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Article(id=1240631877099385680, tenantId=1146029695717560320, journalId=1235980550691926019, issueId=1240631872800215183, articleNumber=null, orderNo=null, doi=10.3969/j.issn.0253-6099.2025.01.031, pmid=null, cstr=null, oa=null, hot=null, price=null, onlineType=0, articleFormat=0, articleType=null, articleTypeStr=null, receivedDate=1726070400000, receivedDateStr=2024-09-12, revisedDate=null, revisedDateStr=null, acceptedDate=null, acceptedDateStr=null, onlineDate=1773719289325, onlineDateStr=2026-03-17, pubDate=1738339200000, pubDateStr=2025-02-01, doiRegisterDate=null, doiRegisterDateStr=null, onlineIssueDate=1773719289325, onlineIssueDateStr=2026-03-17, onlineJustAcceptDate=null, onlineJustAcceptDateStr=null, onlineFirstDate=null, onlineFirstDateStr=null, sourceXml=null, magXml=null, createTime=1773719289325, creator=13701087609, updateTime=1773719289325, updator=13701087609, issue=Issue{id=1240631872800215183, tenantId=1146029695717560320, journalId=1235980550691926019, year='2025', volume='45', issue='1', pageStart='1', pageEnd='187', issueExtLink='null', onlineDate='null', pubDate='null', beforeIssueId=null, nextIssueId=null, price=null, status=1, issueComplete=1, articleOrder=1, issueType=-1, specialIssue=null, createTime=1773719288300, creator=13701087609, updateTime=1773724138257, updator=13701087609, preIssue=null, nextIssue=null, ext={EN=IssueExt(id=1240652215052989235, tenantId=1146029695717560320, journalId=1235980550691926019, issueId=1240631872800215183, language=EN, specialIssueTitle=, coverIllustrator=null, specialIssueEditor=, specialIssueAbout=), CN=IssueExt(id=1240652215052989236, tenantId=1146029695717560320, journalId=1235980550691926019, issueId=1240631872800215183, language=CN, specialIssueTitle=, coverIllustrator=null, specialIssueEditor=, specialIssueAbout=)}, issueFiles=null}, startPage=166, endPage=170, ext={EN=ArticleExt(id=1240631877334266717, articleId=1240631877099385680, tenantId=1146029695717560320, journalId=1235980550691926019, language=EN, title=Microstructure and Mechanical Properties of Al-Si-Mg Alloy Prepared by Selective Laser Melting, columnId=1236276108207902848, journalTitle=Mining and Metallurgical Engineering, columnName=MATERIALS, runingTitle=null, highlight=null, articleAbstract=

A high-strength Al-Si-Mg alloy was prepared by adopting selective laser melting (SLM), and then compared to the as-cast Al-Si-Mg alloy in terms of phase composition, microstructure, element distribution, crystallographic characteristics, and mechanical properties. It is found that Al-Si-Mg alloy prepared by SLM consists of α-Al matrix and eutectic Si particles, and the diffraction peaks of α-Al solid solution shift to lower angles due to the solid solution strengthening effect of Fe and Mg elements. The Al-Si-Mg alloy prepared by SLM has grain size approaching 18.35 μm, the dislocation density of 1.91×1015/m2, the surface hardness of (117.8±4.7) HV, the tensile strength of (436±13) MPa, and the elongation of (7.98±0.27)%, presenting superior performance than the as-cast Al-Si-Mg alloy. The alloy prepared by SLM technology is under the synergetic effect of fine grain strengthening, solid solution strengthening, dislocation strengthening and second phase strengthening, and the ductile fracture is its main failure mechanism.

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采用激光选区熔化（SLM）技术制备了高比强度的Al-Si-Mg合金，并与铸造Al-Si-Mg合金的相组成、微观形貌、元素分布、晶体学特性及力学性能进行了对比。结果表明：SLM技术制备Al-Si-Mg合金的相组成为α-Al基体相和共晶Si颗粒，由于Fe、Mg等元素的固溶强化效应，α-Al固溶体的衍射峰向低角度偏移；SLM技术制备Al-Si-Mg合金晶粒尺寸约18.35 μm，合金内部位错密度1.91×1015/m2，表面硬度（117.8±4.7）HV，抗拉强度（436±13）MPa，延伸率（7.98±0.27）%，远高于铸造Al-Si-Mg合金的相应性能；SLM技术制备合金的强化机制为细晶强化、固溶强化、位错强化和第二相强化的协同作用，断裂机制为韧性断裂。

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刘勇（1981—），男，江西宜春人，硕士，副教授，主要研究方向为材料加工工程。E-mail：

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刘勇（1981—），男，江西宜春人，硕士，副教授，主要研究方向为材料加工工程。E-mail：

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刘勇（1981—），男，江西宜春人，硕士，副教授，主要研究方向为材料加工工程。E-mail：

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Materials Science and Engineering: A, 2019, 746: 416-423., articleTitle=A comparative study on single-laser and multi-laser selective laser melting AlSi10Mg: Defects, microstructure and mechanical properties, refAbstract=null)], funds=[Fund(id=1240651350707589250, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, awardId=GJJ2204305, language=CN, fundingSource=江西省教育厅科学技术研究项目(GJJ2204305), fundOrder=null, country=null)], companyList=[AuthorCompany(id=1240651345028502088, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, xref=null, ext=[AuthorCompanyExt(id=1240651345036890698, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, companyId=1240651345028502088, language=EN, country=null, province=null, city=null, postcode=null, companyName=null, departmentName=null, remark=Yichun Vocational Technical College, Yichun 336000, Jiangxi, China), AuthorCompanyExt(id=1240651345049473613, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, companyId=1240651345028502088, language=CN, country=null, province=null, city=null, postcode=null, companyName=null, departmentName=null, remark=宜春职业技术学院，江西　宜春　336000)])], figs=[ArticleFig(id=1240651348534940572, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, language=EN, label=Fig.1, caption=XRD pattern of Al-Si-Mg alloy sample prepared by SLM technology, figureFileSmall=FDmNIrmIlAIasNJ9ExxH2w==, figureFileBig=V2uG9I3ZluqIRhEVIcaRJg==, tableContent=null), ArticleFig(id=1240651348715295662, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, language=CN, label=图1, caption=SLM技术制备Al-Si-Mg合金样品的XRD图谱, figureFileSmall=FDmNIrmIlAIasNJ9ExxH2w==, figureFileBig=V2uG9I3ZluqIRhEVIcaRJg==, tableContent=null), ArticleFig(id=1240651348912427959, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, language=EN, label=Fig.2, caption=Microstructure and element distribution of Al-Si-Mg alloy prepared by SLM technology, figureFileSmall=FPJDYXeYrFiDSDLCC2x3Kg==, figureFileBig=YIF5WiFlMt8rwaxYtyE2dw==, tableContent=null), ArticleFig(id=1240651349193446346, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, language=CN, label=图2, caption=SLM技术制备Al-Si-Mg合金微观组织形貌及元素分布, figureFileSmall=FPJDYXeYrFiDSDLCC2x3Kg==, figureFileBig=YIF5WiFlMt8rwaxYtyE2dw==, tableContent=null), ArticleFig(id=1240651349373801433, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, language=EN, label=Fig.3, caption=EBSD analysis results of as-cast alloy and alloy prepared by SLM technology, figureFileSmall=f0Z2v1Le0rBHp4eKqxtuVA==, figureFileBig=wKz4yo6II47DPua1bzgtEw==, tableContent=null), ArticleFig(id=1240651349533184999, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, language=CN, label=图3, caption=铸造合金和SLM技术制备合金的EBSD分析结果

（a）铸造合金反极图；（b）铸造合金高、低角度晶界图；（c）铸造合金KAM图；（d）SLM技术制备合金反极图；（e）SLM技术制备合金高、低角度晶界图；（f）SLM技术制备合金KAM图

, figureFileSmall=f0Z2v1Le0rBHp4eKqxtuVA==, figureFileBig=wKz4yo6II47DPua1bzgtEw==, tableContent=null), ArticleFig(id=1240651349638042617, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, language=EN, label=Fig.4, caption=Stress-strain curves of as-cast alloy and Al-Si-Mg alloy prepared by SLM technology, figureFileSmall=JU20iXjDDgP4NL5x3VH0Iw==, figureFileBig=Ernz177ljof0QOwB/tF5yg==, tableContent=null), ArticleFig(id=1240651349742899205, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, language=CN, label=图4, caption=铸造和SLM技术制备Al-Si-Mg合金的应力应变曲线, figureFileSmall=JU20iXjDDgP4NL5x3VH0Iw==, figureFileBig=Ernz177ljof0QOwB/tF5yg==, tableContent=null), ArticleFig(id=1240651349835173908, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, language=EN, label=Fig.5, caption=Typical fracture morphology of as-cast alloy and Al-Si-Mg alloy prepared by SLM technology after room-temperature stretch, figureFileSmall=UzLCG+yllLfgcySIhtOyPw==, figureFileBig=DJbJPRpDqZe/mr0fKiuL9g==, tableContent=null), ArticleFig(id=1240651349935837218, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, language=CN, label=图5, caption=铸造和SLM技术制备Al-Si-Mg合金常温拉伸后的典型断口形貌

（a），（b）铸造合金；（c），（d）SLM技术制备合金

, figureFileSmall=UzLCG+yllLfgcySIhtOyPw==, figureFileBig=DJbJPRpDqZe/mr0fKiuL9g==, tableContent=null), ArticleFig(id=1240651350065860662, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, language=EN, label=Table 1, caption=

Chemical composition of Al-Si-Mg alloy powder

, figureFileSmall=null, figureFileBig=null, tableContent=
MgSiNiFeMnNiAl
0.3010.5013.500.550.450.05余量
), ArticleFig(id=1240651350174912580, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, language=CN, label=表1, caption=

Al-Si-Mg合金粉末化学成分（质量分数）

, figureFileSmall=null, figureFileBig=null, tableContent=
MgSiNiFeMnNiAl
0.3010.5013.500.550.450.05余量
), ArticleFig(id=1240651350317518935, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, language=EN, label=Table 2, caption=

Average microhardness of as-cast alloy and Al-Si-Mg alloy prepared by SLM technology

, figureFileSmall=null, figureFileBig=null, tableContent=
种类平均显微硬度（HV）
SLM技术制备合金表面117.8±4.7
SLM技术制备合金截面124.1±5.9
铸造合金98.4±3.1
), ArticleFig(id=1240651350443348069, tenantId=1146029695717560320, journalId=1235980550691926019, articleId=1240631877099385680, language=CN, label=表2, caption=

铸造和SLM技术制备Al-Si-Mg合金的平均显微硬度

, figureFileSmall=null, figureFileBig=null, tableContent=
种类平均显微硬度（HV）
SLM技术制备合金表面117.8±4.7
SLM技术制备合金截面124.1±5.9
铸造合金98.4±3.1
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激光选区熔化技术制备Al-Si-Mg合金的组织及力学性能研究
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刘勇
矿冶工程杂志 | 材料 2025,45(1): 166-170
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矿冶工程杂志 | 材料 2025, 45(1): 166-170
激光选区熔化技术制备Al-Si-Mg合金的组织及力学性能研究
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刘勇
作者信息
  • 宜春职业技术学院，江西　宜春　336000

    • 刘勇（1981—），男，江西宜春人，硕士，副教授，主要研究方向为材料加工工程。E-mail：

Microstructure and Mechanical Properties of Al-Si-Mg Alloy Prepared by Selective Laser Melting
Yong LIU
Affiliations
  • Yichun Vocational Technical College, Yichun 336000, Jiangxi, China
出版时间: 2025-02-01 doi: 10.3969/j.issn.0253-6099.2025.01.031
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摘要
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采用激光选区熔化（SLM）技术制备了高比强度的Al-Si-Mg合金，并与铸造Al-Si-Mg合金的相组成、微观形貌、元素分布、晶体学特性及力学性能进行了对比。结果表明：SLM技术制备Al-Si-Mg合金的相组成为α-Al基体相和共晶Si颗粒，由于Fe、Mg等元素的固溶强化效应，α-Al固溶体的衍射峰向低角度偏移；SLM技术制备Al-Si-Mg合金晶粒尺寸约18.35 μm，合金内部位错密度1.91×1015/m2，表面硬度（117.8±4.7）HV，抗拉强度（436±13）MPa，延伸率（7.98±0.27）%，远高于铸造Al-Si-Mg合金的相应性能；SLM技术制备合金的强化机制为细晶强化、固溶强化、位错强化和第二相强化的协同作用，断裂机制为韧性断裂。

激光选区熔化  /  3D打印  /  增材制造  /  Al-Si-Mg合金  /  硬度  /  抗拉强度  /  强化机制  /  固溶强化  /  细晶强化  /  位错强化

A high-strength Al-Si-Mg alloy was prepared by adopting selective laser melting (SLM), and then compared to the as-cast Al-Si-Mg alloy in terms of phase composition, microstructure, element distribution, crystallographic characteristics, and mechanical properties. It is found that Al-Si-Mg alloy prepared by SLM consists of α-Al matrix and eutectic Si particles, and the diffraction peaks of α-Al solid solution shift to lower angles due to the solid solution strengthening effect of Fe and Mg elements. The Al-Si-Mg alloy prepared by SLM has grain size approaching 18.35 μm, the dislocation density of 1.91×1015/m2, the surface hardness of (117.8±4.7) HV, the tensile strength of (436±13) MPa, and the elongation of (7.98±0.27)%, presenting superior performance than the as-cast Al-Si-Mg alloy. The alloy prepared by SLM technology is under the synergetic effect of fine grain strengthening, solid solution strengthening, dislocation strengthening and second phase strengthening, and the ductile fracture is its main failure mechanism.

selective laser melting (SLM)  /  3D printing  /  additive manufacturing  /  Al-Si-Mg alloy  /  hardness  /  tensile strength  /  strengthening mechanism  /  solid solution strengthening  /  fine grain strengthening  /  dislocation strengthening
刘勇. 激光选区熔化技术制备Al-Si-Mg合金的组织及力学性能研究. 矿冶工程杂志, 2025 , 45 (1) : 166 -170 . DOI: 10.3969/j.issn.0253-6099.2025.01.031
Yong LIU. Microstructure and Mechanical Properties of Al-Si-Mg Alloy Prepared by Selective Laser Melting[J]. Mining and Metallurgical Engineering, 2025 , 45 (1) : 166 -170 . DOI: 10.3969/j.issn.0253-6099.2025.01.031
正文
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激光选区熔化（SLM）技术是一种以激光为热源、金属粉末为原料，将3D模型分解成2D平面逐层叠加、自下而上的材料制备方法[1-3]。SLM技术作为一种近净成形增材制造工艺，具有精度高、生产周期短、制造复杂零件能力强等优点，被广泛应用于汽车、冶金、航空航天等领域[4-6]。由于输入能量的定向沉积，SLM过程中容易沿沉积方向积累热量，导致合金内部产生强烈的热应力和裂纹[7]，传统高强度、凝固温度范围大的铝合金材料如Al-Zn、Al-Cu等，在加工过程中更容易产生裂纹，导致材料失效[8]。
Al-Si-Mg合金具有优异的强重比、良好的可焊接性，被广泛应用于汽车和航空航天等领域[9]。然而，铸造Al-Si-Mg合金会产生缩松、气孔等缺陷，严重影响Al-Si-Mg合金的力学性能，采用SLM技术可以避免铸造过程中产生的气孔和缩松等缺陷。已有研究证实，SLM具有104～106K/s的高冷却速率，制品组织相对精细，从而具有良好的力学性能[10-11]。本文采用SLM技术制备了适用于汽车配件的具有高比强度的Al-Si-Mg合金，采用X射线衍射技术、扫描电子显微镜、背电子衍射技术研究了Al-Si-Mg合金的相组成、元素分布和晶体学特性，并对合金力学性能进行了测试和表征。
1　实验材料及实验方法
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实验材料为Al-Si-Mg合金粉末，粒度15～53 μm，其化学成分如表1所示。
进行SLM实验前，在氩气保护下对粉末进行烘干处理，氩气纯度99.99%，烘干温度70 ℃。SLM实验用TS-300A金增材制造设备主要由IPG-YLR-500光纤激光器[波长（1 070±10）nm，最大功率500 W]组成。经过一系列前期基础实验，选择SLM工艺参数如下：激光功率350 W，扫描速度1 500 mm/s，单层厚度0.04 mm，光斑尺寸0.1 mm，离焦距离-3.5 mm。
SLM样品制备后，利用电火花切割技术从样品中心切割出10 mm×10 mm×6 mm立方体，进行微观组织表征。根据标准金相试样制备程序对金相试样进行机械研磨和抛光，采用Keller试剂（2.5 mL HNO3+1.5 mL HCl+1.0 mL HF+95 mL蒸馏水）腐蚀金相试样。采用扫描电镜（SEM）和能谱仪（EDS）观察Al-Si-Mg样品的微观结构。采用X射线衍射仪（XRD）分析样品相组成。采用场发射扫描电子显微镜（SEM）和电子背向散射衍射仪（EBSD）表征样品晶粒形貌、取向特征以及晶界特征，在EBSD表征前，利用精密蚀刻涂布器通过离子束蚀刻标准金相试样。采用显微硬度计测试Al-Si-Mg样品的显微硬度，负载200 g，压痕时间10 s，保压时间20 s，每个样品测试20次取平均值。拉伸试样按照ISO 6892-1：2009标准设计，在万能试验机上进行，加载速率0.5 mm/min。
2　实验结果与讨论
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2.1　相组成及微观结构
图1为SLM技术制备Al-Si-Mg合金样品的XRD图谱。结果表明，Al-Si-Mg合金样品的相组成为α-Al基体和共晶Si相。SLM技术制备合金α-Al基体的最强衍射峰在38.32°处，而α-Al基体的标准衍射峰在38.47°处（PDF#04-0787），表明SLM技术制备Al-Si-Mg合金中α-Al基体衍射峰发生了偏移现象，α-Al基体晶格常数发生了变化。这是由于Al-Si-Mg合金中存在少量Fe、Mn等元素，这些元素固溶在α-Al基体中，引发了α-Al的晶格畸变，从而导致α-Al基体衍射峰向低角度偏移[12]。这种偏移现象表明Fe、Mg等元素促进了α-Al基体的固溶强化作用，提升了α-Al基体的强度和硬度。
图2为SLM技术制备Al-Si-Mg合金的微观组织形貌及元素分布。从图中可以观察到基体组织和基体表面析出的第二相颗粒。结合元素面分布图和XRD图谱，表明基体组织为α-Al固溶体，均匀分布的第二相颗粒为共晶Si颗粒，它们在Al-Si-Mg合金中起第二相强化作用，可显著提升Al-Si-Mg合金的强度和硬度[13]。
图3为铸造和SLM技术制备Al-Si-Mg合金的截面中部区域EBSD分析结果。由图3可以看出，SLM技术制备Al-Si-Mg合金具有极为细小的晶粒组织，而铸造Al-Si-Mg合金的晶粒组织较为粗大，且SLM技术制备Al-Si-Mg合金晶粒由柱状晶和等轴晶组成。Channel 5软件计算结果表明，SLM技术制备Al-Si-Mg合金平均晶粒尺寸为18.35 μm，铸造Al-Si-Mg合金平均晶粒尺寸为237.55 μm。SLM技术可显著提升合金的细晶强化效应[10]。铸造Al-Si-Mg合金低角度晶界占比更高，这是铸造Al-Si-Mg合金晶粒尺寸较大，晶粒间取向差异较小，导致高角度晶界占比较小；SLM技术制备Al-Si-Mg合金织构强度较低，晶粒间取向差异较大，大角度晶界占比较高[14]。经计算可得，铸造Al-Si-Mg合金和SLM技术制备Al-Si-Mg合金的核平均错误取向（KAM）值分别为0.47°和1.12°。KAM在一定程度上可以反映合金内部的位错密度，KAM值越高，表明合金内部的位错密度越大。
Al-Si-Mg合金的位错密度（ρGNDs）计算式[15]为：
式中：为所选区域的KAM平均值；μ为EBSD测试的步长，这里取μ=0.5 μm；b为伯格斯向量，为2.35×10-10。经计算，铸造Al-Si-Mg合金和SLM技术制备Al-Si-Mg合金的位错密度分别为0.8×1015/m2和1.91×1015/m2，表明SLM技术制备Al-Si-Mg合金的内部存在较高的位错密度，可显著提升合金强度和韧性[16]。
2.2　Al-Si-Mg合金的力学性能分析
表2为铸造和SLM技术制备Al-Si-Mg合金的平均显微硬度，SLM技术制备Al-Si-Mg合金具有较高的显微硬度。
图4为铸造和SLM技术制备Al-Si-Mg合金的应力应变曲线，附图为Al-Si-Mg合金拉伸样品尺寸。SLM技术制备Al-Si-Mg合金的抗拉强度为（436±13）MPa，延伸率为（7.98±0.27）%，其抗拉强度远高于铸造合金[抗拉强度（248±24）MPa，延伸率（3.66±0.17）%]。SLM技术制备Al-Si-Mg合金具有较高抗拉强度的主要原因如下：①SLM加工过程中具有极高的冷却速度，制备的合金具有细小的晶粒尺寸，Al-Si-Mg合金内部晶界数量增多，产生细晶强化效应[17]；②结合XRD和EDS分析结果，有少量Fe、Mg元素溶解于α-Al基体中，引发α-Al基体产生晶格畸变，从而产生α-Al固溶强化效应；③结合EBSD分析结果，Al-Si-Mg合金内部存在位错，这些位错在合金受到变形作用时会产生阻碍作用，从而进一步提升合金强度；④从图2中观察到大量网格状Si颗粒均匀分布在α-Al基体中，这些Si颗粒起到第二相强化作用，从而显著提升合金强度和抗变形能力[18]。综上所述，SLM制备Al-Si-Mg合金具有较高硬度和抗拉强度可归因于细晶强化、固溶强化、位错强化和第二相强化的协同强化作用。
图5为铸造和SLM技术制备Al-Si-Mg合金常温拉伸后的典型断口形貌。铸造合金断口表面观察到少量韧窝和明显的解理面，这是由于铸造合金的晶粒尺寸较大，粗大的晶粒在拉伸过程中出现沿晶断裂，生成解理面。铸造合金断裂机理为韧性断裂和脆性断裂，且脆性断裂为主导断裂机制。SLM技术制备Al-Si-Mg合金断口形貌中可观察到大量韧窝，且没有明显的解理面。在韧窝内部观察到细小的第二相颗粒，这些第二相颗粒可诱发第二相强化效应，显著提升材料强度。因此，SLM技术制备Al-Si-Mg合金具有较高的抗拉强度和延伸率，其断裂机理为韧性断裂。
综上所述，SLM技术制备Al-Si-Mg合金具有较高的硬度、强度和良好的延伸率，显著优于铸造技术制备的Al-Si-Mg合金。
3　结论
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采用SLM技术制备了Al-Si-Mg合金，并对合金的相组成、微观形貌、元素分布、晶体学特性、显微硬度及力学性能进行研究，结论如下：
1）合金的相组成为α-Al基体相和共晶Si颗粒，且由于Fe、Mg等元素的固溶强化效应，α-Al固溶体衍射峰向低角度偏移。
2）EBSD结果表明：SLM制备Al-Si-Mg合金晶粒尺寸18.35 μm，比铸造合金更细小；SLM制备Al-Si-Mg合金内部位错密度为1.91×1015/m2。
3）SLM技术制备Al-Si-Mg合金具有良好的硬度及力学性能，其表面硬度（117.8±4.7）HV，抗拉强度（436±13）MPa，延伸率（7.98±0.27）%，远高于铸造合金。SLM技术制备合金的强化机制为细晶强化、固溶强化、位错强化和第二相强化的协同强化作用；断裂机制为韧性断裂。
基金
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  • 江西省教育厅科学技术研究项目(GJJ2204305)
文献
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2025年第45卷第1期
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doi: 10.3969/j.issn.0253-6099.2025.01.031
  • 接收时间：2024-09-12
  • 首发时间：2026-03-17
  • 出版时间：2025-02-01
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  • 收稿日期：2024-09-12
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江西省教育厅科学技术研究项目(GJJ2204305)
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    宜春职业技术学院，江西　宜春　336000
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2种不同金属材料的力学参数
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Number of
species		 占总种数比例
Percentage of
total species (%)		 属
Genus		 种数
Number of
species		 占总种数比例
Percentage of total
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鹅膏菌科Amanitaceae 2 11 5.26 鹅膏菌属 Amanita 10 4.78
小菇科 Mycenaceae 2 12 5.74 丝盖伞属 Inocybe 5 2.39
多孔菌科 Polyporaceae 8 14 6.70 蜡蘑属 Laccaria 5 2.39
红菇科 Russulaceae 3 23 11.00 小皮伞属 Marasmius 6 2.87
小菇属 Mycena 11 5.26
光柄菇属 Pluteus 5 2.39
红菇属 Russula 17 8.13
栓菌属 Trametes 5 2.39
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