TiB2 / Al-cu alloys, methods of making and additive manufacturing uses thereof

Abstract

The application provides a TiB2 / Al-Cu alloy, a preparation method thereof and an additive manufacturing purpose, the TiB2 / Al-Cu alloy is prepared by using a mixed salt in-situ self-generation method with magnetic field vibration assisted mechanical stirring, which is beneficial to promote the uniform dispersion of micro-nano TiB2 particles formed in the material, plays a particle heterogenous nucleation role and a strengthening role, and can effectively improve the laser absorption rate of the alloy in the additive manufacturing process; in basic components of the TiB2 / Al-Cu alloy, the mass fraction of Cu is 1-5%, the mass fraction of Mn is 0.1-0.3%, the mass fraction of TiB2 is 1-8%, and the balance is Al. Preferably, trace alloying elements such as Mn and Zr / Y are added in the smelting process, so that the grains can be refined in the alloying process, and the mechanical properties and corrosion resistance of the material are improved.

Description

Technical Field

[0001] This invention relates to the field of additive manufacturing materials technology, and in particular to TiB2 / Al-Cu alloy, its preparation method and additive manufacturing applications. Background Technology

[0002] Al-Cu alloys possess characteristics such as low density, high specific strength and stiffness, good plasticity, excellent thermal conductivity, and corrosion resistance, making them the preferred material for achieving lightweight structures in high-end key equipment and showing broad application prospects in the aerospace and marine equipment fields. However, due to their wide solidification temperature range, Al-Cu alloys exhibit poor casting performance, particularly a high tendency for hot cracking, shrinkage porosity, and other defects. Furthermore, the components are highly sensitive to wall thickness, and defects such as porosity, hot cracking, and oxide inclusions are easily generated during the casting process. Their low laser absorption rate also makes them unsuitable for laser additive manufacturing (also known as 3D printing).

[0003] Currently, methods used to improve the forming quality and mechanical properties of 3D-printed Al-Cu alloys mainly include: 1. Introducing heterogeneous particles into aluminum alloy powder through electrostatic self-assembly, high-energy ball milling, aerosol-delivered binder, and ultrasonic vibration dispersion techniques. These heterogeneous particles, such as nano-ZrH, TiC, TiB2, TiN, and SiC particles, can effectively improve the laser absorption rate of aluminum powder, alter the evolution process of the molten pool solidification structure, exert a dispersion strengthening effect, and significantly improve the mechanical properties of 3D-printed aluminum alloys. However, these preparation methods are generally complex, and heterogeneous particles are difficult to disperse uniformly in the form of nanoparticles, easily introducing other impurities that are difficult to remove, or damaging the sphericity of the aluminum powder and reducing powder flowability. This method can achieve good results in the experimental stage, but it is difficult to achieve mass production, limiting its industrial application. 2. Controlling the chemical composition of aluminum powder during the atomization preparation process and changing the physical properties of aluminum alloy through micro-alloying design to adapt it to the extremely non-equilibrium metallurgical process of 3D printing. Summary of the Invention

[0004] Due to the aforementioned deficiencies in existing technologies, this invention provides a TiB2 / Al-Cu alloy, its preparation method, and its additive manufacturing applications. The TiB2 / Al-Cu alloy is prepared using a mixed salt in-situ self-generating method with magnetic field vibration-assisted mechanical stirring. This method promotes the uniform dispersion of micro / nano TiB2 particles within the material, leveraging their heterogeneous nucleation and reinforcing effects, and effectively improving the laser absorption rate of the alloy during additive manufacturing. The addition of trace alloying elements such as Mn and Zr / Y during the smelting process refines the grains and improves the material's mechanical properties and corrosion resistance.

[0005] To achieve the above objectives, in a first aspect, the present invention provides a method for preparing a TiB2 / Al-Cu alloy and the prepared TiB2 / Al-Cu alloy, characterized in that, by mass fraction, the TiB2 / Al-Cu alloy composition comprises Cu: 1~5%; Mn: 0.1~0.3%; TiB2: 1~8%, with the balance being Al; the preparation process includes the following steps:

[0006] Step S1: According to the TiB2 / Al-Cu alloy composition ratio, place high-purity Al, Al-Cu master alloy, and Al-Mn master alloy in a melting crucible and melt them into a melt.

[0007] Step S2: The melt is heated to 760~850℃, and KBF4 and K2TiF6 mixed salts are added according to the TiB2 / Al-Cu alloy composition ratio. At the same time, a transverse eddy current magnetic field is applied, the current intensity of which does not exceed 20A, and mechanical stirring is performed. Then the melt is cast at 720~740℃ to obtain TiB2 / Al-Cu alloy ingots.

[0008] Secondly, the present invention provides a method for preparing a TiB2 / Al-Cu alloy and the prepared TiB2 / Al-Cu alloy, characterized in that, by mass fraction, the TiB2 / Al-Cu alloy composition comprises: Cu: 1~5%; Mn: 0.1~0.3%; Zr: 0.1~0.3%; TiB2: 1~8%, with the balance being Al; the preparation process includes the following steps:

[0009] Step S1: According to the TiB2 / Al-Cu alloy composition ratio, place high-purity Al, Al-Cu master alloy, Al-Mn master alloy, and Al-Zr master alloy in a melting crucible and melt them into a melt.

[0010] Step S2: The melt is heated to 760~850℃, and KBF4 and K2TiF6 mixed salts are added according to the TiB2 / Al-Cu alloy composition ratio. At the same time, a transverse eddy current magnetic field is applied, the current intensity of which does not exceed 20A, and mechanical stirring is performed. Then the melt is cast at 720~740℃ to obtain TiB2 / Al-Cu alloy ingots.

[0011] Thirdly, the present invention provides a method for preparing a TiB2 / Al-Cu alloy and the prepared TiB2 / Al-Cu alloy, characterized in that, by mass fraction, the TiB2 / Al-Cu alloy composition comprises: Cu: 1~5%; Mn: 0.1~0.3%; Y: 0.1~0.3%; TiB2: 1~8%, with the balance being Al; the preparation process includes the following steps:

[0012] Step S1: According to the TiB2 / Al-Cu alloy composition ratio, place high-purity Al, Al-Cu master alloy, and Al-Mn master alloy in a melting crucible and melt them into a melt.

[0013] Step S2: Heat the melt to 760~850℃, add KBF4 and K2TiF6 mixed salt according to the TiB2 / Al-Cu alloy composition ratio, and apply a transverse eddy current magnetic field with a current intensity not exceeding 20A, and perform mechanical stirring.

[0014] Step S3: Cool the melt to 700~710℃, add Al-Y master alloy according to the TiB2 / Al-Cu alloy composition ratio, continuously apply transverse eddy current magnetic field and mechanical stirring, and add an additional amount of Al-Y master alloy on the basis of the rated amount to increase the burn-off amount; then cast the melt at 720~740℃ to obtain TiB2 / Al-Cu alloy ingot.

[0015] Furthermore, the amount of Al-Y master alloy added is increased by an additional 3% to 6% on top of the rated amount.

[0016] Fourthly, the present invention provides a TiB2 / Al-Cu alloy prepared by the above preparation method, comprising nano-TiB2 ceramic particles and spherical nano-precipitates dispersed within the microstructure.

[0017] Furthermore, by mass fraction, the TiB2 / Al-Cu alloy composition comprises: Cu: 4%; Mn: 0.2%; Y: 0.1%; TiB2: 3%, with the balance being Al.

[0018] Furthermore, the TiB2 / Al-Cu alloy ingot is subjected to vacuum atomization powder preparation: under the action of protective gas, the alloy ingot is melted at a superheat of 450~650℃ to obtain alloy ingot melt, and then vacuum atomization powder preparation is carried out at an atomization pressure of 2~6 MPa to obtain TiB2 / Al-Cu alloy powder.

[0019] Fifthly, the present invention provides an additive manufacturing application of a TiB2 / Al-Cu alloy, characterized in that the TiB2 / Al-Cu alloy is a powder with a particle size of 20~50μm obtained by sieving TiB2 / Al-Cu alloy powder prepared by the preparation method described above, which is formed by laser powder bed melting equipment and 3D printed layer by layer by high-energy laser beam.

[0020] Compared with the prior art, the present invention has the following advantages or beneficial effects:

[0021] (1) The present invention innovatively uses a mixed salt in-situ self-generation method with magnetic field vibration assisted mechanical stirring to prepare TiB2 / Al-Cu alloy, which is beneficial to promote the uniform dispersion of micro and nano TiB2 particles formed in the material, exert the heterogeneous nucleation and reinforcement effects of particles, and can effectively improve the laser absorption rate of the alloy in the additive manufacturing process.

[0022] (2) In this invention, trace alloying elements such as Mn and Zr / Y are added during the smelting process, which can refine the grains during the alloying process, improve the mechanical properties and corrosion resistance of the material, and the aluminum alloy obtained by gas atomization powdering has a high sphericity, which can realize large-scale production.

[0023] (3) Since rare earth element Y is easy to float on the surface of the alloy liquid and become scum and is easily burned off, the method of adding Y element in this invention is to add Al-Y intermediate alloy at a lower temperature, and to make up for the burn-off, so as to ensure that the alloy composition ratio is without deviation.

[0024] (4) This invention refines the microstructure of Al-Cu alloy by adding trace alloying elements (Mn, Zr / Y) and TiB2 ceramic particles, and simultaneously makes the microstructure contain dispersed nano TiB2 ceramic particles and spherical nano precipitates, thereby improving defects such as shrinkage porosity, shrinkage cavities, hot cracks and segregation of the alloy, and improving the laser absorption rate, so that it can be used for additive manufacturing of complex components. The additively manufactured components obtained have uniform microstructure, small grain size, high high temperature strength and corrosion resistance, providing optional materials for the lightweighting of key equipment. Attached Figure Description

[0025] The invention, its features, and advantages will become more apparent from the following detailed description of non-limiting embodiments with reference to the accompanying drawings. The same reference numerals denote the same parts throughout the drawings. The drawings are not drawn to scale; the focus is on illustrating the main points of the invention.

[0026] Figure 1 The images show scanning electron microscope (SEM) images of Al-4Cu-0.2Mn-0.1Y alloy (a) and 3TiB2 / Al-4Cu-0.2Mn-0.1Y alloy (b) in Comparative Example 2 and Example 2 of this invention.

[0027] Figure 2 The images show magnified views of different regions within the 3TiB2 / Al-4Cu-0.2Mn-0.1Y alloy in Example 2 of this invention, along with their corresponding elemental EDS surface distribution diagrams.

[0028] Figure 3 SEM images of Al-4Cu alloy powder (a) and 3TiB2 / Al-4Cu-0.2Mn-0.1Y alloy powder (b) in Example 4 of this invention;

[0029] Figure 4 This is a SEM image of the deposited state of the 3D-printed Al-4Cu alloy sample in Example 5 of the present invention. Detailed Implementation

[0030] Exemplary embodiments of the present disclosure will now be described in more detail with reference to the accompanying drawings. It should be understood that all of these exemplary embodiments described are merely some embodiments and examples of the present invention, and not all of them. Rather, these exemplary embodiments are provided so that those skilled in the art can more thoroughly understand the present disclosure and to more completely convey the technical content of the present disclosure to those skilled in the art.

[0031] Comparative Example 1

[0032] 400 g of Al-50Cu and 4600 g of high-purity Al with a purity of 99.9% were placed in a melting crucible and melted. The temperature was raised to 780 °C and stirred evenly with a stone mill rod. The melt was then cast at 730 °C to obtain an Al-4Cu alloy ingot.

[0033] Comparative Example 2

[0034] 400 g of Al-50Cu, 100 g of Al-10Mn, and 4450 g of high-purity Al (99.9% purity) were sequentially placed in a melting crucible and melted. The temperature was raised to 780 °C while a transverse eddy current magnetic field was applied with a current intensity of 16 A for 10 min. The temperature was then lowered to 700 °C, and 50 g of Al-10Y master alloy was added. After stirring with a stone mill rod, a transverse eddy current magnetic field was applied for another 5 min with a current of 10 A. The melt was then cast at 730 °C to obtain an Al-4Cu-0.2Mn-0.1Y alloy ingot.

[0035] See Figure 1 (a) The Mn and Y modified Al-Cu alloy prepared by magnetic field vibration-assisted mechanical stirring has non-spherical grains with an average grain size of 62 μm and uniform distribution of Mn, Y, Al and Cu elements.

[0036] Example 1

[0037] This embodiment provides a method for preparing a TiB2 / Al-Cu alloy and the prepared TiB2 / Al-Cu alloy. By mass fraction, the TiB2 / Al-Cu alloy composition contains Cu: 1~5%; Mn: 0.1~0.3%; TiB2: 1~8%, with the balance being Al. The preparation process includes the following steps:

[0038] Step S1: According to the TiB2 / Al-Cu alloy composition ratio, place high-purity Al, Al-Cu master alloy, and Al-Mn master alloy in a melting crucible and melt them into a melt.

[0039] Step S2: The melt is heated to 760~850℃, and KBF4 and K2TiF6 mixed salts are added according to the TiB2 / Al-Cu alloy composition ratio. At the same time, a transverse eddy current magnetic field is applied, the current intensity of which does not exceed 20A, and mechanical stirring is performed. Then the melt is cast at 720~740℃ to obtain TiB2 / Al-Cu alloy ingots.

[0040] The applicable range of melt homogeneity and casting temperature varies depending on the alloy composition and is determined based on the alloy's phase diagram or melting point.

[0041] The following is a preferred example to help those skilled in the art understand the technical solution and effects of the present invention.

[0042] 400g of Al-50Cu, 100g of Al-10Mn, and 4493.5g of high-purity Al (99.9% purity) were sequentially placed in a melting crucible and melted. The temperature was raised to 780℃, and mechanical stirring was performed for 5 min. The temperature was then raised to 850℃, and 540g of KBF4 and 514.5g of K2TiF6 mixed salt were added. Simultaneously, a transverse eddy current magnetic field was applied with a current intensity of 16A for 10 min. The melt was then cast at 730℃ to obtain a 3TiB2 / Al-4Cu-0.2Mn alloy ingot. Electron microscopy analysis showed that the elemental distribution of the 3TiB2 / Al-4Cu-0.2Mn alloy was uniform, with an average grain size of 6.1μm.

[0043] Example 2

[0044] This embodiment provides a method for preparing a TiB2 / Al-Cu alloy and the prepared TiB2 / Al-Cu alloy. By mass fraction, the TiB2 / Al-Cu alloy composition includes Cu: 1~5%; Mn: 0.1~0.3%; Y: 0.1~0.3%; TiB2: 1~8%, with the balance being Al. The preparation process includes the following steps:

[0045] Step S1: According to the TiB2 / Al-Cu alloy composition ratio, place high-purity Al, Al-Cu master alloy, and Al-Mn master alloy in a melting crucible and melt them into a melt.

[0046] Step S2: Heat the melt to 760~850℃, add KBF4 and K2TiF6 mixed salt according to the TiB2 / Al-Cu alloy composition ratio, and apply a transverse eddy current magnetic field with a current intensity not exceeding 20A, and perform mechanical stirring.

[0047] Step S3: Cool the melt to 700~710℃, add Al-Y master alloy according to the TiB2 / Al-Cu alloy composition ratio, and continuously apply a transverse eddy current magnetic field and mechanical stirring. The amount of Al-Y master alloy added is additional to the rated amount to compensate for burn-off. The melt is then cast at 720~740℃ to obtain a TiB2 / Al-Cu alloy ingot. The amount of Al-Y master alloy added is 3%-6% additional to the rated amount; the specific value is determined based on the melt treatment temperature. Higher melt treatment temperatures require more additional burn-off compensation.

[0048] The following is a preferred example to help those skilled in the art understand the technical solution and effects of the present invention.

[0049] 400g of Al-50Cu, 100g of Al-10Mn, and 4493.5g of 99.9% pure Al were sequentially placed in a melting crucible and melted. The temperature was raised to 780℃, and mechanical stirring was performed for 5 min. The temperature was then raised to 850℃, and 540g of KBF4 and 514.5g of K2TiF6 mixed salt were added. Simultaneously, a transverse eddy current magnetic field was applied with a current intensity of 16A for 10 min. The temperature was then lowered to 700℃, and 50g of Al-10Y master alloy was added. After stirring with a stone mill rod, a transverse eddy current magnetic field was applied again for 5 min with a current of 10A. The melt was then cast at 730℃ to obtain a 3TiB2 / Al-4Cu-0.2Mn-0.1Y alloy ingot. Since rare earth element Y tends to float on the surface of the alloy liquid as scum and is easily burned off, in this embodiment, Y is added by adding Al-Y intermediate alloy at a lower temperature to compensate for burn-off and ensure that the alloy composition ratio is without deviation.

[0050] See Figure 1 (b) and Figure 2 The TiB2, Mn, and Y modified Al-Cu alloy has non-spherical grains with an average grain size of 3.8 μm, and contains Al6Mn nanoparticles and TiB2 nanoparticles.

[0051] Example 3

[0052] This embodiment provides a method for preparing a TiB2 / Al-Cu alloy and the prepared TiB2 / Al-Cu alloy. By mass fraction, the TiB2 / Al-Cu alloy composition includes Cu: 1~5%; Mn: 0.1~0.3%; Zr: 0.1~0.3%; TiB2: 1~8%, with the balance being Al. The preparation process includes the following steps:

[0053] Step S1: According to the TiB2 / Al-Cu alloy composition ratio, place high-purity Al, Al-Cu master alloy, Al-Mn master alloy, and Al-Zr master alloy in a melting crucible and melt them into a melt.

[0054] Step S2: The melt is heated to 760~850℃, and KBF4 and K2TiF6 mixed salts are added according to the TiB2 / Al-Cu alloy composition ratio. At the same time, a transverse eddy current magnetic field is applied, the current intensity of which does not exceed 20A, and mechanical stirring is performed. Then the melt is cast at 720~740℃ to obtain TiB2 / Al-Cu alloy ingots.

[0055] The applicable range of melt homogeneity and casting temperature varies depending on the alloy composition and is determined based on the alloy's phase diagram or melting point.

[0056] In this embodiment, Zr is added to the TiB2 / Al-Cu alloy instead of Y in Example 2, which simplifies the preparation process and makes it more suitable for large-scale production.

[0057] Example 4

[0058] In this embodiment, the alloy ingot described in the comparative example and the embodiment above is subjected to vacuum atomization powdering. More specifically, under the action of a protective gas, the alloy ingot is melted at a superheat of 450~650°C to obtain an alloy ingot melt, and then vacuum atomization powdering is performed at an atomization pressure of 2~6 MPa to obtain alloy powder.

[0059] The following is a preferred example to help those skilled in the art understand the technical solution and effects of the present invention.

[0060] The Al-4Cu-0.2Mn-0.1Y and 3TiB2 / Al-4Cu-0.2Mn-0.1Y alloy ingots prepared in the above embodiments were pulverized by vacuum atomization to obtain alloy powder. The atomization process was as follows: atomization pressure of 5.5 MPa, mass flow rate of 4.28 Kg / min, nozzle diameter of 3.5 mm, superheat of 500 ℃, and Ar as the process protective gas. The powder obtained by gas atomization was sieved through a 400-mesh sieve to obtain Al-4Cu-0.2Mn-0.1Y and 3TiB2 / Al-4Cu-0.2Mn-0.1Y powders with a particle size between 20 and 50 μm.

[0061] See Figure 3 The prepared 3TiB2 / Al-4Cu-0.2Mn-0.1Y powder has high sphericity and is suitable as a 3D printing material.

[0062] Example 5

[0063] This embodiment employs a BLT-S500 laser powder bed equipment, utilizing the Al-Cu alloy and TiB2 / Al-Cu alloy powders from the comparative example and embodiment described above for high-energy laser beam layer-by-layer 3D printing. More specifically, a powder spreading tool evenly spreads the powder onto the forming substrate, and the laser beam melts the powder layer by layer according to the computer-designed CAD model until a three-dimensional block is formed. The parameters for laser additive manufacturing include: substrate 2024Al alloy; laser spot diameter 70-130 μm; scanning power 200-350 W; scanning speed 100-500 mm / s; scanning spacing 70-130 μm; powder thickness 30-50 μm; protective gas Ar with a flow rate of 10-30 kg / min, ensuring the oxygen content of the manufacturing system is below 20 ppm; scanning strategy of strip, checkerboard, or honeycomb pattern; and substrate preheating temperature of 250-400℃. A preferred example is provided below to help those skilled in the art understand the technical solution and effects of this invention.

[0064] The forming parameters are as follows: laser spot diameter: 75 μm, scanning power: 250 W, scanning speed maintained at 300 mm / s, scanning spacing 110 μm, powder thickness 30 μm, and scanning strategy is strip-shaped; substrate: 2024Al alloy; substrate preheating temperature: 350℃; protective gas is Ar with oxygen content less than 20 ppm.

[0065] The laser absorption rates of Al-4Cu and TiB2 / Al-Cu are 45% and 60%, respectively. This shows that uniformly dispersed micro- and nano-TiB2 particles in the alloy can effectively improve the laser absorption rate of the alloy during additive manufacturing.

[0066] Cross-sectional SEM testing revealed significant corrosion cracks in the 3D-printed Al-4Cu alloy (see [link]). Figure 4 The TiB2 / Al-Cu alloy sample showed no obvious structural defects. Table 1 shows the mechanical properties of the 3D-printed Al-4Cu, 3TiB2 / Al-4Cu, and 3TiB2 / Al-4Cu-0.2Mn-0.1Y alloy samples under the same conditions. The table shows that the structure obtained by additive manufacturing of Al-4Cu alloy with uniformly dispersed micro / nano TiB2 particles exhibits better mechanical properties than the original Al-4Cu alloy. The mechanical properties of the TiB2 / Al-Cu alloy additive manufacturing structure with added microalloying elements such as Mn are even more superior. After immersing the 3D-printed Al-4Cu alloy and TiB2 / Al-Cu alloy samples in 3.5% NaCl solution for 30 days, surface defects were tested. The corrosion rate of the Al-4Cu alloy was 0.27 mm / a, and the corrosion rate of the TiB2 / Al-Cu alloy was 0.1 mm / a; no obvious corrosion traces were found.

[0067] Table 1. Mechanical property data of 3D-printed alloy samples obtained under the same conditions.

[0068]

[0069] In summary, this application provides a TiB2 / Al-Cu alloy, its preparation method, and its additive manufacturing application. The TiB2 / Al-Cu alloy is prepared using a mixed salt in-situ self-generating method with magnetic field vibration-assisted mechanical stirring. This method promotes the uniform dispersion of micro / nano TiB2 particles within the material, leveraging their heterogeneous nucleation and reinforcing effects, and effectively improving the laser absorption rate of the alloy during additive manufacturing. By mass fraction, the basic components of the TiB2 / Al-Cu alloy are: Cu: 1-5%; Mn: 0.1-0.3%; TiB2: 1-8%, with the balance being Al. Preferably, trace alloying elements such as Mn and Zr / Y are added during the smelting process, which can refine the grains and improve the material's mechanical properties and corrosion resistance.

[0070] The preferred embodiments of the present invention have been described above. It should be understood that the present invention is not limited to the specific embodiments described above, and the devices and structures not described in detail should be understood as being implemented in a conventional manner in the art. Any person skilled in the art can make many possible variations and modifications to the technical solutions of the present invention using the methods and techniques disclosed above, or modify them into equivalent embodiments with equivalent changes, without departing from the scope of the present invention. This does not affect the essential content of the present invention. Therefore, any simple modifications, equivalent changes, and modifications made to the above embodiments based on the technical essence of the present invention without departing from the content of the present invention's technical solutions still fall within the protection scope of the present invention.

Claims

1. A method for producing a TiB2 / Al-Cu alloy, characterized by, The Cu in the TiB2 / Al-Cu alloy component is 1-5% by mass fraction; the Mn is 0.1-0.3% by mass fraction; Y: 0.1-0.3%; TiB2: 1-8%, the balance being Al. Step S1, according to the TiB2 / Al-Cu alloy component ratio, high-purity Al, Al-Cu intermediate alloy, and Al-Mn intermediate alloy are placed in a smelting crucible to be melted into a melt; Step S2, the melt is heated to 760-850°C, according to the TiB2 / Al-Cu alloy component ratio, KBF4 and K2TiF6 mixed salt is added, a transverse vortex magnetic field with a current intensity not exceeding 20A is applied, and mechanical stirring is carried out; Step S3, the melt is cooled to 700-710°C, according to the TiB2 / Al-Cu alloy component ratio, Al-Y intermediate alloy is added, the transverse vortex magnetic field and mechanical stirring are continuously applied, the addition amount of Al-Y intermediate alloy is additionally increased by 3-6% based on the rated addition amount; then the melt is cast at 720-740°C to obtain a TiB2 / Al-Cu alloy ingot.

2. The method of claim 1, wherein the TiB2 / Al-Cu alloy is prepared by the steps of: The addition amount of the Al-Y intermediate alloy is additionally increased by 3-6% based on the rated addition amount. ​ 3. A TiB2 / Al-Cu alloy, characterized by, Prepared by the preparation method of claim 1, including nanometer TiB2 ceramic particles and spherical nanometer precipitated phases dispersedly distributed in the structure; The Cu in the alloy component is 1-5% by mass fraction; the Mn is 0.1-0.3% by mass fraction; Y: 0.1-0.3%; TiB2: 1-8%, the balance being Al.

4. The TiB2 / Al-Cu alloy according to claim 3, characterized in that, The Cu in the alloy component is 4% by mass fraction; the Mn is 0.2% by mass fraction; Y: 0.1% by mass fraction; TiB2: 3% by mass fraction, the balance being Al.

5. A method for preparing a TiB2 / Al-Cu alloy according to claim 1 or 2, characterized in that, The TiB2 / Al-Cu alloy ingot is vacuum gas atomized to powder: under the action of a protective gas, the alloy ingot is melted to obtain an alloy ingot melt at a superheat of 450-650°C, and then vacuum gas atomization is carried out at an atomization pressure of 2-6 MPa to obtain a TiB2 / Al-Cu alloy powder.

6. Use of a TiB2 / Al-Cu alloy for additive manufacturing, characterized in that, The TiB2 / Al-Cu alloy is a powder with a particle size of 20-50 μm obtained by sieving the TiB2 / Al-Cu alloy powder prepared by the preparation method of claim 5, and is formed by using a laser powder bed melting device and is 3D printed layer by layer by using a high-energy laser beam.

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