the like, can inhibit alloy recrystallization, improve the strength, but reduce the alloy plasticity; in particular, a coarse Mn-containing phase is easy to become an alloy crack source region, and the plasticity and fatigue performance of the material are obviously reduced. The rare earth Er element can form Al3M dispersed phase to refine grains. However, a primary Al3Er phase and a secondary Al3Er phase are formed in the preparation process, and only the secondary Al3Er phase can effectively inhibit the growth of recrystallized grains. How to obtain high-content secondary Al3Er phase is the key for developing Er-containing aluminum alloy.
Disclosure of Invention
The invention provides a medium-strength high-plasticity aluminum alloy, a preparation method and application thereof, which are used for solving one or more technical problems in the prior art and at least providing a beneficial selection or creation condition. The invention designs a novel Al-Mg-Si alloy and a preparation method thereof based on a multi-element microalloying principle so as to improve the strength and the plasticity of the alloy.
In order to overcome the technical problems, the technical scheme adopted by the invention is as follows:
the aluminum alloy contains a main component Al and also comprises the following components in percentage by weight: 0.6 to 1.0 percent of Mg, 0.75 to 1.1 percent of Si, 0.1 to 0.3 percent of Cu, 0.2 to 0.4 percent of Mn, 0.05 to 0.2 percent of Ge, 0.1 to 0.3 percent of Er, 0.1 to 0.25 percent of Zr and less than or equal to 0.5 percent of Fe.
The invention reduces primary Al by adding trace Ge element and improving the solid solubility of Er element3Er phase content, increased secondary Al formation3Content of (Er, Zr) phase; three-stage homogenization heat treatment is adopted, particularly the first-stage homogenization treatment at the temperature of 300-3The (Er, Zr) phase inhibits the growth of recrystallized grains, refines the grains and improves the plasticity of the alloy; the content and the proportion of Mg, Si and Cu elements are optimized, aging Cu-Si-Ge early clusters are formed with vacancies, the dispersion and precipitation of a strengthening phase are promoted, the alloy strength is improved, a Q phase and an equal Cu-containing phase are avoided, and the good plasticity and the corrosion resistance are maintained.
Preferably, the aluminum alloy contains a main component Al, and further comprises the following components in percentage by weight: 0.8 to 1.0 percent of Mg, 0.9 to 1.1 percent of Si, 0.15 to 0.25 percent of Cu, 0.2 to 0.4 percent of Mn, 0.05 to 0.1 percent of Ge, 0.15 to 0.25 percent of Er, 0.15 to 0.25 percent of Zr and less than or equal to 0.5 percent of Fe.
As a further improvement of the above aspect, the mass ratio of Mg to Si is (0.7-1): 1.
As a further improvement of the above aspect, the mass ratio of Mn to Fe is (0.5-0.6): 1. The mass ratio of Mn to Fe is controlled to promote the transformation of spherical beta-AlMnFeSi aiming at the alpha-AlFeSi, the phase size of the beta-AlMnFeSi is refined in the hot processing process, and the probability of crack initiation is reduced.
As a further improvement of the scheme, the content of impurity elements in the aluminum alloy is less than or equal to 0.15 percent by weight. The impurity element includes Ti.
The preparation method of the aluminum alloy comprises the following steps:
1) preparing raw materials: weighing the raw materials with the formula content of the aluminum alloy for later use;
2) preparing an alloy ingot: smelting, refining and pouring the raw materials to obtain an alloy ingot;
3) three-stage homogenization heat treatment: carrying out three-stage homogenization heat treatment on the alloy ingot obtained in the step 2);
4) quenching treatment: carrying out solid solution and quenching treatment on the sample obtained in the step 3);
5) aging treatment: carrying out aging treatment on the quenched aluminum alloy under the isothermal condition to obtain the aluminum alloy;
in the step 3), the three-stage homogenization heat treatment process comprises the following steps: heating the alloy ingot at a heating rate of 20-50 ℃/h, and keeping the temperature for 12-16h when the temperature is increased from room temperature to 300-400 ℃; then continuously heating to 420-480 ℃ at the speed of 20-50 ℃/h, and preserving the heat for 15-30 h; then continuously heating to 500-540 ℃ at the heating rate of 20-50 ℃/h, and preserving the heat for 15-30 h; finally, cooling to below 100 ℃ at a cooling rate of 20-50 ℃/h, and finishing.
In the invention, the smelting process of the raw materials comprises the following steps: firstly melting a high-purity aluminum ingot at the temperature of 735-755 ℃, then adding Al-Mn10, Al-Cu50, Al-Si15, Al-Ge6, Al-Er10 and Al-Zr5 intermediate alloy, and adding 99.99% of magnesium and a covering agent after the intermediate alloy is melted to obtain completely melted metal.
The refining process comprises the following steps: adding hexachloroethane into the completely molten metal solution for degassing treatment, fully stirring, maintaining the metal temperature in the range of 730-750 ℃ during refining, fully standing after refining, and keeping the standing time for not less than 30 minutes;
the pouring process comprises the following steps: when the temperature of the molten metal is reduced to 700-720 ℃, then when the temperature of the melt is reduced to about 720 ℃, adding Al-5 wt% Ti-1 wt% B grain refiner, stirring properly, fully standing, and pouring the molten metal into a metal mold with the temperature of 400-450 ℃ to obtain an alloy ingot;
solution treatment: carrying out solution treatment on the cold-rolled sheet, and the specific process comprises the following steps: carrying out solid solution treatment for 15-45min in a heat treatment furnace with the temperature of 540-;
quenching treatment: and quenching the alloy sample subjected to the solution treatment into water at room temperature from the solution treatment temperature.
As a further improvement of the scheme, the treatment processes between the step 3) and the step 4) are hot rolling treatment and cold rolling treatment.
The hot rolling deformation process comprises the following steps: carrying out hot rolling on the alloy ingot: the initial rolling temperature is 530-545 ℃, the pass reduction is 4-32%, the total hot rolling deformation is more than 92%, and the final rolling temperature is lower than 320 ℃ to obtain a hot rolled plate;
the process of the cold rolling treatment is actually cold rolling deformation, intermediate annealing and cold rolling deformation, namely: taking out the hot rolled plate, wherein the cold rolling deformation pass reduction is 10-35%, and the total deformation is 30-60%; the intermediate annealing is carried out by heating to 350-450 ℃ at the heating rate of 80-120 ℃/min for 1-4h, and then directly taking out for air cooling; and (3) continuously performing cold rolling deformation, wherein the total deformation is 50-75%, and the pass reduction is 15-30%, so as to obtain the cold-rolled sheet.
As a further improvement of the scheme, in the step 5), the temperature of the aging treatment is 160-190 ℃, and the time of the aging treatment is 6-14 h.
As a further improvement of the scheme, the temperature of the aging treatment is 170-180 ℃, and the time length of the aging treatment is 12-18 h.
In the step (5), three-stage homogenization process is adopted, wherein the first stage isThe heat preservation is carried out for 12 to 16 hours at the temperature of 300-3(Er, Zr) phase.
The aluminum alloy of the invention is suitable for being used as an aluminum alloy for automobile structural parts or applied to profiles thereof.
The invention has the beneficial effects that:
the invention provides a medium-strength high-plasticity aluminum alloy and a preparation method and application thereof, and compared with the prior art, the invention has the following advantages:
(1) by adding trace Ge element and improving the solid solubility of Er element in the alloy ingot casting matrix, primary Al is reduced3Er phase content is increased, and secondary Al formation is realized3Content of (Er, Zr) phase.
(2) By optimizing the content and proportion of Mg, Si and Cu elements, aging Cu-Si-Ge early clusters are formed with vacancies, strengthening phase dispersion is promoted, and the alloy strength is improved; meanwhile, the formation of a Q phase is avoided, and good plasticity and corrosion resistance are maintained;
(3) through the multi-scale microstructure design, the obtained aluminum alloy with medium strength and high plasticity is suitable for being used as the aluminum alloy for the automobile structural part or applied to the section bar of the automobile structural part.
Drawings
FIG. 1 is a graph showing the aged hardness of the aluminum alloys obtained in example 1 and comparative example 1.
Detailed description of the invention
The present invention is specifically described below with reference to examples in order to facilitate understanding of the present invention by those skilled in the art. It should be particularly noted that the examples are given solely for the purpose of illustration and are not to be construed as limitations on the scope of the invention, as non-essential improvements and modifications to the invention may occur to those skilled in the art upon reading the foregoing disclosure. Meanwhile, the raw materials mentioned below are not specified in detail and are all commercially available products; the process steps or extraction methods not mentioned in detail are all process steps or extraction methods known to the person skilled in the art.
Examples 1 to 4 and comparative examples 1 to 2
Table 1-1 compositions and weight percentages of the obtained aluminum alloys of examples 1 to 4 (ingot numbers corresponding to # 1 to # 4, respectively) and comparative examples 1 to 2 (ingot numbers corresponding to # 5 to # 6, respectively).
| Ingot number | Group of | Mg | Si | Cu | Ge | Er | Zr | Mn | Fe | Al |
| 1# | Example 1 | 0.85 | 0.95 | 0.20 | 0.08 | 0.15 | 0.15 | 0.40 | <0.5 | Balance of |
| 2# | Example 2 | 0.95 | 0.95 | 0.20 | 0.1 | 0.15 | 0.15 | 0.35 | <0.5 | Balance of |
| 3# | Example 3 | 0.85 | 1.0 | 0.20 | 0.05 | 0.15 | 0.15 | 0.35 | <0.5 | Balance of |
| 4# | Example 4 | 1.0 | 0.9 | 0.25 | 0.06 | 0.15 | 0.15 | 0.40 | <0.5 | Balance of |
| 5# | Comparative example 1 | 0.85 | 0.95 | 0.20 | - | 0.15 | 0.15 | 0.40 | <0.5 | Balance of |
| 6# | Comparative example 2 | 0.85 | 0.95 | 0.20 | 0.8 | - | 0.15 | 0.40 | <0.5 | Balance of |
The preparation method of the aluminum alloy comprises the following steps:
1) proportioning raw materials: the raw materials are proportioned according to the components and the weight percentage thereof described in the table 1-1, and 5# alloy without Ge element and 6# alloy without Er element are used as comparison;
2) smelting raw materials: firstly melting a high-purity aluminum ingot at the temperature of 745 ℃, then adding Al-Mn10, Al-Cu50, Al-Si15, Al-Ge6, Al-Er10 and Al-Zr5 intermediate alloy, and adding 99.99% of magnesium and a covering agent after the intermediate alloy is melted;
3) refining: adding hexachloroethane into the completely molten metal solution for degassing treatment, fully stirring, maintaining the metal temperature within the range of 740 ℃ during refining, fully standing after refining, and keeping the standing time for not less than 30 minutes;
4) pouring: when the temperature of the molten metal is reduced to 710 ℃, then the temperature of the melt is reduced to about 700 ℃, Al-5 wt% Ti-1 wt% B grain refiner is added and properly stirred, and the molten metal is poured into a metal mold with the temperature of 420-450 ℃ after fully standing, so as to obtain an alloy ingot;
5) three-stage homogenization heat treatment: heating the alloy sample after smelting and casting at the heating rate of 30 ℃/h, and preserving heat for 16h when the temperature reaches 300-; continuing to heat to 460 ℃ at the speed of 30 ℃/h, preserving heat for 18h, continuing to heat to 520 ℃ at the speed of 30 ℃/h, preserving heat for 24h, and then taking out the sample when the temperature is reduced to 100 ℃ along with the furnace at the speed of 30 ℃/h;
6) hot rolling deformation: carrying out hot rolling on the sample taken out in the step 5): the initial rolling temperature is 540 ℃, the pass reduction is 4-12%, the total deformation of hot rolling is more than 92%, and the final rolling temperature is lower than 320 ℃ to obtain a hot rolled plate;
7) cold rolling deformation, intermediate annealing and cold rolling deformation: taking out the hot rolled plate obtained in the step 6), wherein the cold rolling deformation pass reduction is 10-15%, and the total deformation is 60%; the intermediate annealing is carried out by raising the temperature to 400 ℃ at the heating rate of 100 ℃/min for 2h, and then directly taking out for air cooling; the total deformation of the continuous cold rolling deformation is 75-85%, and the pass reduction is 15-30%.
8) Solution treatment: carrying out solution treatment on the cold-rolled sheet obtained in the step 7), and carrying out solution treatment for 45min in a 545 ℃ heat treatment furnace, wherein the temperature rise rate of the sample is more than 120 ℃/min;
9) quenching treatment: quenching the alloy sample subjected to the solution treatment in the step 8) into water at room temperature from the solution treatment temperature;
10) aging treatment: transferring the sample obtained in the step 9) into an isothermal aging furnace at 180 ℃ for aging treatment for 12 hours, and marking the obtained aluminum alloy finished products as 1# to 6# aluminum alloys respectively.
Product performance testing
The aluminum alloy plates obtained in examples 1-4 and comparative examples 1-2 and subjected to aging treatment were tested for tensile strength, yield strength and elongation. The results obtained are shown in the following tables 1-2.
Tables 1 to 2
As can be seen from tables 1-2: the tensile strength of the rapid aging response aluminum alloy (1# -4#) is over 385MPa, the elongation is over 19.0%, and the 5# and 6# alloys without Ge element and Er element are reduced in strength and plasticity. Therefore, the mechanical property of the rare earth aluminum alloy reaches the requirement of an automobile structure, and the rare earth aluminum alloy has wide application prospect in the field of automobile structure aluminum alloy products.
Further, FIG. 1 is an aging strength curve of the aluminum alloys obtained in example 1 and comparative example 1. As can be seen from FIG. 1, the tensile strength of the aluminum alloy obtained in example 1 reaches 390MPa after isothermal aging at 180 ℃ for 12h, while the tensile strength of the alloy obtained in comparative example 1 is 374MPa without adding Ge trace elements, and the age hardening rate is lower.
It will be obvious to those skilled in the art that many simple derivations or substitutions can be made without inventive effort without departing from the inventive concept. Therefore, simple modifications to the present invention by those skilled in the art according to the present disclosure should be within the scope of the present invention. The above embodiments are preferred embodiments of the present invention, and all similar processes and equivalent variations to those of the present invention should fall within the scope of the present invention.
Claims (10)
1. The aluminum alloy is characterized by comprising the following components in percentage by weight: 0.6 to 1.0 percent of Mg, 0.75 to 1.1 percent of Si, 0.1 to 0.3 percent of Cu, 0.2 to 0.4 percent of Mn, 0.05 to 0.2 percent of Ge, 0.1 to 0.3 percent of Er, 0.1 to 0.25 percent of Zr and less than or equal to 0.5 percent of Fe.
2. The aluminum alloy of claim 1, comprising, in weight percent: 0.8 to 1.0 percent of Mg, 0.9 to 1.1 percent of Si, 0.15 to 0.25 percent of Cu, 0.2 to 0.4 percent of Mn, 0.05 to 0.1 percent of Ge, 0.15 to 0.25 percent of Er, 0.15 to 0.25 percent of Zr and less than or equal to 0.5 percent of Fe.
3. The aluminum alloy of claim 1 or 2, wherein the mass ratio of Mg to Si is (0.7-1): 1.
4. The aluminum alloy of claim 1 or 2, wherein the mass ratio of Mn to Fe is (0.5-0.6): 1.
5. The aluminum alloy of claim 1 or 2, wherein the aluminum alloy has a content of impurity elements of 0.15% by weight or less.
6. A method of producing an aluminium alloy according to any one of claims 1 to 5, comprising the steps of:
1) preparing raw materials: weighing the raw materials with the formula content of the aluminum alloy for later use;
2) preparing an alloy ingot: smelting, refining and pouring the raw materials to obtain an alloy ingot;
3) three-stage homogenization heat treatment: carrying out three-stage homogenization heat treatment on the alloy ingot obtained in the step 2), and taking out a sample;
4) quenching treatment: carrying out solid solution and quenching treatment on the sample obtained in the step 3);
5) aging treatment: carrying out aging treatment on the quenched aluminum alloy under the isothermal condition to obtain the aluminum alloy;
in the step 3), the three-stage homogenization heat treatment process comprises the following steps: heating the alloy ingot at a heating rate of 20-50 ℃/h, and keeping the temperature for 12-16h when the temperature is increased from room temperature to 300-400 ℃; then continuously heating to 420-480 ℃ at the speed of 20-50 ℃/h, and preserving the heat for 15-30 h; then continuously heating to 500-540 ℃ at the heating rate of 20-50 ℃/h, and preserving the heat for 15-30 h; finally, cooling to below 100 ℃ at a cooling rate of 20-50 ℃/h, and finishing.
7. The method according to claim 4, wherein the processes further included between step 3) and step 4) are a hot rolling process and a cold rolling process.
8. The preparation method according to claim 4, wherein in the step 5), the temperature of the aging treatment is 160-190 ℃, and the time length of the aging treatment is 6-14 h.
9. The method for preparing the alloy material according to claim 8, wherein the temperature of the aging treatment is 170-180 ℃, and the time period of the aging treatment is 12-18 h.
10. Use of an aluminium alloy according to any one of claims 1 to 5 as an aluminium alloy for automotive structural parts or in profiles thereof.
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| CN113502417A (en) * | 2021-07-14 | 2021-10-15 | 无锡华星机电制造有限公司 | High-heat-strength aluminum-silicon alloy material and manufacturing method thereof |
| CN114540670A (en) * | 2022-01-27 | 2022-05-27 | 中铝材料应用研究院有限公司 | Aluminum alloy for forging and preparation method thereof |
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Application publication date: 20210409 |