Aluminum alloy material for additive manufacturing and preparation method therefor, and aluminum alloy part

Abstract

Provided are an aluminum alloy material for additive manufacturing and a preparation method therefor, and an aluminum alloy part. The aluminum alloy material comprises the following components in percentages by mass: Mn: greater than or equal to 0.50 wt.% and less than or equal to 6.00 wt.%; Mg: greater than or equal to 0.50 wt.% and less than or equal to 4.00 wt.%; Er: greater than or equal to 3.00 wt.% and less than or equal to 8.00 wt.%; Sc: greater than or equal to 0.30 wt.% and less than or equal to 1.50 wt.%; Cr: greater than or equal to 0.30 wt.% and less than or equal to 1.00 wt.%; Si: greater than or equal to 0.10 wt.% and less than or equal to 0.50 wt.%; Fe: greater than or equal to 0.10 wt.% and less than or equal to 1.00 wt.%; Zr: greater than or equal to 0.50 wt.% and less than or equal to 3.00 wt.%; and the balance of Al and inevitable impurities.

Description

Aluminum alloy materials for additive manufacturing and their preparation methods, aluminum alloy parts

[0001] This application claims priority to the following Chinese patent application: Chinese Patent Application No. 202510478866.1, filed on April 16, 2025, entitled "Aluminum Alloy Material for Additive Manufacturing and Method for Preparing the Same, Aluminum Alloy Parts". The entire contents of that patent application are incorporated herein by reference. Technical Field

[0002] This disclosure relates to the field of metallic materials technology, and in particular to aluminum alloy materials for additive manufacturing, methods for their preparation, and aluminum alloy parts. Background Technology

[0003] Additive manufacturing technologies, such as laser-based powder bed fusion (PBF-LB / M), enable the lightweight and integrated manufacturing of complex structural parts due to their layer-by-layer deposition and near-net-shape characteristics. Furthermore, this additive manufacturing technology, through rapid melting and solidification processes, can significantly suppress the segregation of alloying elements while promoting grain refinement and the formation of highly saturated solid solutions, resulting in parts with excellent strength and toughness balance. Currently, this additive manufacturing technology has become a primary manufacturing technology for high-performance, complex structural parts in aerospace and other industries.

[0004] However, aluminum alloys face significant limitations in additive manufacturing of aluminum alloy parts due to their low laser absorption rate, high linear shrinkage, and susceptibility to oxidation. Specifically, 2XXX (Al-Cu) and 7XXX (Al-Zn) aluminum alloys are prone to cracking during additive manufacturing. Although Al-Si aluminum alloys show reduced hot cracking tendency during additive manufacturing, the resulting parts lack sufficient strength. While Al-Mg-Sc-Zr aluminum alloys produce parts with good mechanical properties after additive manufacturing, their applications are somewhat limited.

[0005] Therefore, developing an aluminum alloy material for additive manufacturing that combines low thermal cracking tendency with high strength, thereby enabling the manufacture of high-strength aluminum alloy parts, has become an urgent problem to be solved. Summary of the Invention

[0006] This disclosure provides aluminum alloy materials for additive manufacturing, methods for preparing the same, and aluminum alloy parts; it can provide an aluminum alloy material for additive manufacturing that has both low thermal cracking tendency and high strength, thereby producing high-strength aluminum alloy parts.

[0007] The technical solution disclosed herein is implemented as follows:

[0008] In a first aspect, this disclosure provides an aluminum alloy material for additive manufacturing, wherein, by weight percentage, the aluminum alloy material comprises:

[0009] Mn: greater than or equal to 0.50 wt.% and less than or equal to 6.00 wt.%;

[0010] Mg: ≥0.50 wt.% and ≤4.00 wt.%;

[0011] Er: Greater than or equal to 3.00 wt.% and less than or equal to 8.00 wt.%;

[0012] Sc: Greater than or equal to 0.30 wt.% and less than or equal to 1.50 wt.%;

[0013] Cr: ≥0.30 wt.% and ≤1.00 wt.%;

[0014] Si: greater than or equal to 0.10 wt.% and less than or equal to 0.50 wt.%;

[0015] Fe: ≥0.10 wt.% and ≤1.00 wt.%;

[0016] Zr: greater than or equal to 0.50 wt.% and less than or equal to 3.00 wt.%;

[0017] The balance consists of Al and unavoidable impurity elements.

[0018] In some possible implementations, by mass percentage, Mg: greater than or equal to 0.50 wt.% and less than or equal to 2.00 wt.%, and Mn: greater than or equal to 3.00 wt.% and less than or equal to 6.00 wt.%.

[0019] In some possible implementations, by mass percentage, Mg: greater than 2.00 wt.% and less than or equal to 4.00 wt.%, and Mn: greater than or equal to 0.50 wt.% and less than 3.00 wt.%.

[0020] In some possible implementations, by mass percentage, Sc: greater than or equal to 0.30 wt.% and less than or equal to 0.60 wt.%, and Zr: greater than or equal to 1.50 wt.% and less than or equal to 3.00 wt.%; or, by mass percentage, Sc: greater than 0.60 wt.% and less than or equal to 1.50 wt.%, and Zr: greater than or equal to 0.50 wt.% and less than 1.50 wt.%.

[0021] In some possible implementations, the aluminum alloy material includes at least one of the impurity elements by weight percentage, and the content of each impurity element is less than or equal to 0.05 wt.%.

[0022] In some possible implementations, the aluminum alloy material is a powder material, and the particle size of the powder in the powder material includes 15 μm to 75 μm.

[0023] In some possible implementations, the aluminum alloy material is a bar, wire, or filament.

[0024] Secondly, this disclosure provides a method for preparing an aluminum alloy material for additive manufacturing, the method comprising:

[0025] The aluminum alloy material is prepared from metal raw materials in a predetermined ratio; wherein, by mass percentage, the metal raw materials include:

[0026] Mn: greater than or equal to 0.50 wt.% and less than or equal to 6.00 wt.%;

[0027] Mg: ≥0.50 wt.% and ≤4.00 wt.%;

[0028] Er: Greater than or equal to 3.00 wt.% and less than or equal to 8.00 wt.%;

[0029] Sc: Greater than or equal to 0.30 wt.% and less than or equal to 1.50 wt.%;

[0030] Cr: ≥0.30 wt.% and ≤1.00 wt.%;

[0031] Si: greater than or equal to 0.10 wt.% and less than or equal to 0.50 wt.%;

[0032] Fe: ≥0.10 wt.% and ≤1.00 wt.%;

[0033] Zr: greater than or equal to 0.50 wt.% and less than or equal to 3.00 wt.%;

[0034] The balance consists of Al and unavoidable impurity elements.

[0035] Thirdly, this disclosure provides an aluminum alloy part, which is obtained by additive manufacturing from the aluminum alloy material for additive manufacturing described in the first aspect.

[0036] In some possible embodiments, the aluminum alloy part, after heat treatment, has a tensile strength greater than or equal to 600 MPa, a yield strength greater than or equal to 560 MPa, and an elongation greater than or equal to 7.0% at room temperature.

[0037] The heat treatment includes: holding the aluminum alloy part at 250°C to 450°C for 2 to 8 hours, and cooling the aluminum alloy part in air.

[0038] This disclosure provides aluminum alloy materials for additive manufacturing, their preparation methods, and aluminum alloy parts. Through compositional design of the aluminum alloy materials, during the rapid solidification process of additive manufacturing, the grain refinement and significant improvement of the mechanical properties of the aluminum alloy parts are achieved by utilizing the Al3Er eutectic phase, Al3Sc and Al3Zr primary phases, and Al3Sc and Al3Zr dispersed phases formed by elements Er, Sc, and Zr with the matrix Al. Simultaneously, the dispersed distribution of the Al3(Sc,Zr) composite phase and Al3(Er,Zr) composite phase formed by Zr with Sc and Er further enhances the recrystallization resistance and mechanical properties of the aluminum alloy parts, ultimately significantly improving their mechanical properties. Brief description of the attached figures

[0039] The features and advantages of one or more embodiments of this disclosure will become more readily apparent from the following description with reference to the accompanying drawings. The drawings are not drawn to scale and some features may be enlarged or reduced to show details of specific components. In the drawings:

[0040] Figure 1 is a morphological diagram of the aluminum alloy material provided in Embodiment 1 of this disclosure.

[0041] Figure 2 is a microstructure diagram of an aluminum alloy part after heat treatment provided in Embodiment 1 of this disclosure.

[0042] Figure 3 is another microstructure diagram of the heat-treated aluminum alloy part provided in Embodiment 1 of this disclosure.

[0043] Figure 4 is a tensile engineering stress-engineering strain curve of the heat-treated aluminum alloy part provided in Embodiment 1 of this disclosure at room temperature.

[0044] Figure 5 is a tensile engineering stress-engineering strain curve of the heat-treated aluminum alloy part provided in Embodiment 2 of this disclosure at room temperature.

[0045] Figure 6 is a tensile engineering stress-engineering strain curve of the heat-treated aluminum alloy part provided in Embodiment 3 of this disclosure at room temperature.

[0046] Figure 7 is a tensile engineering stress-engineering strain curve of the heat-treated aluminum alloy part provided in Embodiment 4 of this disclosure at room temperature.

[0047] Figure 8 is a tensile engineering stress-engineering strain curve of the heat-treated aluminum alloy part provided in Embodiment 5 of this disclosure at room temperature.

[0048] Figure 9 is a tensile engineering stress-engineering strain curve of the heat-treated aluminum alloy part provided in Embodiment 6 of this disclosure at room temperature.

[0049] Figure 10 is a tensile engineering stress-engineering strain curve of the heat-treated aluminum alloy part provided in Embodiment 7 of this disclosure at room temperature.

[0050] Figure 11 is a tensile engineering stress-engineering strain curve of the heat-treated aluminum alloy part provided in Comparative Example 1 of this disclosure at room temperature.

[0051] Figure 12 is a tensile engineering stress-engineering strain curve of the heat-treated aluminum alloy part provided in Comparative Example 2 of this disclosure at room temperature.

[0052] Figure 13 is a tensile engineering stress-engineering strain curve of the heat-treated aluminum alloy part provided in Comparative Example 3 of this disclosure at room temperature.

[0053] Figure 14 is a tensile engineering stress-engineering strain curve of the heat-treated aluminum alloy part provided in Comparative Example 4 of this disclosure at room temperature. Detailed Implementation

[0054] The technical solutions in this disclosure will now be clearly and completely described with reference to the accompanying drawings.

[0055] This disclosure provides an aluminum alloy material for additive manufacturing, comprising, by weight percentage:

[0056] Mn: 0.50 wt.% to 6.00 wt.%;

[0057] Mg: 0.50 wt.% to 4.00 wt.%;

[0058] Er: 3.00 wt.% to 8.00 wt.%;

[0059] Sc: 0.30 wt.% to 1.50 wt.%;

[0060] Cr: 0.30 wt.% to 1.00 wt.%;

[0061] Si: 0.10 wt.% to 0.50 wt.%;

[0062] Fe: 0.10 wt.% to 1.00 wt.%;

[0063] Zr: 0.50 wt.% to 3.00 wt.%;

[0064] The balance consists of Al and unavoidable impurity elements.

[0065] In this disclosure, the roles of each element in the manufacture of aluminum alloy parts are as follows:

[0066] Manganese (Mn), as a major alloying element, enhances the mechanical properties of aluminum alloy parts through solid solution strengthening. Furthermore, Mn forms an Al6Mn reinforcing phase with the Al matrix, distributed at grain boundaries, acting as a second-phase strengthening agent. Additionally, the slow diffusion rate of Mn in the Al matrix reduces hot cracking susceptibility, thereby improving the formability of aluminum alloy materials.

[0067] Elemental magnesium (Mg) can be supersaturated and dissolved in the Al matrix during the rapid solidification process of additive manufacturing, which significantly enhances the effect of solid solution strengthening.

[0068] During the rapid solidification process in additive manufacturing, element Er can combine with the Al matrix at grain boundaries to form an Al3Er eutectic phase. This Al3Er eutectic phase can act as a nucleation site for heterogeneous formation, significantly increasing the nucleation rate and effectively refining the grains. Furthermore, at high temperatures, this Al3Er eutectic phase exhibits high thermal stability, continuously pinning grain boundaries and effectively inhibiting grain growth, thus maintaining the alloy's high-temperature performance. In addition, during heat treatment, element Er can promote the precipitation of Al3Er nanoprecipitates. These Al3Er nanoprecipitates are dispersed in the Al matrix, pinning dislocations and subgrain boundaries, thereby further enhancing precipitation strengthening.

[0069] Scandium (Sc) can form the Al3Sc primary phase with the Al matrix during the rapid solidification process in additive manufacturing. This Al3Sc primary phase can act as a nucleation core for heterogeneous formation, promoting the formation of equiaxed crystals and thus improving grain uniformity. Furthermore, by improving the grain structure, this Al3Sc primary phase can effectively suppress the initiation of hot cracks. In addition, during heat treatment, scandium Sc can promote the precipitation of Al3Sc nano-precipitates. These Al3Sc nano-precipitates are dispersed throughout the Al matrix, significantly enhancing the precipitation strengthening effect and further improving the mechanical properties of aluminum alloy parts.

[0070] Chromium (Cr) effectively inhibits recrystallization by forming intermetallic compounds in the aluminum matrix. This inhibition of recrystallization helps refine the grains, thereby significantly improving the strength and toughness of aluminum alloy parts.

[0071] Elemental silicon (Si) plays multiple roles in the manufacture of aluminum alloy parts. First, Si narrows the solidification temperature range of aluminum alloy parts. This helps reduce microsegregation during the rapid solidification process in additive manufacturing, improving the mechanical properties of the aluminum alloy parts. Second, Si can form a Mg₂Si strengthening phase with magnesium. This Mg₂Si strengthening phase can significantly enhance the strength of aluminum alloy parts. Furthermore, Si can enhance the crack healing ability of aluminum alloy parts, thereby reducing the tendency for hot cracking.

[0072] Elemental iron (Fe) can improve the fluidity of the melt and fill the hot cracks between grains during additive manufacturing, thereby significantly improving the formability of aluminum alloy materials.

[0073] Zirconium (Zr) promotes the precipitation of Al3Zr dispersed phases during the rapid solidification process in additive manufacturing. These Al3Zr dispersed phases can act as nucleation sites for heterogeneous formation, significantly increasing the nucleation rate and effectively refining the grain size. Moreover, at high temperatures, these Al3Zr dispersed phases can pin grain boundaries and hinder dislocation movement, suppressing recrystallization and further refining the grain structure, thereby significantly improving the high-temperature mechanical properties of aluminum alloy parts.

[0074] Based on the above explanation, during the rapid solidification process of additive manufacturing, elements Er, Sc, and Zr can form fine Al3Er eutectic phase, Al3Sc primary phase, and Al3Zr dispersed phase with the matrix Al, respectively, thereby refining the grain size and improving the mechanical properties of aluminum alloy parts. Furthermore, by precisely controlling the content of Sc and Zr, the formation of coarse columnar crystals can be effectively suppressed, reducing the tendency for hot cracking and thus improving the formability of aluminum alloy materials. In addition, Zr can also form Al3(Sc,Zr) composite phase and Al3(Er,Zr) composite phase with Sc and Er, respectively. Compared to the single Al3Sc primary phase and Al3Er eutectic phase, these composite phases have a lower coarsening tendency, further enhancing the age-hardening effect of aluminum alloy parts to obtain high-strength aluminum alloy parts.

[0075] In addition to using Er, Sc, and Zr to refine grains and improve the mechanical properties of aluminum alloy parts by forming the Al3Er eutectic phase, Al3Sc primary phase, and Al3Zr dispersed phase, the mechanical properties of aluminum alloy parts are further optimized by adding Si and Fe. Specifically, the addition of Si and Fe can significantly improve the thermal crack resistance of aluminum alloy parts, while also improving the fluidity of the aluminum alloy material, thereby further improving its formability.

[0076] Furthermore, the aluminum alloy material provided in this embodiment does not contain zinc (Zn), a low-melting-point and volatile element. During additive manufacturing, this effectively avoids problems caused by Zn burn-off, thereby eliminating or reducing porosity defects in the aluminum alloy parts and improving their density.

[0077] In some possible implementations of the above technical solutions, by mass percentage, Mg: greater than or equal to 0.50 wt.% and less than or equal to 2.00 wt.%, and Mn: greater than or equal to 3.00 wt.% and less than or equal to 6.00 wt.%.

[0078] Element magnesium (Mg) enhances solid solution strengthening by supersaturating and dissolving in the Al matrix, thereby significantly improving the tensile strength and yield strength of the manufactured aluminum alloy parts. However, when the Mg content is low, this solid solution strengthening effect is not significant, and thus cannot substantially improve the tensile strength and yield strength of the aluminum alloy parts. Element manganese (Mn) in additive manufacturing not only increases the recrystallization temperature to inhibit the recrystallization process but also refines the recrystallized grains, thereby improving the strength and toughness of the aluminum alloy parts. Therefore, this disclosure utilizes the combined action of elements Mn and Mg to further enhance the strengthening effect.

[0079] Furthermore, element Mn can form the Al6(Fe,Mn) phase with element Fe, thereby effectively reducing the harmful effects of Fe. This is because Fe typically forms coarse needle-like or lamellar phases in the Al matrix, such as β-Al5FeSi. These coarse needle-like or lamellar phases have high hardness and brittleness, which can fracture the Al matrix, thus reducing the mechanical properties of aluminum alloy parts. The addition of Mn promotes the formation of fine, dispersed Al6(Fe,Mn) phases. The morphology of this Al6(Fe,Mn) phase is closer to granular or skeletal, significantly reducing its fracture effect on the Al matrix. Therefore, the addition of Mn can ensure the strength of aluminum alloy parts without negatively impacting other properties.

[0080] Based on this, in this disclosure, when the content of element Mg is 0.50 wt.% to 2.00 wt.%, the content of element Mn is set to 3.00 wt.% to 6.00 wt.%, in order to improve the tensile strength and yield strength of aluminum alloy parts.

[0081] In some possible implementations of the above technical solutions, by mass percentage, Mg: greater than 2.00 wt.% and less than or equal to 4.00 wt.%, and Mn: greater than or equal to 0.50 wt.% and less than 3.00 wt.%.

[0082] This is because when the content of element Mg is between 2.0 wt.% and 4.0 wt.%, although element Mg can play a good solid solution strengthening effect, thereby ensuring a certain improvement in the strength of aluminum alloy parts obtained by additive manufacturing, element Mg has almost no precipitation strengthening effect in the matrix Al. Therefore, in order to obtain high-strength aluminum alloy parts, other strengthening elements usually need to be added to the aluminum alloy material. Element Mn can improve the formability of aluminum alloy materials and reduce cracking. On the other hand, it can form Al6Mn phase with the matrix Al, thereby playing a good age-hardening effect. Therefore, it is suitable for the composition design of high-strength aluminum alloy parts. However, too much Al6Mn phase may lead to the deterioration of the plasticity of aluminum alloy parts. Based on this, in this disclosure, when the content of element Mg is between 2.00 wt.% and 4.00 wt.%, the content of element Mn is set to 0.50 wt.% to 3.00 wt.%, aiming to improve the strength of aluminum alloy parts while ensuring good elongation.

[0083] In some possible implementations of the above technical solutions, by mass percentage, Sc: greater than or equal to 0.30 wt.% and less than or equal to 0.60 wt.%, and Zr: greater than or equal to 1.50 wt.% and less than or equal to 3.00 wt.%; or, by mass percentage, Sc: greater than 0.60 wt.% and less than or equal to 1.50 wt.%, and Zr: greater than or equal to 0.50 wt.% and less than 1.50 wt.%.

[0084] In this disclosure, the movement of dislocations is effectively hindered by the Al3Er eutectic phase, Al3Sc primary phase, and Al3Zr dispersed phase formed by Er, Sc, and Zr with the Al matrix, respectively, as well as the Al3(Sc,Zr) composite phase and Al3(Er,Zr) composite phase formed by Zr with Sc and Er, respectively, thereby improving the strength of aluminum alloy parts. Furthermore, the Al3Er eutectic phase, Al3Sc primary phase, Al3Zr dispersed phase, Al3(Sc,Zr) composite phase, and Al3(Er,Zr) composite phase exhibit good stability at high temperatures, which helps maintain the mechanical properties of aluminum alloy parts and reduces the degradation of mechanical properties caused by prolonged exposure to high temperatures.

[0085] When the content of element Sc is low, the lack of heterogeneous nucleation sites in the Al matrix leads to a weakened grain refinement effect and an increase in the number of coarse columnar crystals. This increases the tendency of aluminum alloy parts to hot crack during additive manufacturing. Element Zr can exert a similar grain refinement effect as element Sc and can also provide good age-hardening effects. Therefore, in this disclosure, when the content of element Sc is low, increasing the content of element Zr can ensure the tensile strength and yield strength of the aluminum alloy parts obtained by additive manufacturing. When the content of element Sc is high, decreasing the content of element Zr can also ensure the tensile strength and yield strength of the aluminum alloy parts obtained by additive manufacturing.

[0086] In some possible implementations of the above technical solution, the aluminum alloy material includes at least one impurity element by mass percentage, and the content of each impurity element is less than or equal to 0.05 wt.%.

[0087] During the preparation of aluminum alloy materials, some impurity elements, such as oxygen (O) and nitrogen (N), are inevitably introduced. If the content of these impurity elements is too high, stress concentration points will form, thereby affecting the strength of the aluminum alloy parts. In addition, in some cases, excessive impurity elements may also affect the strength and hardness of the heat-treated aluminum alloy parts. Therefore, in this disclosure, the content of each impurity element is limited to no more than 0.05 wt.%.

[0088] In some possible implementations of the above technical solution, the aluminum alloy material is a powder material, and the particle size of the powder in the powder material includes 15μm to 75μm.

[0089] In additive manufacturing, when aluminum alloys are in powder form, their particle size has a significant impact on forming performance. Smaller particle sizes improve the flowability of the aluminum alloy; however, if the particle size is too small, electrostatic effects may cause the aluminum alloy particles to adhere to each other, thus reducing flowability and hindering uniform spreading. Therefore, a suitable particle size not only ensures uniform spreading of the aluminum alloy but also provides a larger specific surface area, thereby improving laser energy absorption efficiency and promoting uniform melting and solidification. Furthermore, a suitable particle size helps reduce the porosity of aluminum alloy parts, increasing their density and ultimately enhancing their mechanical properties.

[0090] In some possible implementations of the above technical solutions, the aluminum alloy material is a rod, wire, or filament.

[0091] It should be noted that the aforementioned bars, wires, or filaments are aluminum alloy materials with different shapes and / or sizes. In the embodiments of this disclosure, bars refer to elongated aluminum alloy materials with a circular or non-circular (e.g., rectangular, hexagonal) cross-section. Wires refer to elongated aluminum alloy materials with a diameter between a few millimeters and tens of millimeters (e.g., 5.5mm to 30mm). Fibers refer to elongated aluminum alloy materials with a diameter less than a few millimeters (e.g., less than 5.5mm).

[0092] In this embodiment, the aluminum alloy material can be a bar, wire, or filament. Alternatively, powdered aluminum alloy material can be processed into the aforementioned bars, wires, or filaments using methods such as powder metallurgy.

[0093] Secondly, this disclosure provides a method for preparing an aluminum alloy material for additive manufacturing, the method comprising:

[0094] Aluminum alloy material is prepared from metal raw materials in a predetermined ratio; wherein, by mass percentage, the metal raw materials include:

[0095] Mn: greater than or equal to 0.50 wt.% and less than or equal to 6.00 wt.%;

[0096] Mg: ≥0.50 wt.% and ≤4.00 wt.%;

[0097] Er: Greater than or equal to 3.00 wt.% and less than or equal to 8.00 wt.%;

[0098] Sc: Greater than or equal to 0.30 wt.% and less than or equal to 1.50 wt.%;

[0099] Cr: ≥0.30 wt.% and ≤1.00 wt.%;

[0100] Si: greater than or equal to 0.10 wt.% and less than or equal to 0.50 wt.%;

[0101] Fe: ≥0.10 wt.% and ≤1.00 wt.%;

[0102] Zr: greater than or equal to 0.50 wt.% and less than or equal to 3.00 wt.%;

[0103] The balance consists of Al and unavoidable impurity elements.

[0104] In some examples, powdered aluminum alloy materials can be prepared using methods such as gas atomization, plasma atomization, rotating electrode processing, or mechanical alloying. Specifically, in gas atomization, the aforementioned metal raw materials in a predetermined ratio are heated and melted. The molten metal raw materials are then impacted by a high-speed gas flow, breaking into fine droplets and rapidly cooling and solidifying to form powdered aluminum alloy materials. In plasma atomization, the aforementioned metal raw materials are heated and melted using high-temperature plasma, and then atomized by a high-speed gas flow to form powdered aluminum alloy materials. In rotating electrode processing, the aforementioned metal raw materials are used as a rotating electrode, heated and melted by an electric arc or plasma. The molten metal raw materials are then dispersed and solidified under centrifugal force to form powdered aluminum alloy materials. In mechanical alloying, the aforementioned metal raw materials are repeatedly ground, mixed, and cold-welded using a high-energy ball mill to ultimately form powdered aluminum alloy materials.

[0105] It should be noted that gas atomization can be used to prepare powdered aluminum alloy materials. Compared with other methods, gas atomization can produce a large amount of powdered aluminum alloy material in a shorter time, resulting in high preparation efficiency and minimizing the introduction of impurities and inclusions during the preparation process. Furthermore, the powdered aluminum alloy material prepared by gas atomization exhibits better sphericity, resulting in better flowability and compaction during additive manufacturing. In addition, the rapid cooling rate during gas atomization facilitates the formation of fine and uniform microstructures, contributing to improved mechanical properties of aluminum alloy parts.

[0106] In other examples, aluminum alloy materials for bars can be prepared by casting or forging the aforementioned metal raw materials. Aluminum alloy materials for wires can be obtained by rolling or drawing. Aluminum alloy materials for wire filaments can be obtained by drawing, that is, by repeatedly drawing the aforementioned aluminum alloy materials for bars or wires to gradually reduce the diameter, thereby forming the desired wire filament aluminum alloy material.

[0107] Finally, this disclosure provides an aluminum alloy part, which is obtained by additive manufacturing of the aluminum alloy material used for additive manufacturing according to the foregoing technical solution.

[0108] In some possible embodiments, the aluminum alloy parts, after heat treatment, have a tensile strength greater than or equal to 600 MPa, a yield strength greater than or equal to 560 MPa, and an elongation greater than or equal to 7.0% at room temperature.

[0109] The heat treatment includes holding the aluminum alloy parts at 250°C to 450°C for 2 to 8 hours and then cooling the aluminum alloy parts in air.

[0110] It should be noted that when the aluminum alloy material is in powder form or is a wire with a very small diameter that conforms to the additive manufacturing process, the aforementioned aluminum alloy parts can be manufactured using additive manufacturing in this embodiment. When the aluminum alloy material is in bar, wire, or wire with a large diameter that does not conform to the additive manufacturing process, in this embodiment, the aforementioned bar, wire, or wire needs to be pre-processed into powder or wire that conforms to the additive manufacturing process. The specific processing method is not described in detail in this embodiment.

[0111] It should be noted that after preparing the powdered or wire-like aluminum alloy material conforming to the additive manufacturing process, a drying process is required to remove moisture or other solvents from the aluminum alloy material, thereby ensuring the quality and stability of the aluminum alloy material. After drying, the aluminum alloy material should be sealed and stored in a vacuum or inert gas environment. This storage method can effectively prevent the aluminum alloy material from reacting with moisture and oxygen in the air during storage, preventing oxidation, moisture absorption, and other problems, thus ensuring that the performance of the aluminum alloy material is not affected.

[0112] The technical solution of this disclosure will be described in detail below through specific embodiments.

[0113] Example 1

[0114] An aluminum alloy material for additive manufacturing, comprising, by weight percentage: Mn: 0.60 wt.%, Mg: 4.00 wt.%, Er: 3.00 wt.%, Sc: 0.73 wt.%, Cr: 0.30 wt.%, Si: 0.10 wt.%, Fe: 0.32 wt.%, Zr: 0.50 wt.%, with the remainder being Al and unavoidable impurity elements.

[0115] In some examples, the aluminum alloy material provided in this embodiment 1 is a powdered aluminum alloy material prepared by gas atomization, with a particle size range of 15μm to 75μm. For a specific morphology diagram, please refer to Figure 1.

[0116] Before using the aluminum alloy material provided in Example 1 for additive manufacturing, the three-dimensional model of the aluminum alloy part is first sliced ​​according to a set thickness. Then, the dried aluminum alloy material is added to the powder feeding chamber of the additive manufacturing equipment. After the oxygen content in the forming chamber of the additive manufacturing equipment drops to a set range, the laser beam begins to scan the aluminum alloy material laid on the substrate of the additive manufacturing equipment and melts the aluminum alloy material according to the contour obtained from the slicing process to achieve metallurgical bonding. This process is repeated layer by layer until an aluminum alloy part is manufactured.

[0117] After manufacturing the aluminum alloy part, it was subjected to aging heat treatment at 300°C for 4 hours, followed by cooling in air. The microstructure of the heat-treated aluminum alloy part is shown in Figures 2 and 3, and its tensile stress-strain curve at room temperature is shown in Figure 4. The aluminum alloy part manufactured in Example 1, after heat treatment, has a tensile strength of 611 MPa, a yield strength of 591 MPa, and an elongation of 10.0% at room temperature.

[0118] Example 2

[0119] An aluminum alloy material for additive manufacturing, comprising, by weight percentage: Mn: 6.00 wt.%, Mg: 2.00 wt.%, Er: 3.21 wt.%, Sc: 0.60 wt.%, Cr: 0.65 wt.%, Si: 0.18 wt.%, Fe: 0.26 wt.%, Zr: 1.50 wt.%, with the remainder being Al and unavoidable impurity elements.

[0120] In some examples, the aluminum alloy material provided in this embodiment 2 is a powdered aluminum alloy material prepared by gas atomization, with a particle size range of 15 μm to 75 μm.

[0121] Before using the aluminum alloy material provided in Example 2 for additive manufacturing, the three-dimensional model of the aluminum alloy part is first sliced ​​according to a set thickness. Then, the dried aluminum alloy material is added to the powder feeding chamber of the additive manufacturing equipment. After the oxygen content in the forming chamber of the additive manufacturing equipment drops to a set range, the laser beam begins to scan the aluminum alloy material laid on the substrate of the additive manufacturing equipment and melts the aluminum alloy material according to the contour obtained from the slicing process to achieve metallurgical bonding. This process is repeated layer by layer until an aluminum alloy part is manufactured.

[0122] After manufacturing the aluminum alloy part, it was subjected to aging heat treatment at 350°C for 3.5 hours, followed by cooling in air. The tensile stress-strain curve of the heat-treated aluminum alloy part at room temperature is shown in Figure 5. The aluminum alloy part manufactured in Example 2, after heat treatment, exhibited a tensile strength of 613 MPa, a yield strength of 594 MPa, and an elongation of 8.0% at room temperature.

[0123] Example 3

[0124] An aluminum alloy material for additive manufacturing, comprising, by weight percentage: Mn: 3.00 wt.%, Mg: 0.50 wt.%, Er: 3.10 wt.%, Sc: 0.30 wt.%, Cr: 0.72 wt.%, Si: 0.33 wt.%, Fe: 0.51 wt.%, Zr: 3.00 wt.%, with the remainder being Al and unavoidable impurity elements.

[0125] In some examples, the aluminum alloy material provided in this embodiment 3 is a powdered aluminum alloy material prepared by gas atomization, with a particle size range of 15 μm to 75 μm.

[0126] Before using the aluminum alloy material provided in Embodiment 3 for additive manufacturing, the three-dimensional model of the aluminum alloy part is first sliced ​​according to a set thickness. Then, the dried aluminum alloy material is added to the powder feeding chamber of the additive manufacturing equipment. After the oxygen content in the forming chamber of the additive manufacturing equipment drops to a set range, the laser beam begins to scan the aluminum alloy material laid on the substrate of the additive manufacturing equipment and melts the aluminum alloy material according to the contour obtained from the slicing process to achieve metallurgical bonding. This process is repeated layer by layer until an aluminum alloy part is manufactured.

[0127] After manufacturing the aluminum alloy part, it was subjected to aging heat treatment at 450°C for 2 hours, followed by cooling in air. The tensile stress-strain curve of the heat-treated aluminum alloy part at room temperature is shown in Figure 6. The aluminum alloy part manufactured in Example 3, after heat treatment, has a tensile strength of 617 MPa, a yield strength of 572 MPa, and an elongation of 8.5% at room temperature.

[0128] Example 4

[0129] An aluminum alloy material for additive manufacturing, comprising, by weight percentage: Mn: 1.16 wt.%, Mg: 2.50 wt.%, Er: 4.05 wt.%, Sc: 0.41 wt.%, Cr: 0.46 wt.%, Si: 0.21 wt.%, Fe: 0.15 wt.%, Zr: 2.23 wt.%, with the remainder being Al and unavoidable impurity elements.

[0130] In some examples, the aluminum alloy material provided in this embodiment 4 is a powdered aluminum alloy material prepared by gas atomization, with a particle size range of 15 μm to 75 μm.

[0131] Before using the aluminum alloy material provided in Example 4 for additive manufacturing, the three-dimensional model of the aluminum alloy part is first sliced ​​according to a set thickness. Then, the dried aluminum alloy material is added to the powder feeding chamber of the additive manufacturing equipment. After the oxygen content in the forming chamber of the additive manufacturing equipment drops to a set range, the laser beam begins to scan the aluminum alloy material laid on the substrate of the additive manufacturing equipment and melts the aluminum alloy material according to the contour obtained from the slicing process to achieve metallurgical bonding. This process is repeated layer by layer until an aluminum alloy part is manufactured.

[0132] After manufacturing the aluminum alloy part, it was subjected to aging heat treatment at 300°C for 4 hours, followed by cooling in air. The tensile stress-strain curve of the heat-treated aluminum alloy part at room temperature is shown in Figure 7. The aluminum alloy part manufactured in Example 4, after heat treatment, has a tensile strength of 602 MPa, a yield strength of 598 MPa, and an elongation of 10.5% at room temperature.

[0133] Example 5

[0134] An aluminum alloy material for additive manufacturing, comprising, by weight percentage: Mn: 0.50 wt.%, Mg: 3.25 wt.%, Er: 6.88 wt.%, Sc: 1.50 wt.%, Cr: 1.00 wt.%, Si: 0.50 wt.%, Fe: 0.68 wt.%, Zr: 1.10 wt.%, with the remainder being Al and unavoidable impurity elements.

[0135] In some examples, the aluminum alloy material provided in this embodiment 5 is a powdered aluminum alloy material prepared by gas atomization, with a particle size range of 15 μm to 75 μm.

[0136] Before using the aluminum alloy material provided in Example 5 for additive manufacturing, the three-dimensional model of the aluminum alloy part is first sliced ​​according to a set thickness. Then, the dried aluminum alloy material is added to the powder feeding chamber of the additive manufacturing equipment. After the oxygen content in the forming chamber of the additive manufacturing equipment drops to a set range, the laser beam begins to scan the aluminum alloy material laid on the substrate of the additive manufacturing equipment and melts the aluminum alloy material according to the contour obtained from the slicing process to achieve metallurgical bonding. This process is repeated layer by layer until an aluminum alloy part is manufactured.

[0137] After manufacturing the aluminum alloy part, it was subjected to aging heat treatment at 250°C for 8 hours, followed by cooling in air. The tensile stress-strain curve of the heat-treated aluminum alloy part at room temperature is shown in Figure 8. The aluminum alloy part manufactured in Example 5, after heat treatment, has a tensile strength of 618 MPa, a yield strength of 611 MPa, and an elongation of 8.0% at room temperature.

[0138] Example 6

[0139] An aluminum alloy material for additive manufacturing, comprising, by weight percentage: Mn: 3.98 wt.%, Mg: 1.21 wt.%, Er: 3.34 wt.%, Sc: 0.75 wt.%, Cr: 0.79 wt.%, Si: 0.17 wt.%, Fe: 0.10 wt.%, Zr: 1.34 wt.%, with the remainder being Al and unavoidable impurity elements.

[0140] In some examples, the aluminum alloy material provided in this embodiment 6 is a powdered aluminum alloy material prepared by gas atomization, with a particle size range of 15 μm to 75 μm.

[0141] Before using the aluminum alloy material provided in Example 6 for additive manufacturing, the three-dimensional model of the aluminum alloy part is first sliced ​​according to a set thickness. Then, the dried aluminum alloy material is added to the powder feeding chamber of the additive manufacturing equipment. After the oxygen content in the forming chamber of the additive manufacturing equipment drops to a set range, the laser beam begins to scan the aluminum alloy material laid on the substrate of the additive manufacturing equipment and melts the aluminum alloy material according to the contour obtained from the slicing process to achieve metallurgical bonding. This process is repeated layer by layer until an aluminum alloy part is manufactured.

[0142] After manufacturing the aluminum alloy part, it was subjected to aging heat treatment at 375°C for 3.5 hours, followed by cooling in air. The tensile stress-strain curve of the heat-treated aluminum alloy part at room temperature is shown in Figure 9. The aluminum alloy part manufactured in Example 6, after heat treatment, has a tensile strength of 609 MPa, a yield strength of 566 MPa, and an elongation of 10.0% at room temperature.

[0143] Example 7

[0144] An aluminum alloy material for additive manufacturing, comprising, by weight percentage: Mn: 3.31 wt.%, Mg: 0.97 wt.%, Er: 8.00 wt.%, Sc: 0.35 wt.%, Cr: 0.35 wt.%, Si: 0.21 wt.%, Fe: 1.00 wt.%, Zr: 1.62 wt.%, with the remainder being Al and unavoidable impurity elements.

[0145] In some examples, the aluminum alloy material provided in this embodiment 7 is a powdered aluminum alloy material prepared by gas atomization, with a particle size range of 15 μm to 75 μm.

[0146] Before using the aluminum alloy material provided in Example 7 for additive manufacturing, the three-dimensional model of the aluminum alloy part is first sliced ​​according to a set thickness. Then, the dried aluminum alloy material is added to the powder feeding chamber of the additive manufacturing equipment. After the oxygen content in the forming chamber of the additive manufacturing equipment drops to a set range, the laser beam begins to scan the aluminum alloy material laid on the substrate of the additive manufacturing equipment and melts the aluminum alloy material according to the contour obtained from the slicing process to achieve metallurgical bonding. This process is repeated layer by layer until an aluminum alloy part is manufactured.

[0147] After manufacturing the aluminum alloy part, it was subjected to aging heat treatment at 300°C for 4 hours, followed by cooling in air. The tensile stress-strain curve of the heat-treated aluminum alloy part at room temperature is shown in Figure 10. The aluminum alloy part manufactured in Example 7, after heat treatment, has a tensile strength of 637 MPa, a yield strength of 602 MPa, and an elongation of 7.0% at room temperature.

[0148] Comparative Example 1

[0149] The aluminum alloy material for additive manufacturing provided in Comparative Example 1 is the same as that in Example 2, except that the content of element Mn is different from that in Example 2.

[0150] The aluminum alloy material for additive manufacturing provided in Comparative Example 1 comprises, by mass percentage: Mn: 0.26 wt.%, Mg: 2.00 wt.%, Er: 3.21 wt.%, Sc: 0.60 wt.%, Cr: 0.65 wt.%, Si: 0.18 wt.%, Fe: 0.26 wt.%, Zr: 1.50 wt.%, with the remainder being Al and unavoidable impurity elements.

[0151] In some examples, the aluminum alloy material provided in Comparative Example 1 is a powdered aluminum alloy material prepared by gas atomization, with a particle size ranging from 15 μm to 75 μm.

[0152] Before using the aluminum alloy material provided in Comparative Example 1 for additive manufacturing, the three-dimensional model of the aluminum alloy part is first sliced ​​according to a set thickness. Then, the dried aluminum alloy material is added to the powder feeding chamber of the additive manufacturing equipment. After the oxygen content in the forming chamber of the additive manufacturing equipment drops to a set range, the laser beam begins to scan the aluminum alloy material laid on the substrate of the additive manufacturing equipment and melts the aluminum alloy material according to the contour obtained from the slicing process to achieve metallurgical bonding. This process is repeated layer by layer until an aluminum alloy part is manufactured.

[0153] After manufacturing the aluminum alloy part, it was subjected to aging heat treatment at 350℃ for 3.5 hours, followed by cooling in air. The tensile stress-strain curve of the heat-treated aluminum alloy part at room temperature is shown in Figure 11. The aluminum alloy part manufactured in Comparative Example 1, after heat treatment, has a tensile strength of 553 MPa, a yield strength of 548 MPa, and an elongation of 13.5% at room temperature.

[0154] Comparative Example 2

[0155] The aluminum alloy material for additive manufacturing provided in Comparative Example 2 is the same as that in Example 3 except for the content of element Zr.

[0156] The aluminum alloy material for additive manufacturing provided in Comparative Example 2 comprises, by mass percentage: Mn: 3.00 wt.%, Mg: 0.50 wt.%, Er: 3.10 wt.%, Sc: 0.30 wt.%, Cr: 0.72 wt.%, Si: 0.33 wt.%, Fe: 0.51 wt.%, Zr: 0.42 wt.%, with the remainder being Al and unavoidable impurity elements.

[0157] In some examples, the aluminum alloy material provided in Comparative Example 2 is a powdered aluminum alloy material prepared by gas atomization, with a particle size ranging from 15 μm to 75 μm.

[0158] Before using the aluminum alloy material provided in Comparative Example 2 for additive manufacturing, the three-dimensional model of the aluminum alloy part is first sliced ​​according to a set thickness. Then, the dried aluminum alloy material is added to the powder feeding chamber of the additive manufacturing equipment. After the oxygen content in the forming chamber of the additive manufacturing equipment drops to a set range, the laser beam begins to scan the aluminum alloy material laid on the substrate of the additive manufacturing equipment and melts the aluminum alloy material according to the contour obtained from the slicing process to achieve metallurgical bonding. This process is repeated layer by layer until an aluminum alloy part is manufactured.

[0159] After manufacturing the aluminum alloy part, it was subjected to aging heat treatment at 300℃ for 4 hours, followed by cooling in air. The tensile stress-strain curve of the heat-treated aluminum alloy part at room temperature is shown in Figure 12. The aluminum alloy part manufactured in Comparative Example 2, after heat treatment, has a tensile strength of 561 MPa, a yield strength of 535 MPa, and an elongation of 11.0% at room temperature.

[0160] Comparative Example 3

[0161] The aluminum alloy material for additive manufacturing provided in Comparative Example 3 is the same as that in Example 4, except that the content of element Er is different from that in Example 4.

[0162] The aluminum alloy material for additive manufacturing provided in Comparative Example 3 comprises, by mass percentage: Mn: 1.16 wt.%, Mg: 2.50 wt.%, Er: 8.38 wt.%, Sc: 0.41 wt.%, Cr: 0.46 wt.%, Si: 0.21 wt.%, Fe: 0.15 wt.%, Zr: 2.23 wt.%, with the remainder being Al and unavoidable impurity elements.

[0163] In some examples, the aluminum alloy material provided in Comparative Example 3 is a powdered aluminum alloy material prepared by gas atomization, with a particle size ranging from 15 μm to 75 μm.

[0164] Before using the aluminum alloy material provided in Comparative Example 3 for additive manufacturing, the three-dimensional model of the aluminum alloy part is first sliced ​​according to a set thickness. Then, the dried aluminum alloy material is added to the powder feeding chamber of the additive manufacturing equipment. After the oxygen content in the forming chamber of the additive manufacturing equipment drops to a set range, the laser beam begins to scan the aluminum alloy material laid on the substrate of the additive manufacturing equipment and melts the aluminum alloy material according to the contour obtained from the slicing process to achieve metallurgical bonding. This process is repeated layer by layer until an aluminum alloy part is manufactured.

[0165] After manufacturing the aluminum alloy part, it was subjected to aging heat treatment at 325℃ for 4 hours, followed by cooling in air. The tensile stress-strain curve of the heat-treated aluminum alloy part at room temperature is shown in Figure 13. The aluminum alloy part manufactured in Comparative Example 3, after heat treatment, has a tensile strength of 669 MPa, a yield strength of 634 MPa, and an elongation of 5.5% at room temperature.

[0166] Comparative Example 4

[0167] The aluminum alloy material for additive manufacturing provided in Comparative Example 4 contains the same elements and their contents as in Example 1, except that it does not contain Cr.

[0168] The aluminum alloy material for additive manufacturing provided in Comparative Example 4 comprises, by mass percentage: Mn: 0.60 wt.%, Mg: 4.00 wt.%, Er: 3.00 wt.%, Sc: 0.73 wt.%, Si: 0.10 wt.%, Fe: 0.32 wt.%, Zr: 0.50 wt.%, with the remainder being Al and unavoidable impurity elements.

[0169] In some examples, the aluminum alloy material provided in Comparative Example 4 is a powdered aluminum alloy material prepared by gas atomization, with a particle size ranging from 15 μm to 75 μm.

[0170] Before using the aluminum alloy material provided in Comparative Example 4 for additive manufacturing, the three-dimensional model of the aluminum alloy part is first sliced ​​according to a set thickness. Then, the dried aluminum alloy material is added to the powder feeding chamber of the additive manufacturing equipment. After the oxygen content in the forming chamber of the additive manufacturing equipment drops to a set range, the laser beam begins to scan the aluminum alloy material laid on the substrate of the additive manufacturing equipment and melts the aluminum alloy material according to the contour obtained from the slicing process to achieve metallurgical bonding. This process is repeated layer by layer until an aluminum alloy part is manufactured.

[0171] After manufacturing the aluminum alloy part, it was subjected to aging heat treatment at 325℃ for 4 hours, followed by cooling in air. The tensile stress-strain curve of the heat-treated aluminum alloy part at room temperature is shown in Figure 14. The aluminum alloy part manufactured in Comparative Example 4, after heat treatment, has a tensile strength of 578 MPa, a yield strength of 556 MPa, and an elongation of 10.5% at room temperature.

[0172] The specific data of tensile strength, yield strength and elongation of the aluminum alloy parts after heat treatment in Examples 1 to 7 and Comparative Examples 1 to 4 are shown in Table 1.

[0173] Table 1

[0174] Tensile Strength / MPa Yield Strength / MPa Elongation / % Example 1: 61159110.0 Example 2: 6135948.0 Example 3: 6175728.5 Example 4: 60259810.5 Example 5: 6186118.0 Example 6: 60956610.0 Example 7: 6376027.0 Comparative Example 1: 55354813.5 Comparative Example 2: 56153511.0 Comparative Example 3: 6696345.5 Comparative Example 4: 57855610.5

[0175] As can be seen from Examples 1 to 7, the aluminum alloy material for additive manufacturing provided in this disclosure can produce aluminum alloy parts without cracks or obvious defects. Furthermore, after heat treatment, the aluminum alloy parts exhibit excellent mechanical properties at room temperature. Specifically, the tensile strength of the heat-treated aluminum alloy parts at room temperature is above 600 MPa, the yield strength is above 560 MPa, and the elongation is above 7.0%.

[0176] As can be seen from Example 2 and Comparative Example 1, when the Mn content is insufficient, the tensile strength and yield strength of the heat-treated aluminum alloy parts at room temperature decrease. This is because insufficient Mn content leads to a reduction in solid solution strengthening effect, and the insufficient content of the Al6Mn phase formed in the Al matrix after heat treatment results in a weakened precipitation strengthening effect, which in turn leads to a decrease in the tensile strength and yield strength of the heat-treated aluminum alloy parts at room temperature.

[0177] As can be seen from Example 3 and Comparative Example 2, when the Zr content is insufficient, the tensile strength and yield strength of the heat-treated aluminum alloy parts at room temperature decrease. This is because when the Zr content is insufficient, the number of heterogeneous nucleation nuclei of the Al3Zr phase or Al3(Sc,Zr) composite phase decreases during the rapid solidification process of additive manufacturing, leading to a decrease in the number of fine equiaxed crystals and a weakening of the grain boundary strengthening effect. Furthermore, the insufficient number of Al3(Sc,Zr) composite phases and Al3(Sc,Zr) composite phases generated during heat treatment weakens the precipitation strengthening effect. The weakening of both grain boundary strengthening and precipitation strengthening effects results in reduced tensile strength and yield strength of the heat-treated aluminum alloy parts at room temperature.

[0178] As can be seen from Examples 4 and 3, when the Er content is too high, although the tensile strength and yield strength of the heat-treated aluminum alloy parts at room temperature are improved, their elongation decreases. This is because excessive Er leads to an increase in the amount of Al3Er eutectic phase, causing stress concentration at the Al3Er eutectic phase interface, which intensifies the stress concentration effect during the tensile process of the aluminum alloy parts, resulting in microcracks. Moreover, the Al3Er eutectic phase is prone to segregation at grain boundaries, weakening the grain boundary bonding force and inducing intergranular fracture, thereby reducing the plasticity of the aluminum alloy parts, which manifests as a decrease in elongation during the tensile process.

[0179] As can be seen from Example 1 and Comparative Example 4, when the aluminum alloy material used in additive manufacturing does not contain Cr, the tensile strength and yield strength of the heat-treated aluminum alloy parts decrease at room temperature. This is because Cr can form intermetallic compounds in the Al matrix, and these intermetallic compounds are mostly distributed along the grain boundaries, playing a role in grain boundary strengthening and second-phase strengthening. Therefore, when the aluminum alloy material used in additive manufacturing does not contain Cr, the grain boundary strengthening and second-phase strengthening effects are weakened, resulting in a decrease in the tensile strength and yield strength of the heat-treated aluminum alloy parts at room temperature.

[0180] It should be noted that the technical solutions described in this disclosure can be combined arbitrarily as long as they do not conflict.

[0181] The above description is merely a specific embodiment of this disclosure, but the scope of protection of this disclosure is not limited thereto. Any variations or substitutions that can be easily conceived by those skilled in the art within the scope of the technology disclosed in this disclosure should be included within the scope of protection of this disclosure. Therefore, the scope of protection of this disclosure should be determined by the scope of the claims.

Claims

1. An aluminum alloy material for additive manufacturing, characterized in that, The aluminum alloy material comprises, by weight percentage: Mn: greater than or equal to 0.50 wt.% and less than or equal to 6.00 wt.%; Mg: ≥0.50 wt.% and ≤4.00 wt.%; Er: Greater than or equal to 3.00 wt.% and less than or equal to 8.00 wt.%; Sc: Greater than or equal to 0.30 wt.% and less than or equal to 1.50 wt.%; Cr: ≥0.30 wt.% and ≤1.00 wt.%; Si: greater than or equal to 0.10 wt.% and less than or equal to 0.50 wt.%; Fe: ≥0.10 wt.% and ≤1.00 wt.%; Zr: greater than or equal to 0.50 wt.% and less than or equal to 3.00 wt.%; The balance consists of Al and unavoidable impurity elements.

2. The aluminum alloy material for additive manufacturing according to claim 1, characterized in that, By mass percentage, Mg: greater than or equal to 0.50 wt.% and less than or equal to 2.00 wt.%, and Mn: greater than or equal to 3.00 wt.% and less than or equal to 6.00 wt.%.

3. The aluminum alloy material for additive manufacturing according to claim 1, characterized in that, By mass percentage, Mg: greater than 2.00 wt.% and less than or equal to 4.00 wt.%, and Mn: greater than or equal to 0.50 wt.% and less than 3.00 wt.%.

4. The aluminum alloy material for additive manufacturing according to any one of claims 1 to 3, characterized in that, By mass percentage, Sc: greater than or equal to 0.30 wt.% and less than or equal to 0.60 wt.%, and Zr: greater than or equal to 1.50 wt.% and less than or equal to 3.00 wt.%; or, by mass percentage, Sc: greater than 0.60 wt.% and less than or equal to 1.50 wt.%, and Zr: greater than or equal to 0.50 wt.% and less than 1.50 wt.%.

5. The aluminum alloy material for additive manufacturing according to claim 1, characterized in that, The aluminum alloy material comprises at least one of the impurity elements by weight percentage, and the content of each impurity element is less than or equal to 0.05 wt.%.

6. The aluminum alloy material for additive manufacturing according to claim 1, characterized in that, The aluminum alloy material is a powder material, and the particle size of the powder in the powder material includes 15μm to 75μm.

7. The aluminum alloy material for additive manufacturing according to claim 1, characterized in that, The aluminum alloy material is a bar, wire, or filament.

8. A method for preparing an aluminum alloy material for additive manufacturing, characterized in that, The preparation method includes: The aluminum alloy material is prepared from metal raw materials in a predetermined ratio; wherein, by mass percentage, the metal raw materials include: Mn: greater than or equal to 0.50 wt.% and less than or equal to 6.00 wt.%; Mg: ≥0.50 wt.% and ≤4.00 wt.%; Er: Greater than or equal to 3.00 wt.% and less than or equal to 8.00 wt.%; Sc: Greater than or equal to 0.30 wt.% and less than or equal to 1.50 wt.%; Cr: ≥0.30 wt.% and ≤1.00 wt.%; Si: greater than or equal to 0.10 wt.% and less than or equal to 0.50 wt.%; Fe: ≥0.10 wt.% and ≤1.00 wt.%; Zr: greater than or equal to 0.50 wt.% and less than or equal to 3.00 wt.%; The balance consists of Al and unavoidable impurity elements.

9. An aluminum alloy part, characterized in that, The aluminum alloy part is obtained by additive manufacturing from the aluminum alloy material for additive manufacturing as described in any one of claims 1 to 7.

10. The aluminum alloy part according to claim 9, characterized in that, The aluminum alloy parts, after heat treatment, have a tensile strength greater than or equal to 600 MPa, a yield strength greater than or equal to 560 MPa, and an elongation greater than or equal to 7.0% at room temperature. The heat treatment includes: holding the aluminum alloy part at 250°C to 450°C for 2 to 8 hours, and cooling the aluminum alloy part in air.

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