WO2023019697A1 - High-strength aluminum alloy powder for 3d printing and preparation method for high-strength aluminum alloy powder - Google Patents
High-strength aluminum alloy powder for 3d printing and preparation method for high-strength aluminum alloy powder Download PDFInfo
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- 239000000843 powder Substances 0.000 title claims abstract description 49
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 39
- 238000002360 preparation method Methods 0.000 title claims abstract description 12
- 239000000956 alloy Substances 0.000 claims abstract description 33
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 29
- 238000010146 3D printing Methods 0.000 claims abstract description 18
- 238000000034 method Methods 0.000 claims abstract description 14
- 229910052751 metal Inorganic materials 0.000 claims abstract description 13
- 238000010438 heat treatment Methods 0.000 claims abstract description 11
- 238000002844 melting Methods 0.000 claims description 11
- 230000008018 melting Effects 0.000 claims description 11
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 10
- 239000002184 metal Substances 0.000 claims description 10
- 229910052786 argon Inorganic materials 0.000 claims description 5
- 238000009826 distribution Methods 0.000 claims description 5
- 239000011261 inert gas Substances 0.000 claims description 5
- 239000002994 raw material Substances 0.000 claims description 5
- 238000000889 atomisation Methods 0.000 claims description 4
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims description 3
- 239000001301 oxygen Substances 0.000 claims description 3
- 229910052760 oxygen Inorganic materials 0.000 claims description 3
- 239000002245 particle Substances 0.000 claims description 3
- 238000007711 solidification Methods 0.000 claims description 3
- 230000008023 solidification Effects 0.000 claims description 3
- 229910000914 Mn alloy Inorganic materials 0.000 claims 1
- 238000011010 flushing procedure Methods 0.000 claims 1
- 238000004519 manufacturing process Methods 0.000 abstract description 9
- 239000000654 additive Substances 0.000 abstract description 6
- 230000000996 additive effect Effects 0.000 abstract description 6
- 239000000463 material Substances 0.000 abstract description 6
- 239000000203 mixture Substances 0.000 abstract description 6
- 238000001556 precipitation Methods 0.000 abstract description 4
- 230000000694 effects Effects 0.000 abstract description 3
- 238000005728 strengthening Methods 0.000 abstract description 3
- 238000003723 Smelting Methods 0.000 description 5
- 229910000789 Aluminium-silicon alloy Inorganic materials 0.000 description 4
- 230000032683 aging Effects 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 4
- 238000005516 engineering process Methods 0.000 description 4
- 239000002244 precipitate Substances 0.000 description 4
- 239000012300 argon atmosphere Substances 0.000 description 3
- 238000001035 drying Methods 0.000 description 3
- 238000009689 gas atomisation Methods 0.000 description 3
- 239000012535 impurity Substances 0.000 description 3
- 239000007788 liquid Substances 0.000 description 3
- 239000012798 spherical particle Substances 0.000 description 3
- 239000002131 composite material Substances 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 230000000877 morphologic effect Effects 0.000 description 2
- 239000008188 pellet Substances 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 229910003407 AlSi10Mg Inorganic materials 0.000 description 1
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000004870 electrical engineering Methods 0.000 description 1
- 238000004806 packaging method and process Methods 0.000 description 1
- 230000002195 synergetic effect Effects 0.000 description 1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/20—Direct sintering or melting
- B22F10/28—Powder bed fusion, e.g. selective laser melting [SLM] or electron beam melting [EBM]
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y70/00—Materials specially adapted for additive manufacturing
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
- B22F2009/0824—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid with a specific atomising fluid
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
- B22F2009/0848—Melting process before atomisation
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Definitions
- the invention belongs to the technical field of special materials for additive manufacturing (also known as 3D printing), and in particular relates to a 3D printing high-strength aluminum alloy powder and a preparation method thereof.
- Additive manufacturing technology also known as 3D printing technology, quickly manufactures parts with extremely complex shapes and internal structures through the principle of "layer-by-layer manufacturing and layer-by-layer superposition", which saves a lot of materials and time compared with traditional subtractive manufacturing cost.
- SLM selective laser melting
- Aluminum and aluminum alloys are widely used in aerospace, transportation, mechanical construction, packaging, electrical engineering, etc. field has a wide range of applications.
- the most widely used aluminum alloys are mainly AlSi alloys, such as AlSi10Mg and AlSi12.
- AlSi alloy has good formability and no cracks under the SLM process, its mechanical properties are poor, the yield strength is generally lower than 300MPa, and the elongation is lower than 15%.
- Airbus Group has developed a Sc-Zr modified AlMg alloy, which not only can suppress cracks after forming, but also has a yield strength of over 400MPa and an elongation of over 10% after heat treatment.
- the price of Sc is too expensive, so that the price of AlMg alloy powder modified by Sc and Zr is much higher than that of AlSi alloy powder. Therefore, in terms of special materials for aluminum alloy additive manufacturing, there are common problems such as few types of materials that can be used, poor mechanical properties, and high prices.
- the present invention replaces Sc-Zr composite microalloying with Er-Zr composite microalloying, and adjusts the added Er, Zr
- the technical solution of the present invention provides a 3D printing high-strength aluminum alloy powder, mainly containing Mg, Er, Zr, Si, Mn elements, in terms of mass percentage, wherein Mg content is 3.0-8.0%, Er content is 0.1-1.2%, The content of Zr is 0.5-2.0%, the content of Mn is 0.3-1.0%, the content of Si is 0.01-2.0%, the total content of other unlisted metal elements except Al is not more than 0.5wt%, and the rest is Al.
- the aluminum alloy material includes the following components in mass fraction: Mg content is 3.0-8.0%, Er content is 0.3-0.5%, Zr content is 1.0-1.2%, Mn content is 0.5% ⁇ 0.8%, Si content is 0.01 ⁇ 0.1%, and the rest is Al.
- the aluminum alloy material includes the following components in mass fraction: Mg content is 3.0-8.0%, Er content is 0.5-0.8%, Zr content is 1.3-1.6%, Mn content is 0.5% ⁇ 0.8%, Si content is 0.01 ⁇ 0.1%, and the rest is Al.
- the aluminum alloy material includes the following components in mass fraction: Mg content 3.0-8.0%, Er content 0.3-0.5%, Zr content 1.0-1.2%, Mn content 0.5- 0.8%, the Si content is 1.0-1.6%, and the rest is Al.
- the aluminum alloy material includes the following components in mass fraction: Mg content 3.0-8.0%, Er content 0.5-0.8%, Zr content 1.3-1.6%, Mn content 0.5- 0.8%, the Si content is 1.0-1.6%, and the rest is Al.
- the present invention also provides a method for preparing the above-mentioned aluminum alloy, comprising the following steps:
- the atomization described in the preparation method is vacuum air atomization.
- the inert gas described in the preparation method is argon.
- the layer-by-layer melting and solidification forming described in the application method includes but is not limited to the selective laser melting (SLM) process.
- SLM selective laser melting
- the forming parameters used in the SLM process are: laser power 300-380W, scanning speed 800-1600mm/s, scanning distance 0.1-0.15mm, layer thickness 0.03-0.06mm;
- Benefits of the present invention adding a large amount of Zr element forms Al 3 Zr primary phase to refine grain size and suppresses solidification cracks; adding Er element forms grain boundary Al 3 Er phase, which can effectively prevent grain size coarsening during heat treatment;
- the addition of Si element can increase the diffusion rate of Er and Zr, promote the large amount of dispersed precipitation of Al 3 (Er, Zr) precipitate, and the Al 3 (Er, Zr) dispersed phase has a significant effect of precipitation strengthening. Therefore, after aging heat treatment, the yield strength exceeds 400MPa, the tensile strength exceeds 500MPa, and the elongation exceeds 10%. Its performance is better than that of AlSi alloy, and it is equivalent to that of Sc-Zr modified AlMg alloy.
- the invention expands the types of added elements for 3D printing AlMg alloy microalloying, solves the problems of easy cracking and poor performance of high-strength aluminum alloys, and significantly reduces the cost of high-strength aluminum alloys for 3D printing.
- Figure 1 is a morphological view of the 3D printed high-strength aluminum alloy powder prepared in Example 1 of the present invention.
- Fig. 2 is a SEM structure diagram of the 3D printed high-strength aluminum alloy prepared in Example 1 of the present invention.
- FIG. 3 is a SEM structure diagram of the 3D printed aluminum alloy prepared in Comparative Example 1 of the present invention.
- the percentages in the present invention are percentages by mass, and the aluminum alloy composition adopts the general expression in this field, for example, the aluminum alloy composition of Al-6.0Mg-0.7Mn-0.4Er-1.2Zr is: 6.0%Mg, 0.7 %Mn, 0.4% Er, 1.2% Zr, and the rest are Al.
- the melting composition in a vacuum furnace is Al-6.0Mg-0.7Mn-0.4Er-1.2Zr, and the content of other impurity elements is controlled to be less than 0.1%.
- the aluminum alloy prepared by the above method suppresses internal cracks (as shown in Figure 2) and refines the grain size through the addition of a large amount of Zr elements, and the average grain size is only 3.3um.
- the recrystallization and grain growth stabilized the grain size, and after 10 hours of heat treatment at 375 degrees, a large amount of Al 3 (Er, Zr) precipitated phase was precipitated, which greatly improved the strength of the sample.
- the mechanical properties is tested, the yield strength is 430MPa, the tensile strength is 500MPa, and the elongation is 20%.
- the smelting composition in a vacuum furnace is Al-4.0Mg-0.7Mn-0.8Er-1.5Zr-1.6Si, and the content of other impurity elements is controlled to be less than 0.1%.
- the aluminum alloy prepared by the above method suppresses internal cracks and refines the grain size through the addition of a large amount of Zr elements.
- the average grain size is about 2.0um, and the Er element inhibits recrystallization and grain growth during heat treatment.
- the mechanical properties is tested, the yield strength is 480MPa, the tensile strength is 530MPa, and the elongation is 12%.
- the smelting composition in a vacuum furnace is Al-5.0Mg-0.7Mn-0.4Er-0.3Zr, and the content of other impurity elements is controlled to be less than 0.1%.
- the Zr element content of the aluminum alloy in the comparative example is not within the claims of the present invention, and a large number of cracks (as shown in Figure 3 ) have occurred inside the formed sample and the grain size is coarse, with an average grain size of 12um; the sample formed before aging The morphological hardness is 115HV, and the hardness of 122HV after peak aging has not increased significantly, which means that the number of precipitated phases is small and there is no significant precipitation strengthening effect; the mechanical properties are tested according to the GB/T 228.1-2010 standard. Due to the existence of cracks, the yield The strength is only 170MPa, the tensile strength is 210MPa, and the elongation is 2%.
Abstract
A high-strength aluminum alloy powder for 3D printing and a preparation method for the high-strength aluminum alloy powder, relating to the technical field of special materials for additive manufacturing (also known as 3D printing). The compositions of the alloy are calculated according to a mass percentage: 3.0%-8.0% of Mg, 0.1%-1.2% of Er, 0.5%-2.0% of Zr, 0.3%-1.0% of Mn, 0.01%-2.0% of Si, the total content of the other unlisted metal elements except Al not exceeding 0.5wt%, the balance of Al. The high-strength aluminum alloy powder can effectively inhibit cracks of an AlMg alloy in the 3D printing process and has the remarkable fine grain and precipitation strengthening effect, the yield strength exceeds 400 MPa after heat treatment, the tensile strength exceeds 500 MPa, and the elongation percentage exceeds 10%. The aluminum alloy powder effectively solves the problems that the AlMg alloy is low in strength and poor in formability.
Description
本发明属于增材制造(又称3D打印)专用材料技术领域,具体涉及一种3D打印高强铝合金粉及其制备方法。The invention belongs to the technical field of special materials for additive manufacturing (also known as 3D printing), and in particular relates to a 3D printing high-strength aluminum alloy powder and a preparation method thereof.
增材制造技术又被称之为3D打印技术,通过“分层制造、逐层叠加”的原理快速制造出形状和内部结构极其复杂的零件,相比传统的减材制造大量节约了材料和时间成本。在金属3D打印领域,选区激光熔化成形(SLM)技术是应用和研究最为广泛的一种激光增材制造技术。铝及铝合金以其密度小,比强度和比刚度高,优异的成型性、焊接性和耐蚀性,良好的导电导热性能等优点在航空航天、交通运输、机械建筑、包装、电子电工等领域具有广泛的应用。但是在增材制造专用材料领域,目前应用最广泛的铝合金主要为AlSi合金,如AlSi10Mg,AlSi12。AlSi合金在SLM工艺下虽然成形性好,无裂纹,但是力学性能较差,屈服强度一般低于300MPa,延伸率低于15%。空客集团开发了Sc-Zr改性的AlMg合金,该合金成形后不但能够抑制裂纹,而且热处理后屈服强度超过400MPa,延伸率超过10%。但是Sc的价格过于昂贵导致Sc、Zr改性的AlMg合金粉末价格远高于AlSi合金粉末。因此在铝合金增材制造专用材料方面,面临着可使用的材料种类少,力学性能差,价格昂贵等普遍问题。Additive manufacturing technology, also known as 3D printing technology, quickly manufactures parts with extremely complex shapes and internal structures through the principle of "layer-by-layer manufacturing and layer-by-layer superposition", which saves a lot of materials and time compared with traditional subtractive manufacturing cost. In the field of metal 3D printing, selective laser melting (SLM) technology is the most widely used and researched laser additive manufacturing technology. Aluminum and aluminum alloys are widely used in aerospace, transportation, mechanical construction, packaging, electrical engineering, etc. field has a wide range of applications. However, in the field of special materials for additive manufacturing, the most widely used aluminum alloys are mainly AlSi alloys, such as AlSi10Mg and AlSi12. Although the AlSi alloy has good formability and no cracks under the SLM process, its mechanical properties are poor, the yield strength is generally lower than 300MPa, and the elongation is lower than 15%. Airbus Group has developed a Sc-Zr modified AlMg alloy, which not only can suppress cracks after forming, but also has a yield strength of over 400MPa and an elongation of over 10% after heat treatment. However, the price of Sc is too expensive, so that the price of AlMg alloy powder modified by Sc and Zr is much higher than that of AlSi alloy powder. Therefore, in terms of special materials for aluminum alloy additive manufacturing, there are common problems such as few types of materials that can be used, poor mechanical properties, and high prices.
发明内容Contents of the invention
为解决高强铝合金在3D打印过程中易开裂,合金元素添加种类单一、价格昂贵的问题,本发明通过Er-Zr复合微合金化替代Sc-Zr复合微合金化,通过调整添加的Er、Zr元素含量的比例关系,通过大量Zr元素的添加,抑制了AlMg合金的裂纹,又重点发挥Er-Zr的协同作用,显著的提升合金强度。由于Er的价格远低于Sc,显著的降低了3D打印用的高强铝合金粉末成本。In order to solve the problem that the high-strength aluminum alloy is easy to crack during the 3D printing process, the addition of alloy elements is single and expensive, the present invention replaces Sc-Zr composite microalloying with Er-Zr composite microalloying, and adjusts the added Er, Zr The proportional relationship of the element content, through the addition of a large amount of Zr elements, suppresses the cracks of the AlMg alloy, and focuses on the synergistic effect of Er-Zr to significantly improve the strength of the alloy. Since the price of Er is much lower than that of Sc, the cost of high-strength aluminum alloy powder for 3D printing is significantly reduced.
本发明的技术方案提供了一种3D打印高强铝合金粉末,主要包含Mg、Er、Zr、Si、Mn元素,以质量百分比计,其中Mg含量3.0~8.0%、Er含量为0.1~1.2%、Zr含量为0.5~2.0%、Mn含量为0.3~1.0%,Si含量为0.01~2.0%,除Al外其他未列出的金属元素总含量不超过0.5wt%,剩余为Al。The technical solution of the present invention provides a 3D printing high-strength aluminum alloy powder, mainly containing Mg, Er, Zr, Si, Mn elements, in terms of mass percentage, wherein Mg content is 3.0-8.0%, Er content is 0.1-1.2%, The content of Zr is 0.5-2.0%, the content of Mn is 0.3-1.0%, the content of Si is 0.01-2.0%, the total content of other unlisted metal elements except Al is not more than 0.5wt%, and the rest is Al.
作为本发明的实施方式之一,所述铝合金材料,包括如下质量分数的成分:Mg含量为3.0~8.0%、Er含量为0.3~0.5%、Zr含量为1.0~1.2%、Mn含量为0.5~0.8%、Si含量为0.01~0.1%,其余为Al。As one of the embodiments of the present invention, the aluminum alloy material includes the following components in mass fraction: Mg content is 3.0-8.0%, Er content is 0.3-0.5%, Zr content is 1.0-1.2%, Mn content is 0.5% ~0.8%, Si content is 0.01~0.1%, and the rest is Al.
作为本发明的实施方式之一,所述铝合金材料,包括如下质量分数的成分:Mg含量为3.0~8.0%、Er含量为0.5~0.8%、Zr含量为1.3~1.6%、Mn含量为0.5~0.8%、Si含量为0.01~0.1%,其余为Al。As one of the embodiments of the present invention, the aluminum alloy material includes the following components in mass fraction: Mg content is 3.0-8.0%, Er content is 0.5-0.8%, Zr content is 1.3-1.6%, Mn content is 0.5% ~0.8%, Si content is 0.01~0.1%, and the rest is Al.
作为本发明的实施方式之一,所述铝合金材料,包括如下质量分数的成分:Mg含量3.0~8.0%、Er含量为0.3~0.5%、Zr含量为1.0~1.2%、Mn含量为0.5~0.8%、Si含量为1.0~1.6%,其余为Al。As one of the embodiments of the present invention, the aluminum alloy material includes the following components in mass fraction: Mg content 3.0-8.0%, Er content 0.3-0.5%, Zr content 1.0-1.2%, Mn content 0.5- 0.8%, the Si content is 1.0-1.6%, and the rest is Al.
作为本发明的实施方式之一,所述铝合金材料,包括如下质量分数的成分:Mg含量3.0~8.0%,Er含量为0.5~0.8%、Zr含量为1.3~1.6%、Mn含量为0.5~0.8%、Si含量为1.0~1.6%,其余为Al。As one of the embodiments of the present invention, the aluminum alloy material includes the following components in mass fraction: Mg content 3.0-8.0%, Er content 0.5-0.8%, Zr content 1.3-1.6%, Mn content 0.5- 0.8%, the Si content is 1.0-1.6%, and the rest is Al.
本发明还提供了上述铝合金的制备方法,包括如下步骤:The present invention also provides a method for preparing the above-mentioned aluminum alloy, comprising the following steps:
(1)以纯金属/中间合金为原料进行配料;(1) Carry out batching with pure metal/master alloy as raw material;
(2)将原料进行加热熔化以及雾化制粉;(2) heating and melting raw materials and atomizing powder;
(3)将收得的金属粉末进行干燥,经分级后得到粒径分布为15-63μm的粉末。(3) Dry the collected metal powder, and obtain powder with a particle size distribution of 15-63 μm after classification.
(4)对金属粉末进行筛粉,在真空烘干箱中进行烘干,倒入3D打印设备的供粉室中并冲入惰性气体将氧含量降至0.1%以下。(4) Sieve the metal powder, dry it in a vacuum oven, pour it into the powder supply chamber of the 3D printing equipment and flush it with an inert gas to reduce the oxygen content to below 0.1%.
应用方法:Application method:
设计需要打印的零件模型,对三维模型进行添加支撑、切片,3D打印设备采用优化的成形参数对三维数字模型进行逐层熔化凝固成形。Design the part model that needs to be printed, add supports and slices to the 3D model, and the 3D printing equipment uses optimized forming parameters to melt and solidify the 3D digital model layer by layer.
制备方法中所述的所述雾化为真空气雾化。The atomization described in the preparation method is vacuum air atomization.
制备方法中所述的惰性气体为氩气。The inert gas described in the preparation method is argon.
应用方法中所述的逐层熔化凝固成形包括但不局限于选区激光熔化(SLM)工艺。其中SLM工艺采用的成形参数为:激光功率300-380W,扫描速度800-1600mm/s,扫描间距0.1-0.15mm,层厚为0.03-0.06mm;The layer-by-layer melting and solidification forming described in the application method includes but is not limited to the selective laser melting (SLM) process. The forming parameters used in the SLM process are: laser power 300-380W, scanning speed 800-1600mm/s, scanning distance 0.1-0.15mm, layer thickness 0.03-0.06mm;
本发明的益处:添加大量的Zr元素形成Al
3Zr初生相去细化晶粒尺寸,抑制凝固裂纹;添加Er元素形成晶界Al
3Er相,可以有效阻止热处理过程中晶粒尺寸的粗化;添加Si元素能够增加了Er和Zr的扩散速率,促进Al
3(Er,Zr)沉 淀相大量弥散析出,Al
3(Er,Zr)弥散相起到显著的沉淀强化的效果。因此时效热处理后屈服强度超过400MPa,抗拉强度超过500MPa,延伸率超过10%。性能上优于AlSi合金,与Sc-Zr改性的AlMg合金性能相当。但是比Sc-Zr改性的高强铝合金粉末在原材料成本上降低了30万(每吨)。本发明扩展了3D打印AlMg合金微合金化添加元素的种类,解决了高强铝合金易开裂,性能差的问题,显著的降低了3D打印用高强铝合金的成本。
Benefits of the present invention: adding a large amount of Zr element forms Al 3 Zr primary phase to refine grain size and suppresses solidification cracks; adding Er element forms grain boundary Al 3 Er phase, which can effectively prevent grain size coarsening during heat treatment; The addition of Si element can increase the diffusion rate of Er and Zr, promote the large amount of dispersed precipitation of Al 3 (Er, Zr) precipitate, and the Al 3 (Er, Zr) dispersed phase has a significant effect of precipitation strengthening. Therefore, after aging heat treatment, the yield strength exceeds 400MPa, the tensile strength exceeds 500MPa, and the elongation exceeds 10%. Its performance is better than that of AlSi alloy, and it is equivalent to that of Sc-Zr modified AlMg alloy. However, compared with Sc-Zr modified high-strength aluminum alloy powder, the cost of raw materials is reduced by 300,000 (per ton). The invention expands the types of added elements for 3D printing AlMg alloy microalloying, solves the problems of easy cracking and poor performance of high-strength aluminum alloys, and significantly reduces the cost of high-strength aluminum alloys for 3D printing.
图1为本发明实施例1制备的3D打印高强铝合金粉末形貌图。Figure 1 is a morphological view of the 3D printed high-strength aluminum alloy powder prepared in Example 1 of the present invention.
图2为本发明实施例1制备的3D打印高强铝合金SEM组织图。Fig. 2 is a SEM structure diagram of the 3D printed high-strength aluminum alloy prepared in Example 1 of the present invention.
图3为本发明对比例1制备的3D打印铝合金SEM组织图。FIG. 3 is a SEM structure diagram of the 3D printed aluminum alloy prepared in Comparative Example 1 of the present invention.
下面结合实施例和对比例对本发明作进一步说明,此处所采用的实施例是指本发明存在至少一个实现方式,但是本发明还可以采用不同于此实施例的其他方式来实现,因此本发明不受下面公开具体实施例的限制。The present invention will be further described below in conjunction with embodiment and comparative example, the embodiment adopted herein refers to that the present invention has at least one implementation mode, but the present invention can also be realized in other ways different from this embodiment, so the present invention does not Be limited by the specific examples disclosed below.
除特别说明外,本发明的百分数均为质量百分数,铝合金成分采用本领域的通用表达式,例如Al-6.0Mg-0.7Mn-0.4Er-1.2Zr的铝合金成分为:6.0%Mg、0.7%Mn、0.4%Er、1.2%Zr、其余为Al。Unless otherwise specified, the percentages in the present invention are percentages by mass, and the aluminum alloy composition adopts the general expression in this field, for example, the aluminum alloy composition of Al-6.0Mg-0.7Mn-0.4Er-1.2Zr is: 6.0%Mg, 0.7 %Mn, 0.4% Er, 1.2% Zr, and the rest are Al.
实施例1Example 1
在真空炉中熔炼成分为Al-6.0Mg-0.7Mn-0.4Er-1.2Zr,控制其他杂质元素含量小于0.1%。The melting composition in a vacuum furnace is Al-6.0Mg-0.7Mn-0.4Er-1.2Zr, and the content of other impurity elements is controlled to be less than 0.1%.
上述合金粉末的制备方法:The preparation method of above-mentioned alloy powder:
(1)选用纯Al、纯Mg、Al-5.0%Er中间合金、Al-10.0%Zr中间合金,Al-20.0%Mn中间合金,按照一定配比放入坩埚中先抽真空后充入高纯氩气进行熔炼,待充分熔化后在800-840度温度区间以及氩气氛围下进行气雾化制粉,待液体被粉碎成球形颗粒并冷却后对粉末进行收集和筛粉,最后收得粒径分布在15-63μm之间的粉末(如图1所示)。(1) Select pure Al, pure Mg, Al-5.0% Er master alloy, Al-10.0% Zr master alloy, Al-20.0% Mn master alloy, put them into the crucible according to a certain ratio, first vacuumize and then fill with high-purity Argon is used for smelting. After fully melting, gas atomization powder is carried out in the temperature range of 800-840 degrees and under argon atmosphere. After the liquid is crushed into spherical particles and cooled, the powder is collected and sieved, and finally the pellets are collected. Powder with diameter distribution between 15-63μm (as shown in Figure 1).
(2)将粉末在100目的筛网下过筛,并放在真空干燥箱内进行80度6小时烘干处理。(2) Sieve the powder under a 100-mesh sieve, and place it in a vacuum oven for drying at 80°C for 6 hours.
(3)设计标准拉伸试样的三维模型,并进行分层切片。采用SLM Solution M280金属打印机,预热温度150度,成形的激光功率350W,扫描速度1000mm/s,扫描间距0.13mm,层厚0.03mm的参数成形标准拉伸试样,成形后对拉伸试样进行375度保温10小时热处理。(3) Design the three-dimensional model of the standard tensile specimen, and perform layered slices. Using the SLM Solution M280 metal printer, the preheating temperature is 150 degrees, the forming laser power is 350W, the scanning speed is 1000mm/s, the scanning distance is 0.13mm, and the layer thickness is 0.03mm. Carry out heat treatment at 375 degrees for 10 hours.
通过上述方法制备的铝合金通过大量的Zr元素的添加,抑制了内部裂纹(如图2所示),细化了晶粒尺寸,平均晶粒尺寸仅为3.3um,Er元素抑制了热处理过程中的再结晶和晶粒长大,稳定了晶粒尺寸,经过375度10小时热处理后析出大量的Al
3(Er,Zr)沉淀相大幅提高了试样的强度。按照GB/T 228.1-2010标准进行力学性能检测,屈服强度430MPa,抗拉强度500MPa,延伸率20%。
The aluminum alloy prepared by the above method suppresses internal cracks (as shown in Figure 2) and refines the grain size through the addition of a large amount of Zr elements, and the average grain size is only 3.3um. The recrystallization and grain growth stabilized the grain size, and after 10 hours of heat treatment at 375 degrees, a large amount of Al 3 (Er, Zr) precipitated phase was precipitated, which greatly improved the strength of the sample. According to the GB/T 228.1-2010 standard, the mechanical properties are tested, the yield strength is 430MPa, the tensile strength is 500MPa, and the elongation is 20%.
实施例2Example 2
在真空炉中熔炼成分为Al-4.0Mg-0.7Mn-0.8Er-1.5Zr-1.6Si,控制其他杂质元素含量小于0.1%。The smelting composition in a vacuum furnace is Al-4.0Mg-0.7Mn-0.8Er-1.5Zr-1.6Si, and the content of other impurity elements is controlled to be less than 0.1%.
上述合金粉末的制备方法:The preparation method of above-mentioned alloy powder:
(1)选用纯Al、纯Mg、Al-5.0%Er中间合金、Al-10.0%Zr中间合金,Al-20.0%Mn中间合金和Al-21.0Si中间合金,按照一定配比放入坩埚中先抽真空后充入高纯氩气进行熔炼,待充分熔化后在800-820度温度区间、氩气氛围下进行气雾化制粉,待液体被粉碎成球形颗粒并冷却后对粉末进行收集和筛粉,最后收得粒径分布在15-63um之间的粉末。(1) Select pure Al, pure Mg, Al-5.0% Er master alloy, Al-10.0% Zr master alloy, Al-20.0% Mn master alloy and Al-21.0Si master alloy, put them into the crucible according to a certain ratio After vacuuming, fill it with high-purity argon for smelting. After fully melting, carry out gas atomization powder production in the temperature range of 800-820 degrees under an argon atmosphere. After the liquid is crushed into spherical particles and cooled, the powder is collected and processed. Sieve the powder, and finally collect the powder with particle size distribution between 15-63um.
(2)将粉末在100目的筛网下过筛,并放在真空干燥箱内进行80度6小时烘干处理。(2) Sieve the powder under a 100-mesh sieve, and place it in a vacuum oven for drying at 80°C for 6 hours.
(3)设计标准拉伸试样的三维模型,并进行分层切片。采用SLM Solution M280金属打印机,预热温度200度,成形的激光功率380W,扫描速度1250mm/s,扫描间距0.13mm,层厚0.03mm的参数成形标准拉伸试样,成形后对拉伸试样进行350度保温8小时热处理。(3) Design the three-dimensional model of the standard tensile specimen, and perform layered slices. Using SLM Solution M280 metal printer, the preheating temperature is 200 degrees, the forming laser power is 380W, the scanning speed is 1250mm/s, the scanning distance is 0.13mm, and the layer thickness is 0.03mm. Carry out heat treatment at 350 degrees for 8 hours.
通过上述方法制备的铝合金通过大量的Zr元素的添加,抑制了内部裂纹,细化了晶粒尺寸,平均晶粒尺寸约为2.0um,Er元素抑制了热处理过程中的再结晶和晶粒长大,稳定了晶粒尺寸;Si加速了Er和Zr元素的扩散速率,增加了Al
3(Er,Zr)沉淀相的数量,并且时效过程中析出Mg
2Si沉淀相,提高了试样的强度,按照GB/T 228.1-2010标准进行力学性能检测,屈服强度480MPa,抗拉强度530MPa,延伸率12%。
The aluminum alloy prepared by the above method suppresses internal cracks and refines the grain size through the addition of a large amount of Zr elements. The average grain size is about 2.0um, and the Er element inhibits recrystallization and grain growth during heat treatment. Large, stable grain size; Si accelerates the diffusion rate of Er and Zr elements, increases the number of Al 3 (Er, Zr) precipitates, and precipitates Mg 2 Si precipitates during the aging process, improving the strength of the sample According to the GB/T 228.1-2010 standard, the mechanical properties are tested, the yield strength is 480MPa, the tensile strength is 530MPa, and the elongation is 12%.
对比例1Comparative example 1
在真空炉中熔炼成分为Al-5.0Mg-0.7Mn-0.4Er-0.3Zr,控制其他杂质元素含量小于0.1%。The smelting composition in a vacuum furnace is Al-5.0Mg-0.7Mn-0.4Er-0.3Zr, and the content of other impurity elements is controlled to be less than 0.1%.
上述合金粉末的制备方法:The preparation method of above-mentioned alloy powder:
(1)选用纯Al、纯Mg、Al-5.0%Er中间合金、Al-10.0%Zr中间合金,Al-20.0%Mn中间合金,按照一定配比放入坩埚中先抽真空后充入高纯氩气进行熔炼,待充分熔化后在800-840度温度区间、氩气氛围下进行气雾化制粉,待液体被粉碎成球形颗粒并冷却后对粉末进行收集和筛粉,最后收得粒径分布在15-63um之间的粉末。(1) Select pure Al, pure Mg, Al-5.0% Er master alloy, Al-10.0% Zr master alloy, Al-20.0% Mn master alloy, put them into the crucible according to a certain ratio, first vacuumize and then fill with high-purity Argon is used for smelting. After fully melting, gas atomization powder is carried out in the temperature range of 800-840 degrees under an argon atmosphere. After the liquid is crushed into spherical particles and cooled, the powder is collected and sieved, and finally the pellets are collected. Powder with diameter distribution between 15-63um.
(2)将粉末在100目的筛网下过筛,并放在真空干燥箱内进行80度6小时烘干处理。(2) Sieve the powder under a 100-mesh sieve, and place it in a vacuum oven for drying at 80°C for 6 hours.
(3)设计标准拉伸试样的三维模型,并进行分层切片。采用SLM Solution M280金属打印机,预热温度200度,成形的激光功率350W,扫描速度1200mm/s,扫描间距0.13mm,层厚0.03mm的参数成形标准拉伸试样,成形后对拉伸试样进行375度保温10小时热处理。(3) Design the three-dimensional model of the standard tensile specimen, and perform layered slices. Using the SLM Solution M280 metal printer, the preheating temperature is 200 degrees, the forming laser power is 350W, the scanning speed is 1200mm/s, the scanning distance is 0.13mm, and the layer thickness is 0.03mm. Carry out heat treatment at 375 degrees for 10 hours.
对比例中的铝合金Zr元素含量不在本发明的权利要求内,成形试样内部产生了大量裂纹(如图3所示)并且晶粒尺寸粗大,平均晶粒尺寸为12um;时效前试样成形态硬度115HV,峰时效后硬度122HV并没有大幅提高,这意味着析出的沉淀相数量少,无显著的沉淀强化效果;按照GB/T 228.1-2010标准进行力学性能检测,由于裂纹的存在,屈服强度仅为170MPa,抗拉强度210MPa,延伸率2%。The Zr element content of the aluminum alloy in the comparative example is not within the claims of the present invention, and a large number of cracks (as shown in Figure 3 ) have occurred inside the formed sample and the grain size is coarse, with an average grain size of 12um; the sample formed before aging The morphological hardness is 115HV, and the hardness of 122HV after peak aging has not increased significantly, which means that the number of precipitated phases is small and there is no significant precipitation strengthening effect; the mechanical properties are tested according to the GB/T 228.1-2010 standard. Due to the existence of cracks, the yield The strength is only 170MPa, the tensile strength is 210MPa, and the elongation is 2%.
Claims (7)
- 一种用于3D打印的高强铝合金粉末,其特征在于,所述的铝合金粉末主要包括Mg、Er、Zr、Si、Mn合金元素,以质量百分比计,Mg的含量3.0~8.0%、Er含量为0.1~1.2%、Zr含量为0.5~2.0%、Mn含量为0.3~1.0%,Si含量为0.01~2.0%,除Al外其他未列出的金属元素总含量不超过0.5wt%,剩余为Al。A high-strength aluminum alloy powder for 3D printing, characterized in that the aluminum alloy powder mainly includes Mg, Er, Zr, Si, Mn alloy elements, and the content of Mg is 3.0-8.0%, Er The content of Zr is 0.1-1.2%, the content of Zr is 0.5-2.0%, the content of Mn is 0.3-1.0%, the content of Si is 0.01-2.0%, and the total content of other unlisted metal elements except Al is not more than 0.5wt%. for Al.
- 如权利要求1所述的铝合金粉末,其特征在于,包括如下质量分数的成分:Mg含量为3.0~8.0%、Er含量为0.3~0.5%、Zr含量为1.0~1.2%、Mn含量为0.5~0.8%、Si含量为0.01~0.1%,其余为Al;The aluminum alloy powder according to claim 1, characterized in that it comprises the following components in mass fraction: Mg content is 3.0-8.0%, Er content is 0.3-0.5%, Zr content is 1.0-1.2%, Mn content is 0.5% ~0.8%, Si content is 0.01~0.1%, the rest is Al;或所述铝合金粉末,包括如下质量分数的成分:Mg含量为3.0~8.0%、Er含量为0.5~0.8%、Zr含量为1.3~1.6%、Mn含量为0.5~0.8%、Si含量为0.01~0.1%,其余为Al;Or the aluminum alloy powder includes the following components in mass fraction: Mg content is 3.0-8.0%, Er content is 0.5-0.8%, Zr content is 1.3-1.6%, Mn content is 0.5-0.8%, Si content is 0.01% ~0.1%, the rest is Al;或所述的铝合金粉末,包括如下质量分数的成分:Mg含量3.0~8.0%、Er含量为0.3~0.5%、Zr含量为1.0~1.2%、Mn含量为0.5~0.8%、Si含量为1.0~1.6%,其余为Al;Or the aluminum alloy powder includes the following components in mass fraction: Mg content 3.0-8.0%, Er content 0.3-0.5%, Zr content 1.0-1.2%, Mn content 0.5-0.8%, Si content 1.0% ~1.6%, the rest is Al;或所述的铝合金粉末,包括如下质量分数的成分:Mg含量3.0~8.0%,Er含量为0.5~0.8%、Zr含量为1.3~1.6%、Mn含量为0.5~0.8%、Si含量为1.0~1.6%,其余为Al。Or the aluminum alloy powder includes the following components in mass fraction: Mg content 3.0-8.0%, Er content 0.5-0.8%, Zr content 1.3-1.6%, Mn content 0.5-0.8%, Si content 1.0% ~1.6%, the rest is Al.
- 权利要求1或2所述的铝合金粉末的制备方法,其特征在于,包括如下步骤:The preparation method of aluminum alloy powder described in claim 1 or 2, is characterized in that, comprises the steps:(1)以纯金属/中间合金为原料进行配料;(1) Carry out batching with pure metal/master alloy as raw material;(2)将原料进行加热熔化以及雾化制粉;(2) heating and melting raw materials and atomizing powder;(3)将收得的金属粉末进行干燥,经分级后得到粒径分布为15-63μm的粉末。(3) Dry the collected metal powder, and obtain powder with a particle size distribution of 15-63 μm after classification.(4)对金属粉末进行筛粉,在真空烘干箱中进行烘干,倒入3D打印设备的供粉室中并冲入惰性气体将氧含量降至0.1%以下。(4) Sieve the metal powder, dry it in a vacuum oven, pour it into the powder supply chamber of the 3D printing equipment and flush it with an inert gas to reduce the oxygen content to below 0.1%.
- 如权利要求3所述的制备方法,其特征在于,所述雾化为真空气雾化。The preparation method according to claim 3, characterized in that the atomization is vacuum air atomization.
- 如权利要求3所述的制备方法,其特征在于,所述的惰性气体为氩气。The preparation method according to claim 3, wherein the inert gas is argon.
- 权利要求1或2所述的铝合金粉末的应用方法,其特征在于,铝合金粉末倒入3D打印设备的供粉室中并冲入惰性气体将氧含量降至0.1%以下后,设计需要打印的零件模型,对三维模型进行添加支撑、切片,3D打印设备采用优化的成形参数对三维数字模型进行逐层熔化凝固成形。The application method of aluminum alloy powder according to claim 1 or 2, characterized in that, after pouring the aluminum alloy powder into the powder supply chamber of the 3D printing equipment and flushing the inert gas to reduce the oxygen content to below 0.1%, the design needs to be printed 3D printing equipment uses optimized forming parameters to melt and solidify the 3D digital model layer by layer.
- 如权利要求6所述的制备方法,其特征在于逐层熔化凝固成形包括但不局限于选区激光熔化(SLM)工艺;其中SLM工艺采用的成形参数为:激光功率300-380W,扫描速度800-1600mm/s,扫描间距0.1-0.15mm,层厚为0.03-0.06mm。The preparation method according to claim 6, wherein the layer-by-layer melting and solidification forming includes but is not limited to the selective laser melting (SLM) process; wherein the forming parameters used in the SLM process are: laser power 300-380W, scanning speed 800- 1600mm/s, scanning distance 0.1-0.15mm, layer thickness 0.03-0.06mm.
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