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Article(id=1321935444258967671, tenantId=1146029695717560320, journalId=1220038251117760515, issueId=1321927083589227197, articleNumber=null, orderNo=null, doi=10.11868/j.issn.1001-4381.2025.000143, pmid=null, cstr=32421.14.j.issn.1001-4381.2025.000143, oa=null, hot=null, price=null, onlineType=0, articleFormat=0, articleType=null, articleTypeStr=research-article, receivedDate=1741708800000, receivedDateStr=2025-03-12, revisedDate=null, revisedDateStr=null, acceptedDate=1751299200000, acceptedDateStr=2025-07-01, onlineDate=1793103570283, onlineDateStr=2026-10-27, pubDate=1776614400000, pubDateStr=2026-04-20, doiRegisterDate=null, doiRegisterDateStr=null, onlineIssueDate=1793103570283, onlineIssueDateStr=2026-10-27, onlineJustAcceptDate=null, onlineJustAcceptDateStr=null, onlineFirstDate=null, onlineFirstDateStr=null, sourceXml=null, magXml=null, createTime=1793103570283, creator=13701087609, updateTime=1793103570283, updator=13701087609, issue=Issue{id=1321927083589227197, tenantId=1146029695717560320, journalId=1220038251117760515, year='2026', volume='54', issue='4', pageStart='1', pageEnd='345', issueExtLink='null', onlineDate='null', pubDate='1776614400000', pubDateStr='2026-04-20', beforeIssueId=null, nextIssueId=null, price=null, status=1, issueComplete=1, articleOrder=1, issueType=-1, specialIssue=null, createTime=1793101576945, creator='13701087609', updateTime=1793101576945, updator='13701087609', preIssue=null, nextIssue=null, articleTotal=null, ext=null, issueFiles=null, downloadFileDto=null}, startPage=282, endPage=289, ext={EN=ArticleExt(id=1321935444539986040, articleId=1321935444258967671, tenantId=1146029695717560320, journalId=1220038251117760515, language=EN, title=Microstructures and tensile properties of TiC/GH5188 composites manufactured by laser melting deposition, columnId=1220689384450478826, journalTitle=Journal of Materials Engineering, columnName=RESEARCH ARTICLE, runingTitle=null, highlight=null, articleAbstract=

To improve the high-temperature performance of GH5188 cobalt-based superalloy， 10%（volume fraction） TiC particle-reinforced GH5188 composites are fabricated by laser melting deposition （LMD）. The microstructure and tensile properties are investigated， and the interfacial forming mechanism and the cause of the high-temperature performance degradation are discussed. The results show that the composite consists of TiC， （W，Ti）C1-x， and the austenitic γ phase. The submicron-thick （W，Ti）C1-x interfacial layer forms between the TiC particles and the matrix. The interfacial layer originates from the partial dissolution of TiC and the diffusion and substitution of W elements during the laser melting deposition process. At room temperature， the ultimate tensile strength （UTS） of the composite reaches 1198.9 MPa， which is 24.3% higher than that of the matrix alloy （964.3 MPa）. However， at 1000 ℃， the UTS of the composite is 128.7 MPa， which is lower than the 162.5 MPa of the matrix alloy， with a decrease of 20.8%. The degradation in high-temperature strength is mainly due to the consumption of W elements in the matrix by the （W，Ti）C1-x interfacial layer， resulting in decrease in its mass fraction and weakening the solid-solution strengthening and dislocation-pinning effects on the matrix.

, authors=Yan WANG, Wei LIU, Neng LI, Chao GAO, Huaping XIONG, authorsList=Yan WANG, Wei LIU, Neng LI, Chao GAO, Huaping XIONG, authorCompany=null, correspAuthors=Huaping XIONG, 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=1321935446406451337, articleId=1321935444258967671, tenantId=1146029695717560320, journalId=1220038251117760515, language=CN, title=激光熔化沉积TiC/GH5188复合材料的微观组织及拉伸性能, columnId=1220689384622445292, journalTitle=材料工程, columnName=研究论文, runingTitle=null, highlight=null, articleAbstract=

为提升GH5188钴基高温合金的高温性能，采用激光熔化沉积制备体积分数为10%的TiC颗粒增强GH5188复合材料（10%TiC/GH5188），研究其微观组织和拉伸性能，并分析其界面形成机理及高温性能下降原因。结果表明：10%TiC/GH5188复合材料主要由TiC、（W，Ti）C1-x 和γ奥氏体相组成，其中，TiC颗粒与基体间形成亚微米厚（W，Ti）C1-x 界面层，该界面层的形成源于激光熔化沉积过程中TiC的部分溶解以及W元素的扩散与取代。室温下，10%TiC/GH5188复合材料抗拉强度为1198.9 MPa，较基体合金（964.3 MPa）提高了24.3%，但在1000 ℃时，复合材料抗拉强度为128.7 MPa，低于基体合金的162.5 MPa，降幅达20.8%。高温强度的下降主要是由于（W，Ti）C1-x 界面层消耗基体中的W元素，导致其质量分数下降，削弱对基体的固溶强化与位错钉扎作用。

, authors=王艳, 刘伟, 李能, 高超, 熊华平, authorsList=王艳, 刘伟, 李能, 高超, 熊华平, authorCompany=null, correspAuthors=熊华平, authorNote=null, correspAuthorsNote=
熊华平（1969—），男，研究员，博士生导师，研究方向为航空新材料焊接技术、新型焊接材料研制、增材制造等，联系地址：北京市81信箱20分箱（100095），E-mail：
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Chemical compositions of GH5188 powder（mass fraction/%）

, figureFileSmall=null, figureFileBig=null, tableContent=
CCrNiWFeMnLaSi
0.09922.7822.6414.51.211.000.0230.42
BPSAgBiPbCuCo
<0.003<0.003<0.002<0.0005<0.0001<0.0005<0.010Bal.
), ArticleFig(id=1321935454065250497, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1321935444258967671, language=CN, label=表1, caption=

GH5188粉末化学成分（质量分数/%）

, figureFileSmall=null, figureFileBig=null, tableContent=
CCrNiWFeMnLaSi
0.09922.7822.6414.51.211.000.0230.42
BPSAgBiPbCuCo
<0.003<0.003<0.002<0.0005<0.0001<0.0005<0.010Bal.
), ArticleFig(id=1321935454161719490, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1321935444258967671, language=EN, label=Table 2, caption=

Process parameters of laser melting deposition

, figureFileSmall=null, figureFileBig=null, tableContent=
Laser power/WLaser scanning speed/（mm·min-1）Powder feed rate/（g·min-1）Argon gas flow rate/（L·min-1）Overlap rate/%
50070062050
), ArticleFig(id=1321935454253994179, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1321935444258967671, language=CN, label=表2, caption=

激光熔化沉积工艺参数

, figureFileSmall=null, figureFileBig=null, tableContent=
Laser power/WLaser scanning speed/（mm·min-1）Powder feed rate/（g·min-1）Argon gas flow rate/（L·min-1）Overlap rate/%
50070062050
), ArticleFig(id=1321935454329491652, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1321935444258967671, language=EN, label=Table 3, caption=

EDS analysis results of micro-zones in Fig.5 （mass fraction/%）

, figureFileSmall=null, figureFileBig=null, tableContent=
ZoneCTiCrCoNiMoW
A4.3840.115.291.120.710.6647.72
B3.9041.814.740.890.620.3648.69
), ArticleFig(id=1321935454396600517, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1321935444258967671, language=CN, label=表 3, caption=

图5中微区的EDS分析结果（质量分数/%）

, figureFileSmall=null, figureFileBig=null, tableContent=
ZoneCTiCrCoNiMoW
A4.3840.115.291.120.710.6647.72
B3.9041.814.740.890.620.3648.69
), ArticleFig(id=1321935454459515078, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1321935444258967671, language=EN, label=Table 4, caption=

EDS analysis results of spots 1-10 in Fig.7

, figureFileSmall=null, figureFileBig=null, tableContent=
SpotMass fraction/%
CoNiCrCTiWFe
131.128.121.60.83.110.94.1
232.429.221.30.52.110.64.2
331.829.221.10.62.110.54.2
431.928.920.71.02.310.94.3
532.029.421.11.12.010.54.2
631.228.121.01.13.511.24.2
732.028.921.60.52.210.94.3
831.428.921.40.52.010.74.3
932.129.221.30.62.010.84.3
1030.027.520.70.53.611.64.1
Average31.628.821.20.72.510.94.2
), ArticleFig(id=1321935454539206855, tenantId=1146029695717560320, journalId=1220038251117760515, articleId=1321935444258967671, language=CN, label=表4, caption=

图7 中点1~10的EDS分析结果

, figureFileSmall=null, figureFileBig=null, tableContent=
SpotMass fraction/%
CoNiCrCTiWFe
131.128.121.60.83.110.94.1
232.429.221.30.52.110.64.2
331.829.221.10.62.110.54.2
431.928.920.71.02.310.94.3
532.029.421.11.12.010.54.2
631.228.121.01.13.511.24.2
732.028.921.60.52.210.94.3
831.428.921.40.52.010.74.3
932.129.221.30.62.010.84.3
1030.027.520.70.53.611.64.1
Average31.628.821.20.72.510.94.2
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激光熔化沉积TiC/GH5188复合材料的微观组织及拉伸性能
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王艳 , 刘伟 , 李能 , 高超 , 熊华平
材料工程 | 研究论文 2026,54(4): 282-289
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材料工程 |研究论文 2026 , 54 (4) : 282 -289
激光熔化沉积TiC/GH5188复合材料的微观组织及拉伸性能
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王艳, 刘伟, 李能, 高超, 熊华平
作者信息
  • 中国航发北京航空材料研究院 3D打印研究与工程技术中心，北京 100095
通讯作者:
熊华平（1969—），男，研究员，博士生导师，研究方向为航空新材料焊接技术、新型焊接材料研制、增材制造等，联系地址：北京市81信箱20分箱（100095），E-mail：
Microstructures and tensile properties of TiC/GH5188 composites manufactured by laser melting deposition
Yan WANG, Wei LIU, Neng LI, Chao GAO, Huaping XIONG
Affiliations
  • D Printing Research ＆ Engineering Technology Center，AECC Beijing Institute of Aeronautical Materials，Beijing 100095，China
出版时间: 2026-04-20 doi: 10.11868/j.issn.1001-4381.2025.000143
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摘要
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为提升GH5188钴基高温合金的高温性能，采用激光熔化沉积制备体积分数为10%的TiC颗粒增强GH5188复合材料（10%TiC/GH5188），研究其微观组织和拉伸性能，并分析其界面形成机理及高温性能下降原因。结果表明：10%TiC/GH5188复合材料主要由TiC、（W，Ti）C1-x 和γ奥氏体相组成，其中，TiC颗粒与基体间形成亚微米厚（W，Ti）C1-x 界面层，该界面层的形成源于激光熔化沉积过程中TiC的部分溶解以及W元素的扩散与取代。室温下，10%TiC/GH5188复合材料抗拉强度为1198.9 MPa，较基体合金（964.3 MPa）提高了24.3%，但在1000 ℃时，复合材料抗拉强度为128.7 MPa，低于基体合金的162.5 MPa，降幅达20.8%。高温强度的下降主要是由于（W，Ti）C1-x 界面层消耗基体中的W元素，导致其质量分数下降，削弱对基体的固溶强化与位错钉扎作用。

激光熔化沉积  /  TiC/GH5188复合材料  /  微观组织  /  拉伸性能  /  成形机理

To improve the high-temperature performance of GH5188 cobalt-based superalloy， 10%（volume fraction） TiC particle-reinforced GH5188 composites are fabricated by laser melting deposition （LMD）. The microstructure and tensile properties are investigated， and the interfacial forming mechanism and the cause of the high-temperature performance degradation are discussed. The results show that the composite consists of TiC， （W，Ti）C1-x， and the austenitic γ phase. The submicron-thick （W，Ti）C1-x interfacial layer forms between the TiC particles and the matrix. The interfacial layer originates from the partial dissolution of TiC and the diffusion and substitution of W elements during the laser melting deposition process. At room temperature， the ultimate tensile strength （UTS） of the composite reaches 1198.9 MPa， which is 24.3% higher than that of the matrix alloy （964.3 MPa）. However， at 1000 ℃， the UTS of the composite is 128.7 MPa， which is lower than the 162.5 MPa of the matrix alloy， with a decrease of 20.8%. The degradation in high-temperature strength is mainly due to the consumption of W elements in the matrix by the （W，Ti）C1-x interfacial layer， resulting in decrease in its mass fraction and weakening the solid-solution strengthening and dislocation-pinning effects on the matrix.

laser melting deposition  /  TiC/GH5188 composite  /  microstructure  /  tensile property  /  forming mechanism
王艳, 刘伟, 李能, 高超, 熊华平. 激光熔化沉积TiC/GH5188复合材料的微观组织及拉伸性能. 材料工程, 2026 , 54 (4) : 282 -289 . DOI: 10.11868/j.issn.1001-4381.2025.000143
Yan WANG, Wei LIU, Neng LI, Chao GAO, Huaping XIONG. Microstructures and tensile properties of TiC/GH5188 composites manufactured by laser melting deposition[J]. Journal of Materials Engineering, 2026 , 54 (4) : 282 -289 . DOI: 10.11868/j.issn.1001-4381.2025.000143
正文
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GH5188是添加质量分数为13%~16%的钨、20%~24%的铬和微量镧的一种固溶强化钴基高温合金，具有优异的高温热稳定性和抗氧化性、良好的成形性和可焊性［1］，被广泛应用于燃气轮机、核电、航空航天等领域，如燃烧室、热交换器、火焰管、排气喷嘴等耐高温部件，使用温度接近1000 ℃［2-3］。由于金属基复合材料结合了金属基体的良好韧性和塑性，以及增强相的高强度、高硬度、耐磨、耐热等特性，使得它能够在高温、高压、高磨损等恶劣环境下保持稳定的性能［4］。为了进一步提高合金的高温性能，一般采用陶瓷颗粒增强高温合金形成金属基复合材料。目前，制备颗粒增强金属基复合材料的方法主要有粉末冶金法、铸造法、原位复合法和喷射沉积法等。然而，这些传统制备方法不仅浪费材料，还会增加制造成本和时间。激光增材制造工艺是一种以“3D”数字模型为基础，在激光热源作用下材料逐层累积形成形状复杂近成形致密金属零件的过程［5-7］。在激光选区熔化（selective laser melting， SLM）成形GH5188合金方面，学者们研究了不同工艺参数对试样硬度和拉伸性能的影响，发现SLM成形GH5188试样的硬度和抗拉强度均优于同成分热轧板，但断后伸长率有所降低［8-9］。张元伟等［10］对SLM成形GH5188试样进行了1180 ℃与1200 ℃固溶处理，初步掌握了该合金组织与性能的调控方法。赵楠等［11］发现，超声滚压可以有效改善GH5188涂层的硬度、耐磨性和耐腐蚀性等力学性能。然而，针对激光熔化沉积（laser melting deposition，LMD）制备TiC陶瓷颗粒增强GH5188高温合金复合材料的研究鲜见报道。
本工作选用高熔点（3140 ℃）、高硬度（3400HV）、低密度（4.93 g/cm³）且与钴基高温合金冶金相容性良好的TiC颗粒作为耐高温增强相，采用LMD技术制备TiC体积分数为10%的GH5188钴基复合材料（记为10%TiC/GH5188），重点研究该复合材料的微观组织及其在室温（25 ℃）和高温（1000 ℃）下的拉伸性能，同时分析TiC颗粒在沉积过程中的溶解-再析出行为，阐明颗粒与基体间界面层的形成机制，为高性能钴基复合材料在航空航天高温部件上的设计与应用提供实验依据与技术支撑。
1 实验材料与方法
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1.1 实验材料
本工作所用实验材料为GH5188合金粉末（中航迈特增材科技（北京）有限公司提供），采用气雾化工艺制备，其化学成分如表1所示。各元素含量均符合GH5188合金的标准要求。粉末的粒径分布与形貌如图1所示，可以看出，粉末整体呈球形，粒径分布相对集中，D10、D50和D90分别为60.6、79.8 μm和108.5 μm，表现出良好的流动性与激光增材制造工艺适应性。TiC颗粒由北京兴荣源科技有限公司提供，平均粒径为2.6 μm，其形貌如图2（a）所示。采用高能球磨方式混合GH5188合金粉末与TiC颗粒，TiC颗粒的体积分数设定为10%，使得TiC颗粒均匀包覆在高温合金粉末表面，最终获得TiC颗粒均匀分布的复合粉末（如图2（b）所示）。球磨过程中的球料比为10∶1，转速为300 r/min，球磨时间为3 h。
1.2 实验方法
10%TiC/GH5188复合材料的制备：厚度为12 mm的GH5188锻件板材作为基板，采用激光熔化沉积设备（阿诺德激光加工综合系统）将TiC/GH5188高温合金复合粉末沉积到基板上。沉积试样尺寸为45 mm×15 mm×4 mm，激光熔化沉积工艺参数如表2所示。其中，为了获得高质量沉积试样，相邻层采用垂直交叉打印的方式进行。
1.3 材料微观组织表征和性能测试
采用线切割机将复合材料从基板上分离，随后沿沉积方向切取尺寸为10 mm×4 mm的试样。将试样镶嵌于环氧树脂中，使用QG-4A型金相镶嵌机制备成直径30 mm、高15 mm的圆柱形金相试样。经砂纸打磨后，采用金刚石抛光液进行最终抛光处理。抛光后的试样使用JSM-7900F型扫描电镜（SEM）及配套的JEOL JXA-8230型电子探针（EPMA）进行显微组织与拉伸断口形貌观察。板状拉伸试样总长度为 34 mm，标距段尺寸（长×宽）为 10 mm×1.2 mm。其中，每种状态制备3个平行试样，结果取其平均值。室温与高温拉伸实验分别在MTS Model C45和Instron 8801电子万能试验机上进行，分别依据GB/T 228.2—2010与GB/T 228.2—2015标准执行。高温拉伸实验采用电阻炉加热，试样在1000 ℃保温30 min，然后以1 mm/min的应变速率加载。
2 结果与分析
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2.1 TiC/GH5188复合材料微观组织
10%TiC/GH5188复合材料的微观组织如图3所示。可以看出，组织内主要含有TiC颗粒、条状和块状白色物相以及基体（γ奥氏体），其中部分TiC颗粒被白色物相所包围，即在TiC颗粒和基体之间有界面层物相生成。
采用EPMA分析10%TiC/GH5188复合材料元素面分布，如图4所示。可以看出，黑色颗粒中出现C、Ti元素的富集，推测黑色颗粒为TiC。C、W、Ti三种元素在空间上具有相同的分布，推测白色物相可能由这三种元素组成。Cr、Ni基体元素分布较为均匀，但白色物相区域未见其存在。这是由于电子显微探针在测试微观组织过程中采用15 kV电压，其对应的探测深度大约为300 nm，而本工作中的增强相颗粒尺寸在500 nm之内，因此在白色物相存在的区域检测不到这些元素。
为了确定白色物相的化学成分，采用TEM进行分析。不同形貌白色物相的明场相及相应选区电子衍射（selected area electron diffraction，SAED）如图5所示，各微区的EDS分析结果见表3。根据图5和表3可知，白色物相主要由C、Ti和W元素组成。通过SAED进行标定，发现其均为同一种物相 （W， Ti）C1-x。另外，发现白色物相中还含有Cr、Co、Ni、Mo元素。这可能是由于透射电镜的精度不够，使得探测范围大于块状颗粒的最小尺寸（400 nm）及长条状颗粒的最小尺寸（200 nm），因此基体中的Cr、Co、Ni、Mo元素被探测到，从而带来误差。其中，Cr元素含量相对其他元素（Co、Ni、Mo）含量高，可能是由于Cr与C元素易形成M23C6型碳化物，使得其在白色物相（（W， Ti）C1-x ）附近出现富集现象。
2.2 TiC/GH5188复合材料室温和高温拉伸性能
GH5188沉积试样（0%TiC/GH5188）和10%TiC/GH5188复合材料的室温、高温拉伸性能，如图6所示。可以发现，10%TiC/GH5188复合材料室温下的抗拉强度（UTS）、屈服强度（yield strength，YS）分别为1198.9、759.1 MPa，高于0%TiC/GH5188的964.3、661.7 MPa，抗拉强度提高了24.3%，而伸长率（elongation，EL）反之。这与陶瓷颗粒增强金属基复合材料的现象相一致［12］。然而，在1000 ℃高温下，10%TiC/GH5188复合材料的UTS为128.7 MPa，反而低于0%TiC/GH5188的162.5 MPa，降幅达20.8%。
结合图5发现，基体中W元素富集于TiC颗粒表面，形成（W，Ti）C1-x 界面层，导致基体中W元素含量降低。于潇翔［13］指出，W元素可通过提高割阶形成能和空位扩散势垒有效地抑制位错的攀移，从而提高合金的力学性能。程远等［14］表明，W原子的半径远大于Ni、Co原子的，固溶于镍钴合金中会导致晶格扭曲和剪切模量发生变化，形成较大的长程应力场，提高材料错配度，造成位错运动阻力增大，进而提高材料的力学性能。同时，W元素具有热强性，在合金中添加W元素不但会提高固溶强化效果，还可以单向降低γ相的层错能，显著提高合金的高温力学性能和高温蠕变强度［15］。此外，Pröbstle等［16］和Yuan等［17］研究表明，位错攀移与原子的扩散速率密切相关，而W元素会降低扩散速率，导致位错攀移速率下降，提高材料的力学性能。Hu等［18］和Yu等［19］通过第一性原理计算表明，W元素会与位错周围的Ni原子成键，使得位错更加稳定不易移动，同时可钉扎位错，阻碍位错的移动。上述结果均表明，W元素对于合金的力学性能具有重要作用。复合材料高温性能的降低主要是由于基体中W元素含量的下降，进而导致合金基体的高温性能下降。
采用电子显微探针对10%TiC/GH5188复合材料的基体成分进行测试，如图7所示。图中点1~10的EDS分析结果见表4。由表4发现，合金中Co、Cr元素含量均在GH5188合金范围内，而W元素的质量分数从14.5%（10个点的平均值）降低到10.9%。说明通过调整GH5188合金中W含量，可以保证合金基体的高温性能，进而提高TiC/GH88复合材料的高温性能，因此，未来可通过调控W元素含量或优化界面相成分来实现复合材料高温性能的提升。
2.3 TiC颗粒溶解再析出机制和界面层成形机理
2.3.1 TiC/GH5188复合材料溶解再析出机制
一般情况下，在激光束的作用下复合材料对激光束的吸收率主要依赖激光的波长和材料的电阻率［20］。
α=0.35ρλ
式中：α为激光吸收率；ρ为电阻率；λ为激光波长。该复合材料中，TiC颗粒电阻率为138~188 μΩ·m，GH5188合金电阻率为1.051 μΩ·m，可以看出，TiC颗粒的激光吸收率远大于GH5188合金。当激光束作用到复合粉末上时，TiC优先吸收的大量热量使得熔池温度迅速升高，导致复合粉末表面的小颗粒TiC完全熔化或部分熔化。熔池内温度达到GH5188合金熔点（1300~1360 ℃）时，高温合金粉末开始熔化，随着熔池内温度的升高，TiC颗粒不断熔化进入到熔池内，使得TiC颗粒在液相中的溶解度不断增大。激光束移走后，熔池内温度快速降低，TiC颗粒在液相中的溶解度逐渐减小，促使其从过饱和溶液中析出。
结合图4发现，10%TiC/GH5188复合材料组织中主要有两种析出相，一种为TiC析出相，另一种为（W，Ti）C1-x 析出相。析出相的形貌主要受生长动力学和溶质转移的影响，其中，TiC析出相主要有两种形貌，一种为条状，另一种为块状［21］。然而本工作中观察到的TiC颗粒形貌多为球形，少量为星形［22］。球形形貌的形成原因：一方面，激光熔化沉积过程中熔池温度极高（可达3500 K），这足以使小尺寸TiC颗粒和高温合金粉末完全熔化形成均匀的熔体。TiC颗粒首先溶解于熔池中，随后在快速冷却过程中，TiC倾向于以表面能最低的形态从熔体中重新形核并析出，从而自发形成热力学更稳定的球形或近球形颗粒［23］；另一方面，对于大尺寸TiC颗粒，其不规则的棱角、锐边处由于具有较大的比表面积和内能，因而会吸收更多的热量，使其表面部分熔化形成球形形态［24］。此外，晶体生长后的现行面一般为密排面。TiC物相为面心立方结构，致密面为｛111｝面，因此｛111｝面为现形面。由于TiC晶体各位置的溶质过饱和程度不同，造成浓度梯度不均匀。过饱和程度大的角和边，其生长速度越快。TiC的特征生长方向为〈100〉，因而在〈100〉方向出现枝晶臂，由此呈现星形形貌的TiC颗粒。
在10%TiC/GH5188复合材料的微观组织中观察到，（W，Ti）C1-x 相主要以条状形态析出，块状形态相对较少。由潘卫东［25］的研究可知，尺寸较大的枝晶、花瓣相等一般为初生相，而条状相多为共晶产物。由此推断本工作中的条状（W，Ti）C1-x 相可能主要为共晶反应生成。
2.3.2 TiC/GH5188复合材料界面层成形机理
从图7可以看出，TiC颗粒表面与基体之间存在亚微米厚的界面层。界面层的生成原因是TiC颗粒发生溶解，分解出的Ti原子和C原子向基体扩散，同时基体中W元素是一种亲碳元素，故其向TiC颗粒扩散，导致Ti原子被原子半径更小的W原子取代，生成（W，Ti）C1-x 物相［26-27］。界面层的形成表明，TiC颗粒在激光快速熔融条件下对高温合金基体具有良好的润湿性，TiC颗粒与高温合金基体间发生适度的界面反应，从而形成良好的界面冶金结合。同时，界面层的存在降低了材料中出现孔隙的概率，因此，有利于复合材料力学性能的提高。
为了进一步确定组织内各物相的化学成分，采用TEM进行分析。图8为TiC颗粒与基体界面层形貌及不同物相SAED花样。可以看出，界面层厚度大约为250 nm，说明在TiC/GH5188复合材料中，TiC颗粒和基体之间具有良好的冶金结合，对应力的传递具有积极作用。对不同物相的电子衍射花样标定发现，颗粒中心为TiC，界面层为（W，Ti）C1-x 物相，基体为γ奥氏体。其中（W，Ti）C1-x 物相曾在砂模铸造的（W，Ti）C1-x /Fe基体复合材料中被提及［25］，表明该物相不是在熔体高温过程中形成，而是在金属凝固冷却过程中析出的，这更好地验证了在金属凝固过程中，未熔化的TiC颗粒作为异质形核的核心减小了金属凝固过程中所需的过冷度，促进（W，Ti）C1-x 物相结晶形核的过程。
3 结论
收起
（1） 通过LMD技术制备10%TiC/GH5188复合材料，其微观组织主要由TiC、（W，Ti）C1-x 及γ奥氏体三种物相构成。TiC颗粒与基体之间存在亚微米厚的（W，Ti）C1-x 界面层，该界面层的形成源于LMD过程中TiC的溶解及W元素的扩散与取代。
（2） 室温下，10%TiC/GH5188复合材料的抗拉强度为1198.9 MPa，较GH5188基体（964.3 MPa）显著提升24.3%，但伸长率有所下降。然而，在高温1000 ℃条件下，复合材料的抗拉强度（128.7 MPa）反而低于GH5188基体（162.5 MPa），呈现20.8%的强度衰减。这一现象归因于界面层（W，Ti）C1-x 形成过程中消耗合金基体中的W元素，导致基体中W的质量分数下降，削弱了固溶强化与位错钉扎效应。
（3） 在LMD冷却过程中，未熔的TiC颗粒作为（W，Ti）C1-x 物相异质形核的核心，促进（W，Ti）C1-x 相的析出过程。同时，基体中W元素通过扩散与取代形成界面层，增强颗粒与基体的冶金结合，但消耗基体中的W元素。

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doi: 10.11868/j.issn.1001-4381.2025.000143
  • 接收时间：2025-03-12
  • 首发时间：2026-10-27
  • 出版时间：2026-04-20
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  • 收稿日期：2025-03-12
  • 录用日期：2025-07-01
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    中国航发北京航空材料研究院 3D打印研究与工程技术中心，北京 100095

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熊华平（1969—），男，研究员，博士生导师，研究方向为航空新材料焊接技术、新型焊接材料研制、增材制造等，联系地址：北京市81信箱20分箱（100095），E-mail：
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鹅膏菌科Amanitaceae 2 11 5.26 鹅膏菌属 Amanita 10 4.78
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