工业纯钛TA1退火过程中的应力诱导晶粒长大行为

探究了应力对纯钛再结晶行为的影响。在纯钛板的退火过程中施加弯曲应力,并观察一个截面在拉伸和压缩应力下的再结晶过程。制备了变形量分别为20%、40%和60%的工业纯钛TA1轧制板,然后将这些样品置于600 ℃和30 MPa下保温10 min。结果表明,在变形20%和40%的样品中,只观察到少数再结晶晶粒。此外,受应力区域的平均晶粒尺寸大于无应力区域。进一步将变形40%的轧制薄板在600 ℃和30 MPa下保温60和120 min,拉伸应力区域中晶粒的异常生长一直持续到达到临界尺寸,之后晶粒停止生长。再结晶过程中晶粒生长的持续增加可归因于应力促进的位错调节。具有有利条件的晶粒倾向于沿着所施加的应力方向异常生长。然而,钛板内的高密度残余位错导致晶粒生长的驱动力降低,导致临界尺寸的存在。这些发现解释了钛在拉伸和压缩应力下观察到的不同再结晶行为。     

TA2拉压力学性能不对称性及应变速率敏感性

本文研究了不同应变速率下工业纯钛TA2室温拉伸和压缩力学行为,结果发现TA2具有明显的拉压屈服不对称性和拉压应变硬化不对称性;随着应变速率的增加,拉压不对称性有明显增加。采用电子背散射衍射（EBSD）技术分析了拉伸和压缩时TA2微观变形机制及微观组织演化规律,结果表明,TA2压缩时以孪晶变形机制为主,拉伸时以位错滑移为主;TA2微观变形行为的载荷敏感性导致了宏观力学性能的不对称性。     

Deformation mechanisms of pure Ti during equal channel angular pressing

The microstructural development of commercially pure titanium was investigated to elucidate the mechanisms of grain refinement and strain accommodation during equal channel angular pressing. The samples were processed at 623 K via route C, in which the sample was rotated 180° around its longitudinal axis between the passes. TEM micrographs of the sample undergoing the first pass revealed that the strain imposed by the pressing is accommodated mainly by {1011} deformation twinning. During the second pass, the deformation mechanism was changed to dislocation slip. TEM analysis indicated that the slip system consisted of alternating twin bands containing dislocations ofa slip on a prismatic plane and ofa+c slip on a pyramidal plane. Microstructural evolution in commercially pure titanium subjected to equal channel angular pressing was discussed based on the preferred orientation formed during the first pass and resolved shear stress for the slip systems.     

工业纯钛TA1的双道次热压缩变形及软化行为

在Gleeble-3500热模拟试验机上对工业纯钛TA1进行单、双道次等温热压缩试验,变形温度为650~850 ℃,道次间隙时间为1~60 s,变形速率为10 s^-1,研究了工业纯钛TA1单、双道次热压缩过程中静态软化和动态软化行为。利用光学显微镜对变形后的微观组织进行观察,研究了工业纯钛TA1在不同变形条件下的微观组织演变。结果表明,工业纯钛TA1在单、双道次热压缩变形过程中表现出明显的硬化和软化行为,峰值应力前表现为加工硬化,峰值应力后表现为加工软化,最终达到动态软化和加工硬化的动态平衡。在道次间隙时间内发生静态软化,静态软化程度随着道次间隙时间的增加和温度的升高而增大。随着道次间隙时间的延长和温度的升高,道次间再结晶更加充分,第二道次变形后晶粒尺寸增加更明显,当发生完全再结晶时,软化程度达到最大。在热压缩变形期间,发生动态软化,650 ℃和750 ℃时以动态再结晶为主,850 ℃时以动态回复为主。     

Plastic flow characteristics of ultrafine grained low carbon steel during tensile deformation

In order to explain steady-state plastic deformation, i.e. the absence of strain hardening in ultrafine grained low carbon steel during tensile deformation, steel of different ferrite grain sizes was prepared by intense plastic straining followed by static annealing and then tensile-tested at room temperature. A comparison between the ferrite grain size of ultrafine grained steel and the dislocation cell size of coarse grained steel formed during tensile deformation revealed that uniform dislocation distribution with high density and cell formation were unlikely to occur in this ultrafine grained steel. This is ascribed to the fact that the ultrafine grain size is comparable to or smaller than the cell size at the corresponding stress level. In addition, from a consideration of dynamic recovery, it was found that the characteristic time for trapped lattice dislocations to spread into the grain boundaries was so fast that the accumulation of lattice dislocation causing strain hardening could not occur under this ultrafine grain size condition. Therefore, the extremely low strain hardening rate of ultrafine grained low carbon steel during tensile deformation is attributed to the combined effects of the two main factors described above.     

A STUDY OF RATE-DEPENDENCE AT ELEVATED TEMPERATURE FOR AN AI-Cu-Mg ALLOY

The hot deformation of an Al-Cu-Mg alloy was studied in the two temperature ranges (room temperature-300℃ and 400℃-480℃). The rate-independent flow curves are typical of elasto-plastic response with significant work hardening followed by strain softening below 300℃. Similar dislocation structures with high density tangled into grain interiors were observed by TEM, which suggests that the process of obstacles arresting mobile dislocations results in this macroscopically rate-independence. At 400-480℃, all rate dependent flow behaviors characterized by a continuous softening after an initial work hardening at a small plastic strain show large tensile elongations. Long dislocation segments around the second phases infer their good mobility to climb across obstacles. Grain boundary morphology observed by TEM suggests that the capacity of the grain boundaries to absorb the dislocations sensitively accounts for the rate-dependent mechanical DroDerties.     

A STUDY OF RATE-DEPENDENCE AT ELEVATED TEMPERATURE FOR AN Al-Cu-Mg ALLOY

The hot deformation of an Al-Cu-Mg alloy was studied in the two temperature ranges (room temperature-300℃ and 400℃-480℃). The rate-independent flow curves are typical of elasto-plastic response with significant work hardening followed by strain softening below 300℃. Similar dislocation structures with high density tangled into grain interiors were observed by TEM, which suggests that the process of obstacles arresting mobile dislocations results in this macroscopically rate-independence. At 400-480℃, all rate dependent flow behaviors characterized by a continuous softening after an initial work hardening at a small plastic strain show large tensile elongations. Long dislocation segments around the second phases infer their good mobility to climb across obstacles. Grain boundary morphology observed by TEM suggests that the capacity of the grain boundaries to absorb the dislocations sensitively accounts for the rate-dependent mechanical properties.     

激光冲击铝合金微结构演化及力学行为的分子动力学模拟

目的 揭示激光冲击铝合金的微结构演化过程及塑性变形机制,探究残余应力产生的机理,为激光冲击提升铝合金力学性能提供理论参考。方法 基于分子动力学模拟,采用活塞冲击法实现多晶铝合金(Al-Mg-Zn-Cu)在不同加载速度下的冲击强化。利用共邻分析法和位错提取法,研究铝合金的微结构演化过程、位错分布以及激光冲击影响铝合金力学性能的内在机理。结果 在冲击波加载阶段,当高速冲击波作用时,铝合金出现大量滑移系,产生高密度位错。在保载阶段,位错集中在晶界附近,导致多晶铝合金发生晶界塑性变形。在卸载阶段,不同类型位错之间进行了相互转化。铝合金两端晶粒和晶界的塑性变形,导致了残余压应力的产生。对完全卸载后的铝合金进行单轴拉伸模拟,发现0.7 km/s和1.0 km/s的冲击速度下,残余压应力抵消了部分拉伸应力,变形晶界附近产生新的位错,且晶界发生迁移和合并,导致极限应力分别提升15%和22%。结论 激光冲击对Al-Mg-Zn-Cu铝合金的微结构及力学性能影响显著,在高速冲击波作用下,铝合金两端发生剧烈的塑性变形,导致残余压应力的产生。单轴拉伸时,残余压应力抵消了部分拉伸应力,且铝合金晶粒内发生原子变形产生新的位错,同时晶界发生运动,最终使得极限应力增大,铝合金的力学性能得到提升。     

Effects of grain size and indentation sensitivity on deformation mechanism of nanocrystalline tantalum

Nanoindentation process is performed by molecular dynamics simulations to investigate the plastic deformation phenomena and mechanical properties of the polycrystalline tantalum (Ta) substrate. The comparison of mechanical behaviors between the single crystal and polycrystalline Ta is analyzed. The effects of grain size, indenter radius, indentation velocity, and temperature are deeply investigated. Further, the important factors of mechanical property such as the plastic deformation, dislocation, amorphization process, indentation force, yield pressure, and von Mises stress are evaluated. The results show that the phase transformations and dislocations almost absent in the grains. Instead, the dislocations densely occur in the grain boundaries, the amorphization regions are formed around the indentation areas and develop along the grain boundaries. The high von Mises stresses are mainly distributed around the indentation areas and in the grain boundaries. The single crystal tantalum shows better mechanical characteristics than the polycrystalline tantalum such as harder to deform, higher yield pressure, and lower dislocation.     

原始晶粒尺寸对ECAP变形纯钛组织性能的影响

室温下,对923 及1023 K退火1 h所得的不同原始晶粒尺寸的工业纯钛进行ECAP变形。通过TEM、EBSD、室温拉伸和显微硬度测试研究原始晶粒尺寸对ECAP变形纯钛组织性能的影响。探讨纯钛ECAP变形孪生行为和变形机制。结果表明,退火温度越高,原始晶粒尺寸越大。1道次变形后,1023 K退火纯钛的晶粒细化效果更显著。4道次变形后,923 K退火纯钛的组织更细小均匀。随着变形道次的增加,屈服强度不断增大,1道次变形后增幅最大,约为100%,且原始晶粒尺寸越大,强度增幅越大。纯钛ECAP变形机制包括位错滑移和孪生,原始晶粒尺寸越大,孪晶数量越多。     

固溶-大变形-时效下7085铝合金的强化机理

以固溶—时效和固溶—大变形(压缩、ECAP)—时效加工的7085铝合金为实验对象,分别采用拉伸试验机、X射线衍射仪(XRD)和晶体微区取向分析技术(EBSD)对7085铝合金的拉伸性能、内部的位错密度、单元边界(小角度晶界)和晶粒边界(大角度晶界)进行研究,结合拉伸试验测得的屈服强度,定量计算强化项对不同状态下铝合金的强化贡献。结果表明,相比常规固溶—时效工艺,固溶—大变形—时效工艺加工的7085铝合金的拉伸强度从381.2MPa分别提升到475.6和543.3 MPa;位错强化显著提高,从零分别提高到107.4和180.6 MPa;小角度强化显著提高,从10.4 MPa分别提高到89.1和116.4 MPa。7085铝合金强度提高来源于材料内部的位错和小角度晶界;固溶后的大变形加速了时效,降低了时效沉淀强化。并且发现强烈塑性变形加工(ECAP)的强化效果高于传统塑性变形加工(压缩变形)的效果。     

铸态AZ31镁合金的超塑性性能及流变应力

通过连铸AZ31镁合金的单向拉伸实验,研究了该合金的超塑性变形性能及不同拉伸变形条件下的流变应力。结果表明,在温度为300℃~450℃,应变速率.ε为4.25×10-4s-1的情况下,连铸ZA31镁合金表现出超塑性。在温度为400℃,应变速率.ε为4.25×10-4s-1时,延伸率增加了200%,具有较好的超塑性性能。用光学显微镜观察变形前后拉伸试样的微观组织发现:试样的初始晶粒尺寸约为15μm,在变形之后颈缩区域的晶粒长大现象不是很明显,晶粒沿着变形方向有所伸长,但晶粒形状基本保持为等轴状。     

退火温度对Fe-Mn-Al-C钢组织和拉伸性能的影响

采用OM、SEM、TEM和拉伸试验等手段研究了退火温度对Fe-19Mn-2Al-0.6C钢组织和性能的影响。结果表明,退火后试验钢的基体组织为奥氏体。由于回复再结晶的完成程度不同,随着退火温度的升高,晶粒尺寸先减小再增大。同时,退火孪晶的数量逐渐增加,抗拉强度持续降低,但总伸长率先升高然后降低。当施加一定的外部载荷时,在变形过程中会产生大量的变形孪晶和位错。高密度位错在晶界或孪晶界处的缠绕和塞积阻碍了位错的进一步运动。一次孪晶和二次孪生的交割产生的动态Hall-Petch效应,以及位错和孪晶的相互作用共同导致试验钢的高加工硬化能力。Fe-19Mn-2Al-0.6C钢获得最佳综合力学性能的退火温度约为900 ℃,其抗拉强度为947.61 MPa,强塑积为49.30 GPa·%,伸长率为52.03%。     

电沉积宽晶粒尺寸分布纳米镍的拉伸变形组织与变形行为

选用直流电沉积制备平均晶粒尺寸为27.2 nm,宽晶粒尺寸分布(5～120 nm)的纳米镍(简称宽晶纳米镍),在室温采用拉伸应变速率(ζ)突变法测量其应变速率敏感指数(m).发现m随的减小而增加,特别在小于2×10-5s-1时,m快速增加,m在=5×10-6s-1时达到0.054,表明塑性变形过程中晶界扩散、晶界滑移很可能被激活.在室温进行循环加载-卸载拉伸测试,结果表明宽晶纳米镍晶内存储位错的能力十分有限,当拉伸应力达到1052 MPa,应变为7.8%时,晶内位错密度达到饱和.通过对拉伸断口附近的TEM观察,证实宽晶纳米镍在塑性变形过程中存在显著的类似粗晶中的晶内位错滑移.     

AZ80镁合金的高温拉伸变形行为

采用拉伸至断裂实验,在温度为300、350、400和450℃,应变率分别为10~（-2）和10~（-3）S~（-1）条件下,研究AZ80镁合金的拉伸行为。并采用变化应变率拉伸实验在5×10弓至2×10~（-2）S~（-1）的应变率范围内进行变形机制研究。结果表明：该材料在400和450℃下具有超过100％的高伸长率,其应力指数为4．29,变形激活能为149．60kJ／mol。初始细晶粒在均匀变形区的高温变形中较为稳定,其变形机制为晶界滑移和位错攀移蠕变的竞争机制。基于该机制所建立的数学模型的模拟结果与实验数据吻合。     

TENSILE CREEP DEFORMATION AND DAMAGE BEHAVIOR IN A NICKEL-BASE SUPERALLOY AT 900℃

The tensile creep deformation and damage evolution in a Ni-base superalloy at 900℃/170MPa were investigated. At the first creep stage, abnormal creep occured due to the resolution of fine particles, and the deformation initiated from grain boundary areas. It is evident that nearly all of the dislocations were in γ matrix channels in form of dislocation pairs and the dislocations were impeded at γ/γ′ interfaces, thus the dislocation networks developed deformation. At the steady creep stage, impeded dislocations at γ /γ′ interfaces climbed over γ′ phases by diffusion-dominant mechanism.At the last creep stage, voids were formed around carbides at grain boundary which leaded to accumulated damage and caused creep rate accelerated. With the dislocation networks being broken, the voids connected and grew into micro-cracks gradually.Finally the cracks propagated along grain boundary area and resulted in failure.     

TENSILE CREEP DEFORMATION AND DAMAGE BEHAVIOR IN A NICKEL-BASE SUPERALLOY AT 900℃

The tensile creep deformation and damage evolution in a Ni-base superalloy at 900℃/170MPa were investigated. At the first creep stage, abnormal creep occured due to the resolution of fine particles, and the deformation initiated from grain boundary areas. It is evident that nearly all of the dislocations were in γ matrix channels in form of dislocation pairs and the dislocations were impeded at γ /γ‘ interfaces, thus the dislocation networks developed deformation. At the steady creep stage, impeded dislocations at γ/γ‘ interfaces climbed over γ‘ phases by diffusion-dominant mechanism. At the last creep stage, voids were formed around carbides at grain boundary which leaded to accumulated damage and caused creep rate accelerated. With the dislocation networks being broken, the voids connected and grew into micro-cracks gradually. Finally the cracks propagated along grain boundary area and resulted in failure.     

定向凝固镍基高温合金的反常屈服和中温脆性行为（英文）

采用真空冶炼和定向凝固工艺制备一种具有优异抗腐蚀性能的镍基高温合金,并利用光学显微镜、扫描电镜和透射电镜研究合金的微观组织,分析合金在不同温度下的拉伸性能。结果表明,除γ′颗粒和γ基体外,在合金晶界上析出了一些MC碳化物、M3B2硼化物和Ni5Hf相。合金拉伸性能对温度有很强的依赖性,并呈现明显的的反常屈服和中温脆性行为。在650°C以下,合金的屈服强度随着温度的升高而略微降低,但抗拉强度几乎没有变化。当温度在650°C和750°C之间时,合金的屈服、抗拉强度快速升高,但拉伸塑性显著降低,并在700°C时达到最低值。当温度进一步升高时,合金的屈服、抗拉强度逐渐降低,塑性升高。透射电镜观察发现,在低温条件下,位错切割γ′是主要的变形机制;在高温条件下,位错绕过γ′是主要的变形机制;由位错切割γ′转变至位错绕过γ′的温度约为800°C。合金的反常屈服和中温脆性行为主要归因于合金中高的γ′含量。此外,碳化物和共晶组织对合金的中温脆性行为也有影响。     

Relationship among microstructure,mechanical properties and texture of TA32 titanium alloy sheets during hot tensile deformation

The relationship among microstructure, mechanical properties and texture of TA32 titanium alloy sheets during hot tensile deformation at 800 °C was investigated. In the test, the original sheet exhibited relatively low flow stress and sound plasticity, and increasing the heat treatment temperature resulted in an increased ultimate tensile strength (UTS) and a decreased elongation (EL). The deformation mechanism of TA32 alloy was dominated by high angle grain boundaries sliding and coordinated by dislocation motion. The coarsening of grains and the annihilation of dislocations in heat-treated specimens weakened the deformation ability of material, which led to the increase in flow stress. Based on the high-temperature creep equation, the quantitative relationship between microstructure and flow stress was established. The grain size exponent and α phase strength constant of TA32 alloy were calculated to be 1.57 and 549.58 MPa, respectively. The flow stress was accurately predicted by combining with the corresponding phase volume fraction and grain size. Besides, the deformation behavior of TA32 alloy was also dependent on the orientation of predominant α phase, and the main slip mode was the activation of prismatic 〈a〉 slip system. The decrease of near prism-oriented texture in heat-treated specimens resulted in the enhancement of strength of the material.