Ti-3Al-2V表面激光熔覆Ti-BN涂层的微观组织及反应行为研究
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摘要
钛合金较差的耐磨性能一直限制钛合金在苛刻摩擦领域的应用。采用激光熔覆的方法在钛合金的表面涂覆耐磨涂层,以其经济、高效、快捷而成为钛合金表面强化技术的重要手段之一。采用原位合成的陶瓷-金属基复合涂层以其优异的抗磨损性能而得到广发的开发和应用。目前，对激光熔覆原位合成陶瓷-金属基复合涂层的组织-工艺-性能之间关系的研究不系统，对原位合成的机理研究相对匮乏。因此采用激光熔覆Ti-BN体系，研究熔覆工艺-组织-性能之间相互作用关系，并探讨原位合成的原位反应机理，对采用激光熔覆方法原位合成陶瓷-金属基复合强化涂层有重要的理论意义和实际应用价值。
研究了激光功率、激光扫描速度、送粉速度、Ti与BN粉末的摩尔比例和BN的粒度分布对组织相分布及形貌的影响。结果表明：在适宜的工艺参数条件下，获得了原位生长的TiB-TiN复合强化钛基涂层。获得的涂层与基体结合良好，无明显的气孔和裂纹。TiN呈等轴晶形貌；TiB呈针棒状组织形貌。当激光扫描速度为6mm/s情况下，随着激光功率的提高，熔覆层厚度、熔覆层的渗透深度、热影响区深度和熔覆宽度升高，而稀释率(γ)降低；熔覆层组织中TiN和TiB晶粒逐渐粗大，激光功率从600W→1000W→1400W→1800W功率变化时，TiB强化相变化呈现出未观测到明显相→细小絮状组织（尺寸大小约为15μm100nm）→尺寸不均匀针棒状组织（尺寸范围为15μm100nm∽20μm1μm）→尺寸均匀针棒状组织（尺寸大小约为20μm1μm）的变化规律。当激光功率为1400W，激光扫描速度从3mm/s增加至12mm/s过程中，随着激光扫描速度的增加，强化相尺寸减小。熔覆层顶部的TiB由均匀的针棒状组织（平均尺寸大小约为15μm2μm）→团聚的须状组织（尺寸范围10μm1μm～10μm500nm）＋针棒状组织→须状组织（尺寸大小为10μm200nm）转变。由于获得的熔覆层组织存在较大的冷却速度差别，组织分布不均匀。送粉量对熔覆组织宏观形貌及显微组织影响不大。发现BN：Ti的比例对形成TiN和TiB的形貌及分布状态具有很大的影响。在BN含量较低的情况下（BN:Ti=1:16）， TiN优先在晶内形核长大，TiB在晶界形核长大；随着BN含量的增多，TiB形核质点增多，当BN：Ti的摩尔计量比为1:4的情况下，TiB与TiN在熔覆层中均匀分布。B元素的含量对TiB的形核与长大起了重要的作用，当Ti与B满足TiB的化学计量比的情况下，发生了TiB的形核与长大。此外，细小粒度的BN作为原材料有利于获得均匀的熔覆组织；
发现Ti-BN体系在BN摩尔含量含量低于20%条件下，激光熔覆Ti-BN体系的凝固过程与平衡凝固过程完全不同，原位合成形成的硼化物强化相为TiB,未发现TiB2相。提出Ti-BN体系激光熔覆快速凝固过程中的凝固过程：（Ⅰ）粗大的初生TiN形核长大；（Ⅱ）液相与初生的TiN发生包晶反应，形成α-Ti；（Ⅲ）初生的TiB形核长大；（Ⅳ）最后液相发生共晶反应形成TiB+β-Ti；（Ⅴ）β-Ti向α-Ti转变；
分析了原位合成强化相TiN和TiB的组织特点及形成机理：原位合成的TiN为面心立方结构，点阵常数为a=0.4245nm，由于其界面能和原子结合能具有高度的各向同性的特点以及激光熔覆快速冷却的共同作用，导致形成的TiN为等轴晶形貌。在激光功率为1400W,扫描速度为6mm/s，BN：Ti=1:8条件下，针棒状TiB结构具有多样性，发现少量粗大的具有空心结构针棒状TiB,空心结构内部孔洞不规则，各处壁厚不均匀，为初生TiB；共晶的TiB呈现细小，实心的针棒状组织形貌。TiB为B27结构，点阵常数为α=0.628nm, b=0.312nm和c=0.461nm。TiB沿[010]方向生长速度最快,TiB的的堆垛层错面平行于（100）面。TiB可以以孪晶的方式形核和长大,原位合成TiB强化相与Ti之间为半共格关系。
系统研究了工艺参数对原位反应机理类型选择的影响。在激光功率越高、激光扫描速度越慢、BN含量越少以及BN粒度越小的情况下，原位合成形成陶瓷强化相颗粒均匀、弥散，反应机制主要由溶解-析出机制控制；激光功率越低、激光扫描速度越快、BN含量越大以及BN粒度越大的情况下，原位合成形成陶瓷强化相分布不均匀，并且在熔覆层顶部易出现“花朵状”组织，反应机制主要由溶解-析出机制和扩散机制共同控制；当BN：Ti=1:4，BN粒度10μm～30μm的条件下，激光热输入大于64.8W h/m时，激光熔覆过程的反应机制为溶解-析出机制控制；激光热输入小于64.8W h/m时，反应机制为溶解-析出机制和扩散机制共同控制；
研究激光熔覆条件下特征”花朵”形貌的形成机理。发现在Ti-3Al-2V基体上激光熔覆Ti-BN粉末沿激光入射方向存在明显组织差异。当激光功率较低、激光扫描速度快、BN含量高和BN粒度粗大的情况下，熔覆层中表层容易形成”花朵”状熔覆层组织，探索其形成机理如下：（1）Ti与BN发生液固-固反应，形成亚计量比的TiNx和TiBx，（2）Ti-BN反应过程中反应热量与输入的激光辐射能量共同作用促进了液相L的形成。（3）从BN上扩散出来的N和B原子进入到Ti的熔体中，在固相TiNx和TiBx表面异质形核形成TiN，TiN包围在TiNx和TiBx表面，并向熔体中排出B原子;(4)当Ti,B原子比例满足TiB的计量比的时候，形成了TiB或者是TiB和Ti的共晶体；
采用激光熔覆Ti-BN体系获得原位合成的TiB和TiN复合强化的涂层具有良好的硬度和抗磨损性能。随着激光功率的提高、激光扫描速度的降低、BN含量的增加，熔覆层中强化相分布均匀化程度升高，强化相体积含量增高，熔覆层的硬度呈上升趋势，熔覆层的最高硬度可达到1250HV0.5，是母材的5倍；耐磨性能呈上升的趋势。在相同的时间内，熔覆层的磨损高度损失量不到母材的1/2。母材的磨损机制主要为疲劳磨损，而熔覆层金属的磨损主要由疲劳磨损和磨粒磨损共同作用，磨粒磨损占主体作用。
Poor wear performance of titanium and titanium alloy is the one of the main factorswhich restrict its widely used in some special field. Lase cladding on titanium alloybecome one of the important surface strenthening methods due to its economy, efficientand speedy. In situ synthesized ceramic particle reforced metal matrix composites iswidely used as the claddding layer because of its outstanding wear performance. However,researches on the relationship among microstructure-processing–properties are notsystematic, especially on the in-situ synethesized mechanism. Besides, rare repotres havebeen published on the Ti-BN system by laser cladding. Therefore, there is meaningful tohave a research on the relationship among microstructure-processing–properties, it canbe used to control microstures and properties and have further study on in-situ synthesizedmechanism.
The effect of laser power, scanning speed, powder feeding rate, the ratio of BN to Tiand the grain size of BN on phases’ morphology and distribution have studied systemly.The results show below: at the proper cladding paramters, the cladding layers of TiN-TiBcomposite have been in-situ synthesized, the cladding layers have good metallurgicalconnection with substrate without obvious pores and cracks. In situ synthesized TiN wascompared with dendrite/equiaxed grains while and TiB exhibit needle platelet type. Withthe laser power increased, the cladding width, the thickness of clad layer, the penetrationdepth and the depth of HAZ increased, but the dilution rate decreased; the grain of TiNand TiB grew coarse. with the laser power changed as600W→1000W→1400W→1800W,the size of TiB phase alter as follow: undetected TiB→small whisker microstucture withsize of15μm100nm→unever needle microstructure with grain size range from15μm100nm to20μm1μm→uniform needle microstruct with size of20μm1μm. The grain size of synthesized become small with the scanning speed increased. With thescanning speed increased from smm/s to12mm/s, the microstrue of TiB at the top fieldvaried much: uniform needle microstructure with mean grain size of15μm2μm→agglomerated whisker with grain size range from10μm1μm to10μm
500nm→mixed neele and whisker micrsture. The high scanning speed leads to unevermicrostructure becasued of high cooling speed. Powder feeding rate plays little role on themacrostructure and microstructure of phases. However, the ration of BN to Ti has greateffect on the microstructure and distrubituion of phases. The results shows that TiNnucleat and grow in the grain but TiB at the grain boundary at low BN content,; with BNcontent add the nucleated amount of TiB increased, TiB and TiN distribut uniformly in theclad layer with the ratio of BN to Ti being1:4. The content of B play an important role onthe crystal of TiB. Nucleation and growth of TiB depend on solubility of B satisfy to formTiB. Besides, BN with small size used as rwa material is benfit to synthesize uniformmicrostructure.
The solidification of Ti-BN system is different with the equilibrium solidifactionprocess at the BN content of20%by laser cladding. TiB formed in the clad layer withoutTiB2. The solidifation process should be the follow:（Ⅰ）Precipitation of primary phaseTiN will nucleate from the liquid phase by the reaction of L→TiN and grow into thecoarse cellular or dendritic shape due to the high cooling rate and space to grow in theliquid alloy;（Ⅱ）Formation of the α-Ti by the peritectic reaction L+TiN→α-Ti at thesurface of TiN. Because of the limited react time and the difficulty of solid diffusion,core-shell structure of TiN-β-Ti formed;（Ⅲ）Primary phase TiB (phase (c) in Fig.3(b))will nucleate on the surface of TiN and grain boundary.（Ⅳ）Formation of the binaryeutectic of β-Ti and TiB(phase (d) in Fig.3(b)) as the temperature gradually reduces by thereaction of L→TiB+β-Ti.（Ⅴ）Formation of α-Ti. β-Ti will be transformed into α-Ti bythe allotropic transformation reaction β-Ti→α-Ti.
The character and forming mechanism of in-situ synthesized TiB and TiN have beenanalysed systemly. In situ synthesized TiN is fcc structure with lattice constant beinga=0.4245nm. The high isotropic structure and high cooling speed of laser cladding lead to TiN with dendrite/equiaxed grains. Little coarse TiB shows needle platelet with hollowshape, and the hollow is not regular with different wall thickness. TiB is B27structurewith lattice constants beingα=0.628nm, b=0.312nm and c=0.461nm。TiB grow fast in thedirection of [010]and its stacking faults being (100). The eutectic TiB exhibit needleplatelet with small size. TiB can nucleated and grow with the twin csystal. In-situsynthesized TiB have semi-coherent relationship with Ti.
Effect of the cladding parameters on the in-situ synthesized mechanism have beeninvestigated systemly.the higher laser power, lower scanning speed, fewer BN content andsmaller BN grain size, the acquired reforced ceramic partiles more uniform and dispersive,the main mechanism control by Dissolving-precipitation mechanism. In contrast, thelower laser power, higher scanning speed, more BN content and coarser BN grain size, theacquired reforced ceramic partiles distribute more unever and “flower” structure observedat the top area of cladding layers. The main mechanism is diffusion mechanism. When usesmall BN as the raw material, Dissolving-precipitation mechanism become the mainreaction mechanism at the laser power density bigger than64.8W·h/m. Otherwise, thediffusion mechanism become the main reaction mechanism at the laser poer densitysmaller than64.8W·h/m.
The forming mechanism of special “flower” structure has been discussed.Microstructures of the cladding layer on the Ti-3Al-2V are vared much at different field.“flower” structure tends to formed at the following situations: low laser power, fastscanning speed, high BN content and coarse BN as raw material. The forming processtends to follow the way (1) forming equilibrium phases TiNx and TiBx betweenliquid/solid Ti and solid BN,(2) the heat relased during the reaction of Ti-BN and laserpower energe input make the solid to melt and form liquid,(3) atom B and N from BNdiffuse into the liquid Ti and form TiN at the surface of TiNx ndTiBx, atom B diffused intothe liquid. TiNx ndTiBx works as the nucleation of TiN,(4) TiB from as sigle phase oreutectic phase with Ti when the solubility of B satisfy to form TiB.
In-situ synthesized TiB-TiN reinforced Ti based coating exhibited excellect hardnessand wear performance. With the laser power increase, scanning speed desease, BN content add, the distribution of reinforced particles in the cladding layer more uniform, the amoutincrease and the micohardness increased with the highest of1250HV0.5，which is fivetimes more than the substrate; at the same rotating wear time, the wear depth is less halfthan the substrate. The mian mechanism of the sbustrate is severe adhesive wearmechanism. However, the wear mechanism of cladding layer is a combination of adhesiveand abrasive wear characteristics, and the abrasive wear characteristic is the main wearmechanism.
研究了激光功率、激光扫描速度、送粉速度、Ti与BN粉末的摩尔比例和BN的粒度分布对组织相分布及形貌的影响。结果表明：在适宜的工艺参数条件下，获得了原位生长的TiB-TiN复合强化钛基涂层。获得的涂层与基体结合良好，无明显的气孔和裂纹。TiN呈等轴晶形貌；TiB呈针棒状组织形貌。当激光扫描速度为6mm/s情况下，随着激光功率的提高，熔覆层厚度、熔覆层的渗透深度、热影响区深度和熔覆宽度升高，而稀释率(γ)降低；熔覆层组织中TiN和TiB晶粒逐渐粗大，激光功率从600W→1000W→1400W→1800W功率变化时，TiB强化相变化呈现出未观测到明显相→细小絮状组织（尺寸大小约为15μm100nm）→尺寸不均匀针棒状组织（尺寸范围为15μm100nm∽20μm1μm）→尺寸均匀针棒状组织（尺寸大小约为20μm1μm）的变化规律。当激光功率为1400W，激光扫描速度从3mm/s增加至12mm/s过程中，随着激光扫描速度的增加，强化相尺寸减小。熔覆层顶部的TiB由均匀的针棒状组织（平均尺寸大小约为15μm2μm）→团聚的须状组织（尺寸范围10μm1μm～10μm500nm）＋针棒状组织→须状组织（尺寸大小为10μm200nm）转变。由于获得的熔覆层组织存在较大的冷却速度差别，组织分布不均匀。送粉量对熔覆组织宏观形貌及显微组织影响不大。发现BN：Ti的比例对形成TiN和TiB的形貌及分布状态具有很大的影响。在BN含量较低的情况下（BN:Ti=1:16）， TiN优先在晶内形核长大，TiB在晶界形核长大；随着BN含量的增多，TiB形核质点增多，当BN：Ti的摩尔计量比为1:4的情况下，TiB与TiN在熔覆层中均匀分布。B元素的含量对TiB的形核与长大起了重要的作用，当Ti与B满足TiB的化学计量比的情况下，发生了TiB的形核与长大。此外，细小粒度的BN作为原材料有利于获得均匀的熔覆组织；
发现Ti-BN体系在BN摩尔含量含量低于20%条件下，激光熔覆Ti-BN体系的凝固过程与平衡凝固过程完全不同，原位合成形成的硼化物强化相为TiB,未发现TiB2相。提出Ti-BN体系激光熔覆快速凝固过程中的凝固过程：（Ⅰ）粗大的初生TiN形核长大；（Ⅱ）液相与初生的TiN发生包晶反应，形成α-Ti；（Ⅲ）初生的TiB形核长大；（Ⅳ）最后液相发生共晶反应形成TiB+β-Ti；（Ⅴ）β-Ti向α-Ti转变；
分析了原位合成强化相TiN和TiB的组织特点及形成机理：原位合成的TiN为面心立方结构，点阵常数为a=0.4245nm，由于其界面能和原子结合能具有高度的各向同性的特点以及激光熔覆快速冷却的共同作用，导致形成的TiN为等轴晶形貌。在激光功率为1400W,扫描速度为6mm/s，BN：Ti=1:8条件下，针棒状TiB结构具有多样性，发现少量粗大的具有空心结构针棒状TiB,空心结构内部孔洞不规则，各处壁厚不均匀，为初生TiB；共晶的TiB呈现细小，实心的针棒状组织形貌。TiB为B27结构，点阵常数为α=0.628nm, b=0.312nm和c=0.461nm。TiB沿[010]方向生长速度最快,TiB的的堆垛层错面平行于（100）面。TiB可以以孪晶的方式形核和长大,原位合成TiB强化相与Ti之间为半共格关系。
系统研究了工艺参数对原位反应机理类型选择的影响。在激光功率越高、激光扫描速度越慢、BN含量越少以及BN粒度越小的情况下，原位合成形成陶瓷强化相颗粒均匀、弥散，反应机制主要由溶解-析出机制控制；激光功率越低、激光扫描速度越快、BN含量越大以及BN粒度越大的情况下，原位合成形成陶瓷强化相分布不均匀，并且在熔覆层顶部易出现“花朵状”组织，反应机制主要由溶解-析出机制和扩散机制共同控制；当BN：Ti=1:4，BN粒度10μm～30μm的条件下，激光热输入大于64.8W h/m时，激光熔覆过程的反应机制为溶解-析出机制控制；激光热输入小于64.8W h/m时，反应机制为溶解-析出机制和扩散机制共同控制；
研究激光熔覆条件下特征”花朵”形貌的形成机理。发现在Ti-3Al-2V基体上激光熔覆Ti-BN粉末沿激光入射方向存在明显组织差异。当激光功率较低、激光扫描速度快、BN含量高和BN粒度粗大的情况下，熔覆层中表层容易形成”花朵”状熔覆层组织，探索其形成机理如下：（1）Ti与BN发生液固-固反应，形成亚计量比的TiNx和TiBx，（2）Ti-BN反应过程中反应热量与输入的激光辐射能量共同作用促进了液相L的形成。（3）从BN上扩散出来的N和B原子进入到Ti的熔体中，在固相TiNx和TiBx表面异质形核形成TiN，TiN包围在TiNx和TiBx表面，并向熔体中排出B原子;(4)当Ti,B原子比例满足TiB的计量比的时候，形成了TiB或者是TiB和Ti的共晶体；
采用激光熔覆Ti-BN体系获得原位合成的TiB和TiN复合强化的涂层具有良好的硬度和抗磨损性能。随着激光功率的提高、激光扫描速度的降低、BN含量的增加，熔覆层中强化相分布均匀化程度升高，强化相体积含量增高，熔覆层的硬度呈上升趋势，熔覆层的最高硬度可达到1250HV0.5，是母材的5倍；耐磨性能呈上升的趋势。在相同的时间内，熔覆层的磨损高度损失量不到母材的1/2。母材的磨损机制主要为疲劳磨损，而熔覆层金属的磨损主要由疲劳磨损和磨粒磨损共同作用，磨粒磨损占主体作用。
Poor wear performance of titanium and titanium alloy is the one of the main factorswhich restrict its widely used in some special field. Lase cladding on titanium alloybecome one of the important surface strenthening methods due to its economy, efficientand speedy. In situ synthesized ceramic particle reforced metal matrix composites iswidely used as the claddding layer because of its outstanding wear performance. However,researches on the relationship among microstructure-processing–properties are notsystematic, especially on the in-situ synethesized mechanism. Besides, rare repotres havebeen published on the Ti-BN system by laser cladding. Therefore, there is meaningful tohave a research on the relationship among microstructure-processing–properties, it canbe used to control microstures and properties and have further study on in-situ synthesizedmechanism.
The effect of laser power, scanning speed, powder feeding rate, the ratio of BN to Tiand the grain size of BN on phases’ morphology and distribution have studied systemly.The results show below: at the proper cladding paramters, the cladding layers of TiN-TiBcomposite have been in-situ synthesized, the cladding layers have good metallurgicalconnection with substrate without obvious pores and cracks. In situ synthesized TiN wascompared with dendrite/equiaxed grains while and TiB exhibit needle platelet type. Withthe laser power increased, the cladding width, the thickness of clad layer, the penetrationdepth and the depth of HAZ increased, but the dilution rate decreased; the grain of TiNand TiB grew coarse. with the laser power changed as600W→1000W→1400W→1800W,the size of TiB phase alter as follow: undetected TiB→small whisker microstucture withsize of15μm100nm→unever needle microstructure with grain size range from15μm100nm to20μm1μm→uniform needle microstruct with size of20μm1μm. The grain size of synthesized become small with the scanning speed increased. With thescanning speed increased from smm/s to12mm/s, the microstrue of TiB at the top fieldvaried much: uniform needle microstructure with mean grain size of15μm2μm→agglomerated whisker with grain size range from10μm1μm to10μm
500nm→mixed neele and whisker micrsture. The high scanning speed leads to unevermicrostructure becasued of high cooling speed. Powder feeding rate plays little role on themacrostructure and microstructure of phases. However, the ration of BN to Ti has greateffect on the microstructure and distrubituion of phases. The results shows that TiNnucleat and grow in the grain but TiB at the grain boundary at low BN content,; with BNcontent add the nucleated amount of TiB increased, TiB and TiN distribut uniformly in theclad layer with the ratio of BN to Ti being1:4. The content of B play an important role onthe crystal of TiB. Nucleation and growth of TiB depend on solubility of B satisfy to formTiB. Besides, BN with small size used as rwa material is benfit to synthesize uniformmicrostructure.
The solidification of Ti-BN system is different with the equilibrium solidifactionprocess at the BN content of20%by laser cladding. TiB formed in the clad layer withoutTiB2. The solidifation process should be the follow:（Ⅰ）Precipitation of primary phaseTiN will nucleate from the liquid phase by the reaction of L→TiN and grow into thecoarse cellular or dendritic shape due to the high cooling rate and space to grow in theliquid alloy;（Ⅱ）Formation of the α-Ti by the peritectic reaction L+TiN→α-Ti at thesurface of TiN. Because of the limited react time and the difficulty of solid diffusion,core-shell structure of TiN-β-Ti formed;（Ⅲ）Primary phase TiB (phase (c) in Fig.3(b))will nucleate on the surface of TiN and grain boundary.（Ⅳ）Formation of the binaryeutectic of β-Ti and TiB(phase (d) in Fig.3(b)) as the temperature gradually reduces by thereaction of L→TiB+β-Ti.（Ⅴ）Formation of α-Ti. β-Ti will be transformed into α-Ti bythe allotropic transformation reaction β-Ti→α-Ti.
The character and forming mechanism of in-situ synthesized TiB and TiN have beenanalysed systemly. In situ synthesized TiN is fcc structure with lattice constant beinga=0.4245nm. The high isotropic structure and high cooling speed of laser cladding lead to TiN with dendrite/equiaxed grains. Little coarse TiB shows needle platelet with hollowshape, and the hollow is not regular with different wall thickness. TiB is B27structurewith lattice constants beingα=0.628nm, b=0.312nm and c=0.461nm。TiB grow fast in thedirection of [010]and its stacking faults being (100). The eutectic TiB exhibit needleplatelet with small size. TiB can nucleated and grow with the twin csystal. In-situsynthesized TiB have semi-coherent relationship with Ti.
Effect of the cladding parameters on the in-situ synthesized mechanism have beeninvestigated systemly.the higher laser power, lower scanning speed, fewer BN content andsmaller BN grain size, the acquired reforced ceramic partiles more uniform and dispersive,the main mechanism control by Dissolving-precipitation mechanism. In contrast, thelower laser power, higher scanning speed, more BN content and coarser BN grain size, theacquired reforced ceramic partiles distribute more unever and “flower” structure observedat the top area of cladding layers. The main mechanism is diffusion mechanism. When usesmall BN as the raw material, Dissolving-precipitation mechanism become the mainreaction mechanism at the laser power density bigger than64.8W·h/m. Otherwise, thediffusion mechanism become the main reaction mechanism at the laser poer densitysmaller than64.8W·h/m.
The forming mechanism of special “flower” structure has been discussed.Microstructures of the cladding layer on the Ti-3Al-2V are vared much at different field.“flower” structure tends to formed at the following situations: low laser power, fastscanning speed, high BN content and coarse BN as raw material. The forming processtends to follow the way (1) forming equilibrium phases TiNx and TiBx betweenliquid/solid Ti and solid BN,(2) the heat relased during the reaction of Ti-BN and laserpower energe input make the solid to melt and form liquid,(3) atom B and N from BNdiffuse into the liquid Ti and form TiN at the surface of TiNx ndTiBx, atom B diffused intothe liquid. TiNx ndTiBx works as the nucleation of TiN,(4) TiB from as sigle phase oreutectic phase with Ti when the solubility of B satisfy to form TiB.
In-situ synthesized TiB-TiN reinforced Ti based coating exhibited excellect hardnessand wear performance. With the laser power increase, scanning speed desease, BN content add, the distribution of reinforced particles in the cladding layer more uniform, the amoutincrease and the micohardness increased with the highest of1250HV0.5，which is fivetimes more than the substrate; at the same rotating wear time, the wear depth is less halfthan the substrate. The mian mechanism of the sbustrate is severe adhesive wearmechanism. However, the wear mechanism of cladding layer is a combination of adhesiveand abrasive wear characteristics, and the abrasive wear characteristic is the main wearmechanism.
引文
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