Heat-resistant aluminum alloy as well as preparation method and application thereof

Abstract

The invention belongs to the technical field of aluminum alloys, and particularly provides a heat-resistant aluminum alloy and a preparation method and application thereof.The heat-resistant aluminum alloy comprises, by mass, 4.3%-4.8% of Cu, 1.3%-1.8% of (Mn + Fe), 0.8%-1.3% of Si, 0.04%-0.1% of Ti and the balance A, and Fe / Mn = 0-0.5 l. According to the chemical components, the alloy plate prepared through a series of processes such as casting, homogenization, hot rolling, cold rolling, solid solution, quenching and aging has good heat resistance and has the advantage of being low in cost due to the fact that the Ni element is not added.

Description

Technical Field

[0001] The present invention relates to the technical field of aluminum alloys, and in particular to a heat-resistant aluminum alloy and a preparation method and application thereof. Background Art

[0002] 2618 aluminum alloy is an age-hardening, deformation-resistant, heat-resistant aluminum alloy commonly used in aerospace, automotive, and other fields. This alloy belongs to the Al-Cu-Mg-Fe-Ni alloy type, with a chemical composition of Cu: 1.9-2.7%, Mg: 1.3-1.8%, Fe: 0.9-1.3%, Ni: 0.9-1.2%, Si: 0.1-0.25%, and Ti: 0.04-0.1% (GB / T 3190-2020, Chemical Composition of Wrought Aluminum and Aluminum Alloys). The addition of Cu and Mg allows the alloy to undergo solution treatment, quenching, and aging treatments, resulting in the precipitation of a nanoscale S-Al2CuMg phase, which imparts strong age-hardening properties. The addition of Fe and Ni in near-equal proportions results in the precipitation of micron-sized and submicron-sized Al9FeNi particles during ingot solidification and annealing, respectively. Due to the low diffusion coefficients of Fe and Ni, Al9FeNi particles possess high thermal stability, inhibiting dislocation and grain boundary motion. Under the combined action of Al9FeNi particles and S-Al2CuMg precipitates, the 2618 alloy achieves excellent heat resistance. However, the 2618 alloy has some shortcomings: (1) the expensive metal Ni needs to be added, which increases the cost of raw materials; (2) the addition of Mg, which is easily burned and has a lower density than Al, not only causes a large loss of raw materials but also brings certain difficulties to alloy smelting; (3) the need to control the Si content to a low level leads to higher requirements for the purity of the original aluminum. Therefore, it is necessary to develop a heat-resistant aluminum alloy with low cost, good processability and excellent performance. Summary of the Invention

[0003] In response to the shortcomings of the 2618 alloy, the present application provides a heat-resistant aluminum alloy, whose chemical composition by mass percentage is: Cu: 4.3~4.8%, Mn: 1.3~1.8%, Si: 0.8~1.3%, Ti: 0.04~0.1%, and the balance is Al; if the Fe element is used to replace the Mn element, its addition amount shall not exceed half of the Mn content, that is, Fe: 0~0.9%, that is, the heat-resistant aluminum alloy, the chemical composition by mass percentage is: Cu: 4.3~4.8%, (Mn+Fe): 1.3~1.8%, Si: 0.8~1.3%, Ti: 0.04~0.1%, and the balance is Al, where Fe / Mn=0~0.5. Through the above-mentioned composition design, the alloy forms a fine-sized α-AlMnSi or α-Al(Mn,Fe)Si eutectic phase during the solidification process of the ingot, precipitates an α-AlMnSi or α-Al(Mn,Fe)Si dispersed phase during the homogenization treatment, and precipitates a nano-scale θ-Al2Cu phase during the solution treatment and aging treatment after quenching, thereby obtaining good heat resistance.

[0004] The preparation method of the heat-resistant alloy comprises the following steps:

[0005] Melting and casting: Alloy ingots are prepared by melting and casting method according to the chemical composition of the alloy.

[0006] Pure aluminum is heated and melted in a crucible, and then an appropriate amount of master alloys such as Al-Cu, Al-Mn, Al-Fe, Al-Si, and Al-Ti are added. After smelting and stabilization, the ingot is poured into a mold. Generally, the melting temperature is controlled at 750-790°C, the stabilization temperature is 720-740°C, and the smelting time is 10-30 minutes.

[0007] The present application also provides a plate made of the above heat-resistant alloy, the steps of which are as follows:

[0008] (1) Homogenization annealing: The alloy ingot is subjected to homogenization annealing to precipitate dispersed phases, eliminate element segregation, and improve the alloy's plastic deformation ability. Generally speaking, homogenization annealing adopts a two-stage heating process. The first stage heating temperature is relatively low to precipitate α-AlMnSi or α-Al(Mn,Fe)Si dispersed phases, for example, the heating temperature is 260-300℃, and the holding time is 12-24h; the second stage heating temperature is relatively high to eliminate Cu element segregation and its soluble crystalline phase, for example, the heating temperature is 490-510℃, and the holding time is 8-24h. After homogenization annealing, the ingot is cooled to room temperature in the furnace.

[0009] (2) Hot rolling: The homogenized annealed ingot is subjected to multiple hot rolling passes above the recrystallization temperature to cause recrystallization of the hot-rolled plate, refine the grain size, and break up the eutectic phase, thereby achieving good cold deformation resistance. Generally, the hot rolling temperature is 400-440°C, and the hot rolling thickness reduction ratio is controlled to be ≥50%. After hot rolling, the plate is air-cooled to room temperature.

[0010] (3) Cold rolling: The hot-rolled sheet is cold-rolled in multiple passes at room temperature to the final sheet thickness, breaking up the α-AlMnSi or α-Al(Mn,Fe)Si eutectic phase and further refining its size. Generally, the cold rolling thickness reduction ratio is controlled to be ≥60%.

[0011] (4) Solution treatment: The cold-rolled sheet is solution treated and then quenched in water at room temperature to obtain a supersaturated quenched alloy. Generally, the solution treatment temperature is 520-530°C and the holding time is 0.5-1h.

[0012] (5) Aging treatment: The quenched alloy is aged to its peak state. Generally speaking, the heating temperature for quenched plates is 180-200℃ and the heating time is 6-12h.

[0013] Beneficial effects of the present invention:

[0014] The present invention proposes a heat-resistant aluminum alloy based on Al-Cu-Mn-Si. The alloy incorporates only Cu, without Mg, and, through solution treatment, quenching, and aging, precipitates a nanoscale θ-Al2Cu phase, maintaining good age-hardening properties. This simplifies the smelting process and reduces raw material costs. Furthermore, Mn and Si are simultaneously added to the alloy, with controlled amounts, to form only a fine, skeletal α-AlMnSi eutectic phase during casting and solidification, rather than a coarse, blocky α-AlMnSi primary phase. During homogenization annealing of the ingot, supersaturated Mn and Si solute atoms formed by nonequilibrium solidification precipitate a nanoscale α-AlMnSi dispersed phase, while simultaneously dissolving the soluble θ-Al2Cu phase formed by nonequilibrium crystallization. The annealed alloy ingot is then subjected to hot and cold plastic processing, whereby the fine α-AlMnSi eutectic phase is further broken down into even smaller granular dispersed phases. Finally, the alloy undergoes solution treatment, quenching, and aging treatments, resulting in the precipitation of a large number of nanoscale θ-Al2Cu phases, achieving an age-hardening effect. Compared to the 2618 alloy, the α-AlMnSi phase exhibits greater thermal stability than the Al9FeNi particles, due to the lower diffusion coefficient of Mn in aluminum than Fe and Ni. Therefore, the combination of the α-AlMnSi dispersed phase and the θ-Al2Cu precipitated phase ensures excellent heat resistance. Furthermore, since no Ni addition is required, the raw material cost of the alloy is significantly reduced. Furthermore, within a certain content range, Fe and Mn atoms are interchangeable, allowing Fe to partially replace Mn in the α-AlMnSi phase, forming the α-Al(Mn,Fe)Si phase, without altering the alloy's phase characteristics. This means that Fe can replace Mn in the alloy, which reduces the Fe purity requirement for the aluminum ingot raw material. In summary, developing a heat-resistant aluminum alloy based on Al-Cu-Mn-Si not only ensures excellent heat resistance but also significantly reduces alloy cost. BRIEF DESCRIPTION OF THE DRAWINGS

[0015] Figure 1 1 is the as-cast metallographic structure of the alloy of Example 1;

[0016] Figure 2 The metallographic structure of the longitudinal section of the plate in the peak aging state of the alloy in Example 1;

[0017] Figure 3 The longitudinal cross-section metallographic structure of the plate in the peak aging state of the alloy of comparative example 1;

[0018] Figure 4 This is the cast metallographic structure of the alloy in Example 2.

[0019] Figure 5 The metallographic structure of the longitudinal section of the plate in the peak aging state of the alloy in Example 2;

[0020] Figure 6 As-cast metallographic structure of the alloy of Example 8

[0021] Figure 7 As-cast metallographic structure of the alloy of Example 9 DETAILED DESCRIPTION

[0022] The present invention will be further described below with reference to the accompanying drawings and examples.

[0023] Example 1

[0024] The chemical composition of the experimental alloy is set as Cu: 4.5%, Mn: 1.6%, Si: 1%, Ti: 0.08%, and the balance is Al. Pure aluminum and intermediate are melted at 770℃, allowed to stand at 730℃ for 20 minutes, and then poured into an iron mold to obtain a flat ingot. The cast metallographic structure is as follows Figure 1 As shown in the figure, it can be seen that the alloy did not form a bulky α-AlMnSi primary phase during the solidification process, but formed a small-sized skeletal α-Al 15 Mn3Si eutectic phase. The ingot is first subjected to a primary homogenization treatment at 280°C for 24 hours, and then the temperature is raised to 500°C for 24 hours for a secondary homogenization treatment. The homogenization annealing ingot is heated to 420°C and hot rolled to 8mm thick to obtain a hot-rolled plate with a thickness reduction rate of 60%. Then, it is cold rolled to 2mm thick at room temperature to obtain a cold-rolled plate with a thickness reduction rate of 75%. After the cold-rolled plate is solution treated at 525°C for 1 hour and water quenched at room temperature, it is aged at 180°C for 12 hours to the peak state. At this time, the metallographic structure of the longitudinal section of the plate is as follows: Figure 2 Then, a heat exposure treatment was carried out at 250℃ for 120h. The room temperature tensile properties of the peak-aged alloy and the heat-exposed alloy are shown in Table 1.

[0025] Comparative Example 1

[0026] In order to compare the reliability of the alloy of the present invention, a commercially available 8mm thick 2618 alloy hot-rolled plate was used, with a chemical composition of Cu: 2.5%, Mg: 1.6%; Fe: 1.1%; Ni: 1.1%; Si: 0.12%; Ti: 0.08%. The alloy was annealed at 420℃ for 2h and then cold-rolled at room temperature to a thickness of 2mm, obtaining a cold-rolled plate with a thickness reduction of 75%. The cold-rolled plate was solution treated at 525℃ for 1h and water quenched at room temperature, and then aged at 180℃ for 12h to the peak state. At this time, the metallographic structure of the longitudinal section of the plate is as follows: Figure 3 Then, a heat exposure treatment was carried out at 250℃ for 120h. The room temperature tensile properties of the peak-aged alloy and the heat-exposed alloy are shown in Table 1.

[0027] Example 2

[0028] The chemical composition of the experimental alloy is set as Cu: 4.5%, Mn: 1.0%, Fe: 0.6%, Si: 1%, Ti: 0.08%, and the balance is Al. Figure 4 As shown, it can be seen that the alloy still only forms α-Al(Mn,Fe)Si eutectic phase during the solidification process, and no primary crystal phase is formed. Pure aluminum and the intermediate are melted at 770℃, allowed to stand at 730℃ for 20min, and then poured into an iron mold to obtain a flat ingot. The ingot is first subjected to a primary homogenization treatment at 280℃ for 24h, and then the temperature is raised for a secondary homogenization treatment at 500℃ for 24h. The homogenization annealing ingot is heated to 420℃ and hot rolled to 8mm thick to obtain a hot-rolled plate with a thickness reduction rate of 60%, and then cold rolled to 2mm thick at room temperature to obtain a cold-rolled plate with a thickness reduction rate of 75%. After solution treatment at 525℃ for 1h and water quenching at room temperature, the cold-rolled plate is aged to its peak state at 180℃ for 12h. At this time, the metallographic structure of the longitudinal section of the plate is as follows Figure 5 Then, a heat exposure treatment was carried out at 250℃ for 120h. The room temperature tensile properties of the peak-aged alloy and the heat-exposed alloy are shown in Table 1.

[0029] Compared with the alloy of Experimental Example 1, although the alloy of Example 2 uses 0.6Fe instead of 0.6Mn, the cast ( Figure 1 and Figure 4 ) and peak aging state ( Figure 2 and Figure 5 ) have basically the same metallographic structural characteristics.

[0030] Example 3

[0031] The experimental alloy chemical composition was 4.3% Cu, 1.3% Mn, 1.3% Si, 0.06% Ti, and the balance Al. Pure aluminum and the master alloy were melted at 750°C, allowed to stand at 720°C for 30 minutes, and then cast into an iron mold to produce a flat ingot. The ingots were first homogenized at 260°C for 24 hours, followed by a second homogenization at 490°C for 8 hours. The homogenized annealed ingots were heated to 430°C and hot-rolled to a thickness of 10 mm, producing a hot-rolled sheet with a thickness reduction of 50%. They were then cold-rolled at room temperature to a thickness of 2 mm, producing a cold-rolled sheet with a thickness reduction of 80%. The cold-rolled sheet was solution treated at 530°C for 0.5 hours, water quenched at room temperature, and aged at 200°C for 6 hours to a peak condition. Subsequently, they were heat-exposed at 250°C for 120 hours. The room-temperature tensile properties of the peak-aged and heat-exposed alloys are shown in Table 1.

[0032] Example 4

[0033] The experimental alloy's chemical composition was 4.8% Cu, 1.3% Mn, 0.8% Si, 0.09% Ti, and the balance Al. Pure aluminum and the master alloy were melted at 760°C, allowed to stand at 730°C for 15 minutes, and then poured into a cast iron mold to produce a flat ingot. The ingot was first heated at 280°C for 12 hours, then heated to 510°C for 12 hours, and then furnace-cooled to room temperature. After homogenization annealing, the ingot was heated to 410°C for 1 hour and then hot-rolled to 8 mm thick, producing a hot-rolled sheet with a thickness reduction of 60%. The hot-rolled sheet was then cold-rolled at room temperature to a thickness of 1.5 mm, producing a cold-rolled sheet with a thickness reduction of 81%. The cold-rolled sheet was solution treated at 520°C for 0.5 hours and then water-quenched at room temperature. The quenched sheet was then aged at 190°C for 10 hours to reach the peak aging state before undergoing heat exposure. The room temperature tensile properties of the peak-aged alloy and the corresponding heat-exposed alloy are shown in Table 1.

[0034] Example 5

[0035] The experimental alloy's chemical composition was 4.6% Cu, 0.9% Mn, 0.9% Fe, 0.8% Si, 0.10% Ti, and the balance Al. Pure aluminum and the master alloy were melted at 790°C, allowed to stand at 740°C for 30 minutes, and then poured into a cast iron mold to produce a flat ingot. The ingot was first heated at 300°C for 12 hours, then heated to 490°C for 16 hours, and then furnace-cooled to room temperature. After homogenization annealing, the ingot was heated to 440°C for 2 hours and then hot-rolled to a thickness of 7 mm, producing a hot-rolled sheet with a thickness reduction of 65%. The hot-rolled sheet was then cold-rolled at room temperature to a thickness of 2 mm, producing a cold-rolled sheet with a thickness reduction of 71.4%. The cold-rolled sheet was solution treated at 530°C for 1 hour and then water-quenched at room temperature. The quenched sheet was then aged at 180°C for 8 hours to reach the peak aging state before undergoing heat exposure. The room temperature tensile properties of the peak-aged alloy and the corresponding heat-exposed alloy are shown in Table 1.

[0036] Example 6

[0037] The experimental alloy chemical composition was 4.4% Cu, 1.8% Mn, 0.8% Si, 0.04% Ti, and the balance Al. Pure aluminum and the master alloy were melted at 780°C, held at 730°C for 25 minutes, and then poured into a cast iron mold to produce a flat ingot. The ingot was first heated at 290°C for 24 hours, then heated to 510°C for 24 hours, and then furnace-cooled to room temperature. After homogenization annealing, the ingot was heated to 400°C for 1 hour and then hot-rolled to a thickness of 6 mm, producing a hot-rolled sheet with a thickness reduction of 70%. The hot-rolled sheet was then cold-rolled at room temperature to a thickness of 2 mm, producing a cold-rolled sheet with a thickness reduction of 66.7%. The cold-rolled sheet was solution treated at 520°C for 1 hour and then water-quenched at room temperature. The quenched sheet was then aged at 190°C for 8 hours to reach the peak-aged state, and then subjected to heat exposure. The room-temperature tensile properties of the peak-aged alloy and the corresponding heat-exposed alloy are shown in Table 1.

[0038] Example 7

[0039] The experimental alloy composition was 4.7% Cu, 0.65% Mn, 0.65% Fe, 1.3% Si, 0.07% Ti, and the balance Al. Pure aluminum and the master alloy were melted at 760°C, allowed to stand at 740°C for 15 minutes, and then cast into an iron mold to produce a flat ingot. The ingots were first homogenized at 260°C for 12 hours, followed by a second homogenization at 490°C for 8 hours. The homogenized annealed ingots were heated to 430°C and hot-rolled to a thickness of 9 mm, producing a hot-rolled sheet with a thickness reduction of 55%. They were then cold-rolled at room temperature to a thickness of 3 mm, producing a cold-rolled sheet with a thickness reduction of 67%. The cold-rolled sheet was solution-treated at 530°C for 1 hour, water-quenched at room temperature, and then aged at 200°C for 6 hours to a peak condition. Subsequently, they were heat-exposed at 250°C for 120 hours. The room-temperature tensile properties of the peak-aged alloy and the corresponding heat-exposed alloy are shown in Table 1.

[0040] Example 8

[0041] The chemical composition of the experimental alloy is set as Cu: 4.7%, Mn: 0.65%, Fe: 1.1%, Si: 1.3%, Ti: 0.07%, and the balance is Al. Pure aluminum and the intermediate alloy are melted at 760℃, allowed to stand at 740℃ for 15 minutes, and then poured into an iron mold to obtain a flat ingot. The cast metallographic structure is as follows Figure 6The ingots were first homogenized at 260°C for 12 hours, then heated to 490°C for 8 hours for a second homogenization treatment. The homogenized annealed ingots were heated to 440°C and hot-rolled to a thickness of 9 mm, yielding a hot-rolled sheet with a thickness reduction of 55%. The sheets were then cold-rolled at room temperature to a thickness of 3 mm, yielding a cold-rolled sheet with a thickness reduction of 67%. The cold-rolled sheets were solution treated at 530°C for 0.5 hours, water quenched at room temperature, and then aged at 200°C for 6 hours to a peak state. The sheets were then heat-exposed at 250°C for 120 hours. The room-temperature tensile properties of the peak-aged alloy and the corresponding heat-exposed alloys are shown in Table 1.

[0042] from Figure 6 It can be seen that since the Fe addition amount is higher than the Mn content, coarse and long crystalline phase particles appear in the cast alloy, which ultimately leads to a significant decrease in the plasticity of the alloy.

[0043] Example 9

[0044] The chemical composition of the experimental alloy is set as Cu: 4.8%, Mn: 2.2%, Si: 1.0%, Ti: 0.09%, and the balance is Al. Pure aluminum and the intermediate alloy are melted at 760℃, allowed to stand at 730℃ for 15 minutes, and then poured into a cast iron mold to obtain a flat ingot. The cast metallographic structure is as follows Figure 7 As shown. The ingot was first heated at 280°C for 12 hours, then heated to 510°C for 12 hours, and then furnace cooled to room temperature. The homogenized annealed ingot was heated to 410°C for 1 hour and then hot rolled to 8 mm thick, obtaining a hot-rolled plate with a thickness reduction of 60%. The hot-rolled plate was then cold rolled at room temperature to a thickness of 1.5 mm, obtaining a cold-rolled plate with a thickness reduction of 81%. The cold-rolled plate was solution treated at 520°C for 0.5 hours and then water quenched at room temperature. Subsequently, the quenched plate was aged at 190°C for 10 hours to reach the peak-aged state, and then subjected to heat exposure treatment. The room-temperature tensile properties of the peak-aged alloy and the corresponding heat-exposed alloy are shown in Table 1.

[0045] from Figure 7 It can be seen that due to the excessive addition of Mn, coarse equiaxed crystalline phase particles appeared in the cast alloy, which ultimately led to a significant decrease in the plasticity of the alloy.

[0046] Example 10

[0047] The experimental alloy chemical composition was 4.0% Cu, 1.1% Mn, 0.5% Fe, 0.9% Si, 0.1% Ti, and the balance Al. Pure aluminum and the master alloy were melted at 790°C, allowed to stand at 740°C for 10 minutes, and then cast into an iron mold to produce a flat ingot. The ingots were first homogenized at 300°C for 24 hours, followed by a second homogenization at 510°C for 24 hours. The homogenized annealed ingots were heated to 420°C and hot-rolled to a thickness of 10 mm, producing a hot-rolled sheet with a thickness reduction of 50%. They were then cold-rolled at room temperature to a thickness of 2 mm, producing a cold-rolled sheet with a thickness reduction of 80%. The cold-rolled sheet was solution treated at 525°C for 1 hour, water quenched at room temperature, and then aged at 190°C for 12 hours to a peak condition. Subsequently, they were heat-exposed at 250°C for 120 hours. The room-temperature tensile properties of the peak-aged and heat-exposed alloys are shown in Table 1. Obviously, due to the low Cu content of the alloy, the θ-Al2Cu strengthening phase precipitated during peak aging is reduced. Therefore, the strength of the peak aging alloy and the heat-exposed alloy is relatively low, even lower than that of the 2618 alloy which is mainly strengthened by the S-Al2CuMg phase.

[0048] Example 11

[0049] The experimental alloy composition was 5.5% Cu, 1.4% Mn, 0.3% Fe, 1.1% Si, 0.08% Ti, and the balance Al. Pure aluminum and the master alloy were melted at 770°C, allowed to stand at 730°C for 30 minutes, and then cast into an iron mold to produce a flat ingot. The ingots were first homogenized at 290°C for 24 hours, followed by a second homogenization at 500°C for 24 hours. The homogenized annealed ingots were heated to 430°C and hot-rolled to 8 mm thick, producing a hot-rolled sheet with a thickness reduction of 60%. They were then cold-rolled at room temperature to a thickness of 2 mm, producing a cold-rolled sheet with a thickness reduction of 67%. The cold-rolled sheet was solution-treated at 520°C for 1 hour, water-quenched at room temperature, and then aged at 190°C for 8 hours to a peak condition. Subsequently, they were heat-exposed at 250°C for 120 hours. The room-temperature tensile properties of the peak-aged and heat-exposed alloys are shown in Table 1. Adding too high a Cu content will cause the alloy to be easily overburned during solution treatment heating, and will also result in relatively low strength and plasticity of the peak aging alloy and the heat-exposed alloy.

[0050] Table 1 Tensile properties of peak-aged alloy and heat-exposed alloy

[0051]

[0052] The tensile properties data in Table 1 show that the peak aging and heat-exposed strengths of the alloys of the present invention (Examples 1-7) are higher than those of the 2618 alloy (Comparative Example 1), demonstrating that the alloys exhibit excellent heat resistance. Furthermore, the alloys of the present invention not only eliminate the addition of Ni but also utilize an appropriate amount of Fe in place of Mn, both of which contribute to lower material costs.

[0053] With the above-described preferred embodiments of the present invention as a guide, and with reference to the above description, relevant personnel are fully capable of making various changes and modifications without departing from the technical scope of this invention. The technical scope of this invention is not limited to the contents of the specification and must be determined according to the scope of the claims.

Claims

1. A heat-resistant aluminum alloy, characterized in that: The invention comprises the following components in mass percentage: Cu: 4.3-4.8%, (Mn+Fe): 1.3-1.8%, Si: 0.8-1.3%, Ti: 0.04-0.1%, and the balance is Al; wherein Fe / Mn=0-0.

5.

2. A method for preparing a heat-resistant aluminum alloy according to claim 1, characterized in that: According to the alloy composition, the alloy ingot is prepared by a smelting and casting method, which includes the following steps: After pure Al is heated and melted in a crucible, Al-Cu, Al-Mn, Al-Fe, Al-Si, and Al-Ti intermediate alloys are added according to the composition. After smelting and standing, it is cast to obtain an alloy ingot.

3. The method for preparing a heat-resistant aluminum alloy according to claim 3, wherein the melting temperature is 750-790°C, the standing temperature is 720-740°C, and the standing time is 10-30 minutes.

4. An application of the heat-resistant alloy according to claim 1, characterized in that: Used in the preparation of panels.

5. The use according to claim 5, characterized in that The heat-resistant aluminum alloy is subjected to homogenization annealing treatment and then rolled into a thin plate; the thin plate is subjected to solid solution treatment, quenching and aging treatment to obtain the product.

6. The use according to claim 5, characterized in that The homogenization annealing treatment adopts a two-stage heating process, with the first stage heating temperature being 260-300°C and the holding time being 12-24h; the second stage heating temperature being 490-510°C and the holding time being 8-24h; after the ingot is homogenized annealed, it is cooled to room temperature in the furnace.

7. The use according to claim 5, characterized in that The rolling process includes hot rolling and cold rolling; the hot rolling temperature is 420±20° C., the hot rolling thickness reduction rate is ≥50%, and after hot rolling, the product is air-cooled to room temperature; the cold rolling thickness reduction rate is ≥60%.

8. The use according to claim 5, characterized in that The solution temperature is 520-530° C., and the holding time is 0.5-1 h.

9. The use according to claim 5, characterized in that The aging treatment heating temperature is 180-200° C., and the heating time is 6-12 hours.

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