氩弧熔覆原位自生（Ti，Nb）C增强镍基复合涂层的抗磨性能

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等离子熔覆镍基合金的组织及其冲蚀磨损性能

等离子熔覆镍基合金的组织及其冲蚀磨损性能刘胜林;孙冬柏;樊自拴;王国刚;俞宏英【期刊名称】《北京科技大学学报》【年(卷),期】2007(29)10【摘要】为提高不锈钢材料的耐冲蚀磨损性能,以Ni46合金粉末为原料, 采用等离子熔覆工艺在不锈钢1Cr18Ni9Ti基材上制备镍基合金涂层,分析了熔覆层的显微组织以及物相形貌和相结构等,测定了涂层的显微硬度. 使用旋转圆盘实验机研究了Ni基等离子熔覆合金涂层在砂浆中的冲蚀行为. 结果表明: 材料的冲蚀磨损性能受到材料基本力学性能的限制,高硬度镍基涂层的抗冲蚀性能最好,在相同实验条件下其磨损率由小到大排列顺序为镍基涂层＞0Cr13Ni5Mo＞1Cr18Ni9Ti;镍合金层中奥氏体基体的固溶强化和硬质相有效抵御砂砾的冲击,是Ni基等离子熔覆合金层具有高抗冲蚀性能的主要原因.【总页数】6页(P999-1004)【作者】刘胜林;孙冬柏;樊自拴;王国刚;俞宏英【作者单位】北京科技大学腐蚀与防护中心,北京,100083;北京科技大学腐蚀与防护中心,北京,100083;北京科技大学腐蚀与防护中心,北京,100083;北京科技大学腐蚀与防护中心,北京,100083;北京科技大学腐蚀与防护中心,北京,100083【正文语种】中文【中图分类】TG146.21【相关文献】1.Monel合金表面激光熔覆镍基合金的组织及摩擦磨损性能 [J], 张松;周磊;郝玉喜;张春华;王东生;王茂才2.氩弧熔覆含Al_2O_3-TiB_2增强颗粒的自熔性镍基合金复合层的冲蚀磨损性能[J], 董世知;马壮;陶莹;李智超;赵越超3.氧化铝增强镍基合金涂层的组织与耐冲蚀磨损性能研究 [J], 宫文彪;赵贺;孙大千4.718H模具钢表面等离子熔覆Ni60A镍基高温合金层的微观组织形成温度特征与显微硬度分布 [J], 李蓝特;陈雨楠;张天;胡永俊;刘伟聪;肖小亭;刘岗;李风;成晓玲5.激光熔覆镍基合金组织及磨损性能研究 [J], 李养良;白小波;王利;马明亮;席守谋因版权原因，仅展示原文概要，查看原文内容请购买。

氩弧熔敷原位合成TiC_p_Al基复合涂层组织及性能分析

第32卷第5期2011年5月焊接学报TRANSACTI ONS OF T HE C H I N A W ELDI NG I N STI TUTI ONV o.l 32 N o .5M ay 2011收稿日期:2009-12-23基金项目:黑龙江省教育厅基金资助项目(11551419);黑龙江科技学院青年教师基金项目氩弧熔敷原位合成TiC p /A l 基复合涂层组织及性能分析孟君晟, 史晓萍, 王振廷, 王永东(黑龙江科技学院材料科学与工程学院,哈尔滨 150027)摘要:利用氩弧熔敷技术,在ZL104合金表面原位合成了T i C p /A l 复合材料涂层,利用X 射线衍射、扫描电子显微镜及显微硬度计,研究了熔敷层的显微组织及性能.结果表明,(T i+C)含量在30%以下时,复合材料涂层组织由T i C 颗粒和块状的A l 3T i 组成;当(T i+C )含量在30%以上时,氩弧熔敷过程中可以充分反应合成T i C 颗粒;在所形成的T i C p /A l 复合材料层中,T i C 颗粒尺寸细小,约为1.5L m;经氩弧熔敷后的T i C p /A l 复合材料层中T i C 分布均匀,熔敷层与基体呈冶金结合,无裂纹、气孔等缺陷;熔敷层硬度从基体到表面呈梯度分布,涂层的显微硬度达到650HV 0.2,较基体提高近7倍.关键词:氩弧熔敷;原位合成;T i C ;复合涂层中图分类号:TG 174 文献标识码:A 文章编号:0253-360X (2011)05-0073-04孟君晟0 序言颗粒增强铝基复合材料具有制备工艺简单、价格便宜,在航空航天及汽车工业中得到了广泛应用[1].在增强颗粒中,T i C 具有高硬度、高熔点、高弹性模量、高温稳定性好、密度低、电导率高等一系列优点,广泛用于制备高性能复合材料的增强相,具有极大的开发价值和应用前景[2-4].目前,利用熔敷技术制备原位合成T i C 颗粒增强铝基表面复合涂层的研究较多,但主要集中在激光熔敷技术[5-7]等工艺方法上.然而,利用氩弧熔敷方法原位合成T i C p /A l 基复合材料的研究未见报道.文中利用氩弧熔敷原位合成的方法,在氩弧热源的作用下,使铝合金表面的铝粉、钛粉和碳粉发生原位反应,生成T i C 颗粒增强铝基复合材料涂层,通过原位合成工艺使增强体颗粒与基体的界面结合牢固、无污染[8,9].文中试验分析了氩弧熔敷技术制备T i C p /A l 基复合涂层的可行性,并对涂层的组织、结构、性能进行了分析.1 试验方法基体材料选用ZL104合金,试样尺寸为60mm@20mm @10mm ,试样表面经喷砂、碱洗、酸洗和丙酮清洗后,涂刷厚度为0.5~1.0mm 的A -l T -i C 粉末涂层.涂层材料选用平均粒度为20L m 的钛粉、平均粒度为30L m 的石墨粉作为熔敷材料,经搅拌式球磨机在氩气的保护气氛下混制10h 时后,用粘结剂将其调成糊状,涂敷于ZL104合金试样表面,预留2mm 左右的引弧端,放置于通风处24h,进行自然干燥.为保证充分反应,钛与碳的质量比按412B 1设计.涂层成分配比方案如表1所示.利用MW 3000型数字式焊接机对所得涂层进行氩弧熔敷,工艺参数为:电流100A,气体流量10L /m i n ,焊接速度6mm /s .表1 A-l T-i C 涂层粉末成分配比Tab le 1 Chem ica l co m positions o f A-l T-i C powde rT i+C (质量分数,%)粉末质量m /gT i C A l 200.600.15 4.25300.800.20 4.00401.000.253.75采用磨光、抛光工序制备金相试样,经腐蚀后利用MX )2600FE 型扫描电镜观察组织形貌,用D /MAX2200型X 射线衍射仪和OXFORD 能谱(EDS)对涂层进行物相分析.采用MHV 2000型显微硬度仪测量氩弧熔敷涂层的显微硬度,使用载荷为1.9674 焊接学报第32卷N,加载时间为10s ,沿氩弧熔敷层横断面的最厚点由表及里测定复合涂层的显微硬度.2 试验结果与分析图1为含量为20%(T i+C )和30%(T i+C)复合涂层的X 射线衍射分析结果.从图1中可以看出,铝粉质量分数不同,X 射线衍射结果也不相同.铝粉质量分数在70%时,反应产物中只有铝和T i C两种相,如图1a 所示;当铝粉的质量分数达到80%时,出现了A l 3T i 相,如图1b 所示.图1 复合涂层的X 射线衍射图谱F ig 11 XRD pa tt e rn o f argon sh i e l d ed a rc clad compo sitecoa ting图2为不同(T i+C )含量复合涂层显微组织形貌.从图2中可以看出,反应生成的T i C 颗粒尺寸变化较大,几乎都是近球形颗粒.当铝含量较高时(大于80%时),反应产物除了T i C 外,还有另一种反应产物条块状的A l 3T i 相生成(图2a).随着铝含量的降低,反应产物只有T i C 颗粒,不存在其它反应产物(图2b ,c),且T i C 颗粒分布比较均匀,这与XRD 的分析结果一致.另外,随着铝含量的增加,反应生成的T i C 尺寸明显变小.10%(T i+C)含量生成的T i C 颗粒尺寸小于0.1L m,20%(T i+C )含量生成的T i C 颗粒尺寸在0.2~0.5L m 之间,30%(T i+C )含量生成的T i C 颗粒尺寸约为1L m,40%(T i+C )含量生成的T i C 颗粒尺寸约为1.5L m .其原因可以认为随着铝含量的增加,钛、碳的浓度相对降低,在相同形核率的情况下,T i C 生长速度慢;而且铝含量的增加,反应的最高温度降低,在随后的冷却过程中反应产物的温度很快降低到固液区或固相区,造成T i 原子和C 原子之间的扩散困难,使T i C 的生长速度降低或无法继续再生长,同时,熔融铝相的存在也有抑制T i C 进一步长大的作用.所以随着铝含量的增加,作为反应生成物的T i C 颗粒尺寸细小.图2 不同(Ti+C)含量复合涂层显微组织形貌Fig 12 M icrostruc t u re o f argon sh ie l d ed a rc c l a d i n d iff e r -en t con t en ts o f (T i+C )compos ite coa ting图3为40%(T i+C )经氩弧熔敷后,熔敷层中部的SE M 照片.图中白色类球状颗粒为T i C ,其平均尺寸约为1.5L m.原位生成的T i C 颗粒尺寸细小且分布均匀.图3b 为图3a 中A 区域的高倍SE M 照片.第5期孟君晟,等:氩弧熔敷原位合成T i C p/A l基复合涂层组织及性能分析75图3复合涂层中TiC分布SEM组织形貌F ig13SEM m icrographs show i n g m icrostruct u re o f T i Cpa rtic l e s图4为40%(T i+C)复合涂层组织由表及里不同区域的SE M照片.其中图4a为熔敷层低倍组织形貌,图4b~d分别为图4a中A,B,C微区的高倍组织形貌.从图4中可以看出,复合涂层表面组织颗粒细小而均匀、数量多,如图4b所示.这与材料制备过程中快速冷却得到的非平衡组织有关,高温下形成的极细T i C初生晶粒在快冷中被保留,以亚稳态保存到室温.由于表面熔化温度高、冷却速度快,一方面石墨粒子与铝和钛充分接触,增加铝液与碳颗粒之间的接触润湿性,使反应充分进行,另一方面,为上述反应的进行提供更多的自由能,使体系的反应物活性得到显著提高,有利于固液界面化学反应的发生,使反应更加彻底.在表层与基体之间存在一个过渡层区域,如图4c所示.该区域的球状T i C颗粒较少,这主要是由于该区域温度较高,冷却速度慢,对于大颗粒而言处于饱和状态的溶体,对于小颗粒仍处于不饱和的状态,这会使小颗粒不稳定,易溶解而消失,即处于高温时重新溶入基体中.图4d所示为熔敷层底部,没有T i C颗粒生成,利用EDS对图中块状组织进行分析,其成分组成为78.32%A,l 21.68%T i(原子分数比为3.6B1),根据其A l/T i比,这种块状组织的物相为A l3T.i从截面整体来看,原图440%(T i+C)复合涂层不同区域的SEM组织形貌Fig14SEM m icrog raphs show i n g m i c rostructure in d iff e r-ent reg ions o f40%(T i+C)clad coa ting位形成的细小T i C弥散地分布在涂层的表层中,涂层与基体界面处无气孔、无裂纹.图5为40%T i C复合涂层显微硬度分布曲线.由图可见,涂层表面显微硬度很高,最高达650 HV0.2,向基体方向逐渐降低,呈梯度逐渐分布.形成梯度分布主要是由于原位形成的T i C颗粒与熔池76 焊接学报第32卷中流体的对流造成.熔敷区有大量的T i C 颗粒,越靠近表面组织越细小,且弥散分布.T i C 颗粒硬度较高,而周围的基体相较软,形成软基体上弥散分布细小硬质点的弥散强化效果,因此,熔敷表层硬度最高;在过渡区域及熔敷层底部,由于生成的T i C 颗粒较少或没有生成,导致硬度下降.图5 40%(Ti+C)复合涂层显微硬度分布曲线F ig 15 M icroha rdness pro fil e o f a rgon sh i e lded a rc clad40%(T i+C)composit e coa ting3 结论(1)利用氩弧熔敷方法在ZL104表面原位合成T i C 颗粒,复合涂层无气孔、夹杂等缺陷,界面呈冶金结合.(2)(T i+C)含量在30%以上时,氩弧熔敷复合涂层组织主要是由T i C 和铝组成.其中T i C 颗粒由球状组成;40%(T i+C )复合涂层由表及里组织不同,表层是球状的T i C 颗粒,存在过渡层,由细小的T i C 颗粒和A l 3T i 组成.(3)氩弧熔敷40%(T i+C)所得复合涂层的硬度高达650HV0.2,比基体提高了7倍.参考文献:[1] 王丽雪,曹丽云,刘海鸥.铝基复合材料研究的进展[J].轻合金加工技术,2005,33(8):10-12.W ang L i xue ,C ao L i yun,L i u H aiou .Progress of al um i n i um m atri x composites [J ].Li ght A lloy Fabr i cati on T echnology ,2005,33(8):10-12.[2] LocciA M,Orr R,C ao G ,et al .Lo w-grav i ty co m busti on s ynthe -s i s theoretical nalysis of experi m en tal evidences[J].Am erican In -stit u t e of Che m i ca l Engineers J ourna,l 2006,52(11):3744-3761.[3] Yang Yafeng ,W ang Hu iyuan,L i ang Yunhong ,et a l .Fab ri cati onof steelm atri x composites l ocall y re i nforced w it h d ifferent rati os of T i C /T i B 2particulates us i ng SH S reacti on s ofN -iT-iB 4C and N -i T -i B 4C-C s yste m s du ri ng casti ng [J].M at eri als S ci en ce and E ng-i neeri ng A,2007,445-446:398-404.[4] 吴玉萍,彭竹琴,林萍华.等离子原位合成T i C 颗粒增强N i基复合涂层[J].材料科学与工艺,2004,12(4):429-432.W u Yup i ng ,Peng Zhuq i n,L i n P i nghua .In-s it u s yn t h es i s of T i C parti cle rei nforced n i ck el base all oy co m posite coati ng by plas m a cladd i ng[J].M ateri als Sci en ce and T echnol ogy ,2004,12(4):429-432.[5] H u C,B aker T ser pressi ng to creat e in -sit u A -l S i C s u rfacem etalm atri x co m pos i tes[J].Jou rnal ofM aterial s Science ,1995,30(4):891-897.[6] M eng Y an ,H u H anq.i In-s it u l aser s u rface coati ng of T i C m eta-lm atrix co mpos i te l ayer[J].J ou rnal ofM aterial s S ci en ce ,1996,31(6):4303-4306.[7] 武晓雷,陈光南.激光形成原位T i C 颗粒增强涂层的组织及性能[J].金属学报,1998,34(12):1284-1288.W u X i aole,i Ch en Guangnan .M i crostr u ctural characteri sti cs and w ear prop erlies of i n s i tu f or m ed T i C particle rei n forced coati ngs by l aser cladd i ng [J ].A cta M etall urgi ca S i n ica ,1998,34(12):1284-1288.[8] 张柏清,马洪涛,李建国,等.A -l T -i C 中间合金细化剂的组织及其细化性能[J].金属学报,2000,36(4):341-346.Zhang Boqing ,M a H ongt ao ,L i Jianguo ,e t a l .Study on the m -i cros tructures and grai n refi n i ng perfoum ance ofA -l T-iC grai n ref -i n i ng m aster all oys[J].Act a M etall u rgica S i n ica ,2000,36(4):341-346.[9] 马乃恒,王浩伟,梁工英,等.激光熔敷原位合成T i C /A l 复合材料的化学反应机制[J].热加工工艺,2003(5):27-29.M a Nai heng ,W ang H ao w e,i Liang Gongyi ng ,e ta l .Che m ical reac -ti on m echan is m of i n-sit u syn t hesis of T i C /A l co mposite by l as er cladd i ng p rocess[J].H otW ork i ng Technol ogy ,2003(5):27-29.作者简介:孟君晟,男,1982年出生,博士研究生,工程师.主要从事材料表面工程科研及教学工作.发表论文10余篇.Ema i :l m eng j s2008@li ve .cnMA I N TOPI CS,ABSTRACTS&KEY WORDS2011,Vo.l32,N o.5 ti c;stress concentrationM i crostru ctures and solderability of SnCuN-i x Pr lead-freesolder LUO Ji adong,XU E Songba,i ZENG G uang,HU Yu-hua(Schoo l o fM ater ials Sc i ence and T echno l ogy,N an ji ng U n-iversity o f A eronau tics and A stronauti cs,N an jing210016,Ch-ina).p57-60Abstrac t:E ffects of ra re ea rt h e le m en t P r on t he w etti ngperfor m ance,m echan i ca l properti es and m icrostruc t ures ofSn017Cu0.05N i lead-free so l der w ere st udied.T he i nheren t re-lati onship bet w een the m i c rostructures and properties of t he so l d-e r w as preli m i naril y discussed.T he experi m ental results showtha t the s u itable amoun t o f P r add ition is0.025%-0.075%,andthe m ost appropriate a m ount is0.05%,a twh ich compositi on theso l der exhibits t he best w etting pe rf o r m ance and m echan i ca lproperties.T he surface tensi on o f the li qu i d so l der w as si gn if-icantl y reduced due t o the add iti on of rare earth P r and t he w e-tti ng perfor m ance w as i m proved.T he m i crostructures o f the so l d-e red jo i nts we re ev identl y refi ned,w hich resulted from the pi n-n i ng effec t on t he gra i n boundar i es m igrati on due t o the add iti onP r,and the s hear streng th was i m proved obv iously.It w as alsofound t hat t he activ it y of t he rare earth ele m ent of P r m ay be re-duced because of excess i ve ox i dati on and t he enlarge m en t of thecomprehens i ve e ffect o f stress field caused by excessive add iti ono f P r.K ey word s:Pb-free so lder;rare ea rt h ele m ent P r;w e-tti ng performance;mechan i ca l properties;m icrostructureAnal ysis on cont i nuous coo li n g tran sformation curves of si m-u lated heat affec ted zone for SA508-3stee l in nu clear po w erC H I L ux i n1,2,MA Y ong li n2,X I NG Shuq i ng2,ZHAOY ong tao2,C H E N Furong1,CHEN Zhongyi2(1.Schoo l o fM ate-rials Sc i ence and Eng i neeri ng,Inner M ongo li a U n i versity ofT echno l ogy,H uhhot010051,Ch i na;2.Schoo l ofM a teria l andM e tall urgy,Inner M ongo lia U niversit y o f Sc ience and T echno l o-gy,Baotou014010,Ch i na).p61-64Abstrac t:The SA508-3steel used in nuclear po w er w asused to deter m ine conti nuous coo ling transfo r m ati on(S H-CCT)d i agra m o f si m ulated heat a ffected zone(HAZ)by t her m a l ex-pansion m et hod on G leeb l e1500D t her m a l si m u l a ti on testi ng m a-ch i ne,and the m icrostructure character i stics o fHAZ a t t8/5fro m3.75s to20000s w ere i nvestigated.It w as found t ha t t he m-icrostructures w ere changed much from the base m eta l because ofthe i n fluence of the coo li ng ti m e(t8/5).W hen the t8/5is lessthan15s,the phase transfor m ation t o obta i n a ll m artensite hap-pens,t he coo li ng ti m e range to get all t he ba i n ite i s fro m60s to 3000s,and if a ll the fe rrite,and pearlite can be obta i ned if the t8/5ism o re than6000s.T he hardness of HA Z i s h i gher t han 350HV and there a re harden quench i ng tendency and t he cracksensitiv it y w hen the t8/5is less than100s,soften i ng pheno m ena eas il y happens and t he ha rdness o fHAZ i s l owe r t han t hat o f thebase m eta lwhen the t8/5ism o re t han20000s.T he co l d crack-i ng can be avo i ded on l y at t he proper preheati ng te m perature.K ey words:S A508-3stee;l coo li ng rate;con tinuous coo ling transfor m ation curves;crack sensiti v ityE ffec t of conten t of Ag on physical prop er ties and sol d er-ability of Sn0.7Cu so l der ZHAO Kua ile,YAN Y an f u, TANG Kun,S HENG Y angyang(Schoo l o f M ater i a l s Sc i ence&Eng i neer i ng,H enan U n i ve rs i ty of Sc i ence&T echno l ogy,L uoy-ang471003,Ch i na).p65-68Abstract:SnCu eutectic so l der is consi dered as t he m ost potenti a l substit utes o f SnPb so l der,particu l a rl y in w ave so lde-ri ng.But co m pared to o t her l ead-free solde rs,its poor phys i ca l properties and spread i ng pefor m ance li m its its w i de appli cation.A new solde r is m ade by add i ng trace A g into Sn0.7Cu a lloy to i m prove i ts pe rf o r m ance.T he resu lts show that content of A g has little i nfl uence on the m e lti ng po i nt of Sn0.7CuxA g solde r.T he m e lti ng po i nt o f Sn0.7Cu0.2A g is h i gher only0.3e than t hat o f ma tr i x so lder.T he resisti v ity increases w i th the i ncrease o f the content of A g.A t the sa m e ti m e,the spread i ng perfor m ance of the ne w so l der i s i m prov ed by add i ng trace A g i nto Sn0.7Cu. T he spreading a rea o f Sn0.7Cu0.2Ag reaches t he max i m u m va-l ue of28161mm2and i s inc reased25.5%than that of the m atr i x so l der,wh i ch is m a i n l y re lated t o the for m ati on of t he r i ch A g phase and t he thickness and shape of the m eta l i nter m eta llic compound bet ween the solder and t he substrate.K ey w ords:eutectic so lder;m e lti ng po i n t;res i sti v ity; spreadi ng areaAnal ysis of fatigue life of e lec tron bea m w elding sea m w ith b ell shap e YANG Bo1,YANG X i nhua1,FU W e i1,HU Shub i ng2,X I AO Ji anzhong2(1.Schoo l o f C i v il Eng i nee ri ng and M echan i cs,H uazhong U niversity of Sc i ence and T echno l ogy, W uhan430074,Ch i na;2.Schoo l o fM ate rials Sc i ence and En-g i neer i ng,Huazhong U n i versity of Science and T echnology,W u-han430074,Ch i na).p69-72Abstract:The bel-l shaped T C4titan i u m a ll oy j o i n t o f e-lectron bea m we l d i ng w ere d i v i ded i nto three zones,na m e l y w eld sea m,heat-a ffected zone and base me ta.l Conside ri ng the g rad-i ent distr i bution of the m ater ial streng th i n the heat-a ffected zone, the fi n ite ele m ent m ode l w as founded.T he series of so ft w are of M SC company we re used to ana l y ze the distri buti on of stress and fati gue life under the si m u lated experi m enta l l oadi ng cond iti ons, and the stress d i str i bution a l ong different paths w ere i nvesti ga-ted,and the si m u l a ti ng resu lts of fati gue life w ere compared w ith tha t of expe ri m en ts.It is shown that the we l d sea m has noticea-b l e e ffect on stress d istri buti on of t he w eld m ent,wh i ch causes the stress concentration w ith t he stress concentrati on facto r of about1.3at the w eld toe.The uneven distributi on o f w eld m ent life is caused by stress concentration,so t hat the fati gue life of w e l d m en t is reduced.The fatigue fa ilure usua lly starts at the w e l d toe.K ey words:TC4titaniu m a lloy;e lectron bea m w eldi ng; be l-l shaped w eld sea m;fatigue lif eM icrostru cture and proper ties of T i Cp/A l co mposite coat i ng by argon arc c l add ing M ENG Junsheng,S H I X i aopi ng, W ANG Zhenti ng,WANG Y ongdong(Schoo l of M ater i a ls Sc-i ence and Eng i nee ri ng,H e ilong jiang Insti tute of Sc i ence and T echno l ogy,H arb i n150027,Chi na).p73-76Abstract:By usi ng argon arc c ladd i ng,T i Cp/A l compos-ites coati ng was i n-situ syn t hesized on the ZL104a ll oy surface. T he m icrostruc t ures and prope rties o f the composites coati ngs w ere i nvesti ga ted by X-ray diffracto m eter,scann i ng e lectron m-i croscope and m icrohardness tester.T he resu lts show that if the content of(T i+C)i s less than30%dur i ng argon arc c laddi ng,both T i C particle and A l3T i co m pounds can be found.If the con-Ô2011,Vo.l32,N o.5TRANSACT I O NS OF THE C H I NA W ELD I N G I N ST I T UTI O Ntent of(T i+C)i s m ore t han30%duri ng argon arc c laddi ng, the fi ne T i C particles o f1.5L m i n s i ze can be comp l e tely syn-t hesized.T he unifo r m and conti nuous exce llent m eta ll urg i ca l bonding w it hout de fects bet w een the coati ng and the ZL104sub-strate w as obta i ned and the particles were dispe rsive l y distributed in t he coati ng.T he m i c roha rdness o f the coati ng s enhanced by the T i C pa rti c l es can reach650HV0.2,w hich is about7ti m es h i gher than that of the ZL104all oy.K ey word s:argon arc c laddi ng;i n-situ syn t hesis;T i C; composite coati ngN u m er i cal analysis on deformation of we l ded constructionC HEN Zhang lan,X I ONG Y unfeng(F acility of M ar i ne Eng-i neering,Ji m e iU n i versity,X ia m en361021,Ch i na).p77-80 Abstrac t:Some theo ries and m et hods o f structure m e-chan i cs w ere appli ed to s i m u l a te the efficiently w eldi ng defor m a-ti on.Since t he sea m size i s too s m a ll to contri bute itse lf to the streng t hen o f hug e constructi on,it can be rep l aced by resi dua l stra i n and stress in com plicated we l ded structure i n order to i m-prove the qua lity of AN SYS m esh i ng and save ca lculati ng ti m e. R es i dual stress and stra i n d i str i butions obta i ned by ther m a l elas-ti c and p l astic finite AN S Y S m ethod w ere analyzed,respectively. T he pr i nc i ple o f v irt ua l wo rk and the displace m en t m ethod w ere used to load the resi dua l stress and stra i n of we l d seam on the co rrespondi ng node in w elded structure,wh ich m ade t he stress and stra i n l oading process mo re conven i ent and usefu.l T he de-for m ation o fw elded structure i n si m u l a ti on w as proved by co m pa-ri ng t he exper i ence data.It w as proved that the m ethod t o si m u-late the w elding de f o r m ati on based on t he pri nc i ple of v irt ua l w ork and the displace m entm ethod can be used to pred i ct t he de-for m ation o f comp licated w e l ded structure.K ey words:pr i nciple o f v irt ua l w ork;d isplacem ent m ethod;w eldi ng defor m ation;nu m erica l analysisAnal ysis on si ngle arc w eld i ng w ith t w in electrode of TE4303 L I L i y i ng1,ZOU Zengda2,HAN B i n1,L I Chaow en1(1. Schoo l o fM echan ica l and E l ectron i c Eng i nee ri ng,Ch i na U n i ve r-sit y of Pe troleu m(East Ch i na),D ongy i ng257061,Ch i na;2. Schoo l o fM a terials Science and Eng ineer i ng,Shandong U n i v ers-i ty,Ji nan250061,Chi na).p81-84Abstrac t:S i ng le arc we ldi ng w ith t w i n electrode (TE4303)was st udied from the we l d i ng effi c i ency and energy sav i ng,m icro struct u re,m echan i ca l properties,and fracture m o r-pho l ogy.The results sho w t hat m elti ng coeffi c i ent and depo siti on coe fficient o f TE4303si ng le arc we l d i ng are as t w o ti m es h i gher as that o f the traditi onal si ng l e e l ectrode(E4303)arc w eldi ng. Co m pa red w ith E4303arc we l d i ng,TE4303s i ng le arc w e l d i ng can save e lectr i ca l energy about20%~30%t o m e lt per unit w e i ght of electrode me ta.l M ean wh ile,its we l d i ng heat i nput is lo w to ge t the s m all f usion rati o.The co lu mnar g ra i ns i n w e l d are much sli m m er at the sam e we l d i ng current.It i s a l so f ound t hat both the compositi ons and m echan i ca l properties o f the deposited m eta lm eet t he requ irem ents o f standards.T he ana l ys i s on frac-t u re appearance show s t hat it i s ductile fracture w ith d i m p l e m ode,and t he i nc l usi ons a re ox i des wh ich are analyzed by e l ec-tron probe m icroscope.K ey word s:t w i n e lectrode;si ng l e arc w e l d i ng;e fficien-cy and ene rgy sav i ng;m icrostructure;m echan ica l prope rties H eat sou rce model for partial p ene trati on lap laser w eld i ng of stain less steel ra il way veh icles S H I Chunyuan1,GUG uochen1,W ANG H ongx i ao1,2,JI N Cheng1,W ANG Chuns heng2(1.Schoo l ofM ater i a ls Sc i ence and Eng ineer i ng,D a lian Jiao t ong U niversit y,D ali an116028,China;2.Changchun R a il w ay V eh-i cles L td.,Co.,Changchun130062,Chi na).p85-88 Abstract:It i s an opti m u m m ethod to so l ve the prob l em on the appearance qua lity and tight ness o f sta i n l ess stee l ca r body by replaci ng resistance spot w e l d i ng w ith lap laser w e l ding.But in the expe ri m en ts o f partial penetrati on l ap l ase r w eldi ng,the shape o f mo lten poo l was f ound to be s i m il ar w ith a vase i n the comm on process i ng parame ters,wh i ch w as d ifferent fro m the no r-m al laser conducti ve w e l ding o r the l aser deep penetrati on w eld-ing.By usi ng the soft w are o f ABAQU S,the w eldi ng te mperature fi e l ds w ere si m ulated w it h d ifferent heat source models,such as G auss heat source,G auss heat source+con i ca l heat source, and3-D con i ca l heat source+i nverted con i ca l heat source+e-l li pso i d hea t source.The resu lts ind i cate that the shapes of m o-l ten poo l si m ulated by using3-D con i ca l heat source+i nverted con i ca l heat source+e lli pso i d hea t source agree w e ll w ith the experi m enta l resu lts.K ey word s:sta i n less steel ra il w ay veh i c les;lap l aser w e l ding;heat source mode;l nu m erica l s i m u l a ti onNon linear co m b i nation n eural network m odel of i n te lli gen t p red iction on electrod e prop er ties HUANG Jun,XU Y ue-lan(Schoo l ofM ate rials Sc i ence and Eng i neering,N an jing U n-i ve rsity o f Sc ience and T echno logy,N anji ng210094,Ch i na).p 89-92Abstract:The e l onga ti on a fter fracture and i m pac t energy o f the depos i ted m eta l by electrode w ere tested by expe ri m en ts.A non li nea r comb i nati on neura l net w ork model t o predict t he de-posited m etal m echanica l properti es by e lectrode w as bu ilt by taki ng predicted da ta acqu ired by s uch s i ng le m ode l s as BP, R BF and adap tive f uzzy neural net w ork as i nput para m eters.42 g roups o f exper i m enta l samp l es w ere used to trai n and verify the m ode.l T he resu lts sho w that the averag e re l a ti ve predicti on e r-ro rs of both e l ongati on after fracture and i m pact energy are less than5%and it sati sfies the de m ands of practical producti on.A n intelligent pred icti on system of e l ectrode properti es w as deve-l oped by M a tlab and v isual C++and it can co rrectly pred ict the elongation a fter fracture and i m pact ene rgy o f deposited m eta l by electrode accordi ng to the raw m ater i a l components.It prov i des a ne w,si m ple and effective way t o predict and contro l t he e l ec-trode qua lity.K ey words:adaptive fuzzy neura l net wo rk;deposited m eta;l carbon stee l e l ectrode;nonli near comb i nation pred i ctionM etallograph ic s a m p le p reparation of T i3A l alloy l aser we-l d ed joints for EB SD SONG Zh i hua1,WU A i p i ng1,ZOU G u i sheng1,W ANG G uoqi ng1,2,REN Jiali e1(1.D epart ment of M echan i ca l Eng i neer i ng,T si nghua U niversity,B eiji ng100084, Chi na;2.Chi na A cade m y o f L aunch V eh i c le T echno logy,Be-i ji ng100076,Ch i na).p93-96Abstract:R esearch of t he m icrostructure and tex t ure oflaser we l ded j o i n ts of T i3A l based all oy plays an i m portant ro le in i m prov i ng the properties o f the j o ints,wh ile the techn i que of electron backscatter diffrac ti on(EBSD)is an a ttracti ve me t hodÕ。

水轮机叶片氩弧熔覆WC涂层的组织和性能

水轮机叶片氩弧熔覆WC涂层的组织和性能魏仕勇;付青峰;张友亮【摘要】采用氩弧熔覆法对用于水轮机叶片的45碳钢进行WC涂层表面强化处理.利用扫描电镜、XRD、显微硬度计和磨损试验机对未熔覆涂层和熔覆WC涂层的45碳钢进行组织和性能分析.结果表明,氩弧电流对涂层表面形貌产生影响,电流为100 A时表面形貌最均匀.涂层组织除了稳态相Fe、WC外,还出现亚稳态W2C、Fe6W6C相.与未熔覆涂层相比,熔覆WC的碳钢表面显微硬度,磨损强度等性能显著提高.【期刊名称】《热处理技术与装备》【年(卷),期】2015(036)006【总页数】5页(P16-20)【关键词】氩弧熔覆;水轮机叶片;WC涂层【作者】魏仕勇;付青峰;张友亮【作者单位】江西省科学院铜钨新材料重点实验室,江西南昌330029;江西省科学院铜钨新材料重点实验室,江西南昌330029;江西省科学院铜钨新材料重点实验室,江西南昌330029【正文语种】中文【中图分类】TG174.444我国虽然是水力资源丰富的国家，但大部分河流水质却很差，尤其是小型河流，随着环境恶化(如水土流失，化学物品排放等)，导致河流中泥沙含量和腐蚀性偏重。

在这种环境下运行的水轮机机组，尤其是水轮机叶片不可避免地会遭受到气蚀或磨蚀的破坏。

全国每年因磨蚀问题而导致水轮机组更换、停机或检修造成的损失达数十亿元［1］，这严重制约着水电站的健康生产。

因此，解决水轮机机组磨蚀，尤其是水轮机叶片的磨蚀问题十分迫切。

目前，解决水轮机叶片抗磨蚀破坏主要有两种方法：一种是通过改变叶片的造型结构来提高叶片的流通性能;另外一种方法是运用耐气蚀、抗磨蚀性能强的材料作为叶片的加工材料。

从目前的应用来看，改变结构这种方法主要针对较大型的混流式和轴流式水轮机［2-3］，但对中小型水轮机的抗磨蚀效果并不明显。

而第二种方法对提高水轮机叶片的抗磨蚀性是有一定成效，但抗磨蚀性能好的材料(如0Cr13Ni4Mo，硼不锈钢等)却存在加工难，成本高等缺点，无法大面积推广应用。

氩弧熔敷原位自生TiC／Ni60A复合涂层的滑动磨损特性

（ｐｒｍｅｔｆＭａｅｉｌＳｉｎｅａｄＥｎｉｅｒｎＤｅａｔｎｔｒａｓｃｅｃｎｇｎｅｉｇ，ＨｅｌｎｊｎｎｔｕｅｏｏｉｇｉｇＩｓｉｔｆｏａｔｃｅｃｎｃｎｌｇ，ｒｉ５０７，ｉａＳｉｎｅａｄＴｅｈｏｏｙＨａｂｎ１０２Ｃｈｎ）
王振廷一孟君晟赵国刚
（龙江科技学院材料科学与工程学院，尔滨１０２）黑哈５０７
摘
要：利用氩弧熔敷技术，ＮｉＡ自熔合金粉、粉和石墨粉为原料，１Ｍｎ钢表面原位合成了ＴＣ以６０钛在６ｉ
ｃｍｐｓｔｏｔｎｇｙａｇｎａｃｃａｄｉｇｏｏｉｅａｇＺｅｔｎＭｅｇＪｎｈｎ，ａｏａｇｎｈｎｉｇ，ｎｕｓｅｇＺｈｏＧｕｇｎ
增强Ｎｉ复合材料涂层以提高基体的耐磨性。借助扫描电镜、基ｘ射线衍射仪、微硬度计对复合涂层的组织显和性能进行了分析。结果表明：敷层与基体呈冶金结合，裂纹、孑等缺陷，ｉ颗粒弥散分布于熔敷层熔无气ＬＴＣ中；合涂层有很高的硬度，室温干滑动磨损试验条件下具有优异的耐磨性能并随着（ｉ复在ｒ＋ｃ）量的增加ｒ含
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原位生成NbC颗粒增强镍基激光熔覆层

文章编号:0258 7025(2006)07 098706原位生成NbC 颗粒增强镍基激光熔覆层牛薪,晁明举,王文丽,袁斌,梁二军(郑州大学物理工程学院教育部材料物理重点实验室,河南郑州450052)摘要激光熔覆技术是金属材料表面强化和改性的有效方法之一。

利用该技术,在A 3钢表面激光熔覆预置涂层,成功制备出了原位生成N bC 颗粒增强的镍基复合涂层,并进行了硬度、摩擦性能测试,X 射线衍射(X RD)和显微组织分析。

扫描电镜(SEM )、能谱分析(EDS)和X 射线衍射分析结果表明,原位生成N bC 颗粒增强的镍基复合涂层与基材呈现良好的冶金结合,熔覆层的组织为先共晶析出的树枝晶(Cr,Fe 碳化物相)和原位生成的NbC 颗粒相均匀分布在 (N i Fe)基体中。

硬度测试和摩擦磨损实验表明,激光熔覆原位生成N bC 颗粒增强镍基复合涂层平均硬度高达H V 0.31200,耐磨性是纯N i60激光熔覆层的2.5倍。

分析认为,其硬度和耐磨性提高的原因在于涂层中形成了大量的、原位生长的NbC 颗粒增强相,且均匀分布于基体中。

关键词激光技术;激光熔覆;原位生成;碳化铌;显微组织;耐磨性中图分类号 T N 249;T G 665 文献标识码 AIn Situ S ynthesized NbC Particulate Reinforced Ni Based Composite Coatings by Laser CladdingN IU Xin,CH AO M ing ju,WANG Wen li,YU AN Bin,LIANG Er jun(D ep ar tment of Phy sics &K ey L abor ator y of M ater ial P hy s ics of M inis tr y of Education,Zhengz hou Univ er sity ,Zhengz hou,H enan 450052,China)Abstract Laser cladding is the one o f the eff icient methods for the surface har dening and mo difying o f metal material.U sing this technolog y,N bC particulate r einforced N i based composite coating has been successfully in situ sy nt hesized o n st eel A3substr ate by prio r to pasting.T he micr ostr ucture obser vation and hardness test on the cr oss sectio n o f the laser clad layer w ere per formed.A nd that X ray diffr action (XR D)ana lysis and t ribot esting o n the surface o f the coating s w ere also accomplished.T he micro st ruct ur al and metallo gr aphic analyses by a scanning electro n micr oscope (SEM ),ener gy disper sive spectr ometer (EDS)and X r ay diffracto meter reveal that the coating epit axia l g row ing fro m the substr ate with ex cellent bonding between the co ating and subst rate is ensured by the st rong met allur gical interface and sug gest the presence of the in situ synthesized NbC par ticles in the clad lay er.T hese N bC part icles tog ether w ith the car bide dendrites present as r einfo rcement s o f the composite coating s and ar e ho mog enously dispr ead in the (Ni F e)matrix.T he ex per imenta l results show that the co mpo site co at ing gives hig h averag e ha rdness of H V 0.31200and ex cellent w ea r resistance,w hich is 2.5t imes as high as that o f pur e N i60co atings.T he impro vement of wear resistance is due to the presence of t he substantiv e in situ synthesized NbC par ticles and their homog eno us distr ibution in the co atings.Key words laser technique;laser cladding;in situ sy nt hesis;NbC;micr ostr ucture;wear resistance收稿日期:2005 11 29;收到修改稿日期:2006 02 08基金项目:河南省高校青年骨干教师计划(2002 218)和河南省教育厅自然科学研究计划(200510459005,2006140009)资助项目。

激光熔覆原位自生TiC颗粒增强镍基复合涂层的组织与耐磨性

激光熔覆原位自生TiC颗粒增强镍基复合涂层的组织与耐磨性马世榜;夏振伟;徐杨;施焕儒;王旭;郑越【摘要】采用预置粉末法在45钢表面进行激光熔覆镍基Ni60A+x%(SiC+Ti)(质量分数,下同)复合粉末涂层的实验研究.使用往复式磨损试验机对不同涂层材料的熔覆层进行干摩擦磨损实验,利用金相显微镜、扫描电镜(SEM)观察和分析熔覆层的显微组织与磨损形貌.结果表明:复合粉末通过原位反应生成弥散分布的TiC颗粒增强复合涂层,随着(SiC+Ti)含量的增加,颗粒状TiC的尺寸和数目逐渐增加;复合粉(SiC+Ti)含量达到60%时,微观组织有气孔和夹杂缺陷;复合粉(SiC+Ti)含量为48%时,熔覆层耐磨性最佳;复合涂层的磨损主要为磨粒磨损,机理为微观切削和挤压剥落.%Laser cladding of Ni-based Ni60A+x% (SiC+Ti)(mass fraction,the same below) composite powder coating on 45 steel substrate was studied by using the method of preplaced powder.The dry friction and wear experiments of different material coatings were carried out by reciprocating friction wear tester.The microstructure and worn morphology of cladding layers were observed and analyzed by using metallographic microscope, scanning electron microscope(SEM) respectively.The results show that the prepared composite coating with dispersively distributed TiC enhanced particles are obtained in-situ, the size and number of the granular TiC gradually increase with the increase of the composite powder SiC+Ti.When the composite powder SiC+Ti reaches 60%, pores and inclusions defects exist in microstructure.When the composite powder SiC+Ti reaches 48%, wear resistance of cladding coating is the best.Thewear behavior of the composite coating is abrasive wear, and the mechanism is micro cutting and extrusion spalling.【期刊名称】《材料工程》【年(卷),期】2017(045)006【总页数】7页(P24-30)【关键词】激光熔覆;原位自生;TiC;耐磨性;强化机理【作者】马世榜;夏振伟;徐杨;施焕儒;王旭;郑越【作者单位】中国农业大学工学院,北京 100083;南阳师范学院机电工程学院,河南南阳 473061;中国农业大学工学院,北京 100083;中国农业大学工学院,北京100083;中国农业大学工学院,北京 100083;中国农业大学工学院,北京 100083;中国农业大学工学院,北京 100083【正文语种】中文【中图分类】TG115.5+8激光熔覆原位自生技术是指采用激光加工工艺，利用不同元素或化合物之间熔融状态下发生化学反应，在金属基体内生成一种或几种陶瓷相颗粒，以达到改善单一金属合金性能的方法[1-3]。

fe基耐磨堆焊涂层中(nb,m)c复合碳化物的结构与调控

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WC增强镍基复合喷焊层的组织与磨粒磨损性能研究

第27卷　第3期2006年　6月材　料　热　处　理　学　报TRANS ACTIONS OF M ATERIA LS AND HE AT TRE AT ME NTV ol .27　N o .3June2006WC 增强镍基复合喷焊层的组织与磨粒磨损性能研究于美杰1,　王成国1,　孙宏飞2,　徐　勇3,　朱　波1(1.山东大学材料科学与工程学院,山东济南　250061;2.山东科技大学材料科学与工程学院,山东青岛　266510;3.北京科技大学新金属材料国家重点实验室,北京　100083)摘　要:采用扫描电镜、电子探针、X 射线衍射和透射电镜技术分析了氧乙炔火焰喷焊WC 增强镍基自熔性合金复合涂层的组织结构,并采用湿砂橡胶轮式磨粒磨损试验机对该涂层与等离子喷涂NiCr ΠCr 3C 2涂层的磨损性能进行了实验比较。

结果表明,复合喷焊层内形成了γ2Ni 固溶体基体,其中弥散分布着大量细小的碳化物硬质相Cr 3C 2、B 4C 、Cr 7C 3、Cr 23C 6等。

WC 颗粒仅在边缘处发生部分溶解,与涂层基体形成了冶金结合,周围生成针状的碳化铬枝晶。

该组织决定了喷焊层基体具有较高的硬度,WC 增强颗粒与基体之间具有很高的结合强度。

复合喷焊层具有很好的耐磨粒磨损性能,其磨损失重量仅为NiCr ΠCr 3C 2涂层的57%。

关键词:磨损;　喷焊;　涂层;　镍基自熔性合金中图分类号:TG 13516;　TG 113 文献标识码:A 文章编号:100926264(2006)0320116205收稿日期:　2005208209;　修订日期:　2006203216作者简介:　于美杰(1979—),女,山东大学材料学院、山东省碳纤维工程技术研究中心博士研究生,目前主要从事聚丙烯腈基碳纤维制备工艺的研究,T el :0531283953362802,E 2mail :ym j -79@ 。

磨粒磨损是工业中最常见、磨损率极高的磨损形式,据统计大约有50%的机械零件损坏是由于磨粒磨损所致[1]。

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氩弧熔覆原位自生（Ti，Nb）C增强镍基复合涂层的抗磨性能王永东;李柏茹;金国;郑光海;刘爱莲【摘要】Ni60A composite coating and C-Ti-Nb-Ni reinforced Ni-based composite coating were fabricated on the surface of 16Mn steel by means of argon arc cladding technique using pre-alloyed powders of Ni60A and Nb, Ti and C powders as raw materials. The microstructure, phase constituent, micro-hardness, wear properties of these two kinds of composite coatings were investigated through OM, SEM, XRD, HV2000 Micro-hardness tester and MMS-2B ring block wear test machine, and the wear mechanism was also explored. The results show that excellent metallurgy bonding is formed at the interface between the coating and substrate, there are no pores and cracks in the interface. The micro-hardness of Ti-Nb-C reinforced Ni-based coating is about 5 times higher than that of the substrate, and 0.45 time than that of Ni60A coating. At room temperature, the wear property of Ti-Nb-C reinforced Ni-based coating is 6 times higher than that of the substrate, and 2 times higher than that of Ni60A coating. Severe abrasive wear and adhesive wear occur on the surface of 16Mn steel and abrasive wear is the main wear mechanism occurred in the surface of Ni60A composite coating. The wear mechanism of Ti-Nb-C reinforced Ni-based coating is microscopic abrasions wear.%以Ti、C、Nb粉和Ni60A合金粉末为原料，采用氩弧熔覆技术在16Mn钢基材表面分别制备(Ti, Nb)C颗粒增强Ni60A复合涂层(C-Ti-Nb-Ni60A涂层)和Ni60A涂层。

应用金相显微镜(OM)、扫描电镜(SEM)、X射线衍射(XRD)对2种涂层的显微组织和物相进行观察与分析，测试涂层的显微硬度和不同载荷下的磨损性能，分析磨损机制。

结果表明：C-Ti-Nb-Ni60A 复合涂层与基体间呈冶金结合，界面间无气孔和裂纹；C-Ti-Nb-Ni60A 复合涂层的显微硬度较基体16Mn钢提高近5倍，较Ni60A涂层提高0.45倍；常温干滑动200 N载荷条件下，C- Ti-Nb-Ni60A复合涂层的耐磨性能较基体16Mn钢提高6倍，较Ni60A涂层提高近2倍。

16Mn钢表面发生严重的磨粒磨损和粘着磨损，Ni60A涂层表面以磨粒磨损为主，C-Ti-Nb-Ni60A复合涂层的磨损机理为显微檫伤磨损。

【期刊名称】《粉末冶金材料科学与工程》【年(卷),期】2014(000)006【总页数】6页(P983-988)【关键词】氩弧熔覆;复合涂层;原位合成;抗磨性能【作者】王永东;李柏茹;金国;郑光海;刘爱莲【作者单位】黑龙江科技大学材料科学与工程学院，哈尔滨 150022;黑龙江科技大学材料科学与工程学院，哈尔滨 150022;哈尔滨工程大学材料科学与化学工程学院，哈尔滨 150001;黑龙江科技大学材料科学与工程学院，哈尔滨 150022;黑龙江科技大学材料科学与工程学院，哈尔滨 150022【正文语种】中文【中图分类】TG174通过熔覆技术在廉价材料表面制备耐磨和耐蚀涂层具有重要的实用价值。

常用的表面熔覆技术有激光熔覆、等离子熔覆、堆焊、热喷涂、感应熔覆和钨极氩弧熔覆等。

这些表面熔覆技术由于能获得与基体结合良好、厚度适中的表面涂层而被广泛应用于工业生产中[1−6]，其中氩弧熔覆的热量集中，在熔覆的整个过程中，电极和电弧及金属粉末都处在氩气的保护之中，加热、冷却过程中无氧化、烧损现象；而且可实现手工操作，灵活性高，可对形状复杂的基件进行熔覆，并可在野外进行作业。

TiC颗粒具有硬度、模量和抗弯强度高等特点，是很有潜力的增强相。

原位自生TiC增强相具有热力学稳定、尺寸细小、分布均匀、界面洁净并与基体结合良好的特点，具有广阔的应用前景[7−10]。

为了进一步提高原位自生TiC增强镍基复合涂层的性能，本文作者在复合涂层中加入Nb，利用氩弧熔覆技术在16Mn钢表面制备原位自生(Ti,Nb)C颗粒增强Ni基复合涂层，并研究涂层在常温干滑动摩擦条件下的耐磨性能，与Ni60A镍基涂层进行对比，为该复合涂层的制备及工程应用提供理论依据。

1 实验选用热轧态16Mn钢作为基体材料，基材尺寸为20 mm×10 mm×10 mm，表面除油去锈。

以C、Ti、Nb和Ni60A合金粉末为原料，粉末的平均粒度为40～45μm。

首先按照3%C-10%Ti-3%Nb-84%Ni60A的质量配比称量原料粉末，在研磨罐中混合均匀。

然后采用普通胶水作为粘结剂，将混合粉末调成糊状，涂覆在16Mn钢表面，涂层厚度约为1.0～1.5 mm，自然烘干24 h后，在RT3-15-9型电炉中于100℃×2 h烘干，最后通过氩弧熔覆获得原位自生(Ti,Nb)C颗粒增强镍基复合涂层(即C-Ti-Nb-Ni60A涂层)。

采用同样方法在16Mn钢表面制备Ni60A 镍基涂层。

采用Nephot型光学金相显微镜和MX2600型扫描电镜(SEM)观察涂层的组织与形貌；MHV2000型显微硬度仪测量涂层的显微硬度，载荷200 g，加载时间为10 s；在MM-200摩擦磨损试验机上测定16Mn钢与涂层试样的摩擦磨损性能，对偶件为淬火态的GGr15钢环，法向载荷分别为100 N和200 N，磨损时间为20 min；用精度为0.1 mg的Sartorius BS110电子天平称量试样的质量，计算磨损后的质量损失。

2 结果与分析2.1 组织结构图1 复合涂层的XRD谱Fig.1 XRD patterns of composite coatings图1所示为16Mn钢表面Ni60A合金涂层和C-Ti-Nb-Ni复合涂层的XRD谱。

对衍射峰标定表明，Ni60A涂层由γ-Ni，Cr23C6和Cr2B相组成，C-Ti-Nb-Ni复合涂层由γ-Ni，TiC和Cr23C6组成。

图2所示为16Mn钢表面的Ni60A复合涂层和CTi-Nb-Ni复合涂层的截面组织形貌。

从图中看出，颗粒相弥散地分布在涂层中，涂层与基体之间有一条白亮带，无气孔、裂纹等缺陷。

众所周知，氩弧熔覆过程是快速加热及快速凝固过程，凝固组织的生长形态主要由固液界面稳定因子(温度梯度G与凝固速率R的比值)决定。

在熔覆速度一定的情况下，氩弧熔池中从熔池的底部到顶部，温度梯度逐渐减小，而在同一截面上的晶体生长速度从底部到顶部逐渐增大。

因此，在熔池与基体的结合区域G/R的值很大，趋近于∞。

根据成分过冷理论[11]，此时固液界面的生长以低速平界面的方式进行，最终在熔池与基体的结合区域出现无微观偏析的组织，即“白亮带”。

它是由于熔覆合金与基体金属在氩弧热源作用下交互扩散而形成的固溶结合层，熔覆层与基体形成良好的冶金结合。

随离熔池底部距离增加，G/R值减小，故平界面失稳，出现胞状晶区。

但由于G/R值迅速减小，很快出现树枝晶组织，此处的树枝晶组织沿逆热流方向外延生长，生长速率仍较低，因此枝晶较粗大。

随结晶过程向熔覆层内部推进，固液界面前沿温度梯度减小，凝固速率增大，则G/R进一步减小，胞晶全部变为枝晶，同时枝晶逐渐变细，因此熔覆层中部是较细树枝晶区[12](如图2(a)所示)。

图2 复合涂层横截面的组织形貌Fig.2 Microstructures of transverse cross-section of the composite coatings with different coating(a)—Ni60A coating;(b)—C-Ti-Nb-Ni coating图3所示为C-Ti-Nb-Ni复合涂层截面的SEM组织。

其中图3(a)、(b)、(c)分别为图2(b)中A、B和C区域的高倍SEM组织。

由图可见在熔覆层里层，TiC和(Ti,Nb)C颗粒分布较少，颗粒相主要分布在晶界处；熔覆层中间部位和表面，TiC 和(Ti,Nb)C颗粒以花瓣状形态存在，尺寸约为2μm左右。

TiC和(Ti,Nb)C颗粒在涂层厚度方向具有明显的梯度分布特征，在表层TiC和(Ti,Nb)C的体积分数较大，并且从涂层的底部到表面，由单个细小颗粒逐步演化成多个颗粒的团絮状。

其主要形成原因为熔池的快速流动及其速度场的不均匀性加速陶瓷颗粒上浮，导致涂层凝固后出现颗粒梯度分布的特征。

图4所示为Ni60A涂层和C-Ti-Nb-Ni涂层表面的SEM形貌。

从图看出，Ni60A 复合涂层的组织为黑色基体上分布着网状结构(见图3(a))，C-Ti-Nb-Ni复合涂层的组织为黑色基体上分布着长条状和粒状结构。

结合物相分析可以确定黑色基体为γ-Ni，Ni60A复合涂层中网状结构为Cr23C6和Cr2B共晶组织；C-Ti-Nb-Ni复合涂层中的长条状为Cr23C6物相，颗粒状由TiC和(Ti,Nb)C组成，Nb占据Ti的点阵位置。

2.2 硬度与抗磨性能图4 Ni60A涂层和C-Ti-Nb-Ni涂层的表面SEM形貌Fig.4 SEM images ofNi60A coating(a)and C-Ti-Nb-Ni coating(b)图5 复合涂层试样从涂层表面到基体的显微硬度分布Fig.5 Microhardness profile of composite coating图5所示为复合涂层试样的显微硬度分布。