WO2023019697A1 - 一种用于3d打印的高强铝合金粉及其制备方法 - Google Patents

一种用于3d打印的高强铝合金粉及其制备方法 Download PDF

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WO2023019697A1
WO2023019697A1 PCT/CN2021/121982 CN2021121982W WO2023019697A1 WO 2023019697 A1 WO2023019697 A1 WO 2023019697A1 CN 2021121982 W CN2021121982 W CN 2021121982W WO 2023019697 A1 WO2023019697 A1 WO 2023019697A1
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aluminum alloy
alloy powder
powder
preparation
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French (fr)
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聂祚仁
郭彦梧
黄晖
魏午
文胜平
高坤元
吴晓蓝
荣莉
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北京工业大学
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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]
    • 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
    • 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
    • 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
    • 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
    • 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%.

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Abstract

一种用于3D打印的高强铝合金粉及其制备方法，属于增材制造(又称3D打印)专用材料技术领域。按照质量百分比计算，该合金的成分为：Mg：3.0～8.0％、Er：0.1～1.2％，Zr：0.5～2.0％、Mn：0.3～1.0％、Si：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。所述的高强铝合金粉能够有效抑制AlMg合金3D打印过程中的裂纹，并且具有显著的细晶和沉淀强化效果，热处理后屈服强度超过400MPa，抗拉强度超过500MPa，延伸率超过10％，该铝合金粉末有效解决了AlMg合金强度低，成形性差的问题。

Description

一种用于3D打印的高强铝合金粉及其制备方法 技术领域
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。
背景技术
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。
发明内容
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。
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。
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。
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。
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。
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。
本发明还提供了上述铝合金的制备方法，包括如下步骤：
(1)以纯金属/中间合金为原料进行配料；
(2)将原料进行加热熔化以及雾化制粉；
(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。
(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。
应用方法：
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。
制备方法中所述的所述雾化为真空气雾化。
制备方法中所述的惰性气体为氩气。
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；
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。
附图说明
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。
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。
图3为本发明对比例1制备的3D打印铝合金SEM组织图。
具体实施方式
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。
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。
实施例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％。
上述合金粉末的制备方法：
(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)。
(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。
(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。
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％。
实施例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％。
上述合金粉末的制备方法：
(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。
(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。
(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。
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％。
对比例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％。
上述合金粉末的制备方法：
(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。
(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。
(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。
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％。

Claims (7)

  1. 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。
  2. 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；
    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；
    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；
    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。
  3. 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：
    (1)以纯金属/中间合金为原料进行配料；
    (2)将原料进行加热熔化以及雾化制粉；
    (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。
    (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. 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。
  5. 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。
  6. 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。
  7. 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。
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