A multi-principal alloy particle reinforced aluminum-based composite material and preparation method thereof

Abstract

The present invention discloses a multi-principal alloy particle reinforced aluminum-based composite material and a preparation method thereof, wherein the reinforcement is a multi-principal alloy particle with a mass content of 0.1%-30%, and the constituent elements include aluminum or an element with high solid solubility or high diffusion capacity in aluminum; the matrix is ​​selected from cast aluminum alloy and / or deformed aluminum alloy, with a mass content of 70%-99.9%, and a surface active element is added, and the composite material is prepared by the steps of multi-principal alloy reinforcement particle preparation and pretreatment, stirring casting and heat treatment. The present invention contains aluminum or an element with high solid solubility or diffusion capacity in aluminum, and the surface active element can improve the wettability and compatibility between the reinforcement and the matrix interface, and the high-temperature heat treatment forms a solute supersaturated transition layer at the reinforcement and matrix interface, and the low-temperature heat treatment precipitates nano-precipitates in the transition layer, strengthens the reinforcement and matrix interface, improves the strength of the composite material, and keeps the material in good plasticity.

Description

Technical Field

[0001] The present invention belongs to the field of metal matrix composite materials, and relates to a particle-reinforced aluminum matrix composite material and a preparation method thereof, and in particular to a multi-principal alloy particle-reinforced aluminum matrix composite material and a preparation method thereof. Background Art

[0002] Particle-reinforced aluminum-based composites are composite materials with aluminum or aluminum alloy as the matrix and metal or non-metallic particles as the reinforcement. With the advantages of low density, high specific strength and high specific modulus, particle-reinforced aluminum-based composites are widely used in aerospace, transportation, instrumentation, military, automobile and other fields.

[0003] Reinforcement is one of the important factors that determine the performance of particle-reinforced aluminum-based composites. At the same time, the wettability and stress state between the reinforcement and matrix interface will significantly affect the performance of particle-reinforced aluminum-based composites. Reinforcements such as oxides, nitrides, carbides, ceramics and intermetallic compounds are widely used in aluminum-based composites. They have advantages such as high hardness. However, these particles have poor wettability with the aluminum matrix and may generate brittle interface products with the matrix, resulting in low interface bonding strength, making the particle-matrix interface inevitably become the weak link in the material fracture process; furthermore, the elastic modulus and linear expansion coefficient of these particles and the matrix are quite different, which makes it easy to produce obvious stress concentration at the particle-matrix interface, resulting in cracks that are easy to initiate and expand at the interface. In addition, these particles have poor deformation ability and are very likely to break under the action of stress. The above problems will lead to a sharp decrease in the strength and plasticity of the composite material.

[0004] Multi-principal alloys have the advantages of high strength, high hardness, and large elastic strain limit. Aluminum-based composites with multi-principal alloy particles as reinforcement are a very promising structural material with broad application prospects. At present, there have been some case reports of multi-principal alloy particle reinforced aluminum-based composites, such as patent document CN114807712A, which discloses a high entropy alloy reinforced aluminum-based composite material and its preparation method. However, the current reports also have the following problems:

[0005] (1) The multi-principal alloy reinforcement particles are simply mechanically added to the aluminum matrix, and the selection of reinforcement particles is not restricted. However, not all multi-principal alloys have good interface wettability and compatibility with the aluminum matrix, and it is necessary to screen out an appropriate multi-principal alloy system to ensure the wettability and compatibility between the particles and the matrix.

[0006] (2) Even if a suitable multi-principal component alloy system has been selected, other means still need to be further developed to improve the wettability and compatibility between the multi-principal component alloy particles and the matrix, reduce the stress concentration at the interface between the reinforcement particles and the matrix, and improve the ability of the interface between the reinforcement particles and the matrix to resist deformation and damage, so as to maximize the performance of the composite material. This has not been mentioned in existing reports. Summary of the invention

[0007] In order to overcome the shortcomings of the prior art, the main purpose of the present invention is to provide a multi-principal alloy particle reinforced aluminum-based composite material. The selected multi-principal alloy reinforcement particles contain aluminum or elements with high solid solubility or diffusion ability in aluminum, and surfactant elements are added to improve the wettability and compatibility between the reinforcement and matrix interface.

[0008] Another object of the present invention is to provide a method for preparing a multi-principal alloy particle reinforced aluminum-based composite material, by forming a solute supersaturated transition layer at the interface between the reinforcement and the matrix through high-temperature heat treatment, and avoiding the formation of brittle intermetallic compounds at the interface, further improving the wettability and compatibility between the reinforcement and the matrix interface, alleviating stress concentration at the interface, and precipitating nano-precipitates in the above-mentioned transition layer through low-temperature heat treatment, further strengthening the interface between the reinforcement and the matrix, thereby improving the strength of the composite material while maintaining good plasticity of the material.

[0009] To achieve the above object, the present invention adopts the following technical solution:

[0010] A first aspect of the present invention provides a multi-principal alloy particle reinforced aluminum-based composite material, which comprises a reinforcement body and a matrix body;

[0011] The reinforcement is a multi-principal alloy particle with a mass content of 0.1%-30%, and the constituent elements include aluminum, or an element with high solid solubility or high diffusion capacity in aluminum, selected from AlBeFeSiTi system, AlCrFeMnTi system, AlCrTiV system, Mg x (MnAlZnCu) 100-x Series, AlMgZnCuSi series, AlLiMgZnCu series, AlLiMgZnSn series, AlLiMgScTi series, AlNbTiV series, AlFeMgTiZn series, AlLiMgCaSi series, AlCuCrFeSi series, AlCaCuNiSiTi series, AlFeCuCrMg series, AlCuMnNiZnSi series high entropy alloys and (CoCrNi) 100-x Al x One or a combination of two or more alloys in the entropy alloy, wherein x = 0-30%;

[0012] The matrix is ​​an aluminum alloy with a mass content of 70%-99.9%, selected from cast aluminum alloy and / or deformed aluminum alloy;

[0013] 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.

[0014] Preferably, the multi-principal alloy is selected from the AlBeFeSiTi system (such as Al 20 Be 20 Fe 10 Si 15 Ti 35 alloy), AlCrFeMnTi system (such as Al 2 CrFeMnTi alloy), AlCrTiV series (such as AlCrTiV alloy), Mg x (MnAlZnCu) 100-x System (such as Mg 20 (MnAlZnCu) 80 alloy), AlMgZnCuSi system (such as Al 63 Mg 27 Zn 4.5 Cu 4.5 Si 1 Alloy), AlLiMgZnCu system (such as AlLi 0.5 MgZn 0.5 Cu 0.5 alloy), AlLiMgZnSn system (such as AlLiMgZnSn alloy), AlLiMgScTi system (such as Al 20 Li 20 Mg 10 Sc 20 Ti 30 alloy), AlNbTiV series (such as AlNbTiV alloy), AlFeMgTiZn series (such as AlFeMgTiZn alloy), AlLiMgCaSi series (such as Al 15 Li 35 Mg 48 Ca 1 Si 1 alloy), AlCuCrFeSi system (such as Al 40 Cu 15 Cr 15 Fe 15 Si 15 alloy), AlCaCuNiSiTi system (such as Al 50 Ca 5 Cu 5 Ni10 Si 20 Ti 10 alloy), AlFeCuCrMg series (such as AlFeCuCrMg 1.7 alloy), AlCuMnNiZnSi system (such as Al 8 Cu 3 MnNiSi 4 Zn 3 Alloy) High Entropy Alloy and (CoCrNi) l00-x Al x It is one or a combination of two or more entropy alloys, wherein x=0-30%.

[0015] Preferably, the multi-principal alloy is selected from AlLiMgScTi system, AlLiMgZnSn system, AlMgZnCuSi system, Mg x (MnAlZnCu) 100-x series, AlCrTiV series, AlFeCuCrMg series, AlCrFeMnTi series, AlCuMnNiZnSi series, AlNbTiV series, (CoCrNi) l00-x Al x One or a combination of two or more alloys in the series, where x = 0-30%.

[0016] As a more preferred embodiment, the multi-principal alloy is selected from AlLiMg 0.5 STi 1.5 、AlLiMgZnSn、Al 63 Mg 27 Zn 4.5 Cu 4.5 Si 1 Mg 50 (MnAlZnCu) 50 、AlCrTiV、AlFeCuCrMg 1.7 、AlCrFeMnTi 0.25 、Al 8 Cu 3 MnNiSi 4 Zn 3 、AlNbTiV、(CoCrNi) 20 Al 80 One or a combination of two or more alloys.

[0017] The reinforcement selected in the present invention is a multi-principal alloy, which contains aluminum or a large amount of elements with high solid solubility in aluminum or high diffusion rate in aluminum, which helps the elements to diffuse bidirectionally between the reinforcement and matrix interface, thereby improving the wettability and compatibility of the interface.

[0018] 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 alloys and cast Al-Li series aluminum alloys.

[0019] 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.

[0020] More preferably, the aluminum alloy is selected from one or a combination of two or more of ZL101, ZL305, ZL205A, and ZL401 casting aluminum alloys, and one or a combination of two or more of AA2014, AA3003, AA4032, AA5083, AA6061, and AA7075 deformed aluminum alloys.

[0021] Preferably, the mass content of the surfactant element is 0.01%-0.5%, preferably 0.05%-0.2%. The surfactant element is added to improve the wettability of the reinforcement particle-matrix interface. It is easy to concentrate at the reinforcement particle-aluminum matrix interface to form a surfactant film between the two phases, thereby reducing the interfacial tension between the two phases, which can significantly improve the contact relationship between the aluminum matrix and the multi-principal alloy particles, thereby greatly improving the interface wettability between the aluminum-containing multi-principal reinforcement particles and the matrix. When the addition amount is greater than 0.01%, the surfactant element significantly improves the wettability of the multi-principal alloy reinforcement particle-matrix interface, but when the addition amount exceeds 0.5%, these elements will form brittle intermetallic compounds with aluminum, thereby deteriorating the strength and toughness of the composite material.

[0022] Preferably, the mass content of the multi-principal alloy in the composite material is 1%-30%, and the mass content of the aluminum alloy is 70%-99%. When the amount of multi-principal alloy reinforcement particles added is greater than 1%, the strength of the composite material increases rapidly with the increase in the amount of reinforcement added, while the plasticity remains at a high level and does not deteriorate significantly. When the amount of reinforcement particles added exceeds 30%, due to reasons such as the agglomeration of reinforcement particles, the strength of the composite material is no longer significantly improved, but the plasticity will deteriorate sharply.

[0023] The second aspect of the present invention provides a method for preparing the aluminum-containing multi-principal alloy particle reinforced aluminum-based composite material, comprising the following steps:

[0024] (1) Preparation and pretreatment of multi-principal alloy reinforcement particles: prepare multi-principal alloy particles according to the designed multi-principal alloy composition, weigh the multi-principal alloy particles according to the ratio of the composite material, wrap them with aluminum foil, and perform preheating treatment;

[0025] (2) Stirring casting: weigh the matrix and the surfactant element master alloy according to the ratio, and use the smelting method to obtain the melt of the matrix material. During the smelting period, the superheat of the melt is always maintained at 20-100°C. Then, the surfactant element is added in the form of the master alloy. After the master alloy is completely melted, the melt is slowly stirred to make the surfactant element uniformly distributed in the melt, and Al-5Ti-1 B master alloy is added to refine the grains of the matrix alloy. For the matrix material containing eutectic silicon, Al-Sr master alloy is added to modify the eutectic silicon; then, the multi-principal alloy reinforcement particles are pressed into the bottom of the matrix melt, and the melt is stirred at a speed of 60-600r / min for 10-30min to ensure that the reinforcement particles are uniformly distributed in the melt; the melt is adjusted to a pure liquid or semi-solid state and then cast into a mold, and the alloy is solidified at normal pressure or high pressure to obtain a composite material ingot;

[0026] (3) Heat treatment: subjecting the composite material ingot prepared in step (2) to high-temperature heat treatment, 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 4-50 hours, so as to form a solute supersaturated transition layer between the reinforcement particles and the matrix; and then subjecting the composite material ingot to low-temperature heat treatment, wherein the low-temperature heat treatment temperature is 100-200°C, and the low-temperature heat treatment time is 4-100 hours, thereby obtaining a multi-principal alloy particle reinforced aluminum-based composite material.

[0027] Preferably, in step (1), the multi-principal component alloy particles are prepared by atomization, mechanical alloying, rotating electrode method or spheroidization method, and the particle size of the screened multi-principal component alloy reinforcement particles is 10-100 microns, thereby obtaining multi-principal component alloy reinforcement particles.

[0028] Preferably, in step (1), the particle size of the multi-principal alloy reinforcement particles is 10-60 microns.

[0029] Preferably, in step (2), the temperature of the melt is adjusted to within 80°C of the liquidus temperature before casting, the pressure of the melt during solidification is controlled at 0-150 MPa, and the holding time is 1-180 s.

[0030] Preferably, in step (3), the high-temperature heat treatment temperature is 10-30°C below the solidus temperature of the matrix material, and the high-temperature heat treatment time is 10-50h. During the high-temperature heat treatment, due to the concentration difference of different elements on both sides of the interface between the reinforcement particles and the matrix, 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 make full use of the fast diffusion characteristics of the elements at high temperatures to form a solute supersaturated transition layer between the reinforcement particles and the matrix. The composition of this transition layer is still within the composition range of the multi-principal alloy, so that the formation of brittle intermetallic compounds at the interface can be avoided, thereby effectively alleviating the stress concentration at the reinforcement-matrix interface.

[0031] Preferably, in step (3), the temperature of the low temperature heat treatment is 120-180° C., and the time of the low temperature heat treatment is 10-100 hours. During the low temperature heat treatment, nano-scale precipitates will precipitate in the solute supersaturated transition layer at the reinforcement-matrix interface, and these nano-precipitates can effectively hinder the dislocation movement, thereby effectively strengthening the transition zone, making the transition zone no longer the weakest position in the composite material, and improving the overall performance of the composite material.

[0032] The principle of the present invention can be summarized as follows: from the reinforcement material itself, the surface active elements and the heat treatment, the wettability and compatibility of the reinforcement-matrix interface are improved at the same time, and the interface microstructure of the reinforcement-matrix is ​​improved. First, the multi-principal alloy particles selected by the present invention have a certain deformation ability, and because there are a large number of elements with high solubility or high diffusion ability in aluminum in the multi-principal alloy reinforcement particles, the reinforcement and the matrix naturally have interface bonding characteristics, and the wettability and compatibility of the interface are good. Further, the wettability of the reinforcement particles and the matrix interface is further improved by the surface active elements. Again, during the high-temperature heat treatment process, the reinforcement and the matrix are bidirectionally diffused through the interface, and the solute supersaturated transition zone is formed between the reinforcement particles and the matrix by reasonably regulating the temperature and time of the high-temperature heat treatment. 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 the low-temperature heat treatment process, nano-scale precipitates are precipitated in the transition zone, thereby improving the ability of the reinforcement-matrix interface to resist deformation and destruction. Through the above measures, the wettability and compatibility between the reinforcement and matrix interface are greatly improved, the stress concentration at the interface is relieved, and the interface is strengthened, thereby improving the overall strength and toughness of the composite material.

[0033] Compared with the prior art, the present invention has the following beneficial effects:

[0034] 1. The constituent elements of the multi-principal alloy particle reinforcement 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 reinforcement particle-aluminum matrix interface.

[0035] 2. Adding surfactant elements during the preparation of composite materials can further change the wettability of the reinforcement particle-aluminum matrix interface.

[0036] 3. Through heat treatment, a solute supersaturated transition zone is formed at the interface of the reinforcement particles and the matrix. Then, nano-scale precipitates are precipitated in the transition zone through low-temperature heat treatment to relieve stress concentration at the interface of the reinforcement particles and the aluminum matrix, while strengthening the interface.

[0037] 4. The aluminum-containing multi-principal alloy particle-reinforced aluminum-based composite material prepared by the present invention has good plasticity while ensuring high strength and hardness.

[0038] 5. The preparation method of the aluminum-containing multi-principal alloy particle reinforced aluminum-based composite material provided by the present invention has strong operability and high efficiency. DETAILED DESCRIPTION

[0039] The technical solution of the present invention is further described in detail below in conjunction with embodiments.

[0040] Example 1: AlLiMg 0.5 STi 1.5 Multi-principal alloy particle reinforced ZL101-based composite material, no addition of surface active elements, no heat treatment

[0041] The reinforcement particles used in this embodiment are Al 20 Li 20 Mg 10 Sc 20 Ti 30 The matrix material of the multi-principal alloy is ZL101 aluminum alloy. The specific components of the matrix material are as follows: silicon: 7%, magnesium 0.35%, titanium: 0.1%, and the rest is aluminum. The specific implementation steps are as follows:

[0042] (1) Preparation and pretreatment of multi-principal alloy reinforcement particles. According to the nominal composition of the required multi-principal alloy, aluminum powder, magnesium powder, magnesium-lithium intermediate alloy, aluminum-lithium intermediate alloy, scandium powder and titanium powder are weighed. Since the Li element is very active, the present invention uses magnesium-lithium intermediate alloy and aluminum-lithium intermediate alloy. Stearic acid with a mass fraction of 3% is used as the process control agent. The ball milling medium uses stainless steel balls, and the ball-to-material ratio is 10:1. Pour the weighed alloy powder, ball milling medium and process control agent into a stainless steel grinding jar and mix them evenly. After sealing, fill it with high-purity argon gas. Then use a planetary ball mill for ball milling at a speed of 500r / min, 25min per ball milling, and 10min interval. The total ball milling time is 30h. Then use a standard mesh sieve to sieve to obtain multi-principal alloy particles with an average particle size of 45μm, that is, the required reinforcement particles. Subsequently, the multi-principal alloy particles of the required weight were weighed according to the ratio of the composite material, wrapped with aluminum foil, and preheated at 300°C.

[0043] (2) Stirring casting. The ZL101 alloy ingot was melted in a crucible resistance furnace, and then 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 to refine and modify the base alloy. Then, the preheated Al 20 Li 20Mg 10 Sc 20 Ti 30 The multi-principal alloy was pressed into the bottom of the melt and stirred at a speed of 400 r / min for 10 minutes. After that, the melt was allowed to stand for 10 minutes, and then the melt temperature was adjusted to 700°C and cast into a metal mold. After the melt solidified, a composite material ingot was obtained.

[0044] The obtained multi-principal alloy particle reinforced aluminum-based composite ingot was air-cooled to room temperature, and then a uniaxial tensile test was performed to determine the strength and elongation of the composite material. The experiment showed that the tensile strength of the composite material was 220.4 MPa and the elongation was 2.3%.

[0045] Example 2: AlLiMg 0.5 STi 1.5 Multi-principal alloy particle reinforced ZL101-based composite material, adding surface active elements, without heat treatment

[0046] The reinforcement particles used in this embodiment are Al 20 Li 20 Mg 10 Sc 20 Ti 30 The multi-principal alloy, the base material is ZL101 aluminum alloy, the specific components of the base material are as follows by weight percentage: silicon: 7%, magnesium 0.35%, titanium: 0.1%, the rest is aluminum, and the surface active element is Ca element. The specific implementation steps are as follows:

[0047] (1) Preparation and pretreatment of multi-principal alloy reinforcement particles. According to the nominal composition of the required multi-principal alloy, weigh aluminum powder, magnesium powder, magnesium-lithium master alloy, aluminum-lithium master alloy, scandium powder and titanium powder. Since the Li element is very active, the present invention uses magnesium-lithium master alloy and aluminum-lithium master alloy. Use 3% by mass of stearic acid as the process control agent. The ball milling medium uses stainless steel balls, and the ball-to-material ratio is 10:1. Pour the weighed alloy powder, ball milling medium and process control agent into a stainless steel grinding jar and mix them evenly. After sealing, fill it with high-purity argon gas. Then use a planetary ball mill for ball milling at a speed of 500r / min, 25min per ball milling, and 10min interval. The total ball milling time is 30h. Then use a standard mesh sieve to sieve to obtain multi-principal alloy particles with an average particle size of 90μm, that is, the required reinforcement particles. Subsequently, the multi-principal alloy particles of the required weight were weighed according to the ratio of the composite material, wrapped with aluminum foil, and preheated at 300°C.

[0048] (2) Stirring casting. The ZL101 alloy ingot was melted in a crucible resistance furnace, and then the melt temperature was adjusted to 710°C. Al-5Ti-1 B and Al-10Sr master alloys were added at a ratio of 0.5% and 0.4% of the melt mass to refine and modify the base alloy. Subsequently, Al-10Ca master alloy was added at a ratio of 0.1% Ca target content. After it was completely melted, the melt was slowly stirred to make Ca evenly distributed in the melt. Then, the preheated Al-10Sr master alloy was added at a ratio of 5% by mass. 20 Li 20 Mg 10 Sc 20 Ti 30 The multi-principal alloy was pressed into the bottom of the melt and stirred at a speed of 400 r / min for 10 minutes. After that, the melt was allowed to stand for 10 minutes, and then the melt temperature was adjusted to 700°C and cast into a metal mold. After the melt solidified, a composite material ingot was obtained.

[0049] The obtained multi-principal alloy particle reinforced aluminum-based composite ingot was air-cooled to room temperature, and then a uniaxial tensile test was performed to determine the strength and elongation of the composite material. The experiment showed that the tensile strength of the composite material was 252.7 MPa and the elongation was 6.3%.

[0050] Example 3: AlLiMg 0.5 STi 1.5 Multi-principal alloy particle reinforced ZL101-based composite material, adding surface active elements, and heat treatment

[0051] The reinforcement particles used in this embodiment are Al 20 Li 20 Mg 10 Sc 20 Ti 30 The multi-principal alloy, the base material is ZL101 aluminum alloy, the specific components of the base material are as follows by weight percentage: silicon: 7%, magnesium 0.35%, titanium: 0.1%, the rest is aluminum, and the surface active element is Ca element. The specific implementation steps are as follows:

[0052] (1) Preparation and pretreatment of multi-principal alloy reinforcement particles. According to the nominal composition of the required multi-principal alloy, aluminum powder, magnesium powder, magnesium-lithium intermediate alloy, aluminum-lithium intermediate alloy, scandium powder and titanium powder are weighed. Since the Li element is very active, the present invention uses magnesium-lithium intermediate alloy and aluminum-lithium intermediate alloy. Stearic acid with a mass fraction of 3% is used as the process control agent. The ball milling medium uses stainless steel balls, and the ball-to-material ratio is 10:1. Pour the weighed alloy powder, ball milling medium and process control agent into a stainless steel grinding jar and mix them evenly. After sealing, fill it with high-purity argon gas. Then use a planetary ball mill for ball milling at a speed of 500r / min, 25min per ball milling, and 10min interval. The total ball milling time is 30h. Then use a standard mesh sieve to sieve to obtain multi-principal alloy particles with an average particle size of 38μm, that is, the required reinforcement particles. Subsequently, the multi-principal alloy particles of the required weight were weighed according to the ratio of the composite material, wrapped with aluminum foil, and preheated at 300°C.

[0053] (2) Stirring casting. The ZL101 alloy ingot was melted in a crucible resistance furnace, and then the melt temperature was adjusted to 710°C. Al-5Ti-1 B and Al-10Sr master alloys were added at a ratio of 0.5% and 0.4% of the melt mass to refine and modify the base alloy. Subsequently, Al-10Ca master alloy was added at a ratio of 0.1% Ca target content. After it was completely melted, the melt was slowly stirred to make Ca evenly distributed in the melt. Then, the preheated Al-10Sr master alloy was added at a ratio of 5% by mass. 20 Li 20 Mg 10 Sc 20 Ti 30 The multi-principal alloy was pressed into the bottom of the melt and stirred at a speed of 400 r / min for 10 minutes. After that, the melt was allowed to stand for 10 minutes, and then the melt temperature was adjusted to 700°C and cast into a metal mold. After the melt solidified, a composite material ingot was obtained.

[0054] (3) Heat treatment. The obtained multi-principal alloy particle reinforced aluminum matrix composite ingot was kept at 535°C for 10 hours, then water-cooled to room temperature, then kept at 175°C for 3 hours, and then air-cooled to room temperature. The tensile test showed that the tensile strength of the composite material was 297.6 MPa and the elongation was 6.1%.

[0055] Example 4: AlLiMgZnSn multi-principal alloy particle reinforced ZL305-based composite material, adding surface active elements, and heat treatment

[0056] The reinforcement particles used in this embodiment are AlLiMgZnSn multi-principal alloy, the matrix material is ZL305 aluminum alloy, and the specific components of the matrix material are as follows: magnesium: 8%, zinc 1.2%, titanium: 0.15%, and the rest is aluminum. The surface active element is Sr element. The specific implementation steps are as follows:

[0057] (1) Preparation and pretreatment of multi-principal alloy reinforcement particles. According to the nominal composition of the required multi-principal alloy, aluminum powder, magnesium powder, magnesium-lithium intermediate alloy, aluminum-lithium intermediate alloy, zinc powder and tin powder are weighed. Since the Li element is very active, the present invention uses magnesium-lithium intermediate alloy and aluminum-lithium intermediate alloy. Stearic acid with a mass fraction of 3.5% is used as the process control agent. The ball milling medium uses stainless steel balls, and the ball-to-material ratio is 9:1. Pour the weighed alloy powder, ball milling medium and process control agent into a stainless steel grinding jar and mix them evenly. After sealing, fill it with high-purity argon gas. Then use a planetary ball mill for ball milling at a speed of 600r / min, each ball milling for 20min, and rest for 15min. The total ball milling time is 30h. Then use a standard mesh sieve to sieve to obtain multi-principal alloy particles with an average particle size of 53μm, that is, the required reinforcement particles. Subsequently, multi-principal alloy particles of a required weight were weighed according to the ratio of the composite material, wrapped with aluminum foil, and preheated at 320°C.

[0058] (2) Stirring casting. The ZL305 alloy ingot was melted in a crucible resistance furnace, and then the melt temperature was adjusted to 680°C. Al-5Ti-1 B master alloy was added at a ratio of 0.5% of the melt mass to refine the matrix alloy. Subsequently, Al-10Sr master alloy was added at a ratio of 0.05% of the target Sr content. After it was completely melted, the melt was slowly stirred to allow Sr to be evenly distributed in the melt. Then, the preheated AlLiMgZnSn multi-principal alloy was pressed into the bottom of the melt at a mass fraction of 10%, and stirred at a speed of 500r / min for 15 minutes. Subsequently, the melt was allowed to stand for 5 minutes, and then the melt temperature was adjusted to 660°C and cast into a metal mold. After the melt solidified, a composite material ingot was obtained.

[0059] (3) Heat treatment. The obtained multi-principal alloy particle reinforced aluminum matrix composite ingot was kept at 450°C for 12 hours, air-cooled to room temperature, then kept at 150°C for 4 hours, and then air-cooled to room temperature. The tensile test showed that the tensile strength of the composite material was 340 MPa and the elongation was 14%.

[0060] Example 5: Al 63 Mg 27 Zn 4.5 Cu 4.5 Si 1Multi-principal alloy particle reinforced ZL205A-based composite material, adding surface active elements, and heat treatment

[0061] The reinforcement particles used in this embodiment are Al 63 Mg 27 Zn 4.5 Cu 4.5 Si 1 The multi-principal alloy, the base material is ZL205A aluminum alloy, the specific components of the base material are as follows by weight percentage: copper: 5.1%, manganese 0.4%, titanium: 0.28%, cadmium: 0.19%, zirconium: 0.11%, the rest is aluminum, and the surface active element is Sr element. The specific implementation steps are as follows:

[0062] (1) Preparation and pretreatment of multi-principal alloy reinforcement particles. According to the nominal composition of the required multi-principal alloy, appropriate amounts of pure aluminum, pure magnesium, pure zinc, aluminum copper and aluminum silicon master alloy are weighed and smelted in a medium frequency induction furnace to obtain Al 63 Mg 27 Zn 4.5 Cu 4.5 Si 1 Multi-component alloy ingot. Then, the multi-component alloy ingot is used as a raw material to prepare multi-principal alloy reinforcement particles with an average particle size of 60 μm by vacuum atomization. Subsequently, the multi-principal alloy particles of the required weight are weighed according to the ratio of the composite material, wrapped with aluminum foil, and preheated at 350°C.

[0063] (2) Stirring casting. The ZL205A alloy ingot was melted in a crucible resistance furnace, and then the melt temperature was adjusted to 730°C. Al-5Ti-1 B master alloy was added at a ratio of 0.5% of the melt mass to refine the matrix alloy. Subsequently, Al-10Sr master 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 make Sr evenly distributed in the melt. Then, the preheated Al-10Sr master alloy was added at a ratio of 15% by mass. 63 Mg 27 Zn 4.5 Cu 4.5 Si 1 The multi-principal alloy particles were pressed into the bottom of the melt and stirred at a speed of 600 r / min for 10 minutes. After that, the melt was allowed to stand for 10 minutes, and then the melt temperature was adjusted to 720°C and cast into a metal mold. After the melt solidified, a composite material ingot was obtained.

[0064] (3) Heat treatment. The obtained multi-principal alloy particle reinforced aluminum matrix composite ingot was kept at 530°C for 15 hours, air-cooled to room temperature, then kept at 155°C for 8 hours, and then air-cooled to room temperature. The tensile test showed that the tensile strength of the composite material was 603 MPa and the elongation was 6.5%.

[0065] Example 6: Mg 50 (MnAlZnCu) 50 Multi-principal alloy particle reinforced ZL401-based composite material, adding surface active elements, and heat treatment

[0066] The reinforcement particles used in this example are Mg 50 (MnAlZnCu) 50 The multi-principal alloy, the base material is ZL401 aluminum alloy, the specific components of the base material are as follows by weight percentage: silicon: 7.2%, magnesium: 0.2%, zinc: 12.3%, titanium: 0.15%, the rest is aluminum, and the surface active element is Be element. The specific implementation steps are as follows:

[0067] (1) Preparation and pretreatment of multi-principal alloy reinforcement particles. According to the nominal composition of the required multi-principal alloy, aluminum powder, magnesium powder, zinc powder, copper powder and manganese powder were weighed. Stearic acid with a mass fraction of 3% was used as the process control agent. Stainless steel balls were used as the ball-to-material ratio at a 10:1 ratio. The weighed alloy powder, ball-milling medium and process control agent were poured into a stainless steel grinding jar and mixed evenly. After sealing, high-purity argon gas was filled in. Then, a planetary ball mill was used for abbreviated ball milling at a speed of 550 r / min, 30 min per ball milling, and 15 min rest. The total ball milling time was 35 h. Then, a standard mesh sieve was used to sieve to obtain multi-principal alloy particles with an average particle size of 48 μm, i.e., the required reinforcement particles. Subsequently, the required weight of multi-principal alloy particles was weighed according to the ratio of the composite material, wrapped with aluminum foil, and preheated at 350 °C.

[0068] (2) Stirring casting. The ZL401 alloy ingot was melted in a crucible resistance furnace, and then the melt temperature was adjusted to 730°C. Al-5Ti-1 B and Al-10Sr master alloys were added at a ratio of 0.5% and 0.4% of the melt mass, respectively, to refine and modify the base alloy. Subsequently, Al-3Be master alloy was added at a ratio of 0.15% Be content. After it was completely melted, the melt was slowly stirred to make Be evenly distributed in the melt. Then, the preheated MgO was added at a ratio of 20% by mass. 50 (MnAlZnCu) 50The multi-principal alloy was pressed into the bottom of the melt and stirred at a speed of 550 r / min for 15 minutes. After that, the melt was allowed to stand for 15 minutes, and then the melt temperature was adjusted to 710°C and cast into a metal mold. After the melt solidified, a composite material ingot was obtained.

[0069] (3) Heat treatment. The obtained multi-principal alloy particle reinforced aluminum matrix composite ingot was kept at 550°C for 6 hours, air-cooled to room temperature, then kept at 120°C for 3 hours, and then air-cooled to room temperature. The tensile test showed that the tensile strength of the composite material was 310 MPa and the elongation was 2.4%.

[0070] Example 7: AlCrTiV multi-principal alloy particle reinforced AA2014-based composite material, adding surface active elements, and heat treatment

[0071] The reinforcement particles used in this embodiment are AlCrTiV multi-principal alloy, the matrix material is AA2014 aluminum alloy, and the specific components of the matrix material are as follows: magnesium: 0.62%, copper: 4.4%, titanium: 0.15%, silicon: 0.96%, manganese: 0.8%, and the rest is aluminum. The surface active element is La element. The specific implementation steps are as follows:

[0072] (1) Preparation and pretreatment of multi-principal alloy reinforcement particles. According to the nominal composition of the required multi-principal alloy, appropriate amounts of pure aluminum, aluminum-chromium, aluminum-titanium, and aluminum-vanadium intermediate alloys were weighed and smelted in a medium-frequency induction furnace to obtain AlCrTiV multi-principal alloy ingots. Then, using this multi-component alloy ingot as raw material, multi-principal alloy reinforcement particles with an average particle size of 27 μm were prepared by vacuum atomization. Subsequently, the required weight of multi-principal alloy particles was weighed according to the ratio of the composite material, wrapped in aluminum foil, and preheated at a preheating temperature of 450°C.

[0073] (2) Stirring casting. Use a crucible resistance furnace to melt the AA2014 alloy ingot, then adjust the melt temperature to 730°C, then add Al-10La intermediate alloy according to the target La content of 0.12%. After it is completely melted, slowly stir the melt to make La evenly distributed in the melt, then press the preheated AlCrTiV multi-principal alloy into the bottom of the melt at a mass fraction of 15%, and stir at a speed of 520r / min for 15 minutes. After the melt is allowed to stand for 15 minutes, the melt temperature is adjusted to 690°C. The extrusion casting method is used to form the composite material ingot. The melt is cast into a metal mold, and then a hydraulic press is used to apply a pressure of 70MPa to the melt. After maintaining the pressure for 60 seconds, the composite material ingot is obtained.

[0074] (3) Heat treatment. The obtained multi-principal alloy particle reinforced aluminum matrix composite ingot was kept at 502°C for 24 hours, air-cooled to room temperature, then kept at 170°C for 10 hours, and then air-cooled to room temperature. The tensile test showed that the tensile strength of the composite material was 520 MPa and the elongation was 9.8%.

[0075] Example 8: AlFeCuCrMg 1.7 Multi-principal alloy particle reinforced AA3003 matrix composite material, adding surface active elements, and heat treatment

[0076] The reinforcement particles used in this embodiment are AlFeCuCrMg 1.7 The multi-principal alloy, the base material is AA3003 aluminum alloy, the specific components of the base material are as follows by weight percentage: manganese: 1.3%, copper: 0.17%, iron: 0.7%, silicon: 0.6%, zinc: 0.1%, titanium: 0.15%, the rest is aluminum, and the surface active element is Ce element. The specific implementation steps are as follows:

[0077] (1) Preparation and pretreatment of multi-principal alloy reinforcement particles. According to the nominal composition of the required multi-principal alloy, aluminum powder, chromium powder, iron powder, copper powder and magnesium powder were weighed. Stearic acid with a mass fraction of 3.5% was used as the process control agent. Stainless steel balls were used as the ball-to-material ratio of 8:1. The weighed alloy powder, ball-milling medium and process control agent were poured into a stainless steel grinding jar and mixed evenly. After sealing, high-purity argon gas was filled in. Then, a planetary ball mill was used for abbreviated ball milling at a speed of 530 r / min, 30 min per ball milling, and 15 min rest. The total ball milling time was 35 h. Then, a standard mesh sieve was used to screen the multi-principal alloy particles with an average particle size of 23 μm, which was the required reinforcement particles. Subsequently, the required weight of multi-principal alloy particles was weighed according to the ratio of the composite material, wrapped with aluminum foil, and preheated at 375 °C.

[0078] (2) Stirring casting. The AA3003 alloy ingot was melted in a crucible resistance furnace, and then the melt temperature was adjusted to 750°C. Al-5Ti-1 B master alloy was added at a ratio of 0.5% of the melt mass to refine the matrix alloy. Subsequently, Al-20Ce master alloy was added at a ratio of 0.21% of Ce target content. After it was completely melted, the melt was slowly stirred to make Ce evenly distributed in the melt. Then, the preheated AlFeCuCrMg 1.7The multi-principal alloy was pressed into the bottom of the melt and stirred at a speed of 550 r / min for 20 min. Subsequently, the melt was allowed to stand for 15 min and the melt temperature was adjusted to 710 ° C. The melt was cast into a metal mold in a hydraulic press, and then the alloy melt was extruded and cast at a pressure of 150 MPa. After holding the pressure for 50 seconds, a composite material ingot was obtained.

[0079] (3) Heat treatment. The obtained multi-principal alloy particle reinforced aluminum matrix composite ingot was kept at 600°C for 2 hours, air-cooled to room temperature, then kept at 180°C for 3 hours, and then air-cooled to room temperature. Tensile tests showed that the tensile strength of the composite material was 150 MPa and the elongation was 20.8%.

[0080] Example 9: AlCrFeMnTi 0.25 Multi-principal alloy particle reinforced AA4032-based composite material, adding surface active elements, and heat treatment

[0081] The reinforcement particles used in this example are AlCrFeMnTi 0.25 The multi-principal alloy, the base material is AA4032 aluminum alloy, the specific components of the base material are as follows by weight percentage: silicon: 12.8%, iron: 0.8%, copper: 0.9%, magnesium: 1.1%, nickel: 0.6%, the rest is aluminum, and the surface active element is Sc element. The specific implementation steps are as follows:

[0082] (1) Preparation and pretreatment of multi-principal alloy reinforcement particles. According to the nominal composition of the required multi-principal alloy, appropriate amounts of pure aluminum, aluminum chromium, aluminum iron, aluminum manganese, and aluminum titanium master alloy are weighed and smelted in a medium frequency induction furnace to obtain AlCrFeMnTi 0.25 Multi-principal alloy ingot. Then, the multi-component alloy ingot was used as raw material to prepare multi-principal alloy reinforcement particles with an average particle size of 13 μm by vacuum atomization. Subsequently, the multi-principal alloy particles of the required weight were weighed according to the ratio of the composite material, wrapped with aluminum foil, and preheated at 470°C.

[0083] (2) Stirring casting. Use a crucible resistance furnace to melt the AA4032 alloy ingot, then adjust the melt temperature to 730°C, add Al-5Ti-1 B master alloy at a ratio of 0.5% of the melt mass, and refine the matrix alloy. Then add Al-2Sc master alloy at a ratio of 0.5% of the target Sc content. After it is completely melted, slowly stir the melt to make Sc evenly distributed in the melt, and then add the preheated AlCrFeMnTi at a ratio of 29% by mass. 0.25The multi-principal alloy was pressed into the bottom of the melt and stirred at a speed of 540 r / min for 35 minutes. After that, the melt was allowed to stand for 15 minutes, the melt temperature was adjusted to 690°C, and the melt was cast into a metal mold. After the melt solidified, a composite material ingot was obtained.

[0084] (3) Heat treatment. The obtained multi-principal alloy particle reinforced aluminum matrix composite ingot was kept at 515°C for 10 hours, air-cooled to room temperature, and then kept at 180°C for 3.5 hours, and then air-cooled to room temperature. The tensile test showed that the tensile strength of the composite material was 382.7 MPa and the elongation was 8.4%.

[0085] Example 10: Al 8 Cu 3 MnNiSi 4 Zn 3 Multi-principal alloy particle reinforced AA5083-based composite material, adding surface active elements, and heat treatment

[0086] The reinforcement particles used in this embodiment are Al 8 Cu 3 MnNiSi 4 Zn 3 The multi-principal alloy, the base material is AA5083 aluminum alloy, the specific components of the base material are as follows by weight percentage: magnesium: 4.6%, zinc 0.1%, titanium: 0.12%, manganese: 0.6%, silicon: 0.2%, chromium: 0.2%, the rest is aluminum, and the surface active element is Gd element. The specific implementation steps are as follows:

[0087] (1) Preparation and pretreatment of multi-principal alloy reinforcement particles. According to the nominal composition of the required multi-principal alloy, appropriate amounts of pure aluminum, aluminum copper, aluminum manganese, aluminum nickel, and aluminum silicon master alloy are weighed and smelted in a medium frequency induction furnace to obtain Al 8 Cu 3 MnNiSi 4 Zn 3 Multi-principal alloy ingot. Then, the multi-component alloy ingot was used as raw material to prepare multi-principal alloy reinforcement particles with an average particle size of 21 μm by vacuum atomization. Subsequently, the multi-principal alloy particles of the required weight were weighed according to the ratio of the composite material, wrapped with aluminum foil, and preheated at 420°C.

[0088] (2) Stirring casting. The AA5083 alloy ingot was melted in a crucible resistance furnace, and then the melt temperature was adjusted to 690°C. Al-5Ti-1 B master alloy was added at a ratio of 0.5% of the melt mass to refine the matrix alloy. Subsequently, Al-10Gd master 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 make Gd evenly distributed in the melt. Then, the preheated Al-10Gd master alloy was added at a ratio of 1% by mass. 8 Cu 3 MnNiSi 4 Zn 3 The multi-principal alloy was pressed into the bottom of the melt and stirred at a speed of 505 r / min for 30 min. After that, the melt was allowed to stand for 15 min, the melt temperature was adjusted to 670°C and then cast into a metal mold. After the melt solidified, a composite material ingot was obtained.

[0089] (3) Heat treatment. The obtained multi-principal alloy particle reinforced aluminum matrix composite ingot was kept at 450°C for 20 hours, air-cooled to room temperature, then kept at 140°C for 3 hours, and then air-cooled to room temperature. Tensile tests showed that the tensile strength of the composite material was 400 MPa and the elongation was 16%.

[0090] Example 11: AlNbTiV multi-principal alloy particle reinforced AA6061-based composite material, adding surface active elements, and heat treatment

[0091] The reinforcement particles used in this embodiment are AlNbTiV multi-principal alloy, the matrix material is AA6061 aluminum alloy, and the specific components of the matrix material are as follows by weight percentage: magnesium: 1.1%, zinc: 0.2%, titanium: 0.15%, copper: 0.3%, silicon: 0.6%, manganese: 0.1%, and the rest is aluminum. The surface active element is Er element. The specific implementation steps are as follows:

[0092] (1) Preparation and pretreatment of multi-principal alloy reinforcement particles. According to the nominal composition of the required multi-principal alloy, appropriate amounts of pure aluminum, aluminum niobium, aluminum titanium, and aluminum vanadium intermediate alloys were weighed and smelted in a medium-frequency induction furnace to obtain AlNbTiV multi-principal alloy ingots. Then, using this multi-component alloy ingot as raw material, multi-principal alloy reinforcement particles with an average particle size of 33 μm were prepared by vacuum atomization. Subsequently, the required weight of multi-principal alloy particles was weighed according to the ratio of the composite material, wrapped in aluminum foil, and preheated at 460°C.

[0093] (2) Stirring casting. The AA6061 alloy ingot was melted in a crucible resistance furnace, and then the melt temperature was adjusted to 720°C. Al-5Ti-1 B intermediate alloy was added at a ratio of 0.5% of the melt mass to refine the matrix alloy. Subsequently, Al-20Er intermediate alloy was added at a ratio of 0.15% of the target Er content. After it was completely melted, the melt was slowly stirred to allow Er to be evenly distributed in the melt. Then, the preheated AlNbTiV multi-principal alloy was pressed into the bottom of the melt at a mass fraction of 15%, and stirred at a speed of 480r / min for 30min. Subsequently, the melt was allowed to stand for 15min, and then the aluminum melt was cooled to 500°C to form a semi-solid slurry, and then the slurry was completely solidified in a metal mold at a pressure of 50MPa to obtain a composite material ingot.

[0094] (3) Heat treatment. The obtained multi-principal alloy particle reinforced aluminum matrix composite ingot was kept at 530°C for 15 hours, air-cooled to room temperature, then kept at 180°C for 3 hours, and then air-cooled to room temperature. The tensile test showed that the tensile strength of the composite material was 341 MPa and the elongation was 11%.

[0095] Example 12: (CoCrNi) 20 Al 80 Multi-principal alloy particle reinforced AA7075-based composite material, adding surface active elements, and heat treatment

[0096] The reinforcement particles used in this embodiment are (CoCrNi) 20 Al 80 The multi-principal alloy, the base material is AA7075 aluminum alloy, the specific components of the base material are as follows by weight percentage: magnesium: 2.6%, zinc: 5.7%, titanium: 0.13%, copper: 1.6%, silicon: 0.2%, manganese: 0.2%, chromium: 0.21%, the rest is aluminum, and the surface active element is Sr element. The specific implementation steps are as follows:

[0097] (1) Preparation and pretreatment of multi-principal alloy reinforcement particles. According to the nominal composition of the required multi-principal alloy, appropriate amounts of pure aluminum, aluminum cobalt, aluminum chromium, and aluminum nickel master alloy are weighed and smelted in a medium frequency induction furnace to obtain (CoCrNi) 20 Al 80 Multi-principal alloy ingot. Then, the multi-component alloy ingot was used as raw material to prepare multi-principal alloy reinforcement particles with an average particle size of 38 μm by vacuum atomization. Subsequently, the multi-principal alloy particles of the required weight were weighed according to the ratio of the composite material, wrapped with aluminum foil, and preheated at 450°C.

[0098] (2) Stirring casting. The AA7075 alloy ingot was melted in a crucible resistance furnace, and then the melt temperature was adjusted to 720°C. Al-5Ti-1 B master alloy was added at a ratio of 0.5% of the melt mass to refine the matrix alloy. Subsequently, Al-10Sr master alloy was added at a ratio of 0.13% of the target Sr content. After it was completely melted, the melt was slowly stirred to make Sr evenly distributed in the melt. Then, the preheated (CoCrNi) was added at a ratio of 16% by mass. 20 Al 80 The multi-principal alloy was pressed into the bottom of the melt and stirred at a speed of 510 r / min for 35 min. After that, the melt was allowed to stand for 15 min, the melt temperature was adjusted to 700 °C and then cast into a metal mold, and then the melt was completely solidified at a pressure of 50 MPa to obtain a composite material ingot.

[0099] (3) Heat treatment. The cast multi-principal alloy particle reinforced aluminum matrix composite ingot was kept at 470°C for 24 hours, then air-cooled to room temperature, then kept at 150°C for 12 hours, and then air-cooled to room temperature. The tensile test showed that the tensile strength of the composite material was 658 MPa and the elongation was 9.3%.

[0100] The mechanical properties of the aluminum-based composite materials obtained in the above Examples 1-12 are shown in Table 1:

[0101] Table 1: Mechanical properties of the aluminum-based composite materials involved in the examples

[0102]

[0103]

[0104] It can be seen from Examples 1-3 and Table 1 that the addition of surfactant elements can simultaneously improve the strength and plasticity of the composite material, and after subsequent high-temperature and low-temperature heat treatments, the composite material can further significantly improve its strength while maintaining its plasticity. It can be seen from Examples 3-12 and Table 1 that the method described in the present invention has good applicability to different types of multi-principal alloys and aluminum alloy matrix materials.

[0105] The above description of the embodiments is to facilitate the understanding and use of the present invention by those skilled in the art. It is obvious that those skilled in the art can easily make various modifications to these embodiments and apply the general principles described herein to other embodiments without having to go through creative work. Therefore, the present invention is not limited to the above embodiments, and 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 be within the scope of protection of the present invention.

Claims

1. A multi-principal alloy particle reinforced aluminum matrix composite material, It is characterized in that It includes reinforcement and matrix; The reinforcement is a multi-principal alloy particle with a mass content of 0.1%-30%, and the constituent elements include aluminum, or an element with high solid solubility or high diffusion capacity in aluminum, selected from AlBeFeSiTi system, AlCrFeMnTi system, AlCrTiV system, Mg x (MnAlZnCu) 100-x Series, AlMgZnCuSi series, AlLiMgZnCu series, AlLiMgZnSn series, AlLiMgScTi series, AlNbTiV series, AlFeMgTiZn series, AlLiMgCaSi series, AlCuCrFeSi series, AlCaCuNiSiTi series, AlFeCuCrMg series, AlCuMnNiZnSi series high entropy alloys and (CoCrNi) 100-x Al x One or a combination of two or more alloys in the entropy alloy, wherein x = 0-30%; The matrix is ​​an aluminum alloy with a mass content of 70%-99.9%, selected from cast aluminum alloy and / or 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 particle reinforced aluminum-based composite material comprises the following steps: (1) Preparation and pretreatment of multi-principal alloy reinforcement particles: multi-principal alloy particles are prepared according to the designed multi-principal alloy composition, and the multi-principal alloy particles are weighed according to the proportion, wrapped with aluminum foil, and preheated to obtain multi-principal alloy reinforcement particles; (2) Stirring casting: weighing the matrix and the surfactant element master alloy according to the ratio, smelting to obtain a melt of the matrix material, maintaining the superheat of the melt at 20-100°C during smelting, then adding the surfactant element in the form of the master alloy, and slowly stirring the melt after the master alloy is completely melted to uniformly distribute the surfactant element in the melt, and adding Al-5Ti-1B master alloy to refine the grains of the matrix alloy, and adding Al-Sr master alloy to the matrix material containing eutectic silicon to modify the eutectic silicon; then pressing the multi-principal alloy reinforcement particles obtained in step (1) into the bottom of the matrix melt, and stirring the melt at a speed of 60-600r / min for 10-30min to ensure that the reinforcement particles are uniformly distributed in the melt; adjusting the melt to a pure liquid or semi-solid state and casting it into a mold, and solidifying the alloy at normal pressure or high pressure to obtain a composite material ingot; (3) Heat treatment: The composite material ingot obtained in step (2) is subjected to high-temperature heat treatment, 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 4-50 hours, so as to form a solute supersaturated transition layer between the reinforcement particles and the matrix; and then 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 4-100 hours, thereby obtaining a multi-principal alloy particle reinforced aluminum-based composite material.

2. The multi-principal alloy particle reinforced aluminum matrix composite material according to claim 1, It is characterized in that The multi-principal alloy is selected from Al 20 Be 20 Fe 10 Si 15 Ti 35 Alloy, Al 2 CrFeMnTi alloy, AlCrTiV alloy, Mg 20 (MnAlZnCu) 80 Alloy, Al 63 Mg 27 Zn 4.5 Cu 4.5 Si 1 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 Ca 1 Si 1 Alloy, Al 40 Cu 15 Cr 15 Fe 15 Si 15 Alloy, Al 50 Ca 5 Cu 5 Ni 10 Si 20 Ti 10 Alloy, AlFeCuCrMg 1.7 Alloy, Al 8 Cu 3 MnNiSi 4 Zn 3 Alloy and (CoCrNi) l00-x Al x It is one or a combination of two or more entropy alloys, wherein x=0-30%.

3. The multi-principal alloy particle reinforced aluminum matrix composite material according to claim 1, It is characterized in that The multi-principal alloy is selected from AlLiMgScTi system, AlLiMgZnSn system, AlMgZnCuSi system, Mg x (MnAlZnCu) 100-x series, AlCrTiV series, AlFeCuCrMg series, AlCrFeMnTi series, AlCuMnNiZnSi series, AlNbTiV series, (CoCrNi) l00-x Al x One or a combination of two or more alloys in the series, where x = 0-30%.

4. The multi-principal alloy particle reinforced aluminum matrix composite material according to claim 3, It is characterized in that The multi-principal alloy is selected from AlLiMg 0.5 STi 1.5 Alloy, AlLiMgZnSn alloy, Al 63 Mg 27 Zn 4.5 Cu 4.5 Si 1 Alloy, Mg 50 (MnAlZnCu) 50 Alloy, AlCrTiV alloy, AlFeCuCrMg 1.7 Alloy, AlCrFeMnTi 0.25 Alloy, Al 8 Cu 3 MnNiSi 4 Zn 3 Alloy, AlNbTiV alloy, (CoCrNi) 20 Al 80 One or a combination of two or more alloys.

5. The multi-principal alloy particle reinforced aluminum matrix composite material according to claim 1, It is 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 alloys and cast Al-Li series aluminum alloys; 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 particle reinforced aluminum matrix composite material according to claim 1, It is characterized in that The aluminum alloy is selected from one or a combination of two or more of ZL101, ZL305, ZL205A, 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 multi-principal alloy particle reinforced aluminum matrix composite material according to claim 1, It is characterized in that In step (1), multi-principal alloy particles are prepared by atomization, mechanical alloying, rotating electrode method or spheroidization method, and sieved to obtain multi-principal alloy particles with a particle size of 10-100 microns.

8. The multi-principal alloy particle reinforced aluminum matrix composite material according to claim 1, It is characterized in that In step (2), the melt temperature is adjusted to within 80°C of the liquidus temperature before casting, the pressure of the melt during solidification is controlled at 0-150 MPa, and the holding time is 1-180 s.

9. The multi-principal alloy particle reinforced aluminum matrix composite material according to claim 1, It is characterized in that In step (3), the high temperature heat treatment temperature is 10-30°C below the solidus temperature of the matrix material, 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 10-100h.

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