激光冲击强化对TC17钛合金微观组织和力学性能的影响

针对航空发动机TC17钛合金叶片易受外来物打伤实际问题,需要进一步提高叶片的疲劳强度。对板状TC17钛合金进行不同激光功率密度下的激光冲击,分别利用X射线衍射仪、透射电子显微镜、残余应力测试仪和显微硬度计分别对激光冲击前后TC17钛合金的组织和力学性能进行了观察和测试,再选取强化效果较好的功率密度为4 GW/cm2时对叶片强化后进行振动疲劳试验。结果表明:TC17钛合金在不同功率密度激光冲击后,表面组织产生大量高密度位错和纳米晶,随着功率密度的增大,晶粒细化程度越大;残余应力值和显微硬度都随深度增加而减小,表面显微硬度提高了20%,并形成800μm左右的硬度影响层;而功率密度为4 GW/cm2时提高幅度最大,HV0.1硬度为4310 MPa,表面残余压应力达到628.2 MPa,且残余应力在280和450℃下具有较好的热稳定性;TC17钛合金叶片在4 GW/cm2参数下强化后,其振动疲劳寿命提高了2倍。     

激光冲击强化对7050-T7451铝合金残余应力和力学性能的影响

对7050-T7451铝合金试样进行激光冲击强化,研究不同激光功率密度和冲击次数对铝合金残余应力和性能的影响。试验结果表明:激光冲击强化可以有效提高试样表面显微硬度,且硬度随着冲击次数的增加而增大,最高达172 HV0.05,较未强化试样提高了17%,硬度影响层深度可达750 μm。当激光功率密度为7.28 GW/cm²时,激光冲击1次后试样表面粗糙度为0.279 μm,比原始磨削表面的粗糙度下降了22.5%,随着冲击次数的增加,表面粗糙度逐渐增大,但均小于原始表面粗糙度。激光冲击强化可以大幅提高试样表面残余压应力,当激光功率密度为7.28 GW/cm²、冲击3次时残余压应力最大,可达－227.0 MPa。当激光功率密度为4.37 GW/cm²、冲击3次时,激光冲击强化可以有效提高试样的疲劳寿命(大于10⁶次),相比未强化试样提高2.3倍。激光冲击强化后表面残余压应力和显微硬度大幅提升可以有效抑制疲劳裂纹的萌生和扩展,从而提升7050-T7451铝合金的抗疲劳性能。     

激光冲击功率密度对W18Cr4V钢表面性能影响的研究

采用波长1.06μm、脉宽20 ns的钕玻璃激光对W18Cr4V高速钢进行强化。研究了激光功率密度对W18Cr4V钢强化层显微硬度和残余应力的影响。结果表明:经激光冲击强化后的W18Cr4V钢奥氏体晶粒细化,细晶强化作用显著;不同的激光功率密度都能在冲击区横截面上形成由表及里的显微硬度梯度和一定深度的残余压应力层。随功率密度的提高,硬度峰值和最大残余压应力增大,硬化层和残余压应力层的深度增加。当采用3.6 GW/cm~2的功率密度时,表面硬度峰高达1125 HV0.1,表面残余压应力最大值约-220 MPa,并可获得0.8 mm左右的硬化层和1.4 mm左右的残余压应力层。     

激光表面改性主要技术

<正>(1)激光相变硬化:功率密度可达106W/cm2以上,能在0.001～0.01 s时间内使工件加热到1 000℃以上,冷却速度可达104℃/s,硬化层深度0.1～2.5 mm。(2)激光表面熔化处理:激光表面合金化、激光表面熔覆、激光表面重熔、激光表面复合改性、激光上釉(功率密度107～108W/cm2)。(3)激光冲击硬化。     

球墨铸铁QT600-3激光相变硬化试验研究

采用CO2激光对模具材料球墨铸铁QT600-3进行激光相变硬化的试验研究。结果表明,在较大光斑直径,较低的激光功率密度,较低激光扫描速度的工艺条件下,激光扫描后的硬化层组织中含有较多的针状马氏体;硬化层表面的宏观硬度可达60HRC,为基体硬度的2.4倍,硬化层表面处的显微硬度随着扫描速度的减小而增大,随着激光功率的增大而增大。硬化层深度可达到0.95 mm,硬化层的深度随着扫描速度的增加而减小,随着激光功率的增加而略有增加。     

激光冲击处理对304不锈钢力学性能的影响

选用不同涂层对304不锈钢板材激光冲击处理,研究了自主研制的硅酸乙脂涂层与几种常用吸收涂层对304不锈钢的硬度和表面残余应力等冲击力学性能的影响.结果表明,在激光冲击过程中,黑漆涂层、铝箔涂层和硅酸乙脂黑漆涂层都能有效提高激光冲击试样的表面硬度,激光连续冲击后,在304不锈钢试件表面能形成1mm厚的硬化层,其表面硬度最大到240HV;随着激光功率密度的增强,其表面硬度逐渐增强;其表面残余应力也随着激光功率密度的增加而逐渐增大.     

激光冲击7050铝合金表面“残余应力洞”的模拟

采用显式动力学分析软件ANSYS/LS-DYNA对激光冲击加载过程进行模拟,通过调整激光冲击参数,探究其对7050铝合金表面形成"残余应力洞"的影响;将模拟结果与X射线应力分析仪测得的试验结果进行对比,并分析两者的误差来源。结果表明,激光功率密度、脉宽的增加会加剧"残余应力洞"现象,光斑直径的增加会抑制"残余应力洞"现象;当激光功率密度为1.98 GW/cm~2时,模拟与试验有较好的一致性;当激光功率密度提高至2.77 GW/cm~2时,激光能量的增强加剧了冲击区域近表面的塑性变形,引发了模拟与试验的误差;当激光功率密度进一步提高至4.07 GW/cm~2时,冲击区域近表面会形成亚晶粒,甚至晶粒细化形成纳米晶,使冲击区域表面残余应力均匀分布。     

激光冲击690高强钢表面残余应力工艺优化模拟

为研究激光冲击对690高强钢表面残余应力尤其是"残余应力洞"的影响,在ANSYS/LSDYNA平台对690高强钢薄板经激光冲击后的残余应力进行模拟,优化光斑搭接率及激光功率密度。结果表明:采用搭接处理工艺,功率密度为1.98 GW/cm~2,在搭接率为33%、50%、66%时,激光冲击690高强钢表面最大残余压应力和光斑中心最小残余应力差值分别为275.6、241.6、238.3 MPa;搭接率的增加抑制了"残余应力洞";功率密度为2.77 GW/cm~2时,激光冲击表面残余应力优化结果最佳,达到211.0 MPa。     

激光冲击强化对AZ31和AZ91镁合金表面形貌和电化学腐蚀性能的影响

为了研究激光冲击强化对镁合金表面形貌和电化学腐蚀性能的影响,采用电化学方法和钕玻璃脉冲激光(波长1064 nm,脉冲宽度20 ns)研究AZ31热轧板和AZ91-T6铸造镁合金在3.5%NaCl(质量分数)溶液中的动态极化曲线和电化学阻抗谱特征,并对镁合金三维表面形貌、腐蚀试样宏观形貌、自腐蚀电位和电化学阻抗谱进行测试与分析。结果表明:激光冲击改善AZ31热轧板和AZ91-T6镁合金的耐蚀性。当激光功率密度处于0.6~0.9GW/cm2区间,镁合金腐蚀电位和电流密度分别出现峰值和谷值;当功率密度不小于1.0 GW/cm2时,镁合金腐蚀电位和电流密度分别正负移动,与冲击表面的形变、钝化膜和形貌密切相关。     

激光冲击强化对钛合金疲劳寿命影响综述EI北大核心CSCD

对提升钛合金零件的疲劳强度,已有相关技术的试验研究,但缺乏对技术的系统介绍,阻碍了该技术的产业化应用。通过整理大量试验数据及其结果,就激光冲击强化对钛合金零件的疲劳特性的影响展开分析。简要介绍激光冲击强化技术的发展状况,分别从表面形貌、残余应力、微观组织、硬度、表面粗糙度等方面进行分析总结。结果发现,当激光脉冲能量为7 J时,材料塑性变形量最大;当激光功率密度为3 GW/cm^(2),材料表面残余压应力值最高;当冲击次数达到5次以上时,材料表层的位错密度不断增大;当在工件表面覆盖一层高强度的光滑金属接触膜时,材料表面粗糙度将降低。综合数据可知激光功率密度及冲击次数对钛合金疲劳寿命的影响最大。整理了大量试验数据,可为得到最佳的激光冲击强化效果及提升疲劳寿命提供理论参考。     

Ti-6Al-4V钛合金固体渗硼法表面改性

对TC4钛合金(Ti-6Al-4V)进行表面渗硼使其表面硬度显著提高.渗硼温度为1000℃到1050℃,渗硼时间为5 h到20h.文内测量和比较了渗硼后钛合金表面的微结构、形貌、相组成等性质,研究了渗硼过程中Ti,Al,V,B等元素的扩散行为.在低温短时间渗硼时,渗硼层厚度仅0.8μm,而在高温长时间渗硼时,渗硼层厚度可达15 μm.实验证明,渗硼层由TiB和TiB2两相组成,并且它们的含量随渗硼温度提高而增加.渗硼层表面主要含TiB2,其显微硬度可达2200 HV0.01,渗硼层内表层主要含TiB,其显微硬度为1100 HV0.01.渗硼层的硬度远高于TC4钛合金的硬度.     

氢含量对Ti-6Al-4V合金室温高速压缩性能的影响(英文)

利用电磁成形实验研究氢含量对Ti-6Al-4V合金室温高速压缩性能的影响,通过微观组织观察揭示氢致压缩性能机理。结果表明,氢对Ti6Al4V合金的高速压缩性能存在有益的影响。在电磁成形实验放电能量相同的条件下,Ti-6Al-4V合金的变形率随氢含量的增加呈先增加后降低的趋势。当Ti-6Al-4V合金置氢0.2%(质量分数)时,合金的变形率增加了47.0%。确定了有利于Ti6Al4V合金室温电磁成形时的最佳氢含量。分析了氢致压缩性能的机理。     

Self-Nanocrystallization of Ti-6Al-4V Alloy Surface Induced by Laser Shock Processing

应用激光冲击强化技术（也叫激光喷丸）对TC4钛合金表面进行处理。由于其作用过程产生的高幅值压力（GPa量级）、短脉冲（ns量级）、高应变率(>106s-1)使材料表面实现纳米级晶粒细化成为可能,进而进一步提高材料表面性能。同时,应用该技术在TC4钛合金表面实现纳米级晶粒细化较少有系统的研究与报道。采用Q触发钕玻璃激光器,在一定条件、一定参数下,实现了TC4钛合金的表面纳米化,并对其形成机理进行阐述与分析。在实现材料自纳米化的同时,没有引入其它杂质粒子,保持了原母材的成分稳定性,且表面微动耐磨损性能得到了提高。开展该技术的深入研究,也可为材料表面纳米化提供另一种可行的途径与方法     

Effect of power density and pulse repetition on laser shock peening of Ti-6Al-4V

Laser shock peening (LSP) was applied to Ti-6Al-4V (wt. %) simulated airfoil specimens using a Nd:Glass laser. Laser shock peening processing parameters examined in the present study included power density (5.5, 7, and 9 GW/cm²) and number of laser pulses per spot (one and three pulses/spot). The LSP’d Ti-6Al-4V samples were examined using x-ray diffraction techniques to determine the residual stress distribution and percent cold work as a function of depth. It was found that the residual stress state and percent of cold work were relatively independent of LSP power density. However, the number of laser pulses per spot had a significant effect on both residual stress and percent of cold work for a given power density level. In addition, there was a strong correlation between the magnitude of residual compressive stresses generated and the percent cold work measured.     

机械合金化制备纳米晶Ti-6Al-4V合金

采用机械合金化制备Ti-6Al-4V粉末。结果表明:采用机械合金化可以制备纳米晶Ti-6Al-4V合金粉,其反应机理以扩散为主,该固态反应是缺陷能和碰撞能共同作用的结果;随球磨时间延长,部分V固溶于Ti中形成置换固溶体Ti(V),球磨过程中没有中间相生成。球磨40 h后都能获得纳米晶,60 h的粉末为纳米晶和非晶的混合物,晶粒尺寸小于60 nm;60 h后晶粒尺寸变化缓慢。球磨后Ti、Al、V的原子比近似为90:6:4,与Ti-6Al-4V元素成分一致。     

Oxygen effects on the mechanical properties and lattice strain of Ti and Ti-6Al-4V

The effects of oxygen on the mechanical properties and the lattice strain of commercial pure CP) Ti and Ti-6Al-4V alloys are discussed here in terms of the Vickers hardness, tensile strength and elongation. The Vickers hardness and tensile strength of the CP Ti and the Ti-6Al-4V alloys increased with an increase in the oxygen concentration. On the other hand, the elongation of the CP Ti decreased considerably as the oxygen concentration increased, while that of the Ti-6Al-4V alloys gradually decreased as the oxygen concentration increased. Thus, the oxygen concentration has a greater effect on the mechanical properties of CP Ti compared to its effects on the Ti-6Al-4V alloy. This can be explained in terms of the difference in the solid solution effect of oxygen between the CP Ti and the Ti-6Al-4V alloy. Where, the mechanical properties of Ti-6Al-4V alloy were previously affected by an earlier lattice expansion caused by an increment in the c/a ratio of the Ti-6Al-4V during the Al and V alloying process.     

Effect of processing parameters on formability,microstructure, and micro-hardness of a novel laser additive manufactured Ti-6.38Al-3.87V-2.43Mo alloy

A novel Ti-6.38Al-3.87V-2.43Mo alloy was designed with a cluster formula of 12[Al-Ti12](V0.75Mo0.25Ti2)+4[Al-Ti12](Al3)by replacing Ti with Mo/V on the basis of the Ti-Al congruent alloy.The effects of laser power and scanning speed on the molten pool size,surface roughness,relative density,microstructure,and micro-hardness of single-track and bulk Ti-6.38Al-3.87V-2.43Mo samples prepared via laser additive manufacturing(LAM)were investigated.The results show that processing parameters significantly affect the formability,microstructure,and micro-hardness of the alloy.With decreasing laser power from 1,900 W to 1,000 W,the relative density is decreased from 99.86%to 90.91%due to the increase of lack-of-fusion;however,with increasing scanning speed,the relative density does not change significantly,but exceeds 99%.In particular,Ti-6.38Al-3.87V-2.43Mo samples of single-track and bulk exhibit a good formability under an input laser power of 1,900 W and a scanning speed of 8 mm·s_-1,and display the lowest surface roughness(Ra=13.33μm)and the highest relative density(99.86%).Besides,the microstructure of LAM Ti-6.38Al-3.87V-2.43Mo alloy coarsens with increasing laser power or decreasing scanning speed due to the greater input energy reducing the cooling rate.The coarsening of the microstructure decreases the microhardness of the alloy.     

Si diffusion behavior during laser welding-brazing of Al alloy and Ti alloy with Al-12Si filler wire

In laser welding-brazing of Al alloy (5A06) and Ti alloy (Ti-6Al-4V) with rectangular CO2 laser spot and with Al-12Si filler wire, element Si enriches at the interface between Ti substrate and the filler metal. It is found that the Si diffusion behavior has a significant effect on the formation of interfacial intermetallic compounds. To analyze the Si diffusion behavior, a model for the prediction of the chemical potential for ternary alloy was established. According to the calculated results of the influen...     

Ti-6Al-4V合金表面激光熔覆TiAlSi+xB4C涂层的组织及耐磨性

利用激光熔覆在Ti-6Al-4V合金表面制备了TiAlSi+xB₄C涂层,分析比较不同B₄C含量对于涂层显微组织、显微硬度和耐磨性能的影响。结果表明:B₄C含量不同,涂层中的物相种类差别不大;涂层的微观形貌由颗粒状晶、层状晶、胞状晶和短棒状晶组成;不同B₄C含量涂层的显微硬度分布趋势大致相同,与基材相比均有明显的提高,随着B₄C含量的增高,整体上涂层显微硬度逐渐增大,当B₄C的含量为8%时,涂层的显微硬度最高,达到1216 HV0.1,约为基体的4.2倍;而当B₄C含量过高时,涂层硬度降低,且涂层中出现微裂纹。通过磨损试验表明,不同B₄C含量的涂层耐磨损性能均明显的优于Ti-6Al-4V合金基体,含8%B₄C的涂层磨损量最小。熔覆不同含量B₄C的涂层明显改善了基体Ti-6Al-4V合金的表面性能。     

Warm die compaction and sintering of titanium and titanium alloy powders

A study has been made of the effect of non-lubricated warm die (200 °C) compaction on the densification of hydride–dehydride (HDH) Ti powder, pre-alloyed (PA) Ti-6Al-4V and Ti-10V-2Fe-3Al powders, and HDH Ti and V-Fe-Al master alloy powder blends, compared to cold die compaction. Depending on the compaction pressure, which was varied from 200 to 1000 MPa, non-lubricated warm die (200 °C) compaction was very effective for −100 mesh HDH Ti powder, increasing the green density by 5.0–9.4% theoretical density (TD). Die wall lubrication with stearic acid showed no influence on the green density when compacted at 800 MPa. With warm die (200 °C) compaction, achieving a green density of greater than 90%TD was straightforward for HDH Ti powder when compacted at ≥750 MPa. Accordingly, near pore-free (≥99.5%TD) Ti microstructures were obtained after sintering at 1300 °C for 120 min in vacuum when compacted at 1000 MPa. The resulting increment in the sintered density was between 2.0%TD and 4.4%TD. Warm die (200 °C) compaction showed no effect on PA Ti-10V-2Fe-3Al powder and only a small effect on PA Ti-6Al-4V powder when compacted at 1000 MPa. However, it was still virtually effective for Ti-10V-2Fe-3Al powder blends made of HDH Ti powder and V-Fe-Al master alloy powder. The observations were compared with literature data and discussed in accordance with the yield strength of Ti, Ti-6Al-4V, Ti-10V-2Fe-3Al and Al₃V as a function of temperature.