TiB2 particle reinforced aluminum alloy and preparation method and application thereof

Abstract

The invention provides a TiB2 particle reinforced aluminum alloy and a preparation method and application thereof. The preparation method of the TiB2 particle reinforced aluminum alloy comprises the following steps: adding a titanium source, a boron source and an aluminum-containing fluxing agent into an aluminum-containing melt at 750-1000 DEG C, and carrying out heat preservation treatment to obtain a first melt; alloying elements are added into the first melt at the temperature of 700-800 DEG C, and a second melt is obtained; and the second melt is subjected to solidification treatment, and the TiB2 particle reinforced aluminum alloy is obtained. According to the method, TiB2 reinforced particles are generated in an aluminum matrix through a chemical in-situ generation method, meanwhile, the morphology and content of the formed TiB2 particles are cooperatively regulated and controlled on the basis of parameters in all the steps, and the purposes that the wide-area elastic modulus is adjustable, the interface bonding strength is high, and the technological process is economical and efficient are achieved; therefore, the technical effects of performance customization, preparation technology simplification and wide application field of the high-elasticity, high-plasticity and high-elasticity-modulus aluminum alloy material are achieved.

Description

Technical Field

[0001] This invention relates to the field of aluminum alloy technology, and more specifically, to a TiB2 particle-reinforced aluminum alloy, its preparation method, and its application. Background Technology

[0002] Aluminum alloys, as lightweight structural materials, hold an irreplaceable position in aerospace, new energy vehicles, and high-end equipment. As next-generation equipment develops towards higher load-bearing capacity, lighter weight, and greater integration, there are differentiated requirements for the elastic modulus of aluminum alloys. However, the elastic modulus of conventional aluminum alloys is limited to 70-75 GPa, while existing material modification technologies suffer from narrow control ranges and poor performance matching, failing to meet the customized needs of various scenarios.

[0003] In existing technologies, there are two main technical routes for controlling the elastic modulus of aluminum alloys, both of which have certain limitations:

[0004] (1) Particle-reinforced composite materials are currently the most widely used method for preparing high-modulus aluminum alloys. The core principle is to improve the stiffness of the material by adding high-modulus ceramic particles (such as SiC, TiB2, and Al2O3). A representative patent, such as CN114032429A (authorized in 2022), discloses a method for preparing high-modulus aluminum alloys with 20% SiC particle content by external addition, which can achieve an elastic modulus of 105 GPa. However, this technology has inherent defects that are difficult to overcome: First, in order to achieve high modulus, a large number of particles (usually more than 20%) are added, which leads to a sharp decrease in the plasticity of the material and the elongation is generally less than 1.5%, which cannot meet the needs of structural engineering applications; Second, the interface between the added particles and the aluminum matrix is ​​a physical-mechanical mixture, which easily forms an oxide layer and pores at the interface, resulting in a sharp decrease in the fatigue life of the material, which is far below the requirements of the aerospace field. In addition, this technology requires multiple processes such as particle ball milling (usually more than 20 hours), surface modification, and mixing, which results in a long production cycle and high processing costs. Meanwhile, academic research (Acta Materialia, 2021) has also confirmed that when the content of spherical SiC particles exceeds 15%, the fracture toughness of the composite material will increase from 35 MPa·m. -1 The pressure dropped sharply to 21 MPa·m -1 This results in a severe "embrittlement effect".

[0005] (2) Alloying technology is another approach, which involves adjusting the alloy modulus by adding specific alloying elements (such as Li, Ag, and Sc) and optimizing the heat treatment process. For example, the elastic modulus of 7A09 aluminum alloy can be increased from 70 GPa to 75 GPa by adding 1.2% Li, and the modulus of 2A12 alloy can be increased by about 3 GPa through alloying combined with heat treatment. However, the adjustment range of traditional technical approaches is very limited, and there is a significant problem of matching strength and toughness. The study in Metallurgical and Materials Transactions A (2022) shows that adding more than 2% Li will lead to a significant increase in the hot brittleness of the alloy, and the hot rolling yield will drop from 90% to below 60%. Although the addition of Ag can improve the modulus to a certain extent, it will lead to a decrease in the stress corrosion resistance of the alloy, which limits its application in marine and other environments. At present, the elastic modulus of commercial high-modulus aluminum alloy grades (such as 7A09 and 2A12) is around 75 GPa, which cannot meet the requirements of the aerospace field for materials with a modulus of 100 GPa or higher.

[0006] Besides the aforementioned limitations in controllability and inability to meet diverse application scenarios, modified aluminum alloys obtained through existing technologies often suffer from weak interfacial bonding and poor performance stability. For example, CN 114032429A uses external particles to physically mix with the matrix, which easily leads to the formation of an oxide layer and pores at the interface, resulting in low interfacial bonding strength. Under alternating loads, interfacial "debonding" easily occurs, affecting the fatigue life of the material. This weak interfacial bonding also causes modulus fluctuations, failing to meet the performance stability requirements of precision equipment. Simultaneously, existing technologies generally suffer from cumbersome processes and lengthy workflows. Particle-reinforced composite materials require multiple pretreatment processes such as particle ball milling (generally requiring over 20 hours) and surface modification, making the production cycle several times longer than that of traditional aluminum alloys. While alloying technology has a relatively simpler process, it requires the addition of rare and precious elements (such as Sc and Li), increasing raw material costs. This invention significantly shortens the process and reduces manufacturing costs through an integrated "endogenous method + alloying" process.

[0007] Therefore, how to provide a method for strengthening and modifying aluminum alloys, so as to achieve wide-range control of the elastic modulus of aluminum alloys under low cost and low energy consumption, and obtain new aluminum alloy materials with high elastic modulus and high strength, is one of the technical problems that need to be solved in this field. Summary of the Invention

[0008] The main objective of this invention is to provide a TiB2 particle-reinforced aluminum alloy, its preparation method, and its application, in order to solve the problem that existing technologies cannot prepare aluminum alloys with high strength, high plasticity, and high elastic modulus under conditions of low energy consumption, short process flow, and low cost.

[0009] To achieve the above objectives, the first aspect of the present invention provides a method for preparing TiB2 particle-reinforced aluminum alloy, comprising: step S1, adding a titanium source, a boron source, and an aluminum-containing flux to an aluminum-containing melt at 750°C to 1000°C, and obtaining a first melt after heat treatment; step S2, adding an alloying element to the first melt at 700°C to 800°C to obtain a second melt; and step S3, solidifying the second melt to obtain a TiB2 particle-reinforced aluminum alloy; wherein the alloying element is selected from one or more of Cu, Zr, Zn, and Mg.

[0010] Furthermore, in step S1, the temperature of the aluminum-containing melt is 800℃~850℃, preferably 850℃~950℃, and more preferably 950℃~1000℃.

[0011] Furthermore, in step S1, the heat preservation treatment time is 1h to 3h; and / or, before the solidification treatment, step S3 also includes ultrasonic treatment of the second melt.

[0012] Further, the molar ratio of Ti element in the titanium source to B element in the boron source is 1:(1.8~2.2); and / or, based on 100% of the total weight of the aluminum-containing melt, the total addition amount of the titanium source and the boron source is 5%~30%; and / or, based on 100% of the total weight of the aluminum-containing melt, the addition amount of the aluminum-containing flux is 2%~5%; and / or, the titanium source is selected from one or more of K2TiF6, Na2TiF6 and Li2TiF6; and / or, the boron source is selected from one or more of KBF4, NaBF4 and LiBF4; and / or, the aluminum-containing flux is selected from one or more of Na3AlF6, K3AlF6 and Li3AlF6.

[0013] Furthermore, step S1 also includes adding CeO2 to the aluminum-containing melt, and the amount of CeO2 added is 0.05% to 1% based on the total weight of the aluminum-containing melt as 100%.

[0014] Furthermore, in step S3, the cooling rate of the solidification treatment is 10 K / s~10 4 K / s.

[0015] A second aspect of the present invention provides a TiB2 particle-reinforced aluminum alloy, which is prepared by the above-described method for preparing TiB2 particle-reinforced aluminum alloy, and the TiB2 particle-reinforced aluminum alloy includes an aluminum matrix and TiB2 reinforcing particles.

[0016] Further, the aspect ratio of the TiB2 reinforcing particles is 1 to 10; and / or, based on 100% of the total weight of the TiB2 particle-reinforced aluminum alloy, the content of TiB2 reinforcing particles is 5% to 20%; and / or, the elastic modulus of the TiB2 particle-reinforced aluminum alloy is 70 GPa to 120 GPa; preferably, the aspect ratio of the TiB2 reinforcing particles is 3 to 10; and / or, based on 100% of the total weight of the TiB2 particle-reinforced aluminum alloy, the content of TiB2 reinforcing particles is 8% to 20%; and / or, the elastic modulus of the TiB2 particle-reinforced aluminum alloy is 80 GPa to 120 GPa; more preferably... Preferably, the aspect ratio of the TiB2 reinforcing particles is 5 to 10; and / or, based on 100% of the total weight of the TiB2 particle-reinforced aluminum alloy, the content of TiB2 reinforcing particles is 12% to 20%; and / or, the elastic modulus of the TiB2 particle-reinforced aluminum alloy is 95 GPa to 120 GPa; more preferably, the aspect ratio of the TiB2 reinforcing particles is 8 to 10; and / or, based on 100% of the total weight of the TiB2 particle-reinforced aluminum alloy, the content of TiB2 reinforcing particles is 15% to 20%; and / or, the elastic modulus of the TiB2 particle-reinforced aluminum alloy is 110 GPa to 120 GPa.

[0017] Furthermore, by weight percentage, the aluminum matrix comprises 0.5% to 6.0% Cu, 0% to 8.0% Zn, 0.1% to 3.5% Mg, 0% to 12.0% Si, 0% to 1.0% Mn, 0% to 0.3% Cr, 0% to 1.0% Zr, and 0% to 2.5% Li, with the balance being Al and unavoidable impurities.

[0018] A third aspect of the present invention provides an application of the above-mentioned TiB2 particle-reinforced aluminum alloy as an alloy material in the fields of aerospace, optics and electronic devices.

[0019] By applying the technical solution of this invention, TiB2 reinforcing particles are generated in an aluminum matrix through a chemical in-situ generation method. Simultaneously, based on the synergistic control of parameters in each step, the morphology and content of the TiB2 particles are controlled, achieving the goals of adjustable elastic modulus over a wide range, high interfacial bonding strength, and economical and efficient process flow. This results in the technical effects of customized performance of high-elasticity, high-plasticity, and high-elasticity modulus aluminum alloy materials, simplified preparation technology, and wide application fields. Attached Figure Description

[0020] The accompanying drawings, which form part of this application, are used to provide a further understanding of the invention. The illustrative embodiments of the invention and their descriptions are used to explain the invention and do not constitute an undue limitation of the invention. In the drawings:

[0021] Figure 1The graph shows the relationship between the content of TiB2 reinforcing particles and the elastic modulus of TiB2 particle-reinforced aluminum alloys under different aspect ratios of TiB2 reinforcing particles, based on the Tsai-Halpin equation.

[0022] Figure 2 The results of scanning electron microscopy (SEM) characterization of the alloy billet obtained in Example 1 of this invention are shown.

[0023] Figure 3 The above are the SEM characterization results of the alloy billet obtained in Example 3 of this invention;

[0024] Figure 4 The above are the SEM characterization results of the alloy billet obtained in Example 4 of this invention. Detailed Implementation

[0025] It should be noted that, unless otherwise specified, the embodiments and features described in this application can be combined with each other. The present invention will now be described in detail with reference to the embodiments.

[0026] As described in the background art, the existing technologies for strengthening and modifying aluminum alloys have the following problems: (1) limited control range, making it difficult to meet the needs of multiple scenarios; (2) weak interface bonding and poor performance stability; (3) complex process and high cost. In order to solve the above technical problems, the first aspect of the present invention provides a method for preparing TiB2 particle-reinforced aluminum alloy, comprising: step S1, adding a titanium source, a boron source and an aluminum-containing flux to an aluminum-containing melt at 750℃~1000℃, and obtaining a first melt after heat preservation treatment; step S2, adding alloying elements to the first melt at 700℃~800℃ to obtain a second melt; step S3, solidifying the second melt to obtain a TiB2 particle-reinforced aluminum alloy; the alloying elements are selected from one or more of Cu, Zr, Zn and Mg.

[0027] This invention generates TiB2 reinforcing particles in an aluminum matrix through an in-situ chemical formation method. Simultaneously, by synergistically controlling the morphology and content of the TiB2 particles at each step, the elastic modulus of the resulting TiB2-reinforced aluminum alloy is significantly improved. Specifically: In step S1, a titanium source, a boron source, and an aluminum-containing flux are added to the aluminum-containing melt, followed by heat treatment to form a first melt. During this process, the temperature of the first melt is controlled within the range of 750℃ to 1000℃ to ensure that TiB2 particles are directly generated in-situ through the reaction of this ternary molten salt system within the melt, optimizing the interface with the aluminum matrix. This also promotes optimal distribution and size control of the in-situ formed TiB2 particles in the aluminum alloy matrix, thereby precisely controlling the elastic modulus of the resulting aluminum alloy material. Then, in step S2, one or more alloying elements such as Cu, Zr, Zn, and Mg are added to the second melt, further enhancing the strength and rigidity of the resulting aluminum alloy through multiple mechanisms such as solid solution strengthening, grain refinement, and phase transformation strengthening. Finally, through solidification treatment, fine TiB2 particles and refined matrix grains are obtained, which also promotes more uniform dispersion between the two, further improves the interfacial bonding strength, and ultimately significantly enhances the comprehensive performance of the obtained TiB2 particle-reinforced aluminum alloy material, especially the elastic modulus.

[0028] In summary, compared with the prior art, the preparation method of TiB2 particle-reinforced aluminum alloy provided by the present invention has the following technical effects:

[0029] Firstly, it solves the problem of limited modulus control in existing technologies: existing technologies are limited to the control of a single parameter (such as particle content or alloying elements), and cannot achieve flexible and adjustable modulus over a wide range. This invention, however, achieves controllable adjustment of the morphology and size of the in-situ generated TiB2 particles by controlling the process steps in the preparation process, thereby ensuring the accuracy of the final aluminum alloy modulus adjustment.

[0030] Secondly, it solves the problem of weak interfacial bonding in existing technologies: Most existing high-modulus aluminum alloy preparation techniques employ the method of adding external particles, resulting in low interfacial bonding strength between the particles and the matrix, leading to poor fatigue performance of the alloy. This invention, however, solves the problem of low interfacial bonding strength between reinforcing particles and the matrix through an in-situ endogenous reaction method. During the reaction process involving titanium sources, boron sources, and aluminum-containing fluxes, the interface is cleaner, ensuring higher interfacial bonding strength.

[0031] Third, it solves the problems of complex processes and high costs in existing technologies: Existing technologies require multi-step manufacturing processes (such as particle surface pretreatment, stirring and mixing, etc.), resulting in long production cycles and high costs. However, this invention solves the problems of lengthy processes and high costs through integrated process design, specifically a short process of "particle endogenous generation - alloying - solidification and blanking", which significantly shortens the manufacturing cycle, eliminates auxiliary processes such as particle surface modification, and reduces manufacturing costs.

[0032] Further, in step S1, the temperature of the aluminum-containing melt is 800℃~850℃, preferably 850℃~950℃, and more preferably 950℃~1000℃. In the above progressively preferred schemes: at lower temperatures (800℃~850℃), the formation of TiB2 particles is relatively slow, but it can promote particle refinement and uniform distribution, and reduce particle agglomeration, which is beneficial to improving the plasticity and processing performance of the alloy. As the temperature increases to 850℃~950℃, the reaction rate accelerates, the driving force for TiB2 particle formation is correspondingly enhanced, the particle size increases, and the aspect ratio increases, which is beneficial to further improving the elastic modulus of the obtained TiB2 particle-reinforced aluminum alloy material. When the temperature is further increased to 950℃~1000℃, the morphology of the in-situ formed TiB2 reinforcing particles becomes more regular, the aspect ratio is better controlled, and the particle size distribution is more uniform, thereby significantly improving the elastic modulus of the obtained TiB2 particle-reinforced aluminum alloy material while maintaining high plasticity.

[0033] In step S1, based on the above melt temperature, the heat treatment is further maintained for 1h to 3h to facilitate a more complete reaction of TiB2 reinforcing particles in the melt, forming a more desirable morphology and size, and further promoting the metallurgical bonding between TiB2 reinforcing particles and the matrix, ultimately improving the interfacial strength of the obtained TiB2 particle-reinforced aluminum alloy material more effectively.

[0034] In several typical embodiments, prior to solidification, step S3 preferably includes ultrasonic treatment of the second melt. Ultrasonic treatment introduces micron-level vibrations into the second melt, more effectively promoting the uniform dispersion of TiB2 reinforcing particles. Simultaneously, the cavitation effect of ultrasound can further refine the matrix grains, improving the microstructure of the aluminum alloy and thus significantly enhancing the overall performance of the resulting aluminum alloy. In several more typical embodiments, to more effectively optimize the distribution of TiB2 reinforcing particles without introducing additional defects, thereby further improving the performance and reliability of the resulting TiB2 particle-reinforced aluminum alloy, the ultrasonic treatment frequency is preferably 10 kHz to 30 kHz (more preferably 20 kHz to 25 kHz), and the time is preferably 1 min to 20 min (more preferably 3 min to 15 min). Furthermore, the ultrasonic treatment is preferably performed at 700°C to 740°C (more preferably 720°C to 730°C) to further promote the uniform dispersion of TiB2 reinforcing particles and reduce their agglomeration.

[0035] To effectively control the amount and morphology of TiB2 reinforcing particles, the preferred molar ratio of Ti in the titanium source to B in the boron source is 1:(1.8~2.2). This ensures effective TiB2 particle formation while better avoiding the introduction of excessive or insufficient B, thereby improving the elastic modulus of the resulting TiB2-reinforced aluminum alloy while significantly maintaining its stability and good plasticity. To further optimize the amount and content of TiB2 particles and promote more uniform distribution in the aluminum alloy matrix, the preferred addition amount is 5%~30% of the total weight of the aluminum melt (100%), including both titanium and boron sources. This preferred addition amount not only generates sufficient TiB2 reinforcing particles but also better matches the temperature conditions during the preparation process, achieving a synergistic mechanism of aspect ratio and content of TiB2 reinforcing particles, particularly significantly optimizing the elastic modulus of the resulting TiB2-reinforced aluminum alloy.

[0036] Furthermore, as a component of the ternary molten salt, the flux plays a crucial role in promoting the reaction between the titanium source, boron source, and the melt, accelerating the formation of TiB2 particles, and improving the morphology and distribution of the particles. Based on this, it is preferable that the amount of aluminum-containing flux added is 2% to 5% based on 100% of the total weight of the aluminum-containing melt. This can more effectively reduce the surface tension of the melt and promote the uniform mixing of various elements. Simultaneously, it can further optimize the growth environment of the TiB2 reinforcing particles, promoting a more robust metallurgical bond between them and the matrix, ultimately significantly improving the elastic modulus and overall performance of the resulting TiB2 particle-reinforced aluminum alloy.

[0037] In practical applications, the titanium source is selected from one or more of K2TiF6, Na2TiF6, and Li2TiF6; and / or, the boron source is selected from one or more of KBF4, NaBF4, and LiBF4; and / or, the aluminum-containing flux is selected from one or more of Na3AlF6, K3AlF6, and Li3AlF6. In particular, the ternary molten salt formed by K2TiF6-KBF4-Na3AlF6 provides a more stable and reactive environment, thereby further optimizing the in-situ generation of TiB2 reinforced particles. In this molten salt system, K2TiF6 acts as the Ti source, and KBF4 acts as the B source, interacting with the Al source in the melt to generate TiB2 particles through a chemical reaction. Na3AlF6, as an aluminum-containing flux, can more effectively reduce the viscosity of the melt, promote element diffusion within it, and thus accelerate the in-situ nucleation and growth of TiB2 reinforced particles. Compared to other types of raw materials, the above-mentioned ternary molten salt system can further improve the chemical activity of the reaction system, making the generation of TiB2 reinforced particles more efficient, and better controlling the size and morphology of the formed TiB2 reinforced particles, ultimately significantly optimizing the various properties of the obtained TiB2 particle reinforced aluminum alloy.

[0038] Furthermore, step S1 also includes adding CeO2 to the aluminum-containing melt, and the amount of CeO2 added is 0.05% to 1% based on 100% of the total weight of the aluminum-containing melt. As an effective grain refiner and interface wetting agent, when CeO2 is added to the alloy system provided by the present invention at the above-mentioned amount, it can further improve the bonding state between TiB2 particles and the aluminum alloy matrix through multiple mechanisms such as reducing interfacial energy, promoting uniform particle dispersion, and refining matrix grains, thereby significantly improving the elastic modulus, fatigue performance, and fracture toughness of the obtained TiB2 particle-reinforced aluminum alloy material.

[0039] In step S3, to further refine the grains and suppress the excessive growth and agglomeration of TiB2 reinforcing particles, thereby promoting a more uniform distribution and more ideal morphology, the cooling rate of the solidification treatment is preferably 10 K / s to 10 K / s. 4 K / s, more preferably 10 3 K / s ~10 4 K / s. The aforementioned cooling rate can also correspondingly reduce internal stress and shrinkage cavities, minimizing potential performance degradation or increased brittleness in the resulting TiB2 particle-reinforced aluminum alloy during subsequent processing or service, ultimately leading to higher long-term reliability and applicability. In practical applications, solidification treatment can be achieved through casting, rolling, planar flow casting, or spray deposition.

[0040] A second aspect of this invention provides a TiB2 particle-reinforced aluminum alloy, which is prepared by the aforementioned method for preparing TiB2 particle-reinforced aluminum alloys, and comprises an aluminum matrix and TiB2 reinforcing particles. This invention, by precisely controlling the temperature conditions at each step of the preparation process, regulates the morphology and size of the in-situ generated TiB2 reinforcing particles, thereby improving the modulus of the resulting TiB2 particle-reinforced aluminum alloy material. This not only reduces the high dependence on particle content to achieve the same modulus level but also achieves a significant improvement in the elastic modulus of the aluminum alloy material.

[0041] It should be noted that due to the complex structural changes and crystal formation during the preparation process, and the limitations of the alloy material field and existing testing and characterization methods, it is difficult to comprehensively and quantitatively characterize the complex microstructure and metallographic features of the obtained TiB2 particle-reinforced aluminum alloy. However, the performance test results have shown that the TiB2 particle-reinforced aluminum alloy obtained in this invention has a good morphology and can also possess a higher elastic modulus while maintaining good plasticity.

[0042] Mechanistically, the modulus control mechanism of the TiB2 particle-reinforced aluminum alloy prepared in this invention is based on the Tsai-Halpin theoretical model. The Tsai-Halpin equation mainly considers the matrix material and the modulus and content of the reinforcing particles, while also considering the particle morphology (particle aspect ratio). Specifically, as shown in Equations I and II below, where E... m and E p E represents the elastic modulus of the aluminum alloy matrix and the reinforcing particles (TiB2), respectively. （TiB2） =529 GPa, E （Al基体） =70.3GPa, V p is the volume content of TiB2 particles in the composite material, and s is the shape factor (aspect ratio) of the reinforcing particles.

[0043] Formula I.

[0044] , Formula II.

[0045] Based on the Tsai-Halpin equation, this invention constructs a "particle content-morphology-modulus" relationship model for the TiB2 particle-reinforced aluminum alloy prepared above, to describe the influence of TiB2 particle content and morphology on the elastic modulus of the alloy. Through this equation, the relationship curves between TiB2 particle content and the elastic modulus of the TiB2 particle-reinforced aluminum alloy under different aspect ratios of TiB2 reinforcing particles are obtained, as shown in the figure. Figure 1 As shown. By Figure 1 As the model shows, the elastic modulus of particle-reinforced aluminum alloys is mainly controlled by the content and shape of the reinforcing particles. Specifically, in Figure 1 In the study, when the aspect ratio (s) of the particles is 1, approximately 27% particle content is required to achieve a modulus of 100 GPa; while when the aspect ratio of the particles increases to 8, only about 13% particle content is required to achieve the same modulus target, indicating that high modulus can be achieved at low content through morphology control.

[0046] In other words, by optimizing the process parameters during the preparation of the TiB2 particle-reinforced aluminum alloy obtained by this invention, the morphology and content of the reinforcing particles can be synergistically controlled, thereby enabling more flexible design and preparation of aluminum alloy materials with different elastic moduli, and also enabling the acquisition of aluminum alloy materials with higher elastic moduli. Based on this, in several preferred embodiments: the aspect ratio of the TiB2 reinforcing particles is 1~10; and / or, based on 100% of the total weight of the TiB2 particle-reinforced aluminum alloy, the content of TiB2 reinforcing particles is 5%~20%; the resulting TiB2 particle-reinforced aluminum alloy has an elastic modulus of 70GPa~120GPa. In several more preferred embodiments: the aspect ratio of the TiB2 reinforcing particles is 3~10; and / or, based on 100% of the total weight of the TiB2 particle-reinforced aluminum alloy, the content of TiB2 reinforcing particles is 8%~20%; the resulting TiB2 particle-reinforced aluminum alloy has an elastic modulus of 80GPa~120GPa. In several further preferred embodiments: the aspect ratio of the TiB2 reinforcing particles is 5 to 10; and / or, based on 100% of the total weight of the TiB2 particle-reinforced aluminum alloy, the content of TiB2 reinforcing particles is 12% to 20%; the resulting TiB2 particle-reinforced aluminum alloy has an elastic modulus of 95 GPa to 120 GPa. In several even more preferred embodiments, the aspect ratio of the TiB2 reinforcing particles is 8 to 10; and / or, based on 100% of the total weight of the TiB2 particle-reinforced aluminum alloy, the content of TiB2 reinforcing particles is 15% to 20%; the resulting TiB2 particle-reinforced aluminum alloy has an elastic modulus of 110 GPa to 120 GPa.

[0047] Furthermore, to further utilize the synergistic effect of the alloying elements, thereby enabling the obtained TiB2 particle-reinforced aluminum alloy to maintain a high elastic modulus while possessing better comprehensive mechanical properties and environmental adaptability, the aluminum matrix preferably comprises, by weight percentage, 0.5%~6.0% Cu, 0%~8.0% Zn, 0.1%~3.5% Mg, 0%~12.0% Si, 0%~1.0% Mn, 0%~0.3% Cr, 0%~1.0% Zr, and 0%~2.5% Li, with the balance being Al and unavoidable impurities. The aluminum matrix is ​​either a wrought aluminum alloy or a cast aluminum alloy.

[0048] A third aspect of this invention provides applications of the aforementioned TiB2 particle-reinforced aluminum alloy as an alloy material in the aerospace, optics, and electronics fields. Because the TiB2 reinforcing particles in the aforementioned TiB2 particle-reinforced aluminum alloy possess superior morphology and size, the resulting aluminum alloy, with its excellent elastic modulus, high strength, good damping properties, and environmental adaptability, has become an ideal alloy material in aerospace, optics, and electronics fields. Specifically, in the aerospace field, the aforementioned TiB2 particle-reinforced aluminum alloy provided by this invention can be applied to satellite supports, launch vehicle bodies, etc., meeting stringent requirements for lightweight and high rigidity of structural components, while reducing the weight of the aircraft and increasing its payload capacity. In the optics field, the high elastic modulus and damping properties of the aforementioned TiB2 particle-reinforced aluminum alloy provided by this invention make it an ideal choice for optical platforms and supports, effectively reducing environmental vibrations and improving the measurement accuracy and stability of equipment. In the electronics field, the lightweight and high-strength characteristics of the aforementioned TiB2 particle-reinforced aluminum alloy provided by this invention make it a suitable material for the shell or frame of high-end electronic products, effectively protecting internal components from external impacts while reducing the overall weight of the product, improving portability and user experience.

[0049] The present application will be further described in detail below with reference to specific embodiments, which should not be construed as limiting the scope of protection claimed in the present application.

[0050] Unless otherwise defined, all technical terms used herein have the same meaning as commonly understood by those skilled in the art. The technical terms used herein are for the purpose of describing particular embodiments only and are not intended to limit the scope of the invention.

[0051] Example 1

[0052] A method for preparing TiB2 particle-reinforced aluminum alloy:

[0053] The following raw materials, by weight percentage, were used as the matrix: Cu: 1.6%, Mg: 2.5%, Zn: 5.6%, Cr: 0.23%, Zr: 0.15%, Ce: 0.1%, with the balance being Al and unavoidable impurities. (The above component contents are as shown in Table 1). Furthermore, the resulting TiB2 particle-reinforced aluminum alloy also includes 17.5% TiB2 reinforcing particles by weight.

[0054] (1) First, the melting furnace is preheated to 950~1000℃, and pure aluminum is added to melt it, resulting in an aluminum-containing melt at 950~1000℃. Then, the oxide layer and impurities on the surface of the melt are removed. Next, dried K2TiF6, KBF4, Na3AlF6 and CeO2 raw materials are added in batches and stirred with a graphite rod until all raw materials are added. The melt is then allowed to stand for 2~3 hours to obtain the first melt. In this process, K2TiF6 is used as a titanium source and KBF4 is used as a boron source, with a molar ratio of 1:2 and a total addition amount of 20 wt.% of the aluminum-containing melt. Na3AlF6 is used as an aluminum-containing flux, with an addition amount of 3.5 wt.% of the aluminum-containing melt. The addition amount of CeO2 is 0.1 wt.% of the aluminum-containing melt.

[0055] (2) After that, remove the slag from the surface of the first melt and stir it for 2 to 3 minutes before quickly transferring it to the alloying crucible. In the alloying furnace, set the temperature to 780°C and melt the Al-50Cu alloy, melt the Al-10Zr alloy and pure Zn at 750°C, and melt the pure Mg at 730°C to obtain the second melt.

[0056] (3) The resulting second melt was subjected to ultrasonic treatment at 730°C at a frequency of 20 kHz for 10 minutes, followed by stirring and degassing at 710°C for 15 minutes. Finally, it was cast in a planar flow casting manner at 710°C with a frequency of 10 kHz. 3 K / s ~10 4 The strip blank is prepared by a cooling rate of K / s, and then the alloy billet is made by hot extrusion.

[0057] The SEM characterization results of the obtained alloy billet are shown in the figure. Figure 2 As can be seen from the figure, the aspect ratio of the TiB2 reinforcing particles in the aluminum matrix is ​​approximately 7.5 to 8.5.

[0058] The resulting alloy billet can be used as a high-strength, ultra-high-modulus aluminum alloy for aerospace applications.

[0059] Example 2

[0060] A method for preparing TiB2 particle-reinforced aluminum alloy:

[0061] The following raw materials, by weight percentage, were used as the matrix: Cu: 1.6%, Mg: 2.5%, Zn: 5.6%, Cr: 0.23%, Zr: 0.15%, Ce: 0.1%, with the balance being Al and unavoidable impurities. (The above component contents are as shown in Table 1). Furthermore, the resulting TiB2 particle-reinforced aluminum alloy also includes 13.4% TiB2 reinforcing particles by weight.

[0062] (1) First, the melting furnace is preheated to 850~950℃, and pure aluminum is added to melt it, resulting in an aluminum-containing melt at 850~950℃. Then, the oxide layer and impurities on the surface of the melt are removed. Next, dried K2TiF6, KBF4, Na3AlF6 and CeO2 raw materials are added in batches and stirred with a graphite rod until all raw materials are added. The melt is then allowed to stand for 1.5~2 hours to obtain the first melt. In this process, K2TiF6 is used as a titanium source and KBF4 is used as a boron source, with a molar ratio of 1:2 and a total addition amount of 15 wt% of the aluminum-containing melt. Na3AlF6 is used as an aluminum-containing flux, with an addition amount of 3.5 wt% of the aluminum-containing melt. The addition amount of CeO2 is 0.1 wt% of the aluminum-containing melt.

[0063] (2) After that, remove the slag from the surface of the first melt and stir it for 2 to 3 minutes before quickly transferring it to the alloying crucible. In the alloying furnace, set the temperature to 750°C and melt the Al-50Cu alloy, melt the Al-10Zr alloy and pure Zn at 730°C, and melt the pure Mg at 720°C to obtain the second melt.

[0064] (3) The resulting second melt was subjected to ultrasonic treatment at 720°C at a frequency of 20 kHz for 5 minutes, followed by stirring and degassing at 700°C for 10 minutes. Finally, it was cast using a water-cooled copper mold at 700°C with a flow rate of 10... 2 K / s ~10 3 Alloy billets are produced by a cooling rate of K / s.

[0065] The resulting alloy billet can be used as a high-modulus aluminum alloy for aerospace applications.

[0066] Example 3

[0067] A method for preparing TiB2 particle-reinforced aluminum alloy:

[0068] The raw materials were formulated as a matrix with the following composition, by weight percentage: Si: 6.8%, Mg: 0.35%, Ce: 0.1%, with the balance being Al and unavoidable impurities. (The above component contents are as shown in Table 1). Furthermore, the resulting TiB2 particle-reinforced aluminum alloy also includes 9.0% TiB2 reinforcing particles by weight.

[0069] (1) First, the melting furnace is preheated to 800~850℃, and pure aluminum is added to melt it, resulting in an aluminum-containing melt at 800~850℃. Then, the oxide layer and impurities on the surface of the melt are removed. Next, dried K2TiF6, KBF4, Na3AlF6 and CeO2 raw materials are added in batches and stirred with a graphite rod until all raw materials are added. The melt is then allowed to stand for 1~1.5 hours to obtain the first melt. In this process, K2TiF6 is used as a titanium source and KBF4 is used as a boron source, with a molar ratio of 1:2 and a total addition amount of 10 wt% of the aluminum-containing melt. Na3AlF6 is used as an aluminum-containing flux, with an addition amount of 3.5 wt% of the aluminum-containing melt. The addition amount of CeO2 is 0.1 wt% of the aluminum-containing melt.

[0070] (2) After that, remove the slag from the surface of the first melt and stir it for 1 to 2 minutes before quickly transferring it to the alloying crucible. In the alloying furnace, set the temperature to 750°C and melt the Al-30Si alloy, and melt pure Mg at 720°C to obtain the second melt.

[0071] (3) The resulting second melt was subjected to ultrasonic treatment at 720°C at a frequency of 20 kHz for 3 minutes, followed by stirring and degassing at 700°C for 10 minutes. Finally, it was cast at 700°C using a water-cooled copper mold with a flow rate of 10... 2 K / s ~10 3 Alloy billets are produced by a cooling rate of K / s.

[0072] The SEM characterization results of the obtained alloy billet are shown in the figure. Figure 3 As can be seen from the figure, the aspect ratio of the TiB2 reinforcing particles in the aluminum matrix is ​​approximately 3.0 to 4.5.

[0073] The resulting alloy billet can be used as a medium-modulus cast aluminum alloy for automobiles.

[0074] Example 4

[0075] A method for preparing TiB2 particle-reinforced aluminum alloy:

[0076] The raw materials used as the matrix are formulated with the following composition, by weight percentage: Mg: 1.0%, Si: 0.6%, Cu: 0.28%, Cr: 0.2%, Ce: 0.1%, with the balance being Al and unavoidable impurities. (The above component contents are as shown in Table 1). Furthermore, the resulting TiB2 particle-reinforced aluminum alloy also includes 6.5% TiB2 reinforcing particles by weight.

[0077] (1) First, the melting furnace is preheated to 750~800℃, and pure aluminum is added to melt it, resulting in an aluminum-containing melt at 750~800℃. Then, the oxide layer and impurities on the surface of the melt are removed. Next, dried K2TiF6, KBF4, Na3AlF6 and CeO2 raw materials are added in batches and stirred with a graphite rod until all raw materials are added. The melt is then allowed to stand for 1~1.5 hours to obtain the first melt. In this process, K2TiF6 is used as a titanium source and KBF4 is used as a boron source, with a molar ratio of 1:2 and a total addition amount of 7 wt% of the aluminum-containing melt. Na3AlF6 is used as an aluminum-containing flux, with an addition amount of 3 wt% of the aluminum-containing melt. The addition amount of CeO2 is 0.1 wt% of the aluminum-containing melt.

[0078] (2) After that, remove the slag from the surface of the first melt and stir it for 1 to 2 minutes before quickly transferring it to an alloying crucible. In the alloying furnace, cool it to 730°C and add Al-50Cu master alloy and pure Mg to obtain the second melt.

[0079] (3) The obtained second melt was subjected to ultrasonic treatment at 720°C at a frequency of 20kHz for 3 minutes, and then stirred and degassed at 700°C for 10 minutes. Finally, the melt was poured directly into a preheated steel mold and naturally cooled to room temperature at a cooling rate of 1~10 K / s to obtain an alloy billet.

[0080] The SEM characterization results of the obtained alloy billet are shown in the figure. Figure 4 As can be seen from the figure, the aspect ratio of the TiB2 reinforcing particles in the aluminum matrix is ​​approximately 2.2 to 3.0.

[0081] The resulting alloy billet can be used as an aluminum alloy for optical inspection equipment (base).

[0082] Example 5

[0083] A method for preparing TiB2 particle-reinforced aluminum alloy:

[0084] The only difference between this embodiment and embodiment 1 is that the amount of K2TiF6 and KBF4 added in step (1) is changed so that the molar ratio of Ti element in K2TiF6 to B element in KBF4 is changed to 1:1.5 while the total amount of both added remains unchanged.

[0085] Example 6

[0086] A method for preparing TiB2 particle-reinforced aluminum alloy:

[0087] The only difference between this embodiment and embodiment 1 is that the amount of K2TiF6 and KBF4 added in step (1) is changed so that the molar ratio of Ti element in K2TiF6 to B element in KBF4 is changed to 1:2.5 while the total amount of both added remains unchanged.

[0088] Example 7

[0089] A method for preparing TiB2 particle-reinforced aluminum alloy:

[0090] The only difference between this embodiment and Embodiment 1 is that the amount of K2TiF6 and KBF4 added in step (1) is changed so that the total amount of the two added relative to the aluminum-containing melt is changed to 3%.

[0091] Example 8

[0092] A method for preparing TiB2 particle-reinforced aluminum alloy:

[0093] The only difference between this embodiment and Embodiment 1 is that the amount of K2TiF6 and KBF4 added in step (1) is changed so that the total amount of the two added relative to the aluminum-containing melt is changed to 35%.

[0094] Example 9

[0095] A method for preparing TiB2 particle-reinforced aluminum alloy:

[0096] The only difference between this embodiment and Embodiment 1 is that the amount of Na3AlF6 added in step (1) is changed to 6% relative to the amount of aluminum-containing melt.

[0097] Example 10

[0098] A method for preparing TiB2 particle-reinforced aluminum alloy:

[0099] The only difference between this embodiment and Embodiment 1 is that the amount of CeO2 added in step (1) is changed to 1.2% relative to the amount of aluminum-containing melt.

[0100] Example 11

[0101] A method for preparing TiB2 particle-reinforced aluminum alloy:

[0102] The only difference between this embodiment and embodiment 1 is that in step (1), the heat preservation time is changed to 0.5~0.8 hours.

[0103] Example 12

[0104] A method for preparing TiB2 particle-reinforced aluminum alloy:

[0105] The only difference between this embodiment and embodiment 1 is that in step (3), the ultrasonic treatment is changed to: ultrasonic treatment at 700°C with a frequency of 10kHz for 20 minutes.

[0106] Example 13

[0107] A method for preparing TiB2 particle-reinforced aluminum alloy:

[0108] The only difference between this embodiment and embodiment 1 is that in step (3), the ultrasonic treatment is changed to: ultrasonic treatment at 740°C with a frequency of 30kHz for 1 minute.

[0109] Comparative Example 1

[0110] A method for preparing SiC particle-reinforced aluminum alloy:

[0111] This comparative example references existing technology CN114032429A, using commercially available SiC particle-reinforced aluminum alloy. The particle aspect ratio distribution is uneven (0.3~1). To achieve the desired target modulus, at least 25 wt.% SiC particles need to be added, and reinforcement is achieved through physical mixing. The specific preparation method is as follows:

[0112] (1) Experimental preparation: SiC particles (average particle size 0.5~5μm, aspect ratio 0.3~1) were ball-milled in a planetary ball mill at 400r / min for 20h, surface modified with silane coupling agent, and dried at 120℃ for 4h.

[0113] (2) Melting and casting process: Preheat the melting furnace to 800℃, add pure aluminum to melt and remove the oxide scale, add modified SiC particles in 3 batches, mechanically stir (200r / min) for 30min, and let stand and keep warm for 1h; pour into steel mold at 720℃ and let cool naturally.

[0114] (3) Heat treatment: homogenization annealing at 520℃ for 4 hours, followed by air cooling to room temperature.

[0115] Although the aluminum alloy obtained in this comparative example has a high elastic modulus, its elongation is only about 0.3%, which is equivalent to almost no plasticity, making it difficult to use in practical applications. At the same time, observation under an optical microscope shows obvious local particle agglomeration and the presence of an oxide layer at the interface, indicating poor morphology.

[0116] Furthermore, it is also important to note that the particle pretreatment process performed in step (1) means that the total cost of preparing this aluminum alloy will increase by more than 40% compared to the above embodiments.

[0117] Comparative Example 2

[0118] A method for preparing SiC particle-reinforced aluminum alloy:

[0119] This comparative example uses traditional Al-Li alloying technology, adding 1.5 wt.% Li to improve the modulus, and strengthening with Cu and Mn elements without introducing ceramic particles. The specific preparation method is as follows:

[0120] (1) Melting: Melt pure aluminum at 750℃, and add Al-20Li master alloy, Al-50Cu alloy (Cu content 2.5%) and pure Mn (0.3%) in sequence, and stir for 20 min.

[0121] (2) Casting: Pour the water-cooled copper mold at 720℃ to obtain an ingot with a diameter of 80mm.

[0122] (3) Heat treatment: solution treatment at 470℃ for 2 hours followed by water quenching, and aging at 120℃ for 24 hours.

[0123] The aluminum alloy obtained in this comparative example not only has a low elastic modulus, but also suffers from a Li element burn-off rate of over 15% during its preparation, and exhibits hot crack defects on the ingot surface. Furthermore, compared to Example 4, which has a comparable elastic modulus, this comparative example has a raw material cost increase of over 30%, making it difficult to implement in practical applications.

[0124] Table 1

[0125]

[0126] Test methods

[0127] The aspect ratio of the TiB2 reinforcing particles in the obtained aluminum alloy samples was obtained by scanning electron microscopy (SEM) combined with image analysis software. Specifically, at least five fields of view were randomly selected from the samples, and high-magnification morphology photographs were acquired using a scanning electron microscope in secondary electron mode. These photographs were then imported into image analysis software (such as Image-Pro Plus, IPP). TiB2 particles were identified and labeled through threshold segmentation and morphological processing. Subsequently, the software automatically calculated the major and minor axis dimensions of at least 500 particles, and the arithmetic mean of their ratios was taken as the average aspect ratio.

[0128] The weight content of TiB2 reinforcing particles in the obtained aluminum alloy samples was determined using scanning electron microscopy (SEM) combined with image analysis software. Specifically, the image analysis software was used to calculate the ratio of the pixel area occupied by TiB2 particles to the total pixel area of ​​the statistical field of view in the acquired SEM images, obtaining the particle area fraction. Based on stereoscopic principles, this was approximated as a volume fraction. Then, based on the theoretical density of TiB2, the weight content of the TiB2 reinforcing particles was calculated.

[0129] The elastic modulus of the obtained aluminum alloy sample was obtained by ultrasonic pulse excitation method, and the test procedure was in accordance with GB / T 22315-2008 "Metallic materials - test method for elastic modulus and Poisson's ratio".

[0130] The above tests were performed on the aluminum alloy samples obtained in each embodiment and comparative example, and the results are shown in Table 2.

[0131] Table 2

[0132]

[0133] As can be seen from the above description, compared with the comparative examples, the above embodiments of the present invention optimize the process parameters in the preparation process of TiB2 particle-reinforced aluminum alloy, thereby synergistically controlling the morphology and content of TiB2 reinforcing particles, and thus more flexibly preparing aluminum alloy materials with different elastic moduli, and also obtaining aluminum alloy materials with higher elastic moduli.

[0134] In various embodiments:

[0135] Comparing Examples 5 and 6 with Example 1, it can be seen that by optimizing the molar ratio of Ti element in the titanium source to B element in the boron source, it is possible to better avoid the introduction of excessive or insufficient B element while ensuring the effective generation of TiB2 particles. This not only improves the elastic modulus of the obtained TiB2 particle-reinforced aluminum alloy, but also significantly maintains its stability and good plasticity.

[0136] Comparing Examples 7 and 8 with Example 1, it can be seen that by optimizing the total amount of titanium and boron sources, the amount and content of TiB2 particles can be further optimized, resulting in a more uniform distribution of TiB2 particles in the aluminum alloy matrix. This better realizes the synergistic mechanism of the aspect ratio and content of TiB2 reinforcing particles, and significantly optimizes the elastic modulus of the resulting TiB2 particle-reinforced aluminum alloy.

[0137] Comparing Example 9 with Example 1, it can be seen that by optimizing the amount of aluminum-containing flux added, the surface tension of the melt can be reduced more effectively, promoting the uniform mixing of various elements. At the same time, the growth environment of the TiB2 reinforcing particles can be further optimized, leading to a more stable metallurgical bond between them and the matrix, ultimately significantly improving the elastic modulus and overall performance of the resulting TiB2 particle-reinforced aluminum alloy material.

[0138] Comparing Example 10 with Example 1, it can be seen that by adding a specific amount of CeO2 during the preparation process, the bonding state between TiB2 particles and the aluminum alloy matrix can be further improved through multiple mechanisms such as reducing interfacial energy, promoting uniform particle dispersion, and refining matrix grains. This results in a more significant improvement in the elastic modulus, fatigue performance, and fracture toughness of the obtained TiB2 particle-reinforced aluminum alloy material.

[0139] Comparing Example 11 with Example 1, it can be seen that by optimizing the holding time in step S1, the TiB2 reinforcing particles can react more fully in the melt, forming a more desirable morphology and size. At the same time, it further promotes the metallurgical bonding between the TiB2 reinforcing particles and the matrix, and ultimately more effectively improves the interfacial strength of the obtained TiB2 particle-reinforced aluminum alloy material.

[0140] Comparing Examples 12 and 13 with Example 1, it can be seen that by optimizing the conditions of ultrasonic treatment in step S3, the distribution of TiB2 reinforcing particles can be optimized more effectively without introducing additional defects, thereby further improving the performance and reliability of the obtained TiB2 particle-reinforced aluminum alloy.

[0141] It should be noted that the terms "first," "second," etc., used in the specification and claims of this application are used to distinguish similar objects and are not necessarily used to describe a specific order or sequence. It should be understood that such terms can be used interchangeably where appropriate so that the embodiments of this application described herein can be implemented, for example, in a sequence other than those described herein.

[0142] The above description is merely a preferred embodiment of the present invention and is not intended to limit the invention. Various modifications and variations can be made to the present invention by those skilled in the art. Any modifications, equivalent substitutions, improvements, etc., made within the spirit and principles of the present invention should be included within the scope of protection of the present invention.

Claims

1. A method for preparing TiB2 particle-reinforced aluminum alloy, characterized in that, include: Step S1: Add titanium source, boron source and aluminum-containing flux to aluminum-containing melt at 750℃~1000℃, and obtain the first melt after heat preservation treatment; Step S2: Add alloying elements to the first melt at 700℃~800℃ to obtain the second melt; Step S3: The second melt is solidified to obtain the TiB2 particle-reinforced aluminum alloy; The alloying element is selected from one or more of Cu, Zr, Zn and Mg.

2. The method for preparing TiB2 particle-reinforced aluminum alloy according to claim 1, characterized in that, In step S1, the temperature of the aluminum-containing melt is 800℃~850℃, preferably 850℃~950℃, and more preferably 950℃~1000℃.

3. The method for preparing TiB2 particle-reinforced aluminum alloy according to claim 1 or 2, characterized in that, In step S1, the heat preservation treatment time is 1 hour to 3 hours; and / or, Prior to the solidification process, step S3 further includes ultrasonic treatment of the second melt.

4. The method for preparing TiB2 particle-reinforced aluminum alloy according to any one of claims 1 to 3, characterized in that, The molar ratio of Ti in the titanium source to B in the boron source is 1:(1.8~2.2); and / or, Based on the total weight of the aluminum-containing melt as 100%, the total addition amount of the titanium source and the boron source is 5% to 30%; and / or, Based on the total weight of the aluminum-containing melt as 100%, the amount of aluminum-containing flux added is 2% to 5%; and / or, The titanium source is selected from one or more of K2TiF6, Na2TiF6, and Li2TiF6; and / or, The boron source is selected from one or more of KBF4, NaBF4, and LiBF4; and / or, The aluminum-containing flux is selected from one or more of Na3AlF6, K3AlF6 and Li3AlF6.

5. The method for preparing TiB2 particle-reinforced aluminum alloy according to any one of claims 1 to 4, characterized in that, Step S1 further includes adding CeO2 to the aluminum-containing melt, and the amount of CeO2 added is 0.05% to 1% based on the total weight of the aluminum-containing melt as 100%.

6. The method for preparing TiB2 particle-reinforced aluminum alloy according to any one of claims 1 to 5, characterized in that, In step S3, the cooling rate of the solidification treatment is 10 K / s~10 4 K / s.

7. A TiB2 particle-reinforced aluminum alloy, characterized in that, The TiB2 particle-reinforced aluminum alloy is prepared by the method for preparing TiB2 particle-reinforced aluminum alloy according to any one of claims 1 to 6, and the TiB2 particle-reinforced aluminum alloy includes an aluminum matrix and TiB2 reinforcing particles.

8. The TiB2 particle-reinforced aluminum alloy according to claim 7, characterized in that, The aspect ratio of the TiB2 reinforcing particles is 1 to 10; and / or, based on the total weight of the TiB2 particle-reinforced aluminum alloy as 100%, the content of the TiB2 reinforcing particles is 5% to 20%; and / or, the elastic modulus of the TiB2 particle-reinforced aluminum alloy is 70 GPa to 120 GPa. Preferably, the aspect ratio of the TiB2 reinforcing particles is 3 to 10; and / or, based on the total weight of the TiB2 particle-reinforced aluminum alloy as 100%, the content of the TiB2 reinforcing particles is 8% to 20%; and / or, the elastic modulus of the TiB2 particle-reinforced aluminum alloy is 80 GPa to 120 GPa. More preferably, the aspect ratio of the TiB2 reinforcing particles is 5 to 10; and / or, based on the total weight of the TiB2 particle-reinforced aluminum alloy as 100%, the content of the TiB2 reinforcing particles is 12% to 20%; and / or, the elastic modulus of the TiB2 particle-reinforced aluminum alloy is 95 GPa to 120 GPa. More preferably, the aspect ratio of the TiB2 reinforcing particles is 8 to 10; and / or, based on the total weight of the TiB2 particle-reinforced aluminum alloy as 100%, the content of the TiB2 reinforcing particles is 15% to 20%; and / or, the elastic modulus of the TiB2 particle-reinforced aluminum alloy is 110 GPa to 120 GPa.

9. The TiB2 particle-reinforced aluminum alloy according to claim 7 or 8, characterized in that, The aluminum matrix comprises, by weight percentage, 0.5% to 6.0% Cu, 0% to 8.0% Zn, 0.1% to 3.5% Mg, 0% to 12.0% Si, 0% to 1.0% Mn, 0% to 0.3% Cr, 0% to 1.0% Zr and 0% to 2.5% Li, with the balance being Al and unavoidable impurities.

10. The application of a TiB2 particle-reinforced aluminum alloy as an alloy material in the aerospace, optical, and electronic device fields, according to any one of claims 7 to 9.

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