喷丸、爆炸和滚压强化对高锰钢组织结构的影响

高锰钢经喷丸、爆炸或滚压强化后表面层内都能形成大量显微变形孪晶,同时伴有一定数量的ε马氏体(爆炸强化层中有时还可发现少量α马氏体)。喷丸在强化层内造成的孪晶栅栏密度最高,爆炸次之,滚压最低。三种强化方式都能使表面层内位错密度急剧升高。位错线的排列方式既有方向性又有形成胞状结构的倾向。喷丸和爆炸强化后位错方向性排列的趋势较强,而滚压则形成胞状结构的成分较大。虽然变形孪晶和ε马氏体都呈条状,但可根据其内部组织的结构形态配合选区电子衍射分析加以区分。     

层错能对Fe-Mn-C系TRIP/TWIP钢变形机制影响

对三种不同层错能(SFE)Fe-Mn-C系TWIP钢的变形机制进行了研究.结果表明:在淬火态下,TWIP钢组织为全奥氏体,奥氏体晶粒内存在少量退火孪晶.TWIP钢的层错能随着C、Mn含量的增加而增加.层错能为7 mJ/m2时,变形后出现大量ε马氏体,且随着应变量的增大,ε马氏体峰增强,表现为单一的TRIP效应;层错能为12 mJ/m2时,应变诱导γ→ε→α或γ→α的转变及形成少量形变孪晶,表现为TRIP/TWIP效应;层错能为18 mJ/m2时,变形后形成大量形变孪晶,表现为单一的TWIP效应,抗拉强度和延伸率分别达到851 MPa及49%.随着层错能增加,TWIP钢的断裂机制由沿晶断裂转变为以韧窝为主的塑性断裂.     

奥氏体不锈钢晶粒细化对形变机制和力学性能的影响

利用相逆转变原理采用冷变形使得亚稳奥氏体转变为形变马氏体,采用不同温度和时间退火分别获得纳米晶/超细晶和粗晶奥氏体不锈钢。通过拉伸实验得到不同晶粒尺寸的奥氏体不锈钢力学性能,采用透射电镜观察形变组织结构并利用扫描电镜观察断口特征。结果表明:高屈服强度纳米晶/超细晶奥氏体不锈钢通过形变孪晶获得优良塑性;而低屈服强度的粗晶奥氏体不锈钢发生形变诱导马氏体效应,得到良好的塑性;两组具有不同形变机制的奥氏体不锈钢拉伸断口均为韧性断裂。形变机制由形变孪晶转变为形变诱导马氏体归因于晶粒细化导致奥氏体稳定性大幅度提高。     

超细晶奥氏体在两相区大变形后的瞬态组织

将一种低碳结构钢循环加热淬火得到超细晶粒奥氏体,再以20℃/s的速率将其冷却至两相区进行真应变量为2的大变形,分析了形变后的瞬态组织.结果表明:用该工艺制备的超细晶奥氏体在两相区的高速大变形的后期,始终呈现应变硬化特征,并伴随有一定程度的形变诱导相变或铁素体动态再结晶等软化行为;同时,在较低温度快速大变形容易在试样的个别碳过饱和区导致应变诱导孪晶马氏体组织的生成,且随着形变温度降低孪晶马氏体量增加-循环加热淬火前的原始组织影响奥氏体内碳浓度分布,在一定程度上影响冷却变形过程的应力应变行为和形变后的瞬态组织.     

马氏体冷轧-回火制备超细晶钢及其热稳定性

在低碳钢和低碳加铌、钒、钛微合金钢中,通过马氏体冷轧--回火的方法获得了尺寸为数百纳米的超细晶粒铁素体组织,研究了超细晶粒组的形成机制和热稳定性.通过马氏体相交在这些钢中引入了大量高密度位错,马氏体冷轧后位错进一步增殖,形成大量位错胞状结构;在500-600℃进行的60min回火将上述胞状结构转变成具有清晰大角晶界的超细晶粒.在回火过程中形成的微合金元素碳化物对位错运动和晶界移动具有有效的"钉扎"作用,有助于获得超细晶组织并明显提高其热稳定性.     

Ultrafine Grains Formed through Tempering Cold Rolled Martensite and the Thermal Stability Analysis

在低碳钢和低碳加铌、钒、钛微合金钢中,通过马氏体冷轧--回火的方法获得了尺寸为数百纳米的超细晶粒铁素体组织,研究了超细晶粒组的形成机制和热稳定性. 通过马氏体相变在这些钢中引入了大量高密度位错,马氏体冷轧后位错进一步增殖, 形成大量位错胞状结构;在500-600℃进行的60 min回火将上述胞状结构转变成具有清晰大角晶界的超细晶粒.在回火过程中形成的微合金元素碳化物对位错运动和晶界移动具有有效的“钉扎”作用,有助于获得超细晶组织并明显提高其热稳定性.     

18-8型奥氏体不锈钢在低周疲劳变形下的微观组织特征

利用透射电镜系统地研究了18—8型奥氏体不锈钢在低周疲劳变形下的微观组织,包括奥氏体位错组态,形变孪晶和形变马氏体。发现奥氏体位错组态与应变幅和温度有关,形变马氏体主要在 SB 交截处形核,在室温和低温下由于母相变形方式的不同而产生不同的组织特征。     

低碳双相钢丝热处理与冷拉拨变形的组织观察

对２０双相钢线热处理与拉拨变形的组织进行了观察，结果表明，随亚温淬火温度的升高，双相组织中马氏体的亚结构由孪晶型变成位错型，两相的变形能力和拉拨性能都得到改善，变形量是影响位错数量及在双相组织中形成错胞的主要因素。     

低温大载荷冲击下纯铜的微观组织演变

本文提出了一种低温大载荷冲击制备块体超细晶纯铜材料的新方法。通过金相、透射电镜和显微硬度测试,研究了粗晶纯铜低温大载荷冲击变形后的微观组织演变以及退火处理对其微观组织的影响。结果表明,粗晶纯铜经低温大载荷冲击后晶粒得到明显细化。应变量为2.21时,材料内部出现高密度位错,晶粒在横截面上为等轴状,尺寸150~450nm;纵截面上为板条状,宽度30~220nm。粗晶纯铜低温大载荷冲击晶粒细化机制主要包括位错胞演变、动态再结晶和机械孪晶细化。经190℃退火60min后,材料内部高密度位错消失,晶粒在横截面上仍为等轴状,尺寸200~450nm;纵截面上仍为板条状,宽度70~100nm。     

MP—159合金强化机制的透射电子显微镜研究EI

本文针对MP—159合金的两种不同处理制度所得两种不同显微组织进行透射电子显微镜观察,从而对合金的强化机制进行探讨。结果表明,MP—159合金冷加工产生形变孪晶和hcp相在晶粒中形成互相交织的网络,使得位错很难长距离运动,进而形成高位错密度的胞状结构,产生加工强化,使合金强度显著提高。     

晶体取向对铜单晶体循环硬化行为的影响

研究了不同取向铜单晶体的循环硬化行为.结果表明,晶体取向对双滑移和多滑移取向铜单晶体的循环硬化行为有强烈的影响.不同取向铜单晶体的初始循环硬化率θ0.2与晶体中的位错反应模式、强度以及交滑移机会密切相关.临界双滑移晶体在循环硬化初始阶段呈现出独特的应变突发行为.     

形变铝合金的形变硬化特性

采用单轴拉伸方法测试了LD10,LF6,LC4和LY12几种形变铝合金的形变硬化指数,分析了合金的硬化率和硬化指数与应变的关系。结果表明,这几种形变铝合金的硬化指数在不同的应变区域具有不同的变化趋势。在低应变区域,形变硬化指数呈上升趋势,在高应变区域,形变硬化指数趋于平稳。四种形变铝合金中,LF6的硬化指数最高,LY12,LD10次之,LC4最低。形变铝合金的硬化率随着应变的增加不断降低。     

基体对高锰钢辙叉爆炸硬化效果的影响

为了研究基体对高锰钢辙叉爆炸硬化效果的影响,使用厚度3mm、密度1.38g/cm3的板状炸药分别在50mm厚钢板上、空气中及沙土上对高锰钢辙叉试件进行爆炸硬化。试验结果表明,在钢板上、空气中和沙土上对高锰钢进行爆炸硬化后,高锰钢辙叉试件的硬度分别提高了85.1%、76.6%和82.6%。与在钢板上和空气中相比,在沙土上对高锰钢辙叉试件进行爆炸硬化既能保证硬化后辙叉试件的硬度≥350HB,又能保证辙叉试件的整体不发生严重的变形。     

CYCLIC DEFORMATION OF A DIRECTIONALLY SOLIDIFIED COBALT-BASE SUPERALLOY

An investigation has been carried out on the cyclic deformation and changes in microstructure of a directionally solidified cobalt-base superalloy. The tests are conducted at 700 °C and 850 °C in air under different total strain amplitudes. The alloy tested at 700 °C exhibits an initial hardening, a short saturation stage and an evident secondary hardening, while the alloy at 850 °C suffers continuous cyclic hardening until fracture. TEM examinations indicate that the initial hardening of the alloy at 700 °C is caused by the pile-ups of dislocations and stacking faults at the stacking fault intersections, while the stress saturation is due to the weakening of obstacles against the dislocation movement. The secondary hardening has a contribution from the formation of sessile dislocation tangles. The early stage of continuous hardening of the alloy at 850 °C is related to the pile-ups of dislocations and stacking faults at the intersections, and the later stage is controlled by the interaction between precipitates and dislocations.     

低层错能奥氏体钢的变形硬化特点

研究了低层错能奥氏体不锈钢和高锰钢低温下的变形行为,根据两者拉伸应力应变曲线硬化阶段的相似性,提出曲线由基体硬化、行为软化和结构硬化三部分合成,应力应变曲线的上凹特征是软化主导与硬化共同作用的结果。分析了两种材料变形过程的相似性与不同点及其原因。     

在多轴载荷下45钢的循环特性

通过多轴疲劳试验，研究了在多轴加载条件下45钢的循环特性变化规律，分析了非比例附加强化、多轴循环软化/硬化特性及疲劳寿命对加载路径参数的依赖性，结果表明，相位角主要影响非比例附加强化程度，幅值比主要影响多轴循环软化/硬化特性，二者都影响多轴疲劳寿命。     

有限变形下的后继屈服面演化规律研究

有限变形下的后继屈服面会出现膨胀或收缩,移动和畸变等变形特征。基于塑性变形的滑移机制,建立了适用于有限变形条件下的多晶塑性本构模型。提出了一种混合硬化假设,可以一致描述后继屈服面演化中的等向、运动和畸变硬化以及正或负交叉效应、包氏效应等。预测了2种加工硬化铝合金（A16061-T6511和annexed1100A1）分...     

Predictive modeling of multi-track laser hardening of AISI 4140 steel

Laser hardening provides benefits over the conventional hardening processes, including minimum distortion in the parts and the absence of a quenchant. This process is also faster than conventional hardening processes and can be used for selective hardening of specific areas of components. One known problem with laser hardening in steels, however, is back tempering when a large area is hardened by multiple, overlapping passes. This study focused on the development of a numerical model to predict the back tempering in multi-track laser hardening. A tempering model was combined with existing models of thermal behavior and phase change kinetics, which were developed earlier in the authors’ group, to predict three-dimensional hardness profiles after multiple track laser hardening. The combined model was first validated through multi-track laser hardening tests and then used to predict and optimize the laser hardened case depth in multi-track laser hardening of AISI 4140 steel. The predictions and parameters optimized to obtain maximum case depth with the least variation along width of the hardened zone were experimentally verified. Case depths up to 2 mm were obtained with 5 mm overlapping of laser tracks.     

Transmission and scanning electron microscope study on the secondary cyclic hardening behavior of interstitial-free steel

Strain controlled fatigue experiment was employed to evaluate automotive grade interstitial-free ferrite steel. Hundreds of grains were examined by scanning electron microscope under electron channeling contrast image technique of backscattered electron image mode for comprehensive comparison of micrographs with those taken under transmission electron microscope. The cyclic stress responses clearly revealed that rapid hardening occurs at the early stage of cycling as a result of multiplication of dislocations to develop loop patches, dipolar walls and dislocation cells at various total strain amplitudes. After primary rapid hardening, stress responses varied from being saturated to further hardening according to dislocation structure evolution at various strain amplitudes. The fatigue failure was always accompanied with further hardening including secondary hardening. The corresponding dislocation structures with the three types of hardening behaviors are discussed. Once the secondary hardening starts, dislocation cells began to develop along grain boundaries in the low strain region and then extended into grain interiors as strain amplitudes increased and cycling went on. The secondary hardening rates were found to be directly proportional to their strain amplitudes.     

Strain hardening and orientation hardening/softening in cold rolled AA 5052 aluminum alloy

The tensile properties of cold rolled sheets were measured for the hot band and annealed hot band of AA 5052 aluminum alloy. The variation in yield strength with rolling true strain was used to represent the hardening rate of cold rolled sheets. The Taylor factor (M?) of cold rolled sheets in tension along the rolling direction was calculated based on the measured orientation distribution functions. The strain hardening and orientation hardening/softening produced by cold deformation were analyzed. The results show that the contribution to the hardening rate of cold rolled sheets comes largely from the deformed microstructure and partly from the texture change. For the annealed hot band the orientation softening occurs at strains below 0.5, while the orientation hardening occurs at strains over 0.5. For the hot band the dM?/dε value is always positive, indicating that orientation softening does not occur.