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Article(id=1322282014942802067, tenantId=1146029695717560320, journalId=1220038251117760515, issueId=1322281938308677669, articleNumber=null, orderNo=null, doi=10.11868/j.issn.1001-4381.2024.000684, pmid=null, cstr=32421.14.j.issn.1001-4381.2024.000684, oa=null, hot=null, price=null, onlineType=0, articleFormat=0, articleType=null, articleTypeStr=research-article, receivedDate=1727625600000, receivedDateStr=2024-09-30, revisedDate=null, revisedDateStr=null, acceptedDate=1730131200000, acceptedDateStr=2024-10-29, onlineDate=1793186199173, onlineDateStr=2026-10-28, pubDate=1784476800000, pubDateStr=2026-07-20, doiRegisterDate=null, doiRegisterDateStr=null, onlineIssueDate=1793186199173, onlineIssueDateStr=2026-10-28, onlineJustAcceptDate=null, onlineJustAcceptDateStr=null, onlineFirstDate=null, onlineFirstDateStr=null, sourceXml=null, magXml=null, createTime=1793186199173, creator=13701087609, updateTime=1793186199173, updator=13701087609, issue=Issue{id=1322281938308677669, tenantId=1146029695717560320, journalId=1220038251117760515, year='2026', volume='54', issue='7', pageStart='1', pageEnd='347', issueExtLink='null', onlineDate='null', pubDate='1784476800000', pubDateStr='2026-07-20', beforeIssueId=null, nextIssueId=null, price=null, status=1, issueComplete=1, articleOrder=1, issueType=-1, specialIssue=0, createTime=1793186180903, creator='13701087609', updateTime=1793186267843, updator='13701087609', preIssue=null, nextIssue=null, articleTotal=null, ext={EN=IssueExt(id=1322282303045349604, tenantId=1146029695717560320, journalId=1220038251117760515, issueId=1322281938308677669, language=EN, specialIssueTitle=, coverIllustrator=null, specialIssueEditor=, specialIssueAbout=), CN=IssueExt(id=1322282303045349605, tenantId=1146029695717560320, journalId=1220038251117760515, issueId=1322281938308677669, language=CN, specialIssueTitle=, coverIllustrator=null, specialIssueEditor=, specialIssueAbout=)}, issueFiles=null, downloadFileDto=null}, startPage=241, endPage=250, ext={EN=ArticleExt(id=1322282015139934356, articleId=1322282014942802067, tenantId=1146029695717560320, journalId=1220038251117760515, language=EN, title=Microstructure and properties of Ti-6Al-4V alloy cladding layer prepared by synchronous composite forging of laser cladding and laser shock peening, columnId=1220689384450478826, journalTitle=Journal of Materials Engineering, columnName=RESEARCH ARTICLE, runingTitle=null, highlight=null, articleAbstract=

Laser cladding is widely used in additive manufacturing， damaged-surface repair， and surface modification of Ti-6Al-4V alloys. However， the performance optimization of laser-cladded layers on this alloy is still limited by several issues， including locally coarse grains， excessive residual tensile stress， and limited improvement in corrosion resistance. In this study， a novel process combining laser cladding with synchronous laser shock peening is proposed. Through this synchronous composite process， a laser-shock forging effect is generated， enabling simultaneous cladding layer fabrication and strengthening. This further refines the microstructure， enhances the mechanical properties， and improves the corrosion resistance of the cladding layer. The results show that the lamellar β-Ti phase and acicular martensitic α′-Ti phase in the cladding layer prepared by the composite process are significantly refined， forming an interwoven and dense basket-weave structure. The microhardness of the cladding layer increases from 360-405HV0.2 to 470-530HV0.2， indicating a remarkable strengthening effect. Meanwhile， the average friction coefficient decreases from 0.42 to 0.35， corresponding to a reduction of 16.67%， and the volume wear loss decreases by 25.93%， confirming the significant improvement in wear resistance of the cladding layer. In addition， the shock wave induced by laser shock processing effectively promotes the transformation of residual tensile stress into compressive stress. The maximum residual compressive stress reaches 390 MPa， and the stress distribution becomes more uniform. The corrosion potential （Ecorr） of the cladding layer increases by 0.027 V， while the corrosion current density （icorr） decreases by 8.71×10-8 A·cm-2， indicating that the corrosion resistance is significantly enhanced and that passivation behavior occurs more readily.

, authors=Haolong JIANG, Weibin REN, Hao JI, Run YUAN, Jun LI, authorsList=Haolong JIANG, Weibin REN, Hao JI, Run YUAN, Jun LI, authorCompany=null, correspAuthors=Weibin REN, authorNote=null, correspAuthorsNote=null, copyrightStatement=null, copyrightOwner=null, extLink=null, articleAbsUrl=null, sourceXml=null, magXml=null, pdfUrl=null, pdf=null, pdfFileSize=null, pdfExtLink=null, richHtmlUrl=null, mobilePdfUrl=null, reviewReport=null, pdfFirstPage=null, abstractGraph=null, abstractGraphContent=null, abstractVideo=null, citation=null, cebUrl=null, magXmlContent=null, mapNumber=null, fund=null), CN=ArticleExt(id=1322282019418124466, articleId=1322282014942802067, tenantId=1146029695717560320, journalId=1220038251117760515, language=CN, title=激光熔覆与激光冲击同步复合锻打制备Ti-6Al-4V合金熔覆层微观组织与性能, columnId=1220689384622445292, journalTitle=材料工程, columnName=研究论文, runingTitle=null, highlight=null, articleAbstract=

激光熔覆在Ti-6Al-4V合金增材制造、修复受损表面以及表面改性等领域获得广泛应用，然而，熔覆层局部晶粒粗大、残余拉应力过大以及耐腐蚀性能提升有限等问题，限制了该类合金激光熔覆层的性能优化。本研究基于激光熔覆与激光冲击同步复合的新工艺方法，通过同步复合形成激光冲击锻打效应，在熔覆层制备的同时进行强化，进一步细化显微组织、提升力学性能并改善耐腐蚀性能。结果表明：复合工艺所制备熔覆层的片状β-Ti和针状马氏体α′-Ti相显著细化，形成了交错密集的网篮状结构。熔覆层的显微硬度从360~405HV0.2提升至470~530HV0.2，提升效果显著。同时，熔覆层的平均摩擦因数从0.42降至0.35，降低了16.67%；体积磨损量减少了25.93%，验证了熔覆层的耐磨性能得到显著改善。此外，激光冲击诱导的冲击波有效促进了残余拉应力向压应力的转化，最大残余压应力达到390 MPa，且应力分布状态更加均匀。熔覆层的腐蚀电位（Ecorr）升高了0.027 V，腐蚀电流密度（icorr）降低了8.71×10-8 A·cm-2，表明其耐腐蚀性能显著提升，且更易发生钝化行为。

, authors=姜浩龙, 任维彬, 姬豪, 袁润, 李军, authorsList=姜浩龙, 任维彬, 姬豪, 袁润, 李军, authorCompany=null, correspAuthors=任维彬, authorNote=null, correspAuthorsNote=
任维彬（1983—），男，副教授，博士，主要研究方向为激光再制造形状与性能控制，联系地址：江苏省常州市中吴大道1801号江苏理工学院机械工程学院（213001），E-mail：
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orderNo=4, keyword=复合制备), Keyword(id=1322282023251718360, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=CN, orderNo=5, keyword=组织与性能)], refs=[Reference(id=1322282025877352695, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, doi=null, pmid=null, pmcid=null, year=2024, volume=172, issue=null, pageStart=107864, pageEnd=null, url=null, language=null, rfNumber=[1], rfOrder=0, authorNames=GHORBANI H, SARKARI KHORRAMI M, GERANMAYEH A, journalName=Optics and Lasers in Engineering, refType=null, unstructuredReference=GHORBANI H， SARKARI KHORRAMI M， GERANMAYEH A，et al. 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companyId=1322282019665588403, language=CN, country=null, province=null, city=null, postcode=null, companyName=null, departmentName=null, remark=江苏理工学院 机械工程学院，江苏 常州 213001)])], figs=[ArticleFig(id=1322282023373353177, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=EN, label=Fig.1, caption=Principle of synchronized laser cladding and laser shock peening composite process, figureFileSmall=QseS5fOTT0SEEjkqNWy6Qg==, figureFileBig=sajV1TEu+BhiV2+jUmEFXg==, tableContent=null), ArticleFig(id=1322282023453044954, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=CN, label=图1, caption=激光熔覆与激光冲击同步复合工艺原理, figureFileSmall=QseS5fOTT0SEEjkqNWy6Qg==, figureFileBig=sajV1TEu+BhiV2+jUmEFXg==, tableContent=null), ArticleFig(id=1322282023645982939, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=EN, label=Fig.2, caption=Correspondence between principles of laser cladding and laser shock peening test and the process equipment, figureFileSmall=c7gyZwby68CwaA1tqI7Ryg==, figureFileBig=N0RNDxK8IARhX0Z47stVxQ==, tableContent=null), ArticleFig(id=1322282023713091804, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=CN, label=图2, caption=激光熔覆与激光冲击实验原理和工艺设备的对应关系, figureFileSmall=c7gyZwby68CwaA1tqI7Ryg==, figureFileBig=N0RNDxK8IARhX0Z47stVxQ==, tableContent=null), ArticleFig(id=1322282023792783581, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=EN, label=Fig.3, caption=Microscopic morphology of cladding alloy powder, figureFileSmall=p+uUv99JFT/4Vo/WW791Tg==, figureFileBig=PFo0ETVs8jebxh4tx8Un/A==, tableContent=null), ArticleFig(id=1322282023880863966, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=CN, label=图3, caption=熔覆合金粉末微观形貌, figureFileSmall=p+uUv99JFT/4Vo/WW791Tg==, figureFileBig=PFo0ETVs8jebxh4tx8Un/A==, tableContent=null), ArticleFig(id=1322282023989915871, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=EN, label=Fig.4, caption=Macroscopic morphologies of Ti-6Al-4V alloy laser cladding layers before（a） and after（b） LSP, figureFileSmall=hr0pg+FkLK6LTGe0p9cWig==, figureFileBig=WNfk9apO8snI/LPsqsPT9g==, tableContent=null), ArticleFig(id=1322282024065413344, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=CN, label=图4, caption=Ti-6Al-4V合金激光熔覆层激光冲击前（a）后（b）宏观形貌, figureFileSmall=hr0pg+FkLK6LTGe0p9cWig==, figureFileBig=WNfk9apO8snI/LPsqsPT9g==, tableContent=null), ArticleFig(id=1322282024136716513, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=EN, label=Fig.5, caption=Microstructural morphologies of the Ti-6Al-4V alloy laser cladding layers before（1） and after（2） LSP（a）at the top of laser cladding layer；（b）in the middle of laser cladding layer；（c）at the bottom of laser cladding layer, figureFileSmall=3iaN+E1BS+HdOrBa1BoHuA==, figureFileBig=pMKNu/8bEkHXbEHcYxiznA==, tableContent=null), ArticleFig(id=1322282024199631074, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=CN, label=图5, caption=Ti-6Al-4V合金激光熔覆层激光冲击前（1）后（2）组织形貌（a）激光熔覆层顶部；（b）激光熔覆层中部；（c）激光熔覆层底部, figureFileSmall=3iaN+E1BS+HdOrBa1BoHuA==, figureFileBig=pMKNu/8bEkHXbEHcYxiznA==, tableContent=null), ArticleFig(id=1322282024266739939, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=EN, label=Fig.6, caption=Schematic diagram of microhardness test point distribution（a） and microhardness distribution curves before and after LSP of the Ti-6Al-4V alloy cladding layer（b）, figureFileSmall=Nwd3QxuCbPLFVJQxVaevhg==, figureFileBig=wgbDXkw0D2vCh+O5gXeZlg==, tableContent=null), ArticleFig(id=1322282024346431716, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=CN, label=图6, caption=Ti-6Al-4V合金熔覆层显微硬度测试点分布示意图（a）与激光冲击前后显微硬度分布曲线（b）, figureFileSmall=Nwd3QxuCbPLFVJQxVaevhg==, figureFileBig=wgbDXkw0D2vCh+O5gXeZlg==, tableContent=null), ArticleFig(id=1322282024438706405, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=EN, label=Fig.7, caption=Schematic diagrams of residual stress test point location（a） and test site（b）, figureFileSmall=A6m0/TCptl6W2Sfl2hn4oA==, figureFileBig=xBkWU2TgGYa+UzcnvkCM1Q==, tableContent=null), ArticleFig(id=1322282024510009574, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=CN, label=图7, caption=残余应力测试点位置（a）与测试现场示意图（b）, figureFileSmall=A6m0/TCptl6W2Sfl2hn4oA==, figureFileBig=xBkWU2TgGYa+UzcnvkCM1Q==, tableContent=null), ArticleFig(id=1322282024577118439, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=EN, label=Fig.8, caption=Residual stress distribution in the cladding layer

（a）stress distribution on the surface parallel to the cladding direction；（b）stress distribution on the surface perpendicular to the cladding direction

, figureFileSmall=rKRjYFlYt20SPSQwsl5QmA==, figureFileBig=pc0c8cEPP3ytvgMiPZ3C+Q==, tableContent=null), ArticleFig(id=1322282024656810216, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=CN, label=图8, caption=熔覆层残余应力分布

（a）熔覆层表面平行熔覆方向应力分布；（b）熔覆层表面垂直熔覆方向应力分布

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（a）before LSP；（b）after LSP

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Main element compositions of cladding material and Ti-6Al-4V alloy （mass fraction/%）

, figureFileSmall=null, figureFileBig=null, tableContent=
MaterialTiAlVCOFe
Substrate80.08-84.025.52-6.823.42-4.533.62-4.561.82-2.44Bal.
Powder82.02-88.424.52-5.333.72-3.952.92-4.432.02-2.53Bal.
), ArticleFig(id=1322282025579557108, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1322282014942802067, language=CN, label=表1, caption=

熔覆材料与Ti-6Al-4V合金的主要元素成分（质量分数/%）

, figureFileSmall=null, figureFileBig=null, tableContent=
MaterialTiAlVCOFe
Substrate80.08-84.025.52-6.823.42-4.533.62-4.561.82-2.44Bal.
Powder82.02-88.424.52-5.333.72-3.952.92-4.432.02-2.53Bal.
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激光熔覆与激光冲击同步复合锻打制备Ti-6Al-4V合金熔覆层微观组织与性能
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姜浩龙 , 任维彬 , 姬豪 , 袁润 , 李军
材料工程 | 研究论文 2026,54(7): 241-250
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材料工程 |研究论文 2026 , 54 (7) : 241 -250
激光熔覆与激光冲击同步复合锻打制备Ti-6Al-4V合金熔覆层微观组织与性能
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姜浩龙, 任维彬 , 姬豪, 袁润, 李军
作者信息
  • 江苏理工学院 机械工程学院，江苏 常州 213001
通讯作者:
任维彬（1983—），男，副教授，博士，主要研究方向为激光再制造形状与性能控制，联系地址：江苏省常州市中吴大道1801号江苏理工学院机械工程学院（213001），E-mail：
Microstructure and properties of Ti-6Al-4V alloy cladding layer prepared by synchronous composite forging of laser cladding and laser shock peening
Haolong JIANG, Weibin REN , Hao JI, Run YUAN, Jun LI
Affiliations
  • School of Mechanical Engineering，Jiangsu University of Technology，Changzhou 213001，Jiangsu，China
出版时间: 2026-07-20 doi: 10.11868/j.issn.1001-4381.2024.000684
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摘要
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激光熔覆在Ti-6Al-4V合金增材制造、修复受损表面以及表面改性等领域获得广泛应用，然而，熔覆层局部晶粒粗大、残余拉应力过大以及耐腐蚀性能提升有限等问题，限制了该类合金激光熔覆层的性能优化。本研究基于激光熔覆与激光冲击同步复合的新工艺方法，通过同步复合形成激光冲击锻打效应，在熔覆层制备的同时进行强化，进一步细化显微组织、提升力学性能并改善耐腐蚀性能。结果表明：复合工艺所制备熔覆层的片状β-Ti和针状马氏体α′-Ti相显著细化，形成了交错密集的网篮状结构。熔覆层的显微硬度从360~405HV0.2提升至470~530HV0.2，提升效果显著。同时，熔覆层的平均摩擦因数从0.42降至0.35，降低了16.67%；体积磨损量减少了25.93%，验证了熔覆层的耐磨性能得到显著改善。此外，激光冲击诱导的冲击波有效促进了残余拉应力向压应力的转化，最大残余压应力达到390 MPa，且应力分布状态更加均匀。熔覆层的腐蚀电位（Ecorr）升高了0.027 V，腐蚀电流密度（icorr）降低了8.71×10-8 A·cm-2，表明其耐腐蚀性能显著提升，且更易发生钝化行为。

激光熔覆  /  激光冲击  /  Ti-6Al-4V合金  /  复合制备  /  组织与性能

Laser cladding is widely used in additive manufacturing， damaged-surface repair， and surface modification of Ti-6Al-4V alloys. However， the performance optimization of laser-cladded layers on this alloy is still limited by several issues， including locally coarse grains， excessive residual tensile stress， and limited improvement in corrosion resistance. In this study， a novel process combining laser cladding with synchronous laser shock peening is proposed. Through this synchronous composite process， a laser-shock forging effect is generated， enabling simultaneous cladding layer fabrication and strengthening. This further refines the microstructure， enhances the mechanical properties， and improves the corrosion resistance of the cladding layer. The results show that the lamellar β-Ti phase and acicular martensitic α′-Ti phase in the cladding layer prepared by the composite process are significantly refined， forming an interwoven and dense basket-weave structure. The microhardness of the cladding layer increases from 360-405HV0.2 to 470-530HV0.2， indicating a remarkable strengthening effect. Meanwhile， the average friction coefficient decreases from 0.42 to 0.35， corresponding to a reduction of 16.67%， and the volume wear loss decreases by 25.93%， confirming the significant improvement in wear resistance of the cladding layer. In addition， the shock wave induced by laser shock processing effectively promotes the transformation of residual tensile stress into compressive stress. The maximum residual compressive stress reaches 390 MPa， and the stress distribution becomes more uniform. The corrosion potential （Ecorr） of the cladding layer increases by 0.027 V， while the corrosion current density （icorr） decreases by 8.71×10-8 A·cm-2， indicating that the corrosion resistance is significantly enhanced and that passivation behavior occurs more readily.

laser cladding  /  laser shock peening  /  Ti-6Al-4V alloy  /  composite preparation  /  microstructure and property
姜浩龙, 任维彬, 姬豪, 袁润, 李军. 激光熔覆与激光冲击同步复合锻打制备Ti-6Al-4V合金熔覆层微观组织与性能. 材料工程, 2026 , 54 (7) : 241 -250 . DOI: 10.11868/j.issn.1001-4381.2024.000684
Haolong JIANG, Weibin REN, Hao JI, Run YUAN, Jun LI. Microstructure and properties of Ti-6Al-4V alloy cladding layer prepared by synchronous composite forging of laser cladding and laser shock peening[J]. Journal of Materials Engineering, 2026 , 54 (7) : 241 -250 . DOI: 10.11868/j.issn.1001-4381.2024.000684
正文
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Ti-6Al-4V合金因其具有优良的比强度、耐腐蚀性和良好的生物相容性，在航空航天、船舶制造及生物医学等领域得到了广泛应用［1-3］。然而，在该类合金部件服役过程中，表面易受到磨损、腐蚀及疲劳等损伤，从而限制了其使用寿命和性能［4-5］。为提升Ti-6Al-4V合金表面的耐磨、耐腐蚀性能，激光熔覆成为重要的表面改性方法，它能够通过在基体表面沉积具有优异性能的合金材料来实现表面强化，使其获得更高的耐磨性、耐腐蚀性和力学性能。尽管激光熔覆在表面修复和增材制造中获得广泛应用，但仍存在一些局限性［6-7］：熔覆层的局部晶粒粗大，导致表面力学性能不均匀；激光熔覆过程中产生的残余拉应力较大，容易导致熔覆层开裂，影响其服役寿命；虽然激光熔覆能提升合金表面的耐磨性，但对耐腐蚀性的改善有限，这些问题制约了Ti-6Al-4V合金的进一步应用。
针对上述难点，研究者们提出了激光熔覆与激光冲击（laser shock peening，LSP）结合的复合工艺方法，Smith等［8］开展了激光熔覆与激光冲击的复合工艺研究，发现激光冲击不仅可以实现β相晶粒细化，还可显著提升材料的显微硬度和抗疲劳性能。经该团队研究证实，经激光冲击处理后，熔覆层显微硬度获得显著提升；Miller团队［9］探究了激光冲击在改善熔覆层耐腐蚀性方面的潜力，结果显示，经过激光冲击的Ti-6Al-4V合金熔覆层，腐蚀电流密度下降了20%，且提升了材料的钝化能力；Jones等［10］采用激光熔覆与激光冲击相结合的方式，成功制备出具有优异力学性能和耐磨性的Ti-6Al-4V合金，研究发现复合工艺可以有效减少磨损机制中的黏着磨损，降低摩擦因数。汪诚等［11］通过TC4钛合金激光熔覆与激光冲击复合处理发现，激光冲击强化可在熔覆层表面诱导纳米晶组织和残余压应力，从而提高材料的高周疲劳性能；陈雪鹏等［12］针对激光增材制造TC4钛合金开展激光冲击强化研究，证实冲击波作用可破碎并细化粗大的α板条组织，诱导位错和形变孪晶形成，同时促使残余拉应力向残余压应力转变，显著提高材料强度和显微硬度，上述研究已证实该复合工艺能够细化晶粒并提升材料的力学性能。然而，分步复合工艺存在工艺复杂、效率较低等问题。由于各步骤独立进行，工艺间的协同作用未得到充分利用。
针对分步复合工艺的局限性，本研究提出了激光熔覆与激光冲击同步复合工艺，通过该工艺能够在熔覆成形的同时，利用激光冲击锻打效应实现熔覆层的塑性变形强化，有效细化晶粒、提升显微硬度、改善残余应力分布，同时提升耐磨性能和耐腐蚀性能。与分步工艺相比，同步复合工艺不仅简化了工艺流程，提升了效率，还能避免因分步工艺中的热影响区再加热导致的晶粒粗化问题，从而获得更均匀的组织结构与更显著的性能提升。
此外，尽管激光淬火、超声冲击等其他表面强化技术也被广泛应用于材料表面改性，但这些技术存在一定的局限性。激光淬火通过热效应强化材料，容易引入较大的热应力，而超声冲击的能量较低，难以实现深层次的晶粒细化和残余应力调整。因此，本研究选择激光冲击作为辅助工艺，并结合激光熔覆形成同步复合工艺，以期最大程度地提升Ti-6Al-4V合金熔覆层的综合性能。
基于此，本研究采用激光熔覆与激光冲击同步复合形成锻打效应的新工艺方法，实现了Ti-6Al-4V合金同成分熔覆层的制备，通过与Ti-6Al-4V合金激光熔覆层的对比，阐明了同步复合再制造Ti-6Al-4V合金熔覆层的组织与性能演变特征，为该类合金高性能表面工程应用提供了理论依据和方法参考。
1 实验材料与过程
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1.1 实验原理
本研究中激光熔覆与冲击同步复合再制造工艺方法原理如图1所示，同步复合中激光熔覆的光束连续熔覆实现熔覆层成形，同时伴随第二束短脉冲激光直接作用在高温激光熔覆金属表面，金属表层吸收激光束能量后气化电离形成冲击波，利用脉冲激光诱导的冲击波（冲击波峰值压力为GPa量级）对易塑性变形的中高温度区金属进行同步冲击强化，形成激光锻打效应，使熔覆层发生塑性变形，具有消除熔覆层气孔等内部缺陷和控制热应力过大的作用，可有效控制宏观变形与开裂问题［13］。
在激光熔覆与激光冲击同步复合过程中，激光熔覆加工头在设置工艺参数以及调整位姿状态（图2）后，保持工艺实现过程中空间位置始终不变，激光冲击发射端口的位置同样固定不变。复合工艺成形路径的实现通过工件夹持机械臂的反向运动实现，在此过程中，激光冲击的部位设置在熔池后方约1/2光斑位置处，这样的相对位置关系既能保证形成稳定形态的熔池，又能实现熔覆层在处于熔融态至凝固态的过程中受到冲击，以实现熔覆层良好的成形性及组织与性能的优化。
1.2 实验材料
实验材料基体为100 mm×100 mm×15 mm的Ti-6Al-4V合金，熔覆合金粉末选择与基材同质的Ti-6Al-4V合金粉末，粉末为球形，粒度约为53~150 μm。该Ti-6Al-4V合金粉末与基材元素含量匹配度高、热物性相近，具有良好的成形性，基体与合金粉末的组成成分如表1所示。
由表1可知，熔覆粉末中Ti元素含量略高，主要是考虑留有一定的烧损裕量，以确保经激光熔覆热输入作用后熔覆层与基体元素含量相近；Al元素为α-Ti稳定化元素，V元素为β-Ti稳定化元素，可使熔覆层保持良好的塑性，此外，Al、V、C以及O元素对熔覆层均具有一定的固溶强化作用，可提升熔覆层的强度和硬度。熔覆合金粉末的微观形貌如图3所示。
1.3 工艺实验过程
激光熔覆实验采用YLS-4000光纤激光器，最大输出功率为4000 W，送粉方式采用四路同轴送粉，熔覆时采用纯度大于99.99%的氩气对熔池进行保护。实验前，为避免基材表面的氧化膜及污垢的影响，同时增加基材对激光的吸收率，先用200#砂纸进行打磨，再用无水乙醇清洗晾干。为保证熔覆粉末具有良好的流动性和干燥性，将熔覆粉末放在150 ℃真空干燥箱内干燥4 h。激光熔覆优化工艺参数为：激光功率1.5 kW，扫描速率5 mm/s，气流量1.5 L/min，送粉速率18.2 g/min，搭接率30%，光斑直径3 mm，离焦量3 mm。
激光冲击实验采用LSP-10000型大功率激光冲击设备，激光冲击发射端口与激光熔覆加工头以及待加工试样的相互位置关系如图2所示。激光冲击实验的工艺参数为：冲击频率3 Hz，脉宽15 ns，冲击能量2 J，光斑直径3 mm，功率密度6 GW/cm2［14］。对熔覆实验后的熔覆层进行冲击强化，冲击前用砂纸对熔覆层进行打磨，降低熔覆层表面粗糙度并去除熔覆层边缘的残余毛刺。冲击时，以去离子水作为约束层，Ti-6Al-4V激光熔覆层经激光冲击前后熔覆层形貌如图4所示。采用激光熔覆以及激光熔覆与激光冲击复合工艺分别制备熔覆层，采用激光熔覆制备的试样作为实验对比样本。
1.4 熔覆层性能测试
对激光冲击前后熔覆层分别进行线切割取样，试样依次用400#、800#、1200#、2000#、3000#砂纸进行打磨，采用粒度为3 μm的金刚石悬浮液抛光30 min，然后置于体积分数为75%的酒精溶液中超声波清洗15 min。使用HF∶HNO3∶去离子水=1∶2∶7（体积比）的溶液对试样进行蚀刻15 s，采用Primotech型正置金相显微镜观察激光冲击前后熔覆层微观组织的变化。
使用HXD-1000TMS数显式显微硬度计对激光冲击前后熔覆层的显微硬度进行测试，显微硬度测试沿熔覆层深度方向，从熔覆层顶部测试至基体。沿熔覆层深度方向的测试点间距为400 μm，在同一深度方向测试5个点，水平间距为200 μm，加载载荷为1.96 N，保压时间为15 s。采用MDW-02摩擦磨损试验机对激光冲击前后熔覆层进行往复摩擦磨损实验，样品尺寸为15 mm×15 mm×10 mm，在室温且无润滑的条件下进行。摩擦副选用直径为Φ6 mm的GCr15钢球，加载力为15 N，加载频率为3 Hz，测试时间为30 min。采用盲孔法测量激光冲击前后熔覆层横向和纵向的残余应力，X方向测试点的间距为5 mm，Y方向测试点的间距为5 mm，实验选用BX120-3CA型电阻应变花，采用慢速钻孔仪在应变花上对应圆孔内打孔，孔径1.5 mm，孔深1 mm。使用NANOPS50型三维形貌仪对激光冲击前后熔覆层磨痕进行三维轮廓提取表征，采用扫描电子显微镜（SEM）观察激光冲击前后磨痕表面的磨损形貌［15］。利用CHI600E电化学工作站进行耐腐蚀性能测试，使用AgCl电极作为参比电极，在标准三电极电池中进行动电位极化测量，以0.003 mV/s的扫描速率测量，通过Tafel外推法拟合极化曲线评估腐蚀电流密度（icorr）和腐蚀电位（Ecorr）。电解液为3.5%NaCl溶液，溶液温度保持在室温。
2 结果与讨论
收起
2.1 熔覆层组织形貌对比
图5为Ti-6Al-4V合金激光熔覆层激光冲击前后的组织形貌，对比图5（a-1）与图5（a-2）可知，激光冲击前熔覆层组织以层片状α相为主，激光冲击后熔覆层的组织形貌发生明显变化。激光冲击强化在熔覆层表面产生高能量、高应变率的冲击波，当冲击波的压力超过熔覆层的动态屈服强度时，熔覆层发生塑性变形，在近表面区域，由于能量最高，组织的变化较为剧烈，粗大的β相出现扭折、破碎等现象［16］。在激光冲击能量的塑性压缩和瞬时高温作用下，部分α相向具有相对高温稳定性的β相转化，同时，熔覆层顶部较高的冷却速率导致β相没有足够的时间回转变为稳定的α相，而是以亚稳态的方式转变为针状马氏体α′相［17］。冲击波的传播方向和大小会影响α′相的变形方式，当冲击波垂直于α′相传播时，完整的针状α′相会被击碎，并被细化分割，从而形成短而细小的针状α′相，同时其晶粒取向发生偏转［18-19］，如图5（a-2）所示。而当冲击波平行于α′相传播时，针状α′相会沿着冲击波方向发生晶粒的拉长和转动，使熔覆层中网篮组织呈现更为密集的交错状态［20］，如图5（b-2）所示。对比图5（b-1）与图5（b-2）可知，激光冲击后熔覆层中部组织与激光冲击前相比，针状马氏体α′-Ti组织得到细化，生长取向与激光冲击能量作用方向大体一致，同时局部α′-Ti马氏体取向重新排列并细化，形成交错的网篮组织，网篮组织的形成有利于避免特定方向上的应力集中，减少局部应力过大而导致材料过早发生塑性变形或断裂的可能性［21］，从而提升了材料的塑性和断裂韧性。进一步对比图5（c-1）与图5（c-2）可知，由于激光诱导的冲击波从表面向材料内部传播时能量逐渐衰减，对熔覆层底部产生的塑性变形效果逐渐降低，组织的细化效果也随之减弱，因此，该部位组织与熔覆层中部组织大体一致，但细化程度略低。
2.2 熔覆层显微硬度对比
Ti-6Al-4V合金熔覆层显微硬度测试点分布示意图与经激光冲击前后显微硬度分布曲线如图6所示。激光冲击前熔覆层显微硬度为360~405HV0.2，这是因为经历激光熔覆的快速熔化凝固过程后，β-Ti相发生马氏体转变，形成了针状马氏体α'，而针状马氏体α'的硬度仅略高于α-Ti［22］，一定程度上使熔覆层性能提升。其中熔覆层顶部硬度最高，这是因为熔覆层顶部的温度梯度最大，针状马氏体的分布更密集，使得熔覆层顶部的硬度更高。
激光冲击后熔覆层显微硬度为470~530HV0.2，实现了显微硬度的进一步提升，这是因为激光冲击使熔覆层表面发生塑性变形，大幅增加了熔覆层表面的位错密度，使熔覆层内的晶粒得到细化，提升了熔覆层硬度［23］。其中，熔覆层顶部硬度约为530HV0.2，较激光冲击前的405HV0.2提升了约30.86%；熔覆层中部硬度约为500HV0.2，较激光冲击前的390HV0.2提升了约28.21%；熔覆层底部硬度约为470HV0.2，较激光冲击前的375HV0.2提升了约25.33%，由此可以发现，随着距熔覆层表面距离的增加，显微硬度的提升效果逐渐减小，这是由于大脉冲激光诱导的冲击波从表面向材料内部传播时能量逐渐衰减，对材料内部产生塑性变形的效果也逐渐降低，因此熔覆层的显微硬度提升效果在截面方向沿着深度随之减小。由图可见，激光冲击强化的显微硬度影响层深度约为1.7 mm，覆盖了熔覆层85%的区域，对基体基本无影响。
2.3 熔覆层残余应力评价
采用盲孔法分别测量激光冲击前后熔覆层横向和纵向的残余应力，应力测试点示意图与测试现场图如图7所示，其中点1到点9的矢量方向定义为X正方向，点10到点12的矢量方向定义为Y正方向，测试后计算出各点X方向和Y方向上的应力值。
图8为激光冲击前熔覆层表面残余应力分布。由图8（a）可知，平行激光熔覆方向拉应力最大值出现在熔覆层边缘，即点1与点9的位置，约为170 MPa，这主要是因为受熔覆层成形路径影响，该位置处于路径转折位置，接受激光热输入时间相对较长，产生的热输入也相对较大，由此产生的热应力也相对较大。由图8（b）可知，垂直激光扫描方向拉应力分布较为均匀，约为140 MPa。对比图8（a）和图8（b）可知，熔覆层表面同一位置X方向应力略大于Y方向应力。
图9为激光冲击前后Ti-6Al-4V合金熔覆层表面沿激光熔覆方向残余应力分布（均取X方向残余应力值），激光冲击强化后，熔覆层表面的残余拉应力转化为残余压应力，最大残余压应力达到390 MPa左右，平均残余压应力约为379 MPa，且残余应力的分布较激光冲击前更均匀。激光冲击波加载到熔覆层表面时，沿着冲击波传播方向冲击区域发生局部塑性变形，使强化区轴向体积压缩，横向体积膨胀，熔覆层向两边延展，对外有挤压作用。当激光冲击结束后，强化区周围材料发生弹性回复，对已经发生塑性应变的强化区形成弹性挤压，促进强化区形成一定深度和大小的残余压应力层［24］。
2.4 熔覆层摩擦磨损性能对比
激光冲击前后熔覆层摩擦因数的变化曲线如图10所示。在相同的实验条件下，两个试样的摩擦因数曲线变化规律基本相同，都经历了磨损过程中3个典型阶段中的前两个阶段，即磨合和稳定两个阶段［25］。激光冲击前熔覆层的摩擦因数相对较大，且曲线波动明显，平均摩擦因数为0.42。一方面未经激光冲击强化的熔覆层组织晶粒尺寸差异大，且分布不均匀，另一方面熔覆层表面存在微气孔缺陷。因此在实验过程中，当GCr15钢球划擦过熔覆层表面时，所受的摩擦阻力波动较大，从而使得摩擦因数产生较大波动。激光冲击后熔覆层的摩擦因数减小，相较于激光冲击前熔覆层，冲击后熔覆层的摩擦因数曲线波动较小，平均摩擦因数为0.35，降低了16.67%。激光冲击强化使熔覆层中粗大的组织实现晶粒细化，熔覆层组织更加致密均匀，显微硬度显著提升，抵抗GCr15钢球表面的微凸体压入犁削的能力提高，减弱了对熔覆层的犁削作用［26］，使得熔覆层表现出较好的减摩效果，摩擦因数曲线波动幅度减小，平均摩擦因数降低。
为进一步评估摩擦磨损情况，对激光冲击前后熔覆层的磨损痕迹进行三维轮廓提取表征，如图11所示。激光冲击前熔覆层与激光冲击后熔覆层的磨痕宽度分别为1450 μm和1300 μm，磨痕深度分别为43 μm和35 μm，熔覆层体积磨损量分别为0.27 mm3和0.20 mm3。二者相比可知，激光冲击强化使熔覆层的磨痕宽度减小了10.34%，磨痕深度减小了18.60%，体积磨损量减少了25.93%，激光冲击后熔覆层的耐磨性能得到显著提升。
采用扫描电子显微镜观察激光冲击前后熔覆层的磨痕形貌，如图12所示。由图12（a）可知，激光冲击前熔覆层磨痕表面形成了沿着摩擦副滑动方向密集且深的犁沟，同时还存在大面积的黏着物和熔覆层材料剥落现象。这是因为部分熔覆层表面材料在摩擦力作用下断裂脱落形成磨屑塞积在对磨面之间，并在循环摩擦力的作用下反复刮擦熔覆层表面形成了较深的犁沟。此外，随着摩擦实验的进行，熔覆层表面温度不断升高，使对磨件与熔覆层材料产生局部焊合，在摩擦力作用下，焊合区域被撕裂，熔覆层材料剥落并附着在磨痕表面，形成凹坑和黏着物。因此，激光冲击前熔覆层的磨损形式为磨粒磨损和黏着磨损［27］。由图12（b）可知，激光冲击后熔覆层磨痕表面犁沟较少且较浅，磨损表面较激光冲击前平整，且黏着物和熔覆材料剥落现象明显减少，其磨损形式主要为磨粒磨损，这些现象的产生表明熔覆层耐磨性较冲击前得到显著提升，相比之下，激光冲击后熔覆层的耐磨性更好。此外，由上述激光冲击前后组织形貌的对比可知，经过激光冲击处理后的组织由层片状α相逐渐转化为具有更高强度和硬度的针状马氏体α′相，同时激光冲击后的熔覆层组织变得更加致密，组织分布也更加均匀，硬度显著提升，在这些优势的共同作用下，激光冲击后的熔覆层抵抗外部压力和磨损的能力大幅度增强，使其耐磨性远高于激光冲击前的熔覆层，表现出良好的耐磨性。
2.5 熔覆层耐腐蚀性能分析
激光冲击前后熔覆层的动电位极化曲线如图13所示。Ti-6Al-4V合金熔覆层激光冲击前后的腐蚀电位（Ecorr）值分别为-0.344 V和-0.317 V，腐蚀电流密度（icorr）值分别为7.342×10-7 A·cm-2和6.471×10-7 A·cm-2，相比之下，激光冲击使得熔覆层的腐蚀电位（Ecorr）值提高了0.027 V，腐蚀电流密度（icorr）值降低了8.71×10-8 A·cm-2，表明激光冲击后的熔覆层腐蚀倾向更低，腐蚀速率更缓慢，具有更好的耐腐蚀性能［28］。从图13可知，激光冲击后熔覆层的动电位极化曲线在0.172~0.120 V电位区间内，阳极电流密度在很小的范围内波动，激光冲击后熔覆层发生了钝化，且无明显的活化-钝化过渡，钝化电位Epp为-0.172 V。钛和氧的亲和力较强，在空气或含氧介质中，Ti-6Al-4V合金表面会形成一层致密且附着力强的惰性氧化膜，从而保护其免受腐蚀［29］。Ti-6Al-4V合金具有强烈的钝化倾向，激光熔覆后熔覆层表现出相似的腐蚀行为，激光冲击后的熔覆层使钝化行为更快且更容易发生，钝化膜将熔覆层与腐蚀介质完全隔开，使熔覆层基本停止溶解形成钝态达到防腐蚀的作用。此外，激光冲击过程中会在Ti-6Al-4V合金熔覆层表面及内部形成残余压应力场，一方面残余压应力能减少熔覆层中裂纹的萌生和扩展，有效阻止腐蚀介质的侵入，从而提高其耐腐蚀性能；另一方面残余压应力使熔覆层的微观结构更加紧密，晶界和相界等微观缺陷得到一定程度的闭合，使得腐蚀介质难以渗透到熔覆层内部，降低了腐蚀发生的概率。如图5（a-2）所示，激光冲击使Ti-6Al-4V合金熔覆层的晶粒得到细化，晶粒尺寸减小，晶界密度大幅增加。腐蚀介质在晶界处的扩散速度比在晶粒内部慢得多，增加晶界密度有利于形成致密的钝化膜［30］，阻碍腐蚀介质的扩散，从而提高熔覆层的耐腐蚀性能。
3 结论
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（1）激光冲击前熔覆层以片层组织为主，激光冲击后熔覆层中片状β-Ti和针状马氏体α′-Ti明显细化，网篮组织呈现更为密集的交错状态，有利于熔覆层强度和硬度的提升。
（2）激光冲击后熔覆层显微硬度为470~530HV0.2，较激光冲击前提升效果显著，激光冲击强化的显微硬度影响层深度约为1.7 mm，覆盖了熔覆层85%的区域，且对基材无影响。激光冲击后熔覆层的平均摩擦因数降低了16.67%，体积磨损量减少了25.93%，激光冲击后熔覆层耐磨性能显著提升。
（3）激光冲击可促进熔覆层表面残余拉应力向压应力的转化，熔覆层表面产生了约379 MPa的残余压应力，且应力分布状态得到改善。
（4）激光冲击后熔覆层的腐蚀电位（Ecorr）值升高了0.027 V，腐蚀电流密度（icorr）值降低了8.71×10-8 A·cm-2，熔覆层腐蚀倾向更低，腐蚀速率更缓慢，具有更好的耐腐蚀性能，且激光冲击后熔覆层更容易发生钝化行为。
基金
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  • 江苏省大学生创新创业计划项目(202411463045Y)
  • 国家重点研发计划(2019YFB1311100)
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2026年第54卷第7期
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doi: 10.11868/j.issn.1001-4381.2024.000684
  • 接收时间：2024-09-30
  • 首发时间：2026-10-28
  • 出版时间：2026-07-20
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  • 收稿日期：2024-09-30
  • 录用日期：2024-10-29
基金
江苏省大学生创新创业计划项目(202411463045Y)
国家重点研发计划(2019YFB1311100)
作者信息
    江苏理工学院 机械工程学院，江苏 常州 213001

通讯作者:

任维彬（1983—），男，副教授，博士，主要研究方向为激光再制造形状与性能控制，联系地址：江苏省常州市中吴大道1801号江苏理工学院机械工程学院（213001），E-mail：
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2种不同金属材料的力学参数
科
Family		 属数
Number of
genus		 种数
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
species (%)
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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