A multi-principal alloy / aluminum alloy bimetallic material and its preparation method

Abstract

The present invention discloses a multi-principal alloy / aluminum alloy bimetallic material and a preparation method thereof, comprising a multi-principal alloy and an aluminum alloy; the multi-principal alloy is selected from the AlCoCrFeNi series, AlBeFeSiTi series, AlCrFeMnTi series, AlCrTiV series, AlMgZnCuSi series, and the like; the aluminum alloy includes cast aluminum alloys and deformed aluminum alloys; and further comprises a surface-active element. In the present invention, the multi-principal alloy contains aluminum or an element with a high solid solubility or high diffusion capacity in aluminum. High-temperature heat treatment forms a solute-supersaturated transition layer at the interface between the multi-principal alloy and the aluminum alloy. Low-temperature heat treatment precipitates nano-precipitates in the transition layer, strengthening the interface between the multi-principal alloy and the aluminum alloy, thereby imparting to the bimetallic material excellent overall mechanical properties and interfacial bonding strength.

Description

Technical Field

[0001] The present invention belongs to the field of bimetallic materials and relates to a multi-principal-element alloy / aluminum alloy bimetallic material and a preparation method thereof. Background Art

[0002] The trend toward integrated components in modern industries like aerospace, transportation, instrumentation, military, and automotive can require significantly different properties in different parts of the same component. For example, a component's surface must exhibit excellent wear resistance while its center exhibits excellent toughness. Conventional single materials are ineffective in addressing these challenges. By combining two materials with different properties, the advantages of each can be leveraged to better meet the specific performance requirements of different parts of the same component. The focus is on developing high-performance bimetallic materials.

[0003] The matrix material fundamentally determines the performance of bimetallic materials, while the interface is the most critical component. Aluminum alloys, with their advantages of high specific strength, low density, and excellent corrosion resistance, are the preferred material for lightweighting in industries such as automotive and transportation, and are also a key consideration in the preparation of bimetallic materials. Currently, there are numerous reports on the formation of bimetallic materials by combining metals such as copper, magnesium, titanium, and steel with aluminum. Some studies have focused on directly combining these materials with aluminum alloys. However, due to the poor wettability of the interface between these metals and aluminum alloys, a good metallurgical bond is difficult to form. Furthermore, brittle intermetallic compounds are easily formed at the interface, making it an inevitable weak link in the material's fracture process. This results in low interface strength, leading to poor overall bimetallic performance. Furthermore, the significant differences in elastic modulus and linear expansion coefficient between these metals and aluminum alloys lead to significant stress concentration at the interface, which makes cracks more likely to initiate and propagate at the interface. In order to improve the bonding ability between these metals and aluminum alloys, a commonly adopted strategy is to introduce a transition layer between the two metals, which greatly complicates the preparation process of bimetallic materials and increases the preparation cost of bimetallic materials.

[0004] Compared with traditional alloys, multi-principal alloys have advantages such as excellent mechanical properties, good wear resistance, and large elastic strain limit. Combining them with aluminum to form bimetallic materials is expected to achieve better comprehensive performance and has broad application prospects. However, there are currently few reports on multi-principal alloy / aluminum alloy bimetallic materials and their preparation processes. Since not all multi-principal alloys have good interfacial wettability and interfacial compatibility with aluminum matrix, (1) it is necessary to screen an appropriate multi-principal alloy system to meet the wettability and compatibility between multi-principal alloy / aluminum alloy and ensure that good metallurgical bonding can be achieved directly without the aid of a transition layer; (2) on the premise of selecting an appropriate multi-principal alloy system, other means are still needed to further improve the wettability and compatibility between multi-principal alloy and aluminum alloy, reduce stress concentration at the interface between multi-principal alloy and aluminum alloy, and improve the ability of the interface between multi-principal alloy and aluminum alloy to resist deformation and damage, so as to maximize the performance of bimetallic materials. Existing reports rarely involve this. Summary of the Invention

[0005] In order to overcome the shortcomings of the prior art, the purpose of the present invention is to provide a multi-principal alloy / aluminum alloy bimetallic material and a preparation method thereof. The selected multi-principal alloy contains aluminum or an element with a high solid solubility or high diffusion ability in aluminum to ensure intrinsic interface compatibility between the multi-principal alloy and the aluminum alloy. Surface active elements are added to further improve the wettability of the multi-principal alloy / aluminum alloy interface, promote the metallurgical bonding of the two alloys, and form a solute-supersaturated transition layer at the interface of the multi-principal alloy and the aluminum alloy through subsequent high-temperature heat treatment, and avoid the formation of brittle intermetallic compounds, further improve the wettability and compatibility between the multi-principal alloy and the aluminum alloy interface, relieve stress concentration at the interface, and precipitate nano-precipitates in the above-mentioned transition layer through subsequent low-temperature heat treatment to further strengthen the interface of the multi-principal alloy and the aluminum alloy, so that the bimetallic material has good overall mechanical properties and interface bonding strength.

[0006] To achieve the above object, the present invention adopts the following technical solutions:

[0007] A first aspect of the present invention provides a multi-principal alloy / aluminum alloy bimetallic material comprising a multi-principal alloy and an aluminum alloy;

[0008] The constituent elements of the multi-principal alloy contain aluminum, or contain an element with a maximum solubility of ≥1% in aluminum or a strong diffusion ability in aluminum, and are selected from AlCoCrFeNi series, AlBeFeSiTi series, AlCrFeMnTi series, AlCrTiV series, AlMgZnCuSi series, AlLiMgZnCu series, AlLiMgZnSn series, AlLiMgScTi series, AlNbTiV series, AlFeMgTiZn series, AlLiMgCaSi series, AlCuCrFeSi series, AlCaCuNiSiTi series high entropy alloy, Mg 20 (MnAlZnCu) 80 Alloy, Mg 50 (MnAlZnCu) 50 Alloy, (CoCrNi) 20 Al 80 One or a combination of two or more alloys;

[0009] The aluminum alloy includes cast aluminum alloy and deformed aluminum alloy;

[0010] It also includes surface active elements, selected from one or a combination of two or more of Be, Sr, Ca and rare earth elements La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, Sc, and Y.

[0011] Preferably, the multi-principal alloy is selected from AlCoCrFeNi 2.1 Alloy, Al 20 Be 20 Fe 10 Si 15 Ti 35 alloy, Al2CrFeMnTi alloy, AlCrTiV alloy, Mg 20 (MnAlZnCu) 80 Alloy, Al 63 Mg 27 Zn 4.5 Cu 4.5 Si1 alloy, AlLi 0.5 MgZn 0.5 Cu 0.5 alloy, AlLiMgZnSn alloy, Al 20 Li 20 Mg 10 Sc 20 Ti 30 alloy, AlNbTiV alloy, AlFeMgTiZn alloy, Al 15 Li 35 Mg 48 Ca1Si1 alloy, Al40 Cu 15 Cr 15 Fe 15 Si 15 Alloy, Al 50 Ca5Cu5Ni 10 Si 20 Ti 10 One or a combination of two or more alloys.

[0012] Preferably, the multi-principal alloy is selected from one or a combination of two or more of AlCoCrFeNi, AlLiMgZnSn, AlMgZnCuSi, AlCrTiV, AlFeCuCrMg, AlCrFeMnTi, AlCuMnNiZnSi, and AlNbTiV alloys.

[0013] More specifically, the multi-principal alloy is selected from AlCoCrFeNi 2.1 、AlLiMgZnSn、Al 63 Mg 27 Zn 4.5 Cu 4.5 Si1、Mg 50 (MnAlZnCu) 50 、AlCrTiV、AlFeCuCrMg 1.7 、AlCrFeMnTi 0.25 , Al8Cu3MnNiSi4Zn3, AlNbTiV, (CoCrNi) 20 Al 80 One or a combination of two or more alloys.

[0014] The multi-principal component alloy selected in the present invention contains aluminum elements or elements with high solid solubility in aluminum or high diffusion rate in aluminum, which helps to improve the wettability and compatibility of the interface by utilizing the bidirectional diffusion of elements between the multi-principal component alloy and the aluminum alloy through the interface.

[0015] Preferably, the cast aluminum alloy is selected from one or a combination of two or more of Al-Si series, Al-Cu series, Al-Mg series, Al-Zn series, Al-rare earth series aluminum alloy, and cast Al-Li series aluminum alloy.

[0016] Preferably, the deformed aluminum alloy is selected from one or a combination of two or more of 1xxx series, 2xxx series, 3xxx series, 4xxx series, 5xxx series, 6xxx series, 7xxx series, and 8xxx series aluminum alloys.

[0017] More preferably, the aluminum alloy is selected from one or a combination of two or more of ZL205A, ZL305, and ZL401 casting aluminum alloys, and / or one or a combination of two or more of AA2014, AA3003, AA4032, AA5083, AA6061, and AA7075 deformed aluminum alloys.

[0018] Preferably, the amount of surfactant added is 0.01%-0.5%, preferably 0.05%-0.2%. The addition of surfactant elements improves the wettability of the reinforcement particle-matrix interface. It is easy to concentrate at the multi-principal alloy / aluminum alloy interface to form a surfactant film, which reduces the interfacial tension. This can significantly improve the contact relationship between the multi-principal alloy / aluminum alloy melt, thereby greatly improving the interfacial wettability between the multi-principal alloy / aluminum alloy, thereby promoting the metallurgical bonding between the two metals. At the same time, the surfactant elements in the matrix can also play a metamorphic role on some secondary phases, which helps to improve the microstructure. When the addition amount is greater than 0.01%, the surfactant elements significantly improve the wettability of the multi-principal alloy / aluminum alloy interface, but when the addition amount exceeds 0.5%, these elements will form brittle intermetallic compounds with aluminum, thereby worsening the strength and toughness of the bimetallic material and the bonding effect of the interface.

[0019] A second aspect of the present invention is to provide a method for preparing the above-mentioned multi-principal alloy / aluminum alloy bimetallic material, using a solid-liquid composite method, comprising the following steps:

[0020] (1) Solid alloy pretreatment: According to the requirements of solid-liquid composite, one of the two base alloys constituting the bimetallic material is selected as the solid alloy. The surface for composite is processed on the solid alloy block material, and the surface is polished with sandpaper. Then, the process of pickling, water washing and drying is carried out to fully remove impurities and oxides on the composite surface. The solid alloy is then degreased, and finally an antioxidant is applied on the surface and dried to prepare for subsequent composite casting.

[0021] (2) Composite casting: Select the other of the two base alloys that make up the bimetallic material as the liquid alloy. First, melt the required alloy according to the target composition to obtain an alloy melt. For aluminum alloys, add Al-5Ti-1 B intermediate alloy to the melt to refine the grains. For aluminum alloys containing eutectic silicon, add Al-Sr intermediate alloy to modify the eutectic silicon. Subsequently, the melt is refined and then left to stand for a period of time. At the same time, the solid alloy preheated to the required temperature is placed in a designated position in the mold cavity in advance. Before casting, the surface active element is added to the melt in the form of an intermediate alloy. After the intermediate alloy is completely melted, the melt is slowly stirred to uniformly distribute the surface active element in the melt. Subsequently, the melt is adjusted in temperature and cast into the mold so that the melt is in full contact with the pre-treated solid alloy composite surface. After the melt solidifies in an appropriate manner (normal pressure solidification or high pressure solidification), the metallurgical bonding of the two alloys is achieved, and finally a multi-principal alloy / aluminum alloy bimetallic ingot is obtained.

[0022] (3) Heat treatment: First, the bimetallic material ingot prepared in step (2) is subjected to high-temperature heat treatment at a high temperature, wherein the high-temperature heat treatment temperature is 5-50°C below the solidus temperature of the matrix material and the high-temperature heat treatment time is 2-50 hours, thereby forming a solute supersaturated transition layer between the multi-principal alloy / aluminum alloy; then, a low-temperature heat treatment is performed, wherein the low-temperature heat treatment temperature is 100-200°C and the low-temperature heat treatment time is 2-100 hours.

[0023] Preferably, in step (2), the pressure during melt solidification is controlled at 0-150 MPa, and the holding time is 1-180 s.

[0024] Preferably, in step (3), the high-temperature heat treatment temperature is 5-50°C below the solidus temperature of the aluminum alloy matrix, and the high-temperature heat treatment time is 2-50h; more preferably, the high-temperature heat treatment temperature is 10-30°C below the solidus temperature of the aluminum alloy matrix, and the high-temperature heat treatment time is 10-50h.

[0025] In step (3), the temperature of the low-temperature heat treatment is 100-200°C, and the time of the low-temperature heat treatment is 2-100 hours; more preferably, the temperature of the low-temperature heat treatment is 120-180°C, and the time of the low-temperature heat treatment is 10-80 hours.

[0026] In the above-mentioned preparation method of the present invention, during the high-temperature heat treatment process, due to the concentration difference of different elements on both sides of the multi-principal alloy / aluminum alloy interface, the solute tends to diffuse from the high-concentration area through the interface to the low-concentration area. The high-temperature heat treatment is to fully utilize the characteristics of the rapid diffusion of elements at high temperatures to form a solute supersaturated transition layer between the multi-principal alloy / aluminum alloy. The composition of this transition layer is still within the composition range of the multi-principal alloy, thereby avoiding the formation of brittle intermetallic compounds at the interface, and thus can effectively alleviate the stress concentration at the multi-principal alloy / aluminum alloy interface. During the low-temperature heat treatment process, nano-scale precipitates will precipitate in the solute supersaturated transition layer at the multi-principal alloy / aluminum alloy interface. These nano-precipitates can effectively hinder dislocation movement, thereby effectively strengthening the interface, thereby improving the overall performance and interface bonding ability of the bimetallic material.

[0027] The principle of the present invention can be summarized as follows: from the three aspects of the alloy itself, the surface active elements and the heat treatment required for the preparation of bimetallic materials, the wettability and compatibility of the multi-principal alloy / aluminum alloy interface are improved at the same time, the interface microstructure of the multi-principal alloy / aluminum alloy is improved, and the interface bonding strength is thereby improved. First, the multi-principal alloy selected by the present invention contains aluminum or a large amount of elements with high solid solubility or high diffusion ability in aluminum. The multi-principal alloy / aluminum alloy naturally has interface bonding characteristics, and the wettability and compatibility of the interface are good. Furthermore, the wettability of the multi-principal alloy / aluminum alloy interface is further improved by the surface active elements. Again, during the high-temperature heat treatment process, bidirectional element diffusion occurs between the multi-principal alloy / aluminum alloy through the interface. By reasonably regulating the temperature and time of the high-temperature heat treatment, a solute supersaturated transition zone is formed between the multi-principal alloy / aluminum alloy. Since the composition of this transition zone is still within the composition range of the multi-principal alloy, the formation of brittle intermetallic compounds is avoided. Finally, during low-temperature heat treatment, nanoscale precipitates form in the transition zone, enhancing the multi-principal alloy / aluminum alloy interface's ability to resist deformation and damage. These measures significantly improve the wettability and compatibility of the multi-principal alloy / aluminum alloy interface, alleviate stress concentration at the interface, strengthen the interface, and enhance the overall toughness and interfacial bonding strength of the bimetallic material.

[0028] Compared with the prior art, the present invention has the following beneficial effects:

[0029] 1. The constituent elements of the multi-principal component alloy selected in the present invention are common elements in aluminum alloys. These elements have high solid solubility or good diffusion ability in aluminum, which fundamentally ensures the wettability and compatibility of the multi-principal component alloy / aluminum alloy interface.

[0030] 2. Adding surface active elements during the preparation of bimetallic materials can further improve the wettability of the multi-principal alloy / aluminum alloy interface.

[0031] 3. Through heat treatment, a solute supersaturated transition zone is formed at the interface of the multi-principal alloy / aluminum alloy, and nano-scale precipitates are precipitated in the transition zone, which relieves the stress concentration at the multi-principal alloy / aluminum alloy interface and strengthens the interface.

[0032] 4. The multi-principal alloy / aluminum alloy bimetallic material prepared by the present invention has good plasticity and interface bonding strength while ensuring high strength and hardness.

[0033] 5. The preparation method of the multi-principal alloy / aluminum alloy bimetallic material provided by the present invention is highly operable and efficient. BRIEF DESCRIPTION OF THE DRAWINGS

[0034] Figure 1 For AlCoCrFeNi in Example 1 2.1 Schematic diagram of the metallographic structure of eutectic high entropy alloy / ZL205A aluminum alloy bimetallic material. It can be found that AlCoCrFeNi 2.1 The eutectic high entropy alloy and ZL205A aluminum alloy achieve good metallurgical bonding, and a transition layer is formed at the interface, which can effectively alleviate the interfacial stress concentration. DETAILED DESCRIPTION

[0035] The technical solution of the present invention is further described in detail below in conjunction with the embodiments.

[0036] Example 1: AlCoCrFeNi 2.1 Multi-principal alloy / ZL205A bimetallic material and its preparation process, without adding surfactant elements and without heat treatment

[0037] The matrix materials used in this embodiment are AlCoCrFeNi 2.1 The multi-principal alloy and ZL205A aluminum alloy, the specific composition of ZL205A aluminum alloy in terms of weight percentage are: copper: 5.1%, manganese 0.4%, titanium: 0.28%, cadmium: 0.19%, zirconium: 0.11%, and the rest is aluminum. The specific implementation steps are as follows:

[0038] (1) Pretreatment of multi-element alloys. AlCoCrFeNi was prepared by ingot metallurgy. 2.1 A eutectic high-entropy alloy (HEA) is milled onto the HEA ingot to create a flat surface for cladding. After sanding the surface, it is pickled, washed, and dried to remove impurities and oxides from the cladding surface. The multi-element alloy is then degreased, and an antioxidant is applied to the cladding surface before drying.

[0039] (2) Composite casting. The ZL205A alloy ingot is melted in a crucible resistance furnace. After refining and degassing the alloy at 720°C, the melt temperature is adjusted to 700°C. Al-5Ti-1 B intermediate alloy is added at a ratio of 0.5% of the melt mass to refine the matrix alloy. At the same time, the pretreated high entropy alloy is preheated at 400°C for 2h and then fixed in the center of the metallic mold cavity. The melt is then cast into the mold cavity so that the melt is in full contact with the high entropy alloy composite surface. When the melt is completely solidified, a multi-principal alloy / aluminum alloy bimetallic ingot is obtained.

[0040] (3) The obtained AlCoCrFeNi 2.1 The multi-principal alloy / ZL205A bimetallic ingot was air-cooled to room temperature. The interfacial bonding strength of the bimetallic was tested using the tensile test method. The results showed that the interfacial bonding strength of the bimetallic material was 214.6 MPa.

[0041] Example 2: AlCoCrFeNi 2.1 Multi-principal alloy / ZL205A bimetallic material and its preparation process, adding surface active elements, without heat treatment

[0042] The matrix materials used in this embodiment are AlCoCrFeNi 2.1 The specific composition of the multi-principal alloy and ZL205A aluminum alloy is as follows: copper: 5.1%, manganese 0.4%, titanium: 0.28%, cadmium: 0.19%, zirconium: 0.11%, and the rest is aluminum. The surface active element is Ca. The specific implementation steps are as follows:

[0043] (1) Pretreatment of multi-element alloys. AlCoCrFeNi was prepared by ingot metallurgy. 2.1 A eutectic high-entropy alloy (HEA) is milled onto the HEA ingot to create a flat surface for cladding. After sanding the surface, it is pickled, washed, and dried to remove impurities and oxides from the cladding surface. The multi-element alloy is then degreased, and an antioxidant is applied to the cladding surface before drying.

[0044] (2) Composite casting. The ZL205A alloy ingot is melted in a crucible resistance furnace. After refining and degassing the alloy at 720°C, the melt temperature is adjusted to 700°C. Al-5Ti-1B master alloy is added at a ratio of 0.5% of the melt mass to refine the matrix alloy. At the same time, the pretreated high entropy alloy is preheated at 400°C for 2h and then fixed in the center of the metallic mold cavity. Before casting, Al-10Ca master alloy is added at a ratio of 0.1% of the target Ca content. After it is completely melted, the melt is slowly stirred to evenly distribute Ca in the melt. The melt is then cast into the mold cavity so that the melt is in full contact with the high entropy alloy composite surface. After the melt is completely solidified, a multi-principal alloy / aluminum alloy bimetallic ingot is obtained.

[0045] (3) The obtained AlCoCrFeNi 2.1 The multi-principal alloy / ZL205A bimetallic ingot was air-cooled to room temperature. The interfacial bonding strength of the bimetallic was tested using the tensile test method. The results showed that the interfacial bonding strength of the bimetallic material was 274.2 MPa.

[0046] Example 3: AlCoCrFeNi 2.1 Multi-principal alloy / ZL205A bimetallic material and its preparation process, addition of surface active elements, and heat treatment

[0047] The matrix materials used in this embodiment are AlCoCrFeNi 2.1 The specific composition of the multi-principal alloy and ZL205A aluminum alloy is as follows: copper: 5.1%, manganese 0.4%, titanium: 0.28%, cadmium: 0.19%, zirconium: 0.11%, and the rest is aluminum. The surface active element is Ca. The specific implementation steps are as follows:

[0048] (1) Pretreatment of multi-element alloys. AlCoCrFeNi was prepared by ingot metallurgy. 2.1 A eutectic high-entropy alloy (HEA) is milled onto the HEA ingot to create a flat surface for cladding. After sanding the surface, it is pickled, washed, and dried to remove impurities and oxides from the cladding surface. The multi-element alloy is then degreased, and an antioxidant is applied to the cladding surface before drying.

[0049] (2) Composite casting. The ZL205A alloy ingot is melted in a crucible resistance furnace. After refining and degassing the alloy at 720°C, the melt temperature is adjusted to 700°C. Al-5Ti-1B master alloy is added at a ratio of 0.5% of the melt mass to refine the matrix alloy. At the same time, the pretreated high entropy alloy is preheated at 400°C for 2h and then fixed in the center of the metallic mold cavity. Before casting, Al-10Ca master alloy is added at a ratio of 0.1% of the target Ca content. After it is completely melted, the melt is slowly stirred to evenly distribute Ca in the melt. The melt is then cast into the mold cavity so that the melt is in full contact with the high entropy alloy composite surface. After the melt is completely solidified, a multi-principal alloy / aluminum alloy bimetallic ingot is obtained.

[0050] (3) Heat treatment. 2.1 The multi-principal alloy / ZL205A bimetallic ingot was held at 550°C for 10 hours, then air-cooled to room temperature. It was then held at 175°C for 3 hours and subsequently air-cooled to room temperature. The interfacial bonding strength of the bimetallic was tested using a tensile test, which showed a strength of 380.7 MPa.

[0051] Example 4: AlLiMgZnSn multi-element alloy / ZL305 aluminum alloy bimetallic material, adding surface active elements and performing heat treatment

[0052] The matrix materials used in this embodiment are AlLiMgZnSn multi-principal alloy and ZL305 aluminum alloy. The specific components of ZL305 aluminum alloy are as follows by weight: magnesium: 8%, zinc: 1.2%, titanium: 0.15%, and the remainder is aluminum. The surface active element is Sr. The specific implementation steps are as follows:

[0053] (1) Pretreatment of the multi-principal alloy. The AlLiMgZnSn multi-principal alloy was prepared by ingot metallurgy. A flat surface for composite material was milled out of the multi-principal alloy ingot. After sanding the surface, it was pickled, washed, and dried to remove impurities and oxides from the composite surface. The multi-principal alloy was then degreased, and an antioxidant was applied to the composite surface before drying.

[0054] (2) Composite casting. The ZL305 alloy ingot was melted in a crucible resistance furnace. After refining and degassing the alloy at 720°C, the melt temperature was adjusted to 680°C. Al-5Ti-1B master alloy was added at a ratio of 0.5% of the melt mass to refine the matrix alloy. At the same time, the pretreated high entropy alloy was preheated at 380°C for 1 hour and then fixed in the center of the metallic mold cavity. Before casting, Al-10Sr master alloy was added at a ratio of 0.02% of Sr target content. After it was completely melted, the melt was slowly stirred to evenly distribute Sr in the melt. The melt was then cast into the mold cavity so that the melt was in full contact with the high entropy alloy composite surface. After the melt was completely solidified, a multi-principal alloy / aluminum alloy bimetallic ingot was obtained.

[0055] (3) Heat Treatment. The resulting AlLiMgZnSn multi-element alloy / ZL305 aluminum alloy bimetallic ingot was held at 450°C for 12 hours, air-cooled to room temperature, then held at 150°C for 4 hours, and subsequently air-cooled to room temperature. The interfacial bonding strength of the bimetallic material was tested using the tensile test method. The results showed that the interfacial bonding strength of the bimetallic material was 252.4 MPa.

[0056] Example 5: Al 63 Mg 27 Zn 4.5 Cu 4.5 Si1 multi-principal alloy / ZL205A aluminum alloy bimetallic material, adding surface active elements and performing heat treatment

[0057] The matrix material used in this embodiment is Al 63 Mg 27 Zn 4.5 Cu 4.5 Si1 multi-principal alloy and ZL205A aluminum alloy. The specific composition of ZL205A aluminum alloy is as follows: copper: 5.1%, manganese 0.4%, titanium: 0.28%, cadmium: 0.19%, zirconium: 0.11%, and the rest is aluminum. The surface active element is Sr. The specific implementation steps are as follows:

[0058] (1) Pretreatment of multi-element alloys. Al was prepared by ingot metallurgy. 63 Mg 27 Zn 4.5 Cu 4.5 For a Si1 multi-principal alloy, a flat surface for cladding is milled from the ingot. After sanding the surface, it is pickled, washed, and dried to remove impurities and oxides from the cladding surface. The multi-principal alloy is then degreased, and an antioxidant is applied to the cladding surface before drying.

[0059] (2) Composite casting. The ZL205A alloy ingot was melted in a crucible resistance furnace. After refining and degassing the alloy at 740°C, the melt temperature was adjusted to 710°C. Al-5Ti-1B intermediate alloy was added at a ratio of 0.5% of the melt mass to refine the matrix alloy. At the same time, the pretreated high entropy alloy was preheated at 410°C for 3 hours and then fixed in the center of the metallic mold cavity. Before casting, Al-10Sr intermediate alloy was added at a ratio of 0.3% of the target Sr content. After it was completely melted, the melt was slowly stirred to evenly distribute Sr in the melt. The melt was then cast into the mold cavity so that the melt was in full contact with the high entropy alloy composite surface. After the melt was completely solidified, a multi-principal alloy / aluminum alloy bimetallic ingot was obtained.

[0060] (3) Heat treatment. 63 Mg 27 Zn 4.5 Cu 4.5 The Si1 multi-principal alloy / ZL205A aluminum alloy bimetallic ingot was held at 530°C for 15 hours, then air-cooled to room temperature. It was then held at 155°C for 8 hours and subsequently air-cooled to room temperature. The interfacial bonding strength of the bimetallic was tested using a tensile test, which showed a strength of 385.6 MPa.

[0061] Example 6: Mg 50 (MnAlZnCu) 50 Multi-element alloy / ZL401 aluminum alloy bimetallic material, adding surface active elements, and heat treatment

[0062] The matrix material used in this embodiment is Mg 50 (MnAlZnCu) 50 The specific composition of the multi-principal alloy and the ZL401 aluminum alloy is as follows: silicon: 7.2%, magnesium: 0.2%, zinc: 12.3%, titanium: 0.15%, and the rest is aluminum. The surface active element is Be. The specific implementation steps are as follows:

[0063] (1) Pretreatment of multi-element alloys. Mg is prepared by ingot metallurgy. 50 (MnAlZnCu) 50 For a multi-principal alloy, a flat surface for cladding is milled from the ingot. After sanding the surface, it is pickled, washed, and dried to remove impurities and oxides from the cladding surface. The multi-principal alloy is then degreased, and an antioxidant is applied to the cladding surface before drying.

[0064] (2) Composite casting. The ZL401 alloy ingot was melted in a crucible resistance furnace. After refining and degassing the alloy at 750°C, the melt temperature was adjusted to 720°C. Al-5Ti-1B and Al-10Sr intermediate alloys were added at a ratio of 0.5% and 0.4% of the melt mass, respectively, to refine and modify the matrix alloy. At the same time, the pretreated high entropy alloy was preheated at 370°C for 2h and then fixed in the center of the metallic mold cavity. Before casting, Al-3Be intermediate alloy was added at a ratio of 0.15% Be content. After it was completely melted, the melt was slowly stirred to evenly distribute Be in the melt. The melt was then cast into the mold cavity so that the melt was in full contact with the high entropy alloy composite surface. After the melt was completely solidified, a multi-principal alloy / aluminum alloy bimetallic ingot was obtained.

[0065] (3) Heat treatment. 50 (MnAlZnCu) 50 The multi-principal alloy / ZL401 aluminum alloy bimetallic ingot was held at 550°C for 6 hours, then air-cooled to room temperature. It was then held at 120°C for 3 hours and subsequently air-cooled to room temperature. The interfacial bonding strength of the bimetallic material was tested using a tensile test, which showed a strength of 214.4 MPa.

[0066] Example 7: AlCrTiV multi-principal alloy / AA2014 aluminum alloy bimetallic material, adding surface active elements, and performing heat treatment

[0067] The matrix materials used in this embodiment are AlCrTiV multi-principal alloy and AA2014 aluminum alloy. The specific components of AA2014 aluminum alloy are as follows by weight: magnesium: 0.62%, copper: 4.4%, titanium: 0.15%, silicon: 0.96%, manganese: 0.8%, and the remainder is aluminum. The surface active element is La. The specific implementation steps are as follows:

[0068] (1) Pretreatment of the multi-principal alloy. The AlCrTiV multi-principal alloy was prepared by ingot casting. A flat surface for composite material was milled out of the multi-principal alloy ingot. After sanding the surface, it was pickled, washed, and dried to remove impurities and oxides from the composite surface. The multi-principal alloy was then degreased. Finally, an antioxidant was applied to the composite surface and dried.

[0069] (2) Composite casting. The AA2014 alloy ingot was melted in a crucible resistance furnace. After refining and degassing the alloy at 730°C, the melt temperature was adjusted to 710°C. Al-5Ti-1B intermediate alloy was added at a ratio of 0.5% of the melt mass to refine the matrix alloy. At the same time, the pretreated high entropy alloy was preheated at 400°C for 1 hour and then fixed in the center of the metallic mold cavity. Before casting, Al-10La intermediate alloy was added at a ratio of 0.12% La target content. After it was completely melted, the melt was slowly stirred to evenly distribute La in the melt. The melt was then cast into the mold cavity so that the melt was in full contact with the high entropy alloy composite surface. A hydraulic press was used to apply a pressure of 70 MPa to the melt and the pressure was maintained for 60 seconds. After the melt was completely solidified, a multi-principal alloy / aluminum alloy bimetallic ingot was obtained.

[0070] (3) Heat Treatment. The resulting AlCrTiV multi-principal alloy / AA2014 aluminum alloy bimetallic ingot was held at 502°C for 24 hours, air-cooled to room temperature, then held at 170°C for 10 hours, and subsequently air-cooled to room temperature. The interfacial bonding strength of the bimetallic material was tested using the tensile test method. The results showed that the interfacial bonding strength of the bimetallic material was 338.4 MPa.

[0071] Example 8: AlFeCuCrMg 1.7 Multi-element alloy / AA3003 aluminum alloy bimetallic material, adding surface active elements, and heat treatment

[0072] The matrix material used in this embodiment is AlFeCuCrMg 1.7 The specific composition of the multi-principal alloy and AA3003 aluminum alloy is as follows: manganese: 1.3%, copper: 0.17%, iron: 0.7%, silicon: 0.6%, zinc: 0.1%, titanium: 0.15%, and the rest is aluminum. The surface active element is Ce. The specific implementation steps are as follows:

[0073] (1) Pretreatment of multi-element alloys. AlFeCuCrMg was prepared by ingot metallurgy. 1.7 For a multi-principal alloy, a flat surface for cladding is milled from the ingot. After sanding the surface, it is pickled, washed, and dried to remove impurities and oxides from the cladding surface. The multi-principal alloy is then degreased, and an antioxidant is applied to the cladding surface before drying.

[0074] (2) Composite casting. The AA3003 alloy ingot was melted in a crucible resistance furnace. After refining and degassing the alloy at 720°C, the melt temperature was adjusted to 710°C. Al-5Ti-1B intermediate alloy was added at a ratio of 0.5% of the melt mass to refine the matrix alloy. At the same time, the pretreated high entropy alloy was preheated at 400°C for 1 hour and then fixed in the center of the metallic mold cavity. Before casting, Al-10Ce intermediate alloy was added at a ratio of 0.12% Ce target content. After it was completely melted, the melt was slowly stirred to evenly distribute Ce in the melt. The melt was then cast into the mold cavity so that the melt was in full contact with the high entropy alloy composite surface. After the melt was completely solidified, a multi-principal alloy / aluminum alloy bimetallic ingot was obtained.

[0075] (3) Heat treatment. 1.7 The multi-principal alloy / AA3003 aluminum alloy bimetallic ingot was held at 620°C for 2 hours, then air-cooled to room temperature. It was then held at 180°C for 3 hours and subsequently air-cooled to room temperature. The interfacial bonding strength of the bimetallic material was tested using a tensile test method, which showed a strength of 134.7 MPa.

[0076] Example 9: AlCrFeMnTi 0.25 Multi-element alloy / AA4032 aluminum alloy bimetallic material, adding surface active elements, and heat treatment

[0077] The matrix material used in this embodiment is AlCrFeMnTi 0.25 The specific composition of the multi-principal alloy and AA4032 aluminum alloy is as follows: silicon: 12.8%, iron: 0.8%, copper: 0.9%, magnesium: 1.1%, nickel: 0.6%, and the rest is aluminum. The surface active element is Sc. The specific implementation steps are as follows:

[0078] (1) Pretreatment of multi-element alloys. AlCrFeMnTi was prepared by ingot metallurgy. 0.25 For a multi-principal alloy, a flat surface for cladding is milled from the ingot. After sanding the surface, it is pickled, washed, and dried to remove impurities and oxides from the cladding surface. The multi-principal alloy is then degreased, and an antioxidant is applied to the cladding surface before drying.

[0079] (2) Composite casting. The AA4032 alloy ingot was melted in a crucible resistance furnace. After refining and degassing the alloy at 720°C, the melt temperature was adjusted to 710°C. Al-5Ti-1 B and Al-10Sr intermediate alloys were added at a ratio of 0.5% and 0.4% of the melt mass, respectively, to refine and modify the matrix alloy. At the same time, the pretreated high entropy alloy was preheated at 400°C for 1 hour and then fixed in the center of the metallic mold cavity. Before casting, Al-2Sc intermediate alloy was added at a ratio of 0.5% of the target Sc content. After it was completely melted, the melt was slowly stirred to evenly distribute Sc in the melt. The melt was then cast into the mold cavity so that the melt was in full contact with the high entropy alloy composite surface. After the melt was completely solidified, a multi-principal alloy / aluminum alloy bimetallic ingot was obtained.

[0080] (3) Heat treatment. 0.25 The multi-principal alloy / AA4032 aluminum alloy bimetallic ingot was held at 515°C for 10 hours, then air-cooled to room temperature. It was then held at 180°C for 3.5 hours and subsequently air-cooled to room temperature. The interfacial bonding strength of the bimetallic material was tested using a tensile test, which showed a strength of 273.6 MPa.

[0081] Example 10: Al8Cu3MnNiSi4Zn3 multi-principal alloy / AA5083 aluminum alloy bimetallic material, adding surface active elements and performing heat treatment

[0082] The matrix materials used in this embodiment are Al8Cu3MnNiSi4Zn3 multi-principal alloy and AA5083 aluminum alloy. The specific components of AA5083 aluminum alloy are as follows by weight percentage: magnesium: 4.6%, zinc: 0.1%, titanium: 0.12%, manganese: 0.6%, silicon: 0.2%, chromium: 0.2%, and the rest is aluminum. The surface active element is Gd. The specific implementation steps are as follows:

[0083] (1) Pretreatment of the multi-principal alloy. The Al8Cu3MnNiSi4Zn3 multi-principal alloy was prepared by ingot metallurgy. A flat surface for composite material was milled out of the multi-principal alloy ingot. After sanding the surface, it was pickled, washed, and dried to fully remove impurities and oxides from the composite surface. The multi-principal alloy was then degreased, and an antioxidant was applied to the composite surface before drying.

[0084] (2) Composite casting. The AA5083 alloy ingot was melted in a crucible resistance furnace. After refining and degassing the alloy at 700°C, the melt temperature was adjusted to 680°C. Al-5Ti-1B intermediate alloy was added at a ratio of 0.5% of the melt mass to refine the matrix alloy. At the same time, the pretreated high entropy alloy was preheated at 400°C for 1 hour and then fixed in the center of the metallic mold cavity. Before casting, Al-10Gd intermediate alloy was added at a ratio of 0.15% of the target Gd content. After it was completely melted, the melt was slowly stirred to evenly distribute the Gd in the melt. The melt was then cast into the mold cavity so that the melt was in full contact with the high entropy alloy composite surface. After the melt was completely solidified, a multi-principal alloy / aluminum alloy bimetallic ingot was obtained.

[0085] (3) Heat Treatment. The resulting Al8Cu3MnNiSi4Zn3 multi-principal alloy / AA5083 aluminum alloy bimetallic ingot was heated at 450°C for 20 hours, air-cooled to room temperature, then heated at 140°C for 3 hours, and then air-cooled to room temperature. The interfacial bonding strength of the bimetallic material was tested using the tensile test method. The results showed that the interfacial bonding strength of the bimetallic material was 183.5 MPa.

[0086] Example 11: AlNbTiV multi-principal alloy / AA6061 aluminum alloy bimetallic material, adding surface active elements, and performing heat treatment

[0087] The matrix materials used in this embodiment are AlNbTiV multi-principal alloy and AA6061 aluminum alloy. The specific components of the AA6061 aluminum alloy are as follows by weight: magnesium: 1.1%, zinc: 0.2%, titanium: 0.15%, copper: 0.3%, silicon: 0.6%, manganese: 0.1%, and the remainder is aluminum. The surface active element is Er. The specific implementation steps are as follows:

[0088] (1) Pretreatment of the multi-principal alloy. The AlNbTiV multi-principal alloy was prepared by ingot casting. A flat surface for composite material was milled out of the multi-principal alloy ingot. After sanding the surface, it was pickled, washed, and dried to remove impurities and oxides from the composite surface. The multi-principal alloy was then degreased. Finally, an antioxidant was applied to the composite surface and dried.

[0089] (2) Composite casting. The AA6061 alloy ingot was melted in a crucible resistance furnace. After refining and degassing the alloy at 710°C, the melt temperature was adjusted to 690°C. Al-5Ti-1B master alloy was added at a ratio of 0.5% of the melt mass to refine the matrix alloy. At the same time, the pretreated high entropy alloy was preheated at 350°C for 2h and then fixed in the center of the metallic mold cavity. Before casting, Al-20Er master alloy was added at a ratio of 0.15% of Er target content. After it was completely melted, the melt was slowly stirred to evenly distribute Er in the melt. The melt was then cast into the mold cavity so that the melt was in full contact with the high entropy alloy composite surface. A hydraulic press was used to apply a pressure of 150MPa to the melt and the pressure was maintained for 180s. After the melt was completely solidified, a multi-principal alloy / aluminum alloy bimetallic ingot was obtained.

[0090] (3) Heat Treatment. The resulting AlNbTiV multi-principal alloy / AA6061 aluminum alloy bimetallic ingot was heated at 530°C for 15 hours, air-cooled to room temperature, then heated at 180°C for 3 hours, and subsequently air-cooled to room temperature. The interfacial bonding strength of the bimetallic material was tested using the tensile test method. The results showed that the interfacial bonding strength of the bimetallic material was 244.8 MPa.

[0091] Example 12: (CoCrNi) 20 Al 80 Multi-element alloy / AA7075 aluminum alloy bimetallic material, adding surface active elements, and heat treatment

[0092] The matrix material used in this embodiment is (CoCrNi) 20 Al 80 The specific composition of the multi-principal alloy and AA7075 aluminum alloy is as follows: magnesium: 2.6%, zinc: 5.7%, titanium: 0.13%, copper: 1.6%, silicon: 0.2%, manganese: 0.2%, chromium: 0.21%, and the rest is aluminum. The surface active element is Sr. The specific implementation steps are as follows:

[0093] (1) Pretreatment of multi-element alloy. Preparation by ingot metallurgy (CoCrNi) 20 Al 80 For a multi-principal alloy, a flat surface for cladding is milled from the ingot. After sanding the surface, it is pickled, washed, and dried to remove impurities and oxides from the cladding surface. The multi-principal alloy is then degreased, and an antioxidant is applied to the cladding surface before drying.

[0094] (2) Composite casting. The AA7075 alloy ingot was melted in a crucible resistance furnace. After refining and degassing the alloy at 720°C, the melt temperature was adjusted to 700°C. Al-5Ti-1B intermediate alloy was added at a ratio of 0.5% of the melt mass to refine the matrix alloy. At the same time, the pretreated high entropy alloy was preheated at 380°C for 2h and then fixed in the center of the metallic mold cavity. Before casting, Al-10Sr intermediate alloy was added at a ratio of 0.15% of the target Sr content. After it was completely melted, the melt was slowly stirred to uniformly distribute Sr in the melt. The two metals were composited using an extrusion casting process. The melt was cast into the mold cavity so that the melt was in full contact with the high entropy alloy composite surface. Then, a pressure of 80MPa was applied to the melt by a hydraulic press. The pressure was maintained for 45s. After the melt was completely solidified, a multi-principal alloy / aluminum alloy bimetallic ingot was obtained.

[0095] (3) Heat treatment. 20 Al 80 The multi-principal alloy / AA7075 aluminum alloy bimetallic ingot was held at 470°C for 24 hours, then air-cooled to room temperature. It was then held at 150°C for 12 hours and subsequently air-cooled to room temperature. The interfacial bonding strength of the bimetallic material was tested using a tensile test, which showed a strength of 436.6 MPa.

[0096] Example 13: Cylindrical AlCoCrFeNi 2.1 Multi-principal alloy / ZL205A bimetallic material and its preparation process, addition of surface active elements, and heat treatment

[0097] The matrix materials used in this embodiment are AlCoCrFeNi 2.1 The specific composition of the multi-principal alloy and ZL205A aluminum alloy is as follows: copper: 5.1%, manganese 0.4%, titanium: 0.28%, cadmium: 0.19%, zirconium: 0.11%, and the rest is aluminum. The surface active element is Ca. The specific implementation steps are as follows:

[0098] (1) Solid alloy pretreatment. ZL205A aluminum alloy was selected as the solid alloy. A cylinder with a diameter of 50 mm and a length of 100 mm was machined. The surface of the solid alloy was sanded and then pickled, washed, and dried to fully remove impurities and oxides on the composite surface. The solid alloy was then degreased, and an antioxidant was applied to the composite surface and then dried.

[0099] (2) Composite casting. Use AlCoCrFeNi 2.1 Eutectic high entropy alloy is used as liquid alloy, and AlCoCrFeNi is melted in a crucible resistance furnace.2.1 Alloy ingot. At the same time, the pretreated ZL205A aluminum alloy is preheated at 200°C for 2h, and then fixed in the center of the metallic mold cavity, and the mold shape is adjusted so that the remaining thickness of the mold cavity is 2mm. Before casting, Al-10Sr intermediate alloy is added to the melt according to the target Sr content of 0.15%. After it is completely melted, the melt is slowly stirred to make Sr evenly distributed in the melt. The melt is then cast into the mold cavity so that the melt is in full contact with the high entropy alloy composite surface. After the melt is completely solidified, a multi-principal alloy / aluminum alloy bimetallic ingot is obtained, in which the multi-principal alloy layer is distributed 2mm on the surface of the ingot.

[0100] (3) Heat treatment. 2.1 The multi-principal alloy / AA7075 aluminum alloy bimetallic ingot was held at 540°C for 24 hours, then air-cooled to room temperature. It was then held at 170°C for 3 hours and subsequently air-cooled to room temperature. The interfacial bonding strength of the bimetallic was tested using a tensile test method. The results showed that the bimetallic material had an interfacial bonding strength of 396.7 MPa. Furthermore, the bimetallic material exhibited excellent wear resistance.

[0101] The mechanical properties of the bimetallic materials obtained in Examples 1-13 above are shown in Table 1:

[0102] Table 1: Mechanical properties of bimetallic materials involved in the examples

[0103]

[0104] It can be seen from Examples 1-3 and Table 1 that the addition of surfactant elements can improve the interfacial bonding strength of the bimetallic material, and after subsequent high-temperature and low-temperature heat treatments, the interfacial bonding strength of the bimetallic material is further significantly improved. It can be seen from Examples 3-13 and Table 1 that the method of the present invention has good applicability to different types of multi-principal element alloys and aluminum alloy matrix materials.

[0105] The above description of the embodiments is intended to facilitate understanding and use of the present invention by those skilled in the art. It will be apparent to those skilled in the art that various modifications to these embodiments can be readily made and the general principles described herein can be applied to other embodiments without requiring creative effort. Therefore, the present invention is not limited to the above-described embodiments. Improvements and modifications made by those skilled in the art based on the principles of the present invention, without departing from the scope of the present invention, should fall within the scope of protection of the present invention.

Claims

1. A multi-principal alloy / aluminum alloy bimetallic material, characterized in that: Including multi-principal alloys and aluminum alloys; The multi-principal alloy is selected from AlCoCrFeNi series, AlBeFeSiTi series, AlCrFeMnTi series, AlCrTiV series, AlMgZnCuSi series, AlLiMgZnCu series, AlLiMgZnSn series, AlLiMgScTi series, AlNbTiV series, AlFeMgTiZn series, AlLiMgCaSi series, AlCuCrFeSi series, AlCaCuNiSiTi series high entropy alloy, Mg 20 (MnAlZnCu) 80 Alloy, Mg 50 (MnAlZnCu) 50 Alloy, (CoCrNi) 20 Al 80 One or a combination of two or more alloys; The aluminum alloy includes cast aluminum alloy and deformed aluminum alloy; It also includes surface active elements selected from one or a combination of two or more of Be, Sr, Ca and rare earth elements La, Ce, Pr, Nd, Pm, Sm, Eu, Gd, Tb, Dy, Ho, Er, Tm, Yb, Lu, Sc, and Y; The preparation method of the multi-principal alloy / aluminum alloy bimetallic material is prepared by a solid-liquid composite method, comprising the following steps: obtaining a multi-principal alloy / aluminum alloy bimetallic ingot according to the solid-liquid composite method, and then subjecting the multi-principal alloy / aluminum alloy bimetallic ingot to high-temperature heat treatment at a high temperature, wherein the high-temperature heat treatment temperature is 5-50°C below the solidus temperature of the matrix material, and the high-temperature heat treatment time is 2-50h, thereby forming a solute supersaturated transition layer between the multi-principal alloy / aluminum alloy; and subsequently subjecting the multi-principal alloy / aluminum alloy bimetallic material to low-temperature heat treatment at a temperature of 100-200°C and a low-temperature heat treatment time of 2-100h.

2. The multi-principal alloy / aluminum alloy bimetallic material according to claim 1, characterized in that: The multi-principal element is selected from AlCoCrFeNi 2.1 、Al 20 Be 20 Fe 10 Si 15 Ti 35 、Al2CrFeMnTi、AlCrTiV、Mg 20 (MnAlZnCu) 80 、Al 63 Mg 27 Zn 4.5 Cu 4.5 Si1、AlLi 0.5 MgZn 0.5 Cu 0.5 、AlLiMgZnSn、Al 20 Li 20 Mg 10 Sc 20 Ti 30 、AlNbTiV、AlFeMgTiZn、Al 15 Li 35 Mg 48 Ca1Si1、Al 40 Cu 15 Cr 15 Fe 15 Si 15 、Al 50 Ca5Cu5Ni 10 Si 20 Ti 10 One or a combination of two or more alloys.

3. The multi-principal alloy / aluminum alloy bimetallic material according to claim 1, characterized in that: The multi-principal alloy is selected from one or a combination of two or more of AlCoCrFeNi, AlLiMgZnSn, AlMgZnCuSi, AlCrTiV, AlFeCuCrMg, AlCrFeMnTi, AlCuMnNiZnSi, and AlNbTiV alloys.

4. The multi-principal alloy / aluminum alloy bimetallic material according to claim 3, characterized in that: The multi-principal alloy is selected from AlCoCrFeNi 2.1 、AlLiMgZnSn、Al 63 Mg 27 Zn 4.5 Cu 4.5 Si1、Mg 50 (MnAlZnCu) 50 、AlCrTiV、AlFeCuCrMg 1.7 、AlCrFeMnTi 0.25 , Al8Cu3MnNiSi4Zn3, AlNbTiV, (CoCrNi) 20 Al 80 One or a combination of two or more alloys.

5. The multi-principal alloy / aluminum alloy bimetallic material according to claim 1, characterized in that: The cast aluminum alloy is selected from one or a combination of two or more of Al-Si series, Al-Cu series, Al-Mg series, Al-Zn series, Al-rare earth series aluminum alloy, and cast Al-Li series aluminum alloy; And / or the deformed aluminum alloy is selected from one or a combination of two or more of 1xxx series, 2xxx series, 3xxx series, 4xxx series, 5xxx series, 6xxx series, 7xxx series, and 8xxx series aluminum alloys.

6. The multi-principal alloy / aluminum alloy bimetallic material according to claim 5, characterized in that: The aluminum alloy is selected from one or a combination of two or more of ZL205A, ZL305, and ZL401 casting aluminum alloys, and / or one or a combination of two or more of AA2014, AA3003, AA4032, AA5083, AA6061, and AA7075 deformed aluminum alloys.

7. The method for preparing the multi-principal-element alloy / aluminum alloy bimetallic material according to any one of claims 1 to 6, characterized in that: The multi-principal alloy / aluminum alloy bimetallic material is prepared by a solid-liquid composite method, which includes the following steps: (1) Solid alloy pretreatment: According to the requirements of solid-liquid composite, one of the two base alloys constituting the bimetallic material is selected as the solid alloy, and the surface for composite is processed on the solid alloy block material, and the surface is polished with sandpaper. Then, the impurities and oxides on the composite surface are fully removed by pickling, water washing and drying processes, and the solid alloy is degreased. Finally, an antioxidant is applied to the composite surface and then dried; (2) Composite casting: Select the other of the two base alloys that make up the bimetallic material as a liquid alloy, first melt the required alloy according to the target composition to obtain an alloy melt, for aluminum alloy, add Al-5Ti-1B intermediate alloy to refine the grains, for aluminum alloy containing eutectic silicon, add Al-Sr intermediate alloy to modify the eutectic silicon; then refine the melt and let it stand; at the same time, preheat the solid alloy to the required temperature and place it in the mold cavity in advance, add the surface active element to the melt in the form of an intermediate alloy before casting, after the intermediate alloy is completely melted, slowly stir the melt to make the surface active element evenly distributed in the melt, then adjust the temperature of the melt and cast it into the mold, so that the melt is in full contact with the pretreated solid alloy composite surface, and the melt solidifies at normal pressure or high pressure to achieve metallurgical bonding of the two alloys, and obtain a multi-principal alloy / aluminum alloy bimetallic ingot; (3) Heat treatment: The multi-principal alloy / aluminum alloy bimetallic ingot prepared in step (2) is subjected to high-temperature heat treatment at a temperature of 5-50°C below the solidus temperature of the matrix material and a high-temperature heat treatment time of 2-50h, thereby forming a solute supersaturated transition layer between the multi-principal alloy / aluminum alloy; and then subjected to low-temperature heat treatment at a temperature of 100-200°C and a low-temperature heat treatment time of 2-100h, thereby obtaining a multi-principal alloy / aluminum alloy bimetallic material.

8. The method for preparing the multi-principal alloy / aluminum alloy bimetallic material according to claim 7, characterized in that: In step (2), the pressure of the melt during atmospheric solidification or high pressure solidification is controlled at 0-150 MPa, and the holding time is 1-180 s.

9. The method for preparing the multi-principal alloy / aluminum alloy bimetallic material according to claim 7, characterized in that: In step (3), the high-temperature heat treatment temperature is 10-30°C below the solidus temperature of the aluminum alloy substrate, and the high-temperature heat treatment time is 10-50h; the low-temperature heat treatment temperature is 120-180°C, and the low-temperature heat treatment time is 10-80h.

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