An additively manufactured Al-Cu-X eutectic phase strengthened aluminum alloy material

Abstract

The present invention belongs to the technical field of aluminum alloy preparation, and more specifically, relates to an additively manufactured Al‑Cu‑X eutectic phase strengthened aluminum alloy material. The Al‑Cu‑X eutectic phase strengthened aluminum alloy material provided by the present invention, in addition to Al, comprises components including: Cu, Mg, V and eutectic elements, as well as unavoidable impurity elements, and the eutectic elements include at least one of Fe, Co, Mn and Ni, and is obtained by pre-treating the raw materials to obtain original alloy powder; and using the original alloy powder for laser melting printing molding to obtain the Al‑Cu‑X eutectic phase strengthened aluminum alloy material. The present invention can controllably prepare multiphase strengthened aluminum alloy materials through additive manufacturing, utilizes a method combining eutectic reaction with fine grain strengthening, and improves the formability of the aluminum alloy and enhances its overall performance by optimizing its component ratio, thereby achieving an improvement in the composite properties of the aluminum alloy such as high strength, high toughness, and high temperature resistance.

Description

Technical Field

[0001] The present invention belongs to the technical field of aluminum alloy preparation, and more specifically relates to an additively manufactured Al-Cu-X eutectic phase strengthened aluminum alloy material. Background Art

[0002] Additive manufacturing technology overcomes the challenges of traditional machining by using computer-aided design and point-by-point, layer-by-layer scanning to form materials. It is a potentially promising alternative for manufacturing high-density aluminum-based composites with minimal defects. Aluminum alloys play a key industrial role as high-strength, lightweight structural materials. Over the past five years, the number of publications on laser powder bed fusion of aluminum alloys has increased from approximately 50 to approximately 250 per year, second only to steel and titanium alloys. The most widely used and researched aluminum alloys for laser powder bed fusion are still based on Al-Si alloys, but the mechanical properties of Al-Si alloys are less than ideal and cannot meet the growing performance demands of industrial production.

[0003] To further improve the mechanical properties of aluminum alloys for additive manufacturing (AM) and expand their applications, recent research has focused on heat-treatable Al-based alloys (particularly 2-series Al-Cu and 7-series Al-Zn alloys). However, conventional high-strength 2-series Al-Cu and 7-series Al-Zn alloys face defects such as poor printability and cracks and voids when used in AM. This is due to the extended solidification temperature range (Table 1) of these alloys in AM. The solid phase that precipitates first resides in the liquid phase and experiences relatively little thermal stress, while the solid phase that solidifies later experiences greater thermal contraction stress. This uneven distribution of thermal stress results in a high susceptibility to thermal cracking during the forming process, a barrier that limits the application of conventional high-strength aluminum alloys in AM. The potential of AM aluminum alloys has yet to be fully exploited, and therefore, an alloy design strategy is urgently needed to enhance the printability-performance synergy of these alloys.

[0004] The shorter the solidification interval, the more uniform the solid phase precipitation, the more evenly distributed the overall thermal stress, and the lower the thermal crack sensitivity. Shortening the solidification temperature interval at the end of solidification is an effective strategy for addressing thermal crack sensitivity. Therefore, how to effectively address the thermal crack sensitivity issue and reduce cracks between grains has become a pressing challenge for those skilled in the art. Summary of the Invention

[0005] The purpose of the present invention is to provide an Al-Cu-X eutectic phase strengthened aluminum alloy material for additive manufacturing, wherein eutectic elements having a solidification interval smaller than that of Al-Cu (as shown in Table 1) are added to react with Al-Cu to generate an Al-Cu-X eutectic phase with a shortened eutectic solidification interval (as shown in Table 1). Figure 1By adding an appropriate amount of eutectic elements to pure aluminum or aluminum alloys, or to aluminum alloys already containing copper, magnesium, and vanadium, a eutectic phase is formed to form an Al-Cu-X (X elements include but are not limited to Fe, Co, Mn, Ni, etc.) eutectic phase. This allows the development of an aluminum alloy material based on eutectic phase strengthening to address the above-mentioned problems in the prior art.

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

[0007] One of the technical solutions of the present invention is to provide an Al-Cu-X eutectic phase strengthened aluminum alloy material, which, in addition to Al, comprises, by mass percentage, 1-10 wt.% Cu, 1-10 wt.% Mg, 0.3-10 wt.% V, 0.3-5 wt.% eutectic elements, and unavoidable impurity elements;

[0008] The eutectic element includes at least one of Fe, Co, Mn and Ni.

[0009] Furthermore, the Al-Cu-X eutectic phase strengthened aluminum alloy material comprises, by mass percentage, 1-10 wt.% Cu, 1-10 wt.% Mg, 0.3-10 wt.% V and 0.3-5 wt.% eutectic elements, with the remainder being Al and unavoidable impurity elements.

[0010] The second technical solution of the present invention is to provide a method for additively manufacturing an Al-Cu-X eutectic phase strengthened aluminum alloy material, comprising the following steps:

[0011] Prepare raw materials according to the composition of the Al-Cu-X eutectic phase strengthened aluminum alloy material, and obtain original alloy powder after pretreatment;

[0012] The original alloy powder is used to perform laser melting printing to obtain the Al-Cu-X eutectic phase strengthened aluminum alloy material.

[0013] Furthermore, the raw materials include multiple types of aluminum alloy powder, Al powder, Cu powder, Mg powder, V powder and eutectic element powder.

[0014] Optionally, the aluminum alloy powder includes at least one of 1000 series aluminum alloy, 2000 series aluminum alloy, 3000 series aluminum alloy, 4000 series aluminum alloy, 5000 series aluminum alloy, 6000 series aluminum alloy, 7000 series aluminum alloy, 8000 series aluminum alloy and 9000 series aluminum alloy.

[0015] Furthermore, the pretreatment includes three-dimensional mixing or pre-alloying.

[0016] The three-dimensional mixing is to prepare the raw materials into the original alloy powder by a mixer; and the pre-alloying is to prepare the raw materials into the original alloy powder by smelting or atomization.

[0017] Furthermore, the printing parameters are: laser power 160-340W, laser scanning rate 400-1600mm / s, scanning line spacing 80-110μm, powder layer thickness 20-40μm, powder feed ratio 1.8-3.4, and laser interlayer rotation angle 0°-90°.

[0018] The third technical solution of the present invention is to provide an application of an added eutectic element in improving the tensile strength and elongation of aluminum alloy.

[0019] Furthermore, the eutectic element includes at least one of Fe, Co, Mn and Ni.

[0020] Furthermore, the eutectic element accounts for 0.3-5 wt.% in the aluminum alloy.

[0021] Furthermore, the aluminum alloy contains copper, magnesium and vanadium elements.

[0022] The present invention discloses the following technical effects:

[0023] The present invention uses additive manufacturing to controllably prepare multiphase strengthened aluminum alloy materials, utilizes a method combining eutectic reaction with fine grain strengthening, and optimizes the composition ratio to improve the formability of the aluminum alloy and enhance its overall performance, thereby achieving improvements in the aluminum alloy's composite properties such as high strength, high toughness, and high temperature resistance.

[0024] Compared with the existing reports on additively manufactured aluminum alloy materials with poor printing formability, low mechanical properties, and inability to meet industrialization needs, the present invention provides a method for additively manufacturing Al-Cu-X eutectic phase-strengthened aluminum alloy materials (a method for additively manufacturing aluminum alloy materials based on in-situ autogenous eutectic phase strengthening), which significantly improves its formability and mechanical properties, effectively solving the problem of poor formability and low mechanical properties of additively manufactured aluminum-based composite materials. At the same time, it has the advantages of simple preparation process, convenient operation, short time consumption, and low cost. BRIEF DESCRIPTION OF THE DRAWINGS

[0025] The accompanying drawings, which constitute part of the present invention, are provided to provide a further understanding of the present invention. The exemplary embodiments of the present invention and their descriptions are provided to explain the present invention and do not constitute an undue limitation of the present invention. In the accompanying drawings:

[0026] Figure 1Comparison of the tensile fracture surfaces of the aluminum alloy material prepared in Example 1 and the original 2024 aluminum alloy, where (a-1), (a-2) and (a-3) are cleavage fractures of the original 2024 aluminum alloy, and (b-1), (b-2) and (b-3) are dimple fractures of Example 1.

[0027] Figure 2 Simulation and comparison of solidification curves of V-modified 2024 aluminum alloy before and after adding eutectic Ni.

[0028] Figure 3 The mechanical properties of V-modified 2024 aluminum alloy at different temperatures after adding eutectic Ni are compared with those of other alloys.

[0029] Figure 4 Room temperature stress-strain curves of 2024 aluminum alloy and Examples 1-2.

[0030] Figure 5 Room temperature stress-strain curves of 2024 aluminum alloy and Examples 3-4.

[0031] Figure 6 Room temperature stress-strain curves of 2024 aluminum alloy and Examples 5-7.

[0032] Figure 7 Room temperature stress-strain curves of 2024 aluminum alloy and Examples 8-11.

[0033] Figure 8 TEM image of the Al-Cu-Ni eutectic phase strengthened aluminum alloy material prepared in Example 10.

[0034] Figure 9 The EDS surface scanning element distribution map of the Al-Cu-Ni eutectic phase strengthened aluminum alloy material prepared in Example 10 under TEM. DETAILED DESCRIPTION

[0035] Various exemplary embodiments of the present invention will now be described in detail. This detailed description should not be considered as limiting the present invention, but rather as a more detailed description of certain aspects, features, and embodiments of the present invention.

[0036] It should be understood that the terms described herein are intended only to describe particular embodiments and are not intended to limit the present invention. In addition, for numerical ranges herein, it should be understood that each intermediate value between the upper and lower limits of the range is also specifically disclosed. The intermediate value within any stated value or stated range, and each smaller range between any other stated value or intermediate value within the stated range, is also encompassed within the present invention. The upper and lower limits of these smaller ranges may be independently included or excluded within the scope.

[0037] Unless otherwise indicated, all technical and scientific terms used herein have the same meaning as commonly understood by those skilled in the art. Although only preferred methods and materials are described herein, any methods and materials similar or equivalent to those described herein may also be used in the practice or testing of the present invention. All documents mentioned in this specification are incorporated by reference to disclose and describe the methods and / or materials associated with the documents. In the event of any conflict with any incorporated document, the contents of this specification shall prevail.

[0038] It will be apparent to those skilled in the art that various modifications and variations may be made to the specific embodiments described herein without departing from the scope or spirit of the invention. Other embodiments will be apparent to those skilled in the art from the description of the invention. The description and examples are intended to be illustrative only.

[0039] The words “include,” “including,” “have,” “contain,” etc. used in this document are open-ended terms, meaning including but not limited to.

[0040] It should be pointed out that the matters not described in detail in the present invention are conventional operating means in this field and are not the focus of the present invention.

[0041] In the specific implementation scheme of the present invention, "room temperature" and "normal temperature" both refer to 20-30°C.

[0042] The following raw materials of the present invention are all commercially available products, among which aluminum powder and 2024 aluminum alloy powder are both sourced from Nantong Baoyang; Fe, Co, Mn, and Ni are sourced from Beijing Zhongke Yannuo.

[0043] Example 1

[0044] The preparation steps of Al-Cu-Fe eutectic phase strengthened aluminum alloy material include:

[0045] S1. Weigh 12.5 g of vanadium powder, 5 g of iron powder, and 482.5 g of 2024 aluminum alloy powder, place them in a 5 L stainless steel tank, and use a three-dimensional mixer to mix and disperse them for 16 h, with a ball-to-powder ratio of 1:1. Take out the mixed powder after three-dimensional mixing and dispersion, sieve the particle size with a 250 mesh sieve, and place the powder with less than 250 mesh in a vacuum oven at 100 ° C for 2 h to obtain the original alloy powder;

[0046] S2. Using the original alloy powder obtained in step S1 as raw material, additive manufacturing was performed using a laser powder bed fusion 3D printer with a laser power of 220 W, a laser scanning rate of 1200 mm / s, a scanning line spacing of 100 μm, a powder layer thickness of 30 μm, a laser interlayer rotation angle of 67°, and a powder feed ratio of 2.6:1 to obtain an Al-Cu-Fe eutectic phase strengthened aluminum alloy material.

[0047] Example 2

[0048] Compared with Example 1, the difference is that the laser power in step S2 is 250W. The specific steps are as follows:

[0049] S1. Weigh 12.5 g of vanadium powder, 5 g of iron powder, and 482.5 g of 2024 aluminum alloy powder, place them in a 5 L stainless steel tank, and use a three-dimensional mixer to mix and disperse them for 16 h, with a ball-to-powder ratio of 1:1. Take out the mixed powder after three-dimensional mixing and dispersion, sieve the particle size with a 250 mesh sieve, and place the powder with less than 250 mesh in a vacuum oven at 100 ° C for 2 h to obtain the original alloy powder;

[0050] S2. Using the original alloy powder obtained in step S1 as raw material, additive manufacturing was performed using a laser powder bed fusion 3D printer with a laser power of 250 W, a laser scanning rate of 1200 mm / s, a scanning line spacing of 100 μm, a powder layer thickness of 30 μm, a laser interlayer rotation angle of 67°, and a powder feed ratio of 2.6:1 to obtain an Al-Cu-Fe eutectic phase strengthened aluminum alloy material.

[0051] Example 3

[0052] The preparation steps of Al-Cu-Co eutectic phase strengthened aluminum alloy material include:

[0053] S1. Weigh 12.5 g of vanadium powder, 2.5 g of cobalt powder, and 485 g of 2024 aluminum alloy powder, place them in a 5 L stainless steel tank, and use a three-dimensional mixer to mix and disperse them for 16 h, with a ball-to-powder ratio of 1:1. Take out the mixed powder after three-dimensional mixing and dispersion, sieve the particle size with a 250 mesh sieve, and place the powder with less than 250 mesh in a vacuum oven at 100 ° C for 2 h to obtain the original alloy powder;

[0054] S2. Using the original alloy powder obtained in step S1 as raw material, additive manufacturing was performed using a laser powder bed fusion 3D printer with a laser power of 250 W, a laser scanning rate of 600 mm / s, a scanning line spacing of 100 μm, a powder layer thickness of 30 μm, a laser interlayer rotation angle of 67°, and a powder feed ratio of 2.6:1 to obtain an Al-Cu-Co eutectic phase strengthened aluminum alloy material.

[0055] Example 4

[0056] Compared with Example 3, the difference is that the laser scanning rate in step S2 is 800 mm / s. The specific steps are as follows:

[0057] S1. Weigh 12.5 g of vanadium powder, 2.5 g of cobalt powder, and 485 g of 2024 aluminum alloy powder, place them in a 5 L stainless steel tank, and use a three-dimensional mixer to mix and disperse them for 16 h, with a ball-to-powder ratio of 1:1. Take out the mixed powder after three-dimensional mixing and dispersion, sieve the particle size with a 250 mesh sieve, and place the powder with less than 250 mesh in a vacuum oven at 100 ° C for 2 h to obtain the original alloy powder;

[0058] S2. Using the original alloy powder obtained in step S1 as raw material, additive manufacturing was performed using a laser powder bed fusion 3D printer with a laser power of 250 W, a laser scanning rate of 800 mm / s, a scanning line spacing of 100 μm, a powder layer thickness of 30 μm, a laser interlayer rotation angle of 67°, and a powder feed ratio of 2.6:1 to obtain an Al-Cu-Co eutectic phase strengthened aluminum alloy material.

[0059] Example 5

[0060] The preparation steps of Al-Cu-Mn eutectic phase strengthened aluminum alloy material include:

[0061] S1. Weigh 12.5 g of vanadium powder, 10.0 g of manganese powder, and 477.5 g of 2024 aluminum alloy powder, place them in a 5 L stainless steel tank, and use a three-dimensional mixer to mix and disperse them for 16 h, with a ball-to-powder ratio of 1:1. Take out the mixed powder after three-dimensional mixing and dispersion, sieve the particle size with a 250 mesh sieve, and place the powder with less than 250 mesh in a vacuum oven at 100° C. and dry it for 2 h to obtain the original alloy powder;

[0062] S2. Using the original alloy powder obtained in step S1 as raw material, additive manufacturing was performed using a laser powder bed fusion 3D printer with a laser power of 220 W, a laser scanning rate of 600 mm / s, a scanning line spacing of 80 μm, a powder layer thickness of 40 μm, a laser interlayer rotation angle of 67°, and a powder feed ratio of 2.6:1 to obtain an Al-Cu-Mn eutectic phase strengthened aluminum alloy material.

[0063] Example 6

[0064] Compared with Example 5, the difference is that the laser scanning rate is 1000 mm / s, and the specific steps are as follows:

[0065] S1. Weigh 12.5 g of vanadium powder, 10.0 g of manganese powder, and 477.5 g of 2024 aluminum alloy powder, place them in a 5 L stainless steel tank, and use a three-dimensional mixer to mix and disperse them for 16 h, with a ball-to-powder ratio of 1:1. Take out the mixed powder after three-dimensional mixing and dispersion, sieve the particle size with a 250 mesh sieve, and place the powder with less than 250 mesh in a vacuum oven at 100° C. and dry it for 2 h to obtain the original alloy powder;

[0066] S2. Using the original alloy powder obtained in step S1 as raw material, additive manufacturing is performed using a laser powder bed fusion 3D printer with a laser power of 220 W, a laser scanning rate of 1000 mm / s, a scanning line spacing of 80 μm, a powder layer thickness of 40 μm, a laser interlayer rotation angle of 67°, and a powder feed ratio of 2.6:1 to obtain an Al-Cu-Mn eutectic phase strengthened aluminum alloy material.

[0067] Example 7

[0068] Compared with Example 5, the difference is that the amount of manganese powder used is 7.5 g, and the amount of 2024 aluminum alloy powder used is 480.0 g. The specific steps are as follows:

[0069] S1. Weigh 12.5 g of vanadium powder, 7.5 g of manganese powder, and 480.0 g of 2024 aluminum alloy powder, place them in a 5 L stainless steel tank, and use a three-dimensional mixer to mix and disperse them for 16 h, with a ball-to-powder ratio of 1:1. Take out the mixed powder after three-dimensional mixing and dispersion, sieve the particle size with a 250 mesh sieve, and place the powder with less than 250 mesh in a vacuum oven at 100° C. and dry it for 2 h to obtain the original alloy powder;

[0070] S2. Using the original alloy powder obtained in step S1 as raw material, additive manufacturing was performed using a laser powder bed fusion 3D printer with a laser power of 220 W, a laser scanning rate of 600 mm / s, a scanning line spacing of 80 μm, a powder layer thickness of 40 μm, a laser interlayer rotation angle of 67°, and a powder feed ratio of 2.6:1 to obtain an Al-Cu-Mn eutectic phase strengthened aluminum alloy material.

[0071] Example 8

[0072] The preparation steps of Al-Cu-Ni eutectic phase strengthened aluminum alloy material include:

[0073] S1. Weigh 12.5 g of vanadium powder, 2.5 g of nickel powder, and 485.0 g of 2024 aluminum alloy powder, place them in a 5 L stainless steel tank, and use a three-dimensional mixer to mix and disperse them for 16 h, with a ball-to-powder ratio of 1:1. Take out the mixed powder after three-dimensional mixing and dispersion, sieve the particle size with a 250 mesh sieve, and dry the powder with less than 250 mesh in a vacuum oven at 100 ° C for 2 h to obtain the original alloy powder;

[0074] S2. Using the original alloy powder obtained in step S1 as raw material, additive manufacturing was performed using a laser powder bed fusion 3D printer with a laser power of 250 W, a laser scanning rate of 600 mm / s, a scanning line spacing of 100 μm, a powder layer thickness of 40 μm, a laser interlayer rotation angle of 67°, and a powder feed ratio of 2.6:1 to obtain an Al-Cu-Ni eutectic phase strengthened aluminum alloy material.

[0075] Example 9

[0076] Compared with Example 8, the difference is that the amount of vanadium powder used is 15.0 g, the amount of 2024 aluminum alloy powder used is 482.5 g, and the specific steps are as follows:

[0077] S1. Weigh 15.0 g of vanadium powder, 2.5 g of nickel powder, and 482.5 g of 2024 aluminum alloy powder, place them in a 5 L stainless steel tank, and use a three-dimensional mixer to mix and disperse them for 16 h, with a ball-to-powder ratio of 1:1. Take out the mixed powder after three-dimensional mixing and dispersion, sieve the particle size with a 250 mesh sieve, and place the powder with less than 250 mesh in a vacuum oven at 100 ° C for 2 h to obtain the original alloy powder;

[0078] S2. Using the original alloy powder obtained in step S1 as raw material, additive manufacturing was performed using a laser powder bed fusion 3D printer with a laser power of 250 W, a laser scanning rate of 600 mm / s, a scanning line spacing of 100 μm, a powder layer thickness of 40 μm, a laser interlayer rotation angle of 67°, and a powder feed ratio of 2.6:1 to obtain an Al-Cu-Ni eutectic phase strengthened aluminum alloy material.

[0079] Example 10

[0080] Compared with Example 9, the difference is that the laser power is 220W, and the specific steps are as follows:

[0081] S1. Weigh 15.0 g of vanadium powder, 2.5 g of nickel powder, and 482.5 g of 2024 aluminum alloy powder, place them in a 5 L stainless steel tank, and use a three-dimensional mixer to mix and disperse them for 16 h, with a ball-to-powder ratio of 1:1. Take out the mixed powder after three-dimensional mixing and dispersion, sieve the particle size with a 250 mesh sieve, and place the powder with less than 250 mesh in a vacuum oven at 100 ° C for 2 h to obtain the original alloy powder;

[0082] S2. Using the original alloy powder obtained in step S1 as raw material, additive manufacturing was performed using a laser powder bed fusion 3D printer with a laser power of 220 W, a laser scanning rate of 600 mm / s, a scanning line spacing of 100 μm, a powder layer thickness of 40 μm, a laser interlayer rotation angle of 67°, and a powder feed ratio of 2.6:1 to obtain an Al-Cu-Ni eutectic phase strengthened aluminum alloy material.

[0083] Example 11

[0084] Compared with Example 8, the difference is that the amount of vanadium powder used is 17.5 g, the amount of 2024 aluminum alloy powder used is 480.0 g, and the specific steps are as follows:

[0085] S1. Weigh 17.5 g of vanadium powder, 2.5 g of nickel powder, and 480.0 g of 2024 aluminum alloy powder, place them in a 5 L stainless steel tank, and use a three-dimensional mixer to mix and disperse them for 16 h, with a ball-to-powder ratio of 1:1. Take out the mixed powder after three-dimensional mixing and dispersion, sieve the particle size with a 250 mesh sieve, and place the powder with less than 250 mesh in a vacuum oven at 100 ° C for 2 h to obtain the original alloy powder;

[0086] S2. Using the original alloy powder obtained in step S1 as raw material, additive manufacturing was performed using a laser powder bed fusion 3D printer with a laser power of 250 W, a laser scanning rate of 600 mm / s, a scanning line spacing of 100 μm, a powder layer thickness of 40 μm, a laser interlayer rotation angle of 67°, and a powder feed ratio of 2.6:1 to obtain an Al-Cu-Ni eutectic phase strengthened aluminum alloy material.

[0087] Comparative Example 1

[0088] Compared with Example 10, the difference is that the nickel powder is replaced with 2024 aluminum alloy powder of equal mass. The specific steps are as follows:

[0089] S1. Weigh 12.5 g of vanadium powder and 487.5 g of 2024 aluminum alloy powder, place them in a 5 L stainless steel tank, and use a three-dimensional mixer to mix and disperse them for 16 h, with a ball-to-powder ratio of 1:1. Take out the mixed powder after three-dimensional mixing and dispersion, sieve the particle size with a 250 mesh sieve, and place the powder with less than 250 mesh in a vacuum oven at 100° C. for 2 h to obtain the original alloy powder;

[0090] S2. Using the original alloy powder obtained in step S1 as raw material, additive manufacturing was performed using a laser powder bed fusion 3D printer with a laser power of 250 W, a laser scanning rate of 600 mm / s, a scanning line spacing of 100 μm, a powder layer thickness of 40 μm, a laser interlayer rotation angle of 67°, and a powder feed ratio of 2.6:1 to obtain an aluminum alloy material.

[0091] Test example

[0092] Figure 1 Comparison of the tensile fracture surfaces of the aluminum alloy material prepared in Example 1 and the original 2024 aluminum alloy. Among them, (a-1), (a-2) and (a-3) are cleavage fractures of the original 2024 aluminum alloy, and (b-1), (b-2) and (b-3) are dimple fractures of Example 1.

[0093] Figure 2 This is a simulation comparison of the solidification curves of V-modified 2024 aluminum alloy before and after adding eutectic Ni (Example 10 and Comparative Example 1).

[0094] Figure 3The mechanical properties of V-modified 2024 aluminum alloy at different temperatures after adding eutectic Ni are compared with the properties of other alloys (Example 10 and Comparative Example 1).

[0095] Depend on Figure 1-Figure 3 It can be seen that the original 2024 aluminum alloy showed obvious cleavage fracture and poor toughness. After Ni+V synergistic modification, there were a large number of dimples on the fracture surface, resulting in ductile fracture. From the solidification curve, it was found that the addition of Ni changed the solidification path of the V-modified 2024 alloy at the solidification end, from a single Al+Al2Cu to Al+Al-Cu-Ni, shortening the Al solidification temperature range. At the same time, the terminal Al-Cu-Ni phase can be filled in the eutectic grain boundary (such as Figure 9 As shown), it reduces defects such as cracks between grain boundaries; Figure 3 Performance comparison found that Ni+V synergistically reinforced 2024 alloy, and the room temperature and high temperature performance were improved. The tensile strength at 200℃, 250℃ and 300℃ reached ~315MPa, ~230MPa and ~133MPa respectively.

[0096] Table 1 Liquidus temperature, solidus temperature and solidification range of different aluminum alloys

[0097] alloy Liquidus temperature (℃) Solidus temperature (℃) Solidification range (℃) Al-Cu ～640-650 ～500-520 ～120-150 Al-Zn ～635 ～475 ～160 Al-Fe 655-660 630-640 20-30 Al-Mn 655-660 640-645 15-20 Al-Co 640-660 600-620 40-60 Al-Ni 640-650 550-570 70-100

[0098] The properties of the aluminum alloys prepared in Examples 1-11 were tested using a universal tensile testing machine. The results are shown in Table 2.

[0099] Table 2

[0100]

[0101] Figure 4 Room temperature stress-strain curves of 2024 aluminum alloy and Examples 1-2.

[0102] Figure 5 Room temperature stress-strain curves of 2024 aluminum alloy and Examples 3-4.

[0103] Figure 6 Room temperature stress-strain curves of 2024 aluminum alloy and Examples 5-7.

[0104] Figure 7 Room temperature stress-strain curves of 2024 aluminum alloy and Examples 8-11.

[0105] According to the data in Table 1 and Figure 4-Figure 7As can be seen, the original 2024 aluminum alloy has mechanical properties of only 33.69 MPa and an elongation of 0.51%. After the eutectic phase is introduced to strengthen the alloy, these properties are significantly improved. However, when the eutectic phase content is too high, an inverted relationship between strength and ductility occurs. Only by introducing an appropriate amount of eutectic phase can defects in additively manufactured aluminum alloys be effectively eliminated, mechanical properties improved, and elongation maintained high without excessive brittle phase formation.

[0106] Figure 8 TEM image of the Al-Cu-Ni eutectic phase strengthened aluminum alloy material prepared in Example 10.

[0107] Figure 9 The EDS surface scanning element distribution map of the Al-Cu-Ni eutectic phase strengthened aluminum alloy material prepared in Example 10 under TEM.

[0108] The various embodiments in this specification are described in a progressive manner, and each embodiment focuses on the differences from other embodiments. The same or similar parts between the various embodiments can be referenced to each other.

[0109] The above description of the disclosed embodiments is intended to enable one skilled in the art to implement or use the present invention. Various modifications to these embodiments will be readily apparent to one skilled in the art, and the general principles defined herein may be implemented in other embodiments without departing from the spirit or scope of the present invention. Therefore, the present invention is not limited to the embodiments shown herein but is intended to conform to the widest scope consistent with the principles and novel features disclosed herein.

Claims

1. An Al-Cu-X eutectic phase strengthened aluminum alloy material, characterized in that: In terms of mass percentage, in addition to Al, the components include: Cu 1-10 wt.%, Mg 1-10 wt.%, V 0.3-10 wt.% and eutectic elements 0.3-5 wt.%, and inevitable impurity elements; The eutectic element includes one of Fe, Co, Mn and Ni.

2. A method for additive manufacturing of Al-Cu-X eutectic phase strengthened aluminum alloy material, characterized in that the steps include: The components of the Al-Cu-X eutectic phase strengthened aluminum alloy material according to claim 1 are prepared as raw materials, and raw alloy powder is obtained after pretreatment; The original alloy powder is used to perform laser melting printing to obtain the Al-Cu-X eutectic phase strengthened aluminum alloy material.

3. The method according to claim 2, wherein The raw materials include aluminum alloy powder, Al powder, Cu powder, Mg powder, V powder and eutectic element powder.

4. The method according to claim 3, wherein The aluminum alloy powder includes at least one of 1000 series aluminum alloy, 2000 series aluminum alloy, 3000 series aluminum alloy, 4000 series aluminum alloy, 5000 series aluminum alloy, 6000 series aluminum alloy, 7000 series aluminum alloy, 8000 series aluminum alloy and 9000 series aluminum alloy.

5. The method according to claim 2, wherein The pretreatment includes three-dimensional mixing or pre-alloying.

6. The method according to claim 2, wherein The printing parameters are as follows: laser power 160-340 W, laser scanning rate 400-1600 mm / s, scanning line spacing 80-110 μm, powder layer thickness 20-40 μm, powder feed ratio 1.8-3.4, and laser interlayer rotation angle 0°-90°.

7. Use of the Al-Cu-X eutectic phase strengthened aluminum alloy material as claimed in claim 1 in improving the tensile strength and elongation of the aluminum alloy by adding eutectic elements.

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