阅读说明：本技术 一种耐热高强Al-Li-Cu-Ce合金板材的制备方法 (Preparation method of heat-resistant high-strength Al-Li-Cu-Ce alloy plate ) 是由 余鑫祥 戴菡 赵志国 史丹丹 史先利 董晓燕 于 2020-12-14 设计创作，主要内容包括：本发明涉及一种耐热高强Al-Li-Cu-Ce合金板材的制备方法,本发明通过Ce的微合金化和其制备过程的全流程的工艺有效控制,提高了Al-Li-Cu合金的耐热性能(热暴露和高温拉伸),实现耐热高强Al-Li-Cu-Ce合金板材的制备。一方面,通过提高合金中的Cu/Li和时效前预变形的协同作用增加合金中具有耐热潜质的T1(Al-2CuLi)相的析出比例,同时微量Ce的添加可以通过抑制合金中主元素Cu扩散的方式有效抑制T1(Al-2CuLi)相的粗化和含Ce金属间化合物的细化,极大地提高了该合金的热稳定性和高温变形均匀性。设备要求简单,可重复性强,适合大规模商业化生产,可作为航空航天领域用新型飞行器耐热结构件材料,具有现实的应用价值。(The invention relates to a preparation method of a heat-resistant high-strength Al-Li-Cu-Ce alloy plate, which effectively controls the processes of microalloying of Ce and the whole flow of the preparation process of the Ce, improves the heat resistance (thermal exposure and high-temperature stretching) of Al-Li-Cu alloy and realizes the preparation of the heat-resistant high-strength Al-Li-Cu-Ce alloy plate. On the one hand, T1 (Al) with heat resistance potential in the alloy is increased by the synergistic effect of increasing Cu/Li in the alloy and pre-deformation before aging 2 The precipitation ratio of CuLi) phase, and the addition of trace Ce can effectively inhibit T1 (Al) by inhibiting the diffusion of Cu as main element in the alloy 2 Coarsening of CuLi) phase and refining of Ce-containing intermetallic compound greatly improve the synthesisThermal stability and high temperature deformation uniformity of gold. The method has the advantages of simple equipment requirement, strong repeatability, suitability for large-scale commercial production, capability of serving as a novel aircraft heat-resistant structural member material in the field of aerospace and practical application value.)

1. The preparation method of the heat-resistant high-strength Al-Li-Cu-Ce alloy plate is characterized by comprising the following steps of:

a. smelting and casting: alloy smelting is carried out in a high-temperature resistance furnace, and pure Al, pure Li, pure Ag, pure Mg and intermediate alloys Al-Cu and Al-Ce are used as alloy smelting raw materials; firstly, adding pure Al, pure Ag and intermediate alloys Al-Cu and Al-Ce into a high-purity graphite crucible, then raising the temperature of the furnace to 780 ℃, simultaneously adding a refining agent to isolate moist air, preventing the melt from absorbing hydrogen, reducing the temperature of the furnace to 740 ℃ after the alloy is completely melted, placing paper-wrapped hexachloroethane into a bell jar, pressing the bell jar into the melt for degassing, then adding pure Mg into the crucible by using a clamp, keeping the pressure below the liquid level, standing for a period of time, and then carrying out secondary degassing and slagging-off; taking out pure Li from kerosene, cleaning the Li by using an acetone reagent, coating the Li by using an aluminum foil, slowly pressing the coated Li into the aluminum liquid by using a bell jar, standing the coated Li for 6 to 8 minutes, and casting the coated Li at the furnace temperature of 710 to 720 ℃; the casting is carried out by adopting an inclined die ingot casting and water-cooling copper die chilling technology, and argon protection and circulating cooling water are introduced to quickly cool the die in the whole casting process;

b. homogenizing and annealing: carrying out homogenizing annealing on the cast ingot in a salt bath furnace, and strictly controlling the temperature error to be +/-2 ℃; adopting a two-stage homogenization annealing process, namely annealing for 6-10h at the temperature of 460-475 +/-2 ℃ in the first step, and annealing for 12-20h at the temperature of 500-520 +/-2 ℃ in the second step;

c. plate forming: after homogenizing annealing, performing head and tail cutting and face milling treatment on the alloy, and then performing hot rolling and cold rolling; before hot rolling, placing the aluminum ingot in an air annealing furnace, preserving heat for 1-2h at the temperature of 440-: 24mm → 23 + -0.5 mm → 22 + -0.5 mm → 20 + -0.5 mm → 18 + -0.5 mm → 16 + -0.5 mm; re-melting and keeping the temperature at 450 +/-5 ℃ for 40min, and then performing 5 hot rolling steps to reach 5 +/-0.5 mm in the second step, wherein the specific hot rolling thickness is changed as follows: 16 +/-0.5 mm → 14 +/-0.5 mm → 12 +/-0.5 mm → 10 +/-0.5 mm → 8 +/-0.5 mm → 5 +/-0.5 mm; before cold rolling, the plate is subjected to intermediate annealing at 450 +/-5 ℃ for about 1.5-2.5 h, cooled to room temperature along with a furnace and taken out; the specific cold rolling thickness change is as follows: 5.0 mm → 4.8 + -0.1 mm → 4.6 + -0.1 mm → 4.4 + -0.1 mm → 4.2 + -0.1 mm → 4.0 + -0.1 mm → 3.8 + -0.1 mm → 3.6 + -0.1 mm → 3.4 + -0.1 mm → 3.2 + -0.1 mm → 3.0 + -0.1 mm → 2.8 + -0.1 mm → 2.6 + -0.1 mm → 2.4 + -0.1 mm → 2.2 + -0.1 mm, and the plate is formed;

d. solution aging heat treatment: solid solution is carried out in a salt bath furnace capable of accurately controlling the temperature, the furnace temperature is strictly controlled within the range of +/-1 ℃, the solid solution temperature is 520 +/-1 ℃, and after 50-70 min of solid solution, the alloy plate is immediately quenched and cooled in a water tank; the aging treatment adopts single-stage aging and is carried out in a blast drying oven; before aging, cold rolling and pre-deformation are needed, the deformation amount is about 6%, the cold rolling and pre-deformation are carried out at 150 ℃, and the aging time is 12-26 h.

2. The method for preparing the heat-resistant high-strength Al-Li-Cu-Ce alloy plate as claimed in claim 1, wherein in the step a, the contents of pure Al, pure Mg, pure Li and pure Ag are 99.9 wt%, the content of the intermediate alloy Al-Cu is 50.0 wt%, and the content of Al-Ce is 10.0 wt%; the addition amount of the refining covering agent is 3-8g each time, the refining covering agent is formed by mixing LiF and LiCl in a ratio of 1:2, and the refining covering agent is always placed in a drying box at 120 ℃ for drying.

3. The method for preparing the heat-resistant high-strength Al-Li-Cu-Ce alloy plate as claimed in claim 1, wherein in the step a, the size of a finished ingot is 100 x 100 mm x 24mm, and the alloy components in parts by mass are as follows: 0.8-1.5Li, 4.0-5.5Cu, 0.2-0.5Ag, 0.2-0.5Mg, 0.05-0.30 Ce, 0.02-0.08Fe, 0.02-0.05 Si.

4. The method as claimed in claim 1, wherein in step b, samples of the top and bottom regions of the alloy ingot are cut before the experimental homogenization annealing, and the secondary homogenization upper limit temperatures of the alloy are 460-475 ℃ and 500-520 ℃ respectively.

5. The method as claimed in claim 1, wherein in step c, before the hot rolling, the liquefied gas burner is used to preheat the mill roll to 180 ℃ at 120-.

6. The method for preparing the heat-resistant high-strength Al-Li-Cu-Ce alloy plate as claimed in claim 1, wherein in the step d, the water temperature of a quenching water tank is controlled below 25 ℃, and the quenching transfer time is less than 5s.

Technical Field

The invention belongs to the field of non-ferrous metal alloys, and particularly relates to a preparation method of a heat-resistant high-strength Al-Li-Cu-Ce alloy plate.

Background

Compared with the traditional commercial aluminum alloy, the Al-Li-Cu alloy has the characteristics of low density, high strength and fracture toughness, and better fatigue resistance and corrosion resistance. The Al-Li-Cu alloy is used as the main structural material of the aircraft, so that the effective carrying capacity and the fuel utilization efficiency of the aircraft can be greatly improved, and the Al-Li-Cu alloy becomes the most competitive material for replacing the traditional 2xxx and 7xxx aluminum alloys in the design of a novel aircraft. Because the Al-Li-Cu alloy has huge potential application prospect in the fuselages, wing structures, bulkheads near engines and other high-temperature structural components needing high temperature resistance, the development of the heat-resistant high-strength Al-Li-Cu alloy and the evaluation of the thermal stability of the Al-Li-Cu alloy are urgently needed. In response to the temperature of the hot environment (70 ℃ to 85 ℃) of the wings and fuselage structures of commercial aircraft, Al-Li-Cu alloys have been developed which have good heat resistance in this temperature range. There are also reports of related studies on the thermal exposure of Al-Li-Cu alloys at medium and high temperatures (below 200 ℃). However, the engine heat dissipation outer wall and other parts are generally required to be exposed to a high temperature environment of more than 200 ℃. Therefore, there is a need to develop a heat-resistant high-strength Al-Li-Cu alloy having thermal stability even in a high temperature environment of more than 200 ℃, but there are few studies and reports on this aspect.

Disclosure of Invention

The inventors have found that the high temperature (> 70 ℃ C.) mechanical properties of Al-Li-Cu alloys depend on the thermal stability of their primary age-strengthening phases, including T1 (Al₂CuLi), δ' (Al₃Li) and θ' (Al)₂Cu), and the strengthening effect of the T1 phase is the mostThe advantages are excellent. Furthermore, the lath-shaped T1 phase thickness was thin (about 1.3 nm) and was very stable when aged at 170 ℃ without significant coarsening. Therefore, the T1 phase is selected as the main strengthening phase of the heat-resistant high-strength Al-Li-Cu alloy. The large precipitation of the T1 phase is promoted by increasing the Cu/Li ratio or pre-deformation before artificial aging. In addition, the thermal stability of the T1 phase can be further improved by adding rare earth elements. If Sc, Y, La and Er are added in trace amount, the diffusion rate of the main element Cu in the alloy can be reduced, so that coarsening of a Cu-containing precipitated phase is delayed. Ce also has similar effect as rare earth element, can delay the coarsening process of Cu-containing nano precipitated phase in Ce-containing alloy at high temperature, and improves the thermal stability of the alloy, for example, the addition of Ce inhibits omega phase (Al) in Al-Cu-Mg-Ag alloy₂Cu) precipitation phase coarsening and T1 (Al) in Al-Cu-Li alloy₂CuLi) phase. Ce also contributes to the refinement of intermetallic compounds in aluminum alloys, such as the refinement of eutectic structures in 7055Al alloys, Al-6.7 Zn-2.6 Mg-2.6 Cu (wt%) alloys, and Al-Cu-Li alloys. The inventor obtains a proper homogenization process through research to form a large amount of fine and dispersed high-temperature resistant phase Al on the Ce-containing Al-Li-Cu alloy₈Cu₄A Ce phase. The dispersion particles distributed in the grain boundary can strengthen the grain boundary and prevent the grain boundary from sliding and creeping at high temperature, thereby improving the high-temperature mechanical property of the Ce-containing Al-Li-Cu alloy.

In view of the above, the invention provides a preparation method of a heat-resistant high-strength Al-Li-Cu-Ce alloy plate, which can be applied to a novel aircraft heat-resistant structural member.

The technical route of the invention is as follows: the heat resistance (thermal exposure and high-temperature stretching) of the Al-Li-Cu alloy is improved by effectively controlling the micro-alloying of Ce and the process of the whole flow of the preparation process of the Ce, and the preparation of the heat-resistant high-strength Al-Li-Cu-Ce alloy plate is realized. On the other hand, T1 (Al) with heat resistance potential in the alloy is increased by the synergistic effect of increasing Cu/Li in the alloy and pre-deformation before aging₂The precipitation ratio of CuLi) phase, and the addition of trace Ce can effectively inhibit T1 (Al) by inhibiting the diffusion of Cu as main element in the alloy₂Coarsening of CuLi) phase and refining of Ce-containing intermetallic compound greatly improveThe thermal stability and high temperature deformation uniformity of the alloy.

The technical scheme adopted by the invention is as follows:

a preparation method of a heat-resistant high-strength Al-Li-Cu-Ce alloy plate comprises the following steps:

a. smelting and casting: alloy smelting is carried out in a high-temperature resistance furnace, and pure Al, pure Li, pure Ag, pure Mg and intermediate alloys Al-Cu and Al-Ce are used as alloy smelting raw materials; firstly, adding pure Al, pure Ag and intermediate alloys Al-Cu and Al-Ce into a high-purity graphite crucible, then raising the temperature of the furnace to 780 ℃, simultaneously adding a refining agent to isolate moist air, preventing the melt from absorbing hydrogen, reducing the temperature of the furnace to 740 ℃ after the alloy is completely melted, placing paper-wrapped hexachloroethane into a bell jar, pressing the bell jar into the melt for degassing, then adding pure Mg into the crucible by using a clamp, keeping the pressure below the liquid level, standing for a period of time, and then carrying out secondary degassing and slagging-off; taking out pure Li from kerosene, cleaning the Li by using an acetone reagent, coating the Li by using an aluminum foil, slowly pressing the coated Li into the aluminum liquid by using a bell jar, standing the coated Li for 6 to 8 minutes, and casting the coated Li at the furnace temperature of 710 to 720 ℃; the casting is carried out by adopting an inclined die ingot casting and water-cooling copper die chilling technology, and argon protection and circulating cooling water are introduced to quickly cool the die in the whole casting process;

b. homogenizing and annealing: carrying out homogenizing annealing on the cast ingot in a salt bath furnace, and strictly controlling the temperature error to be +/-2 ℃; adopting a two-stage homogenization annealing process, namely annealing for 6-10h at the temperature of 460-475 +/-2 ℃ in the first step, and annealing for 12-20h at the temperature of 500-520 +/-2 ℃ in the second step;

c. plate forming: after homogenizing annealing, performing head and tail cutting and face milling treatment on the alloy, and then performing hot rolling and cold rolling; before hot rolling, placing the aluminum ingot in an air annealing furnace, preserving heat for 1-2h at the temperature of 440-: 24mm → 23 + -0.5 mm → 22 + -0.5 mm → 20 + -0.5 mm → 18 + -0.5 mm → 16 + -0.5 mm; re-melting and keeping the temperature at 450 +/-5 ℃ for 40min, and then performing 5 hot rolling steps to reach 5 +/-0.5 mm in the second step, wherein the specific hot rolling thickness is changed as follows: 16 +/-0.5 mm → 14 +/-0.5 mm → 12 +/-0.5 mm → 10 +/-0.5 mm → 8 +/-0.5 mm → 5 +/-0.5 mm; before cold rolling, the plate is subjected to intermediate annealing at 450 +/-5 ℃ for about 1.5-2.5 h, cooled to room temperature along with a furnace and taken out; the specific cold rolling thickness change is as follows: 5.0 mm → 4.8 + -0.1 mm → 4.6 + -0.1 mm → 4.4 + -0.1 mm → 4.2 + -0.1 mm → 4.0 + -0.1 mm → 3.8 + -0.1 mm → 3.6 + -0.1 mm → 3.4 + -0.1 mm → 3.2 + -0.1 mm → 3.0 + -0.1 mm → 2.8 + -0.1 mm → 2.6 + -0.1 mm → 2.4 + -0.1 mm → 2.2 + -0.1 mm, and the plate is formed;

d. solution aging heat treatment: solid solution is carried out in a salt bath furnace capable of accurately controlling the temperature, the furnace temperature is strictly controlled within the range of +/-1 ℃, the solid solution temperature is 520 +/-1 ℃, and after 50-70 min of solid solution, the alloy plate is immediately quenched and cooled in a water tank; the aging treatment adopts single-stage aging and is carried out in a blast drying oven; before aging, cold rolling and pre-deformation are needed, the deformation amount is about 6%, the cold rolling and pre-deformation are carried out at 150 ℃, and the aging time is 12-26 h.

Further, in the step a, the contents of pure Al, pure Mg, pure Li and pure Ag are 99.9 wt%, the content of the intermediate alloy Al-Cu is 50.0 wt%, and the content of Al-Ce is 10.0 wt%; the addition amount of the refining covering agent is 3-8g each time, the refining covering agent is formed by mixing LiF and LiCl in a ratio of 1:2, and the refining covering agent is always placed in a drying box at 120 ℃ for drying.

Further, in the step a, the size of the finished product ingot is 100 × 100 mm × 24mm, and the alloy components in parts by mass are as follows: 0.8-1.5Li, 4.0-5.5Cu, 0.2-0.5Ag, 0.2-0.5Mg, 0.05-0.30 Ce, 0.02-0.08Fe, 0.02-0.05 Si.

Further, in the step b, before the experimental homogenization annealing, samples of the top and bottom regions of the alloy ingot are intercepted, and the secondary homogenization upper limit temperatures of the alloy are 460-475 ℃ and 500-520 ℃ respectively.

Further, in the step c, before the hot rolling is started, a liquefied gas flame thrower is adopted to preheat the roller of the rolling mill to 180 ℃ at 120-.

Furthermore, in the step d, the water temperature of the quenching water tank is controlled below 25 ℃, and the quenching transfer time is less than 5s.

The invention has the followingThe beneficial technical effects are as follows: the invention utilizes the effective regulation and control effect of trace Ce addition on the microstructure of the Al-Li-Cu alloy, and effectively inhibits the main strengthening phase T1 (Al) in the Al-Li-Cu alloy through the trace Ce addition₂CuLi) and the refinement of Ce-containing intermetallic compounds, thereby greatly improving the thermal stability and the high-temperature deformation uniformity of the alloy. The method is characterized in that the diffusion and aggregation of the main element Cu in the alloy on the T1 phase can be effectively prevented by the segregation of solute atoms Ce at the interface of the matrix and the nanometer precipitated phase, and the high-temperature coarsening rate of the T1 phase is slowed down. Therefore, the thermal stability of the Al-Li-Cu-Ce alloy is substantially improved in the heat exposure process of medium-high temperature (130 ℃ -310 ℃). Meanwhile, in a high-temperature tensile test, the increment of the tensile elongation of the Al-Li-Cu-Ce alloy at high temperature is far larger than that of the Al-Li-Cu alloy, and the observation of the microstructure of a corresponding fracture shows that the Al which is fine and dispersed and has high-temperature stability₈Cu₄The Ce intermetallic compound is mainly located in high-temperature tensile fractures having plastic fracture characteristics. The method provides a new effective technical means for the high-temperature structural material of the high-strength heat-resistant aerospace Al-Li-Cu alloy, and provides a new idea for the development and industrial application of the related high-comprehensive-performance aluminum alloy structural material. The microalloying and conventional heat treatment methods have the advantages of simple equipment requirement, easy operation, large range, good controllability and good reproducibility, and the cost is greatly reduced compared with the conventional method. The method specially utilized by the invention has no special condition requirement and mature process condition, thereby being particularly suitable for commercial large-scale production.

Drawings

FIG. 1 is a thermal stability curve of Al-Li-Cu-Ce alloy and Al-Li-Cu alloy in a temperature range of 80-310 ℃ with heat exposure for 250h to 1300 h;

FIG. 2 is a high temperature tensile curve for Al-Li-Cu-Ce alloys and Al-Li-Cu alloys;

FIG. 3 shows the coarsening characteristics of the precipitated phase of the Al-Li-Cu-Ce alloy after being exposed for 250 hours at 230 ℃;

FIG. 4 is a typical fracture morphology (back-scattered electron phase) of an Al-Li-Cu-Ce alloy at high temperature of 250 ℃ under tension;

FIG. 5 shows typical fracture morphology (secondary electron phase) of Al-Li-Cu-Ce alloy at high temperature of 250 ℃.

Detailed Description

The present invention will be further described with reference to specific examples and comparative examples.

The embodiment discloses a preparation method of a heat-resistant high-strength Al-Li-Cu-Ce alloy plate, which comprises the following steps:

a. smelting and casting: alloy smelting is carried out in a high-temperature resistance furnace, pure Al, pure Li, pure Ag, pure Mg and intermediate alloys Al-Cu and Al-Ce are used as alloy smelting raw materials, and experimental raw materials comprise pure Al ((99.9 wt%)), pure Mg (99.9 wt%), pure Li (99.9 wt%) Ag (99.9 wt%), intermediate alloys Al-Cu (50.0 wt%), and Al-Ce (10.0 wt%). Firstly, adding pure Al, pure Ag and intermediate alloys Al-Cu and Al-Ce into a high-purity graphite crucible, and then heating the furnace to 780 ℃. Meanwhile, a refining agent is added to isolate moist air, so that hydrogen absorption of the melt is prevented. After the alloy is completely melted, the furnace temperature is reduced to 740 ℃, and 4g of paper is adopted to wrap hexachloroethane (C)₂Cl₆) Placing in a bell jar, pressing into the melt, degassing (the refining agent is formed by mixing LiF and LiCl in a ratio of 1:2, and the refining covering agent is always placed in a drying oven at 120 ℃ for drying). And then adding pure Mg into the crucible by using a clamp, and carefully pressing the crucible to a region below the liquid level, standing for a period of time, and then performing secondary degassing and slag skimming. Taking pure Li out of kerosene, washing the Li by using an acetone reagent, coating the Li by using an aluminum foil, slowly pressing the coated Li into the aluminum liquid by using a bell jar, standing the coated Li for 6 minutes, and then casting the coated Li at the furnace temperature range of 710-720 ℃. The casting is carried out by adopting an inclined die ingot casting and water-cooling copper die chilling technology, and the die is quickly cooled by introducing argon protection and circulating cooling water in the whole casting process. The size range of the finished cast ingot is 100 mm multiplied by 24 mm. The alloy comprises the following components (in parts by mass): 1.1Li, 5.1Cu, 0.3Ag, 0.3Mg, 0.26 Ce, 0.05Fe, 0.03 Si.

b. Homogenizing and annealing: before experimental homogenization annealing, samples of the top and bottom regions of an alloy ingot are intercepted, and the secondary homogenization upper limit temperatures of the alloy are respectively 470 ℃ and 515 ℃ determined by adopting an experimental result of differential thermal analysis (DSC).

Homogenizing and annealing the cast ingot in a salt bath furnace, and strictly controlling the temperature error to be +/-2 ℃. The invention adopts a two-stage homogenization annealing process, namely annealing at 475 +/-2 ℃ for 10 hours in the first step and annealing at 510 +/-2 ℃ for 20 hours in the second step.

c. Plate forming: and after homogenizing annealing, performing head and tail cutting and face milling treatment on the alloy. Before hot rolling, the aluminum ingot is placed in an air annealing furnace at the temperature of 450 +/-5 ℃ and is kept for 1.5 h. Before hot rolling begins, a roller of a rolling mill is preheated to about 160 ℃ by using a liquefied gas flame thrower, low-speed rolling at 350r/min (the thickness is reduced from 24mm to 16 mm) is adopted in the cogging hot rolling stages from the 1 st pass to the 5 th pass, and high-speed rolling at 800r/min (the thickness is reduced from 16mm to 5 mm) is adopted in the post-5-pass hot rolling. The first step is hot rolled to 16 +/-0.5 mm through 5 passes. The specific hot rolling thickness variation is as follows: 24mm → 23. + -. 0.5mm → 22. + -. 0.5mm → 20. + -. 0.5mm → 18. + -. 0.5mm → 16. + -. 0.5 mm. The furnace is re-melted and kept at 450 + -5 deg.C for 40min, and then the second step is hot rolled to 5 + -0.5 mm by 5 passes. The specific hot rolling thickness variation is as follows: 16 + -0.5 mm → 14 + -0.5 mm → 12 + -0.5 mm → 10 + -0.5 mm → 8 + -0.5 mm → 5 + -0.5 mm. Before cold rolling, the plate is subjected to intermediate annealing at 450 +/-5 ℃ for about 2 hours, and is cooled to room temperature along with a furnace and taken out. The specific cold rolling process of the alloy comprises the following steps: 5.0 mm → 4.8. + -. 0.1 mm → 4.6. + -. 0.1 mm → 4.4. + -. 0.1 mm → 4.2. + -. 0.1 mm → 4.0. + -. 0.1 mm → 3.8. + -. 0.1 mm → 3.6. + -. 0.1 mm → 3.4. + -. 0.1 mm → 3.2. + -. 0.1 mm → 3.0. + -. 0.1 mm → 2.8. + -. 0.1 mm → 2.6. + -. 0.1 mm → 2.4. + -. 0.1 mm → 2.2. + -. 0.1 mm.

d. Solution aging heat treatment: solid solution is carried out in a salt bath furnace capable of accurately controlling the temperature, the furnace temperature is strictly controlled within +/-1 ℃ in the experimental process, the solid solution temperature is 520 +/-1 ℃, the alloy plate is immediately quenched and cooled in a water tank after 1 hour of solid solution, the water temperature of the quenching water tank is controlled below 25 ℃, and the quenching transfer time is less than 5s. The aging treatment adopts single-stage aging and is carried out in a blast drying oven. The T86 sample was cold-rolled to pre-deform before aging, with a deformation of about 6%, at 150 ℃ for 16 h.

Comparative example, except that trace Ce was not contained, the other ingredients were the same as in example, and the preparation process was the same. As can be seen from FIGS. 1 and 2, the thermal stability and high temperature tensile properties of the Al-Li-Cu-Ce alloy are significantly better than those of the alloy without adding trace Ce.