CN116162833A - High-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy and preparation method thereof - Google Patents
High-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy and preparation method thereof Download PDFInfo
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- 229910001371 Er alloy Inorganic materials 0.000 title claims abstract description 36
- 238000002360 preparation method Methods 0.000 title claims abstract description 33
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 85
- 239000000956 alloy Substances 0.000 claims abstract description 85
- 238000010438 heat treatment Methods 0.000 claims abstract description 44
- 230000032683 aging Effects 0.000 claims abstract description 33
- 238000000034 method Methods 0.000 claims abstract description 11
- 239000002994 raw material Substances 0.000 claims description 33
- 238000005266 casting Methods 0.000 claims description 28
- 239000000243 solution Substances 0.000 claims description 26
- 229910052691 Erbium Inorganic materials 0.000 claims description 24
- 238000001816 cooling Methods 0.000 claims description 22
- 239000006104 solid solution Substances 0.000 claims description 20
- 229910052802 copper Inorganic materials 0.000 claims description 19
- 229910052751 metal Inorganic materials 0.000 claims description 19
- 239000002184 metal Substances 0.000 claims description 19
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 18
- 239000002893 slag Substances 0.000 claims description 10
- 229910052786 argon Inorganic materials 0.000 claims description 9
- 238000007670 refining Methods 0.000 claims description 9
- 238000003756 stirring Methods 0.000 claims description 9
- 229910052709 silver Inorganic materials 0.000 claims description 7
- 239000012535 impurity Substances 0.000 claims description 6
- 238000000265 homogenisation Methods 0.000 abstract description 10
- 229910000838 Al alloy Inorganic materials 0.000 abstract description 8
- 229910019015 Mg-Ag Inorganic materials 0.000 abstract description 8
- 239000000463 material Substances 0.000 abstract description 8
- 239000007769 metal material Substances 0.000 abstract 1
- 230000000052 comparative effect Effects 0.000 description 20
- 239000002245 particle Substances 0.000 description 8
- 238000003917 TEM image Methods 0.000 description 4
- 238000003483 aging Methods 0.000 description 4
- 230000005496 eutectics Effects 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 4
- 238000002844 melting Methods 0.000 description 4
- 230000008018 melting Effects 0.000 description 4
- 238000005498 polishing Methods 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 238000010791 quenching Methods 0.000 description 4
- 230000000171 quenching effect Effects 0.000 description 4
- 238000003723 Smelting Methods 0.000 description 3
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 210000001787 dendrite Anatomy 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 239000000155 melt Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 230000003014 reinforcing effect Effects 0.000 description 2
- 239000007858 starting material Substances 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910017818 Cu—Mg Inorganic materials 0.000 description 1
- 230000006978 adaptation Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 229910052761 rare earth metal Inorganic materials 0.000 description 1
- 150000002910 rare earth metals Chemical class 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
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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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Abstract
The invention belongs to the field of metal materials, relates to a cast aluminum alloy, and provides a preparation method of a high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy and a corresponding heat treatment process. The invention adds trace Er element into Al-Cu-Mg-Ag alloy, and adopts a series of heat treatment processes of homogenization treatment, secondary solution treatment and aging treatment. The invention relates to a special aging treatment. After the alloy passes through the aging temperature, the room temperature mechanical property of the material is improved, and meanwhile, the high temperature mechanical property of the Al-Cu-Mg-Ag-Er alloy is obviously improved.
Description
Technical Field
The invention relates to the technical field of cast aluminum alloy, in particular to a high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy and a preparation method thereof.
Background
Recent researches have found that the addition of trace Ag element can significantly enhance the age hardening effect and high temperature creep resistance of the Al-Cu-Mg alloy with high Cu/Mg ratio, because the addition of Ag element promotes the alloy to be in {111} Al Dispersed hexagonal disk shaped omega phase (Al) 2 Cu). Since the slip plane of Al is mainly {111} Al In the surface, the precipitated phase can effectively prevent dislocation from sliding, so that the Al-Cu-Mg-Ag alloy has higher room temperature strength. However, since the omega phase is a metastable phase, it is typically produced during low temperature (150 ℃ C. To 200 ℃ C.) aging of the alloy. Therefore, when the service temperature exceeds 200 ℃, the nanoscale omega phase can be rapidly destabilized and coarsened along with the increase of the temperature, so that the mechanical property of the alloy is rapidly deteriorated, and the service temperature of the Al-Cu-Mg-Ag alloy is generally lower than 200 ℃.
There are two main traditional methods for improving the high temperature mechanical properties of aluminum alloys: first, by introducing high melting point second phase particles, it is ensured that sufficient second phase particles remain at high temperatures, thereby providing high temperature stability. However, the problems are not small, and the plasticity of the material is damaged due to a large amount of reinforcing phase particles, so that the reinforcing phase particles are difficult to use as structural materials. The other method is to add trace high temperature resistant elements (X= Er, sc, zr, ti, mn, etc.) into the Al alloy, and form Al with better thermal stability in the preparation and solid solution stages of the alloy 3 X particles to improve the mechanical properties of the alloy. However, since the solid solubility of these elements is low, al is formed 3 The volume fraction of X particles is generally not high, and the high temperature resistance of the alloy is difficult to effectively improve. On the other hand, al 3 The presence of X particles significantly reduces the plasticity of the material.
In summary, the existing method for improving the high-temperature mechanical property of the Al-Cu-Mg-Ag alloy has limited contribution to the thermal stability of the material and obviously reduces the plasticity of the material.
Disclosure of Invention
The invention aims to provide a high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy and a preparation method thereof. The Al-Cu-Mg-Ag-Er alloy obtained by the preparation method provided by the invention not only has excellent yield strength, tensile strength and extensibility at room temperature, but also has good mechanical properties at high temperature.
In order to achieve the aim of the invention, the high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy contains 3.0 to 7.0 percent of Cu,0.3 to 0.6 percent of Mg,0.3 to 0.6 percent of Ag,0.1 to 0.5 percent of Er, and the balance of Al and unavoidable impurity elements, wherein the total mass percent of the impurity elements is not more than 0.3 percent.
The raw materials are introduced in a mode of pure Al, pure Ag, al-50% Cu intermediate alloy, al-10% Mg intermediate alloy and Al-6% Er intermediate alloy.
The preparation method of the high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy comprises the following steps:
1) Heating pure Al to 750-780 ℃, reducing the temperature to 730 ℃ after the pure Al is completely melted, adding Al-50% Cu intermediate alloy, al-10% Mg intermediate alloy, al-6% Er intermediate alloy and pure Ag, refining all raw materials for 30-40 min under the conditions of argon and stirring after the raw materials are melted, standing for 9-15 min to float slag, and pouring molten metal into a metal mold after skimming to obtain castings;
2) Homogenizing the obtained casting at 450-470 ℃ for 3-6 h, and air-cooling to room temperature;
3) Heating from room temperature to 505-515 ℃ at a heating rate of 1-3 ℃/min, and preserving heat for 10-14 h to perform first-stage solid solution treatment;
4) Then heating from 505-515 ℃ to 540-560 ℃ at a heating rate of 1-3 ℃/min, and preserving heat for 10-14 h to perform second-stage solution treatment;
5) And then aging the castings subjected to the second-stage solution treatment at 110-130 ℃ for 0.5-30 hours, and air-cooling to room temperature to obtain the high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy.
The high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy prepared by the preparation method is characterized in that the yield strength at 25 ℃ is 250-350 MPa, and the elongation is 12-15%; the hardness after the heat exposure at 300 ℃ is improved by 20 to 30 percent compared with the traditional preparation method.
The beneficial effects are that:
the invention obtains a novel precipitated phase by adding a certain amount of rare earth Er into Al-Cu-Mg-Ag aluminum alloy and adopting a heat treatment process of homogenization, secondary solution treatment and aging treatment, which is different from the traditional {111} Al omega-Al of face 2 Cu precipitates in {100}, such precipitates are Al The particles are separated out on the surface and have smaller size and number densityLarger. Therefore, the Al-Cu-Mg-Ag-Er alloy has better room temperature strength and greatly improves the elongation rate; meanwhile, the novel Al-Cu-Mg-Ag-Er alloy precipitated phase has good thermal stability, and the high-temperature mechanical property of the Al-Cu-Mg-Ag-Er alloy is obviously improved. Unlike conventional process of adding Er element into Al-Cu-Mg-Ag aluminum alloy, the present invention adopts homogenization and secondary solution treatment to eliminate eutectic phase of Er and Cu as much as possible and makes full use of Cu and Er element in the alloy. The homogenization treatment is used for ensuring that the structure of the alloy is uniformly distributed and preventing the alloy from being locally overburned during solution treatment; the first-stage solid solution treatment is to eliminate dendrites containing Cu, so that all Cu elements are dissolved into a matrix in a solid solution way, and preparation is carried out for forming a precipitated phase by low-temperature aging; the second-stage solution treatment is to eliminate eutectic phases as much as possible on the premise of ensuring no overburning, and reduce the influence of Er addition on the room-temperature mechanical properties of the Al-Cu-Mg-Ag aluminum alloy. With special ageing treatment, in {100} Al A large amount of strengthening phase is evenly dispersed and precipitated on the surface, and the precipitation has smaller size and larger number density compared with the traditional omega phase. Therefore, the room temperature mechanical property of the material can be effectively improved, the yield strength at 25 ℃ is 250-350 MPa, and the elongation is 12-15%. Meanwhile, the precipitated phase has good stability at high temperature. Experiments show that the hardness of the precipitation is improved by 10 to 20HV under 300 ℃ heat exposure compared with the traditional omega phase.
Drawings
FIG. 1 is a TEM image of an Al-Cu-Mg-Ag-Er alloy after 4h aging of comparative example 1 (FIG. 1-a) and example 1 (FIG. 1-b);
FIG. 2 is a graph of aging time versus hardness statistics for example 2 and comparative example 2 after heat exposure at 300℃for 4-30 hours.
Fig. 3 is a TEM image of example 2 and comparative example 2 after heat exposure at 300 ℃ for 8 h.
Detailed Description
The invention provides a preparation method of a high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy, which comprises the following components (wt.%):
3.0 to 7.0 percent of Cu,0.3 to 0.6 percent of Mg,0.3 to 0.6 percent of Ag,0.1 to 0.5 percent of Er, and the balance of Al and unavoidable impurity elements, wherein the total mass percentage of the impurity elements is not more than 0.3 percent; the raw materials are introduced in a mode of pure Al, pure Ag, al-50% Cu intermediate alloy, al-10% Mg intermediate alloy and Al-6% Er intermediate alloy.
The preparation method comprises the following steps:
preparing raw materials according to the components of the Al-Cu-Mg-Ag-Er alloy;
the preparation raw materials are placed in a smelting furnace to be melted, refined and deslagged, and are poured in a metal mold, so that a casting is finally obtained;
and sequentially carrying out homogenization treatment, secondary solution treatment and aging treatment on the casting to obtain the Al-Cu-Mg-Ag-Er alloy.
In the present invention, the raw materials used in the present invention are preferably commercially available products unless otherwise specified.
The high-temperature resistant Al-Cu-Mg-Ag-Er alloy provided by the invention comprises 3.0-7.0% by mass of Cu, preferably 3.5-6.5% by mass and further preferably 4.5-5% by mass.
The high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy provided by the invention comprises 0.3-0.6% by mass of Mg, and preferably 0.4-0.6% by mass.
The high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy provided by the invention comprises 0.3-0.6% of Ag by mass percent, and preferably 0.4-0.6% of Ag by mass percent.
The high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy provided by the invention comprises 0.1-0.5% by mass of Er, and preferably 0.2-0.4% by mass.
The preparation method comprises the steps of firstly preparing raw materials according to the components of the high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy, and preferably polishing the raw materials before using; the polishing operation of the invention aims at removing the oxide layer and the greasy dirt on the surface of the raw material.
After preparing the preparation raw materials, the preparation raw materials are sequentially melted, refined, deslagged and poured to obtain the casting.
In the present invention, the melting includes: heating pure Al to 750-780 ℃, reducing the temperature to 730 ℃ after the pure Al is completely melted, adding Al-50% Cu intermediate alloy, al-10% Mg intermediate alloy, al-6% Er intermediate alloy and pure Ag, refining all raw materials for 30-40 min under the conditions of argon and stirring after the raw materials are melted, standing for 9-15 min to float slag, and pouring molten metal into a metal mold after skimming to obtain castings;
2) Homogenizing the obtained casting at 450-470 ℃ for 3-6 h, and air-cooling to room temperature;
3) Heating from room temperature to 505-515 ℃ at a heating rate of 1-3 ℃/min, and preserving heat for 10-14 h to perform first-stage solid solution treatment;
4) Then heating from 505-515 ℃ to 540-560 ℃ at a heating rate of 1-3 ℃/min, and preserving heat for 10-14 h to perform second-stage solution treatment;
5) And then aging the castings subjected to the second-stage solution treatment at 110-130 ℃ for 0.5-30 hours, and air-cooling to room temperature to obtain the high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy.
In the invention, the homogenization treatment can lead the structure distribution of the alloy to be as uniform as possible and prevent local overburning from occurring during subsequent solution treatment of the alloy.
In the invention, the secondary solution treatment can eliminate eutectic phases formed by Er and Cu as much as possible, thereby more fully utilizing elements in the alloy. The first-stage solid solution treatment is to eliminate dendrites containing Cu, so that all Cu elements are dissolved into a matrix in a solid solution way, and preparation is carried out for forming a precipitated phase by low-temperature aging; the second-stage solution treatment is to eliminate eutectic phases as much as possible on the premise of ensuring no overburning, and reduce the influence of Er addition on the room-temperature mechanical properties of the Al-Cu-Mg-Ag aluminum alloy.
In the present invention, special aging treatment is adopted in {100} Al A large amount of strengthening phase is evenly dispersed and precipitated on the surface, and the precipitation has smaller size and larger number density compared with the traditional omega phase. Therefore, the room temperature mechanical property of the material can be effectively improved, the yield strength at 25 ℃ is 250-350 MPa, and the elongation is 12-15%. Meanwhile, the precipitated phase has good stability at high temperature. Experiments show that the hardness of the precipitation is improved by 10 to 20HV under 300 ℃ heat exposure compared with the traditional omega phase.
The high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy and the preparation method thereof provided by the invention are described in detail below by combining with examples.
Comparative example 1
Alloy chemistry (wt.%): cu:4.5%, mg:0.3%, ag:0.4%, er:0.3% and the balance Al.
The preparation method of the alloy comprises the following specific steps:
a. preparing a preparation raw material; the raw materials are prepared according to the chemical components, cu, mg and Er are respectively added in the forms of Al-50% Cu intermediate alloy, al-10% Mg intermediate alloy and Al-6% Er intermediate alloy, and Al and Ag are added in the forms of pure Al and pure Ag, wherein the purity of the Al and the Ag should be not less than 99.99%. Before smelting, polishing the surfaces of all the preparation raw materials to remove oxides and greasy dirt on the surfaces of the preparation raw materials.
b. Melting, refining, deslagging and pouring; heating pure Al to 780 ℃, and reducing the temperature to 730 ℃ after the pure Al is completely melted; adding Al-50% Cu, al-10% Mg, al-6% Er and pure Ag, after the Al-6% Er and the pure Ag are completely melted, introducing high-purity argon with the purity more than or equal to 99.9%, strongly stirring to refine the melt for 30min, and standing for 10min to enable slag to float upwards; pouring molten metal into a metal mold after skimming to obtain a casting.
c. Homogenizing: the temperature was kept at 460℃for 3 hours, followed by air cooling.
d. And (3) secondary solid solution treatment: first-stage solution treatment: preserving the heat of the alloy obtained by homogenization treatment for 12 hours at 510 ℃; second-stage solution treatment: and (3) heating the alloy obtained through the first-stage solution treatment from 510 ℃ to 550 ℃ at a heating rate of 3 ℃/min, then preserving heat for 12 hours at 550 ℃, and quenching and cooling the alloy obtained through the second-stage solution treatment.
e. Aging treatment: and (3) preserving the heat of the alloy obtained after quenching for 4 hours at 185 ℃ and performing air cooling.
Example 1
Alloy chemistry (wt.%): cu:4.5%, mg:0.3%, ag:0.4%, er:0.3% and the balance Al.
The preparation method of the alloy comprises the following specific steps:
a. preparing a preparation raw material; the raw materials are prepared according to the chemical components, cu, mg and Er are respectively added in the forms of Al-50% Cu intermediate alloy, al-10% Mg intermediate alloy and Al-6% Er intermediate alloy, and Al and Ag are added in the forms of pure Al and pure Ag, wherein the purity of the Al and the Ag should be not less than 99.99%. Before smelting, polishing the surfaces of all the preparation raw materials to remove oxides and greasy dirt on the surfaces of the preparation raw materials.
b. Melting, refining, deslagging and pouring; heating pure Al to 780 ℃, and reducing the temperature to 730 ℃ after the pure Al is completely melted; adding Al-50% Cu, al-10% Mg, al-6% Er and pure Ag, after the Al-6% Er and the pure Ag are completely melted, introducing high-purity argon with the purity more than or equal to 99.9%, strongly stirring to refine the melt for 30min, and standing for 10min to enable slag to float upwards; pouring molten metal into a metal mold after skimming to obtain a casting.
c. Homogenizing: the temperature was kept at 460℃for 3 hours, followed by air cooling.
d. And (3) secondary solid solution treatment: first-stage solution treatment: preserving the heat of the alloy obtained by homogenization treatment for 12 hours at 510 ℃; second-stage solution treatment: and (3) heating the alloy obtained through the first-stage solution treatment from 510 ℃ to 550 ℃ at a heating rate of 3 ℃/min, then preserving heat for 12 hours at 550 ℃, and quenching and cooling the alloy obtained through the second-stage solution treatment.
e. Aging treatment: and (3) preserving the heat of the alloy obtained after quenching for 4 hours at 120 ℃ and air cooling.
Comparative example 2
Alloy chemistry (wt.%): cu:4.5%, mg:0.3%, ag:0.4%, er:0.3% and the balance Al.
The preparation method of the alloy comprises the following specific steps:
a. the preparation of the starting materials was carried out as in comparative example 1.
b. The melting-refining-deslagging-casting process was the same as that of comparative example 1.
c. Homogenization treatment was the same as in comparative example 1.
d. And (3) secondary solid solution treatment: comparative example 1.
e. Aging treatment: comparative example 1.
f. Heat exposure treatment: and (5) performing heat exposure for 4-30h at 300 ℃, and performing air cooling.
Example 2
Alloy chemistry (wt.%): cu:4.5%, mg:0.3%, ag:0.4%, er:0.3% and the balance Al.
The preparation method of the alloy comprises the following specific steps:
a. the preparation of the starting materials was as in example 1.
b. The melting-refining-deslagging-casting process was the same as in example 1.
c. The homogenization treatment was the same as in example 1.
d. And (3) secondary solid solution treatment: example 1.
e. Aging treatment: example 1.
f. Heat exposure treatment: and (5) performing heat exposure for 4-30h at 300 ℃, and performing air cooling.
The room temperature (25 ℃) yield strength, tensile strength and elongation of the alloys obtained in the examples and comparative examples were measured by GB/T228.1, and the results are shown in Table 1.
Table 1 room temperature mechanical properties of the alloys obtained in examples and comparative examples at different test temperatures
| Yield strength of | Tensile strength of | Elongation percentage | |
| Comparative example 1 | 338MPa | 340MPa | 1.68％ |
| Example 1 | 270MPa | 330MPa | 13.6％ |
As can be seen from table 1: the alloy of example 1 had lower yield and tensile strengths than comparative example 1, but had a significantly higher elongation than comparative example 1. The method shows that the alloy has high yield strength and tensile strength, but has poor plasticity by selecting the traditional aging temperature of 185 ℃ in the Al-Cu-Mg-Ag-Er alloy; the aging temperature of 120 ℃ can ensure that the alloy has higher yield strength and tensile strength, and the elongation rate of the alloy is greatly improved. FIG. 1 is a TEM image of an Al-Cu-Mg-Ag-Er alloy after 4h aging of comparative example 1 (FIG. 1-a) and example 1 (FIG. 1-b), from which it can be seen: after aging for 4 hours at 185 ℃ which is a traditional aging temperature, a large amount of omega phase is precipitated on the 111 face of the Al matrix, and the radius is about 14nm. After aging for 4 hours at 120 ℃ in the aging temperature in example 1, a large amount of fine flaky precipitated phases are precipitated on the 100 faces of the Al matrix, the radius is about 3nm, and the number density is obviously higher than that of the control group. The data above demonstrate that the method provided by the invention can change the original precipitated phase in the alloy to generate a new phase with finer and denser structure. Therefore, the plasticity of the alloy is greatly improved under the condition of keeping higher strength.
FIG. 2 is a graph showing the aging time-hardness statistics of example 2 and comparative example 2 after heat exposure at 300℃for 4 to 30 hours. As can be seen from the figures: the hardness of example 2 (ageing at 120 ℃) is significantly greater than that of comparative example 2 (ageing at 185 ℃). Fig. 3 TEM images of example 2 and comparative example 2 after heat exposure at 300 ℃ for 8h, from which it can be seen: the structure of comparative example 2 (FIG. 3-a) is a coarse equilibrium phase, while the alloy of example 2 (FIG. 3-b) still has a portion of the precipitated phase present, so it can maintain a higher hardness. The results prove that the method provided by the invention can effectively improve the high-temperature mechanical properties of the alloy.
Example 3:
alloy chemistry (wt.%): cu:3%, mg:0.4%, ag:0.3%, er:0.1%, the balance being Al.
1) Heating pure Al to 780 ℃, reducing the temperature to 730 ℃ after the pure Al is completely melted, adding Al-50% Cu intermediate alloy, al-10% Mg intermediate alloy, al-6% Er intermediate alloy and pure Ag, refining all raw materials for 30min under the conditions of argon and stirring after the raw materials are melted, standing for 10min, floating slag, skimming slag, and pouring molten metal into a metal mold to obtain a casting;
2) Homogenizing the obtained casting at 460 ℃ for 3 hours, and air-cooling to room temperature;
3) Heating from room temperature to 510 ℃ at a heating rate of 3 ℃/min, and preserving heat for 12 hours to perform first-stage solid solution treatment;
4) Then heating from 510 ℃ to 550 ℃ at a heating rate of 3 ℃/min, and preserving heat for 12 hours to perform second-stage solid solution treatment;
5) And then aging the casting subjected to the second-stage solution treatment for 4 hours at 120 ℃, and air-cooling to room temperature to obtain the high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy.
Example 4:
alloy chemistry (wt.%): cu:7%, mg:0.5%, ag:0.4%, er:0.2%, the balance being Al.
1) Heating pure Al to 750 ℃, reducing the temperature to 730 ℃ after the pure Al is completely melted, adding Al-50% Cu intermediate alloy, al-10% Mg intermediate alloy, al-6% Er intermediate alloy and pure Ag, refining all raw materials for 40min under the conditions of argon and stirring after the raw materials are melted, standing for 15min, floating slag, and pouring molten metal into a metal mold after skimming to obtain castings;
2) Homogenizing the obtained casting at 450 ℃ for 6 hours, and air-cooling to room temperature;
3) Heating from room temperature to 505 ℃ at a heating rate of 2 ℃/min, and preserving heat for 14h to perform first-stage solid solution treatment;
4) Then heating from 505 ℃ to 540 ℃ at a heating rate of 1 ℃/min, and preserving heat for 14h to perform second-stage solid solution treatment;
5) And then aging the casting subjected to the second-stage solution treatment for 30 hours at 110 ℃, and air-cooling to room temperature to obtain the high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy.
Example 5:
alloy chemistry (wt.%): cu:3.5%, mg:0.6%, ag:0.6%, er:0.5%, the balance being Al.
1) Heating pure Al to 770 ℃, reducing the temperature to 730 ℃ after the pure Al is completely melted, adding Al-50% Cu intermediate alloy, al-10% Mg intermediate alloy, al-6% Er intermediate alloy and pure Ag, refining all raw materials for 33min under the conditions of argon and stirring after the raw materials are melted, standing for 9min, floating slag, and pouring molten metal into a metal mold after skimming to obtain castings;
2) Homogenizing the obtained casting at 470 ℃ for 5 hours, and air-cooling to room temperature;
3) Heating from room temperature to 515 ℃ at a heating rate of 1 ℃/min, and preserving heat for 10 hours to perform first-stage solid solution treatment;
4) Then heating from 515 ℃ to 560 ℃ at a heating rate of 3 ℃/min, and preserving heat for 10 hours to perform second-stage solid solution treatment;
5) And then aging the casting subjected to the second-stage solution treatment for 20 hours at 125 ℃, and air-cooling to room temperature to obtain the high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy.
Example 6:
alloy chemistry (wt.%): cu:6.5%, mg:0.6%, ag:0.5%, er:0.4%, the balance being Al.
1) Heating pure Al to 760 ℃, reducing the temperature to 730 ℃ after the pure Al is completely melted, adding Al-50% Cu intermediate alloy, al-10% Mg intermediate alloy, al-6% Er intermediate alloy and pure Ag, refining all raw materials for 38min under the conditions of argon and stirring after the raw materials are melted, standing for 12min, floating slag, and pouring molten metal into a metal mold after skimming to obtain a casting;
2) Homogenizing the obtained casting at 460 ℃ for 4 hours, and air-cooling to room temperature;
3) Heating from room temperature to 510 ℃ at a heating rate of 3 ℃/min, and preserving heat for 12 hours to perform first-stage solid solution treatment;
4) Then heating from 510 ℃ to 555 ℃ at a heating rate of 2 ℃/min, and preserving heat for 13h to perform second-stage solid solution treatment;
5) And then aging the casting subjected to the second-stage solution treatment for 0.5h at 130 ℃, and air-cooling to room temperature to obtain the high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy.
The foregoing is merely a preferred embodiment of the present invention and it should be noted that modifications and adaptations to those skilled in the art may be made without departing from the principles of the present invention, which are intended to be comprehended within the scope of the present invention.
Claims (4)
1. A high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy is characterized in that: the alloy comprises, by mass, 3.0-7.0% of Cu, 0.3-0.6% of Mg, 0.3-0.6% of Ag, 0.1-0.5% of Er, and the balance of Al and unavoidable impurity elements, wherein the total mass percentage of the impurity elements is not more than 0.3%.
2. The high plasticity high temperature resistant Al-Cu-Mg-Ag-Er alloy of claim 1, wherein: the raw materials are introduced in a mode of pure Al, pure Ag, al-50% Cu intermediate alloy, al-10% Mg intermediate alloy and Al-6% Er intermediate alloy.
3. A method for preparing the high-plasticity and high-temperature-resistant Al-Cu-Mg-Ag-Er alloy as claimed in claim 1 or 2, which is characterized in that:
1) Heating pure Al to 750-780 ℃, reducing the temperature to 730 ℃ after the pure Al is completely melted, adding Al-50% Cu intermediate alloy, al-10% Mg intermediate alloy, al-6% Er intermediate alloy and pure Ag, refining all raw materials for 30-40 min under the conditions of argon and stirring after the raw materials are melted, standing for 9-15 min to float slag, and pouring molten metal into a metal mold after skimming to obtain castings;
2) Homogenizing the obtained casting at 450-470 ℃ for 3-6 h, and air-cooling to room temperature;
3) Heating from room temperature to 505-515 ℃ at a heating rate of 1-3 ℃/min, and preserving heat for 10-14 h to perform first-stage solid solution treatment;
4) Then heating from 505-515 ℃ to 540-560 ℃ at a heating rate of 1-3 ℃/min, and preserving heat for 10-14 h to perform second-stage solution treatment;
5) And then aging the castings subjected to the second-stage solution treatment at 110-130 ℃ for 0.5-30 hours, and air-cooling to room temperature to obtain the high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy.
4. The high-plasticity high-temperature-resistant Al-Cu-Mg-Ag-Er alloy obtained by the preparation method of claim 3, which is characterized in that the yield strength at 25 ℃ is 250-350 MPa, and the elongation is 12-15%; the hardness after the heat exposure at 300 ℃ is improved by 20 to 30 percent compared with the traditional preparation method.
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102634706A (en) * | 2012-04-28 | 2012-08-15 | 中南大学 | High-strength high-toughness corrosion-resistant Al-Cu-Mg aluminum alloy |
| CN104099500A (en) * | 2013-04-03 | 2014-10-15 | 中国石油天然气股份有限公司 | Pipe body for deep well ultra-deep well aluminum alloy drill pipe and manufacturing method thereof |
| CN104711468A (en) * | 2013-12-16 | 2015-06-17 | 北京有色金属研究总院 | High strength and high heat resistant aluminum alloy material and preparation method thereof |
| CN106893910A (en) * | 2017-03-01 | 2017-06-27 | 辽宁忠大铝业有限公司 | A kind of low rare earth high-strength aluminium alloy |
| CN109136696A (en) * | 2018-08-08 | 2019-01-04 | 倧奇健康科技有限公司 | A kind of infrared radiant material and preparation method thereof and infrared emission substrate |
| CN110669969A (en) * | 2019-09-23 | 2020-01-10 | 山东南山铝业股份有限公司 | Low-rare earth high-strength aluminum alloy and preparation method thereof |
-
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Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102634706A (en) * | 2012-04-28 | 2012-08-15 | 中南大学 | High-strength high-toughness corrosion-resistant Al-Cu-Mg aluminum alloy |
| CN104099500A (en) * | 2013-04-03 | 2014-10-15 | 中国石油天然气股份有限公司 | Pipe body for deep well ultra-deep well aluminum alloy drill pipe and manufacturing method thereof |
| CN104711468A (en) * | 2013-12-16 | 2015-06-17 | 北京有色金属研究总院 | High strength and high heat resistant aluminum alloy material and preparation method thereof |
| CN106893910A (en) * | 2017-03-01 | 2017-06-27 | 辽宁忠大铝业有限公司 | A kind of low rare earth high-strength aluminium alloy |
| CN109136696A (en) * | 2018-08-08 | 2019-01-04 | 倧奇健康科技有限公司 | A kind of infrared radiant material and preparation method thereof and infrared emission substrate |
| CN110669969A (en) * | 2019-09-23 | 2020-01-10 | 山东南山铝业股份有限公司 | Low-rare earth high-strength aluminum alloy and preparation method thereof |
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