预拉伸厚铝板内 部残余应力 与晶粒取向均匀性的研究

目的消减预拉伸铝板内部残余应力。方法利用短波长X射线衍射仪(SWXRD),分别对某公司国产25 mm厚2024-T351预拉伸铝板,以及美国铝业公司(ALCOA)20 mm厚7075-T651预拉伸铝板的内部残余应力、内部织构及其沿板厚的分布,进行了无损测定。结果 ALCOA的20mm厚7075预拉伸铝板内部残余应力小于25 MPa,其内部晶粒取向沿板厚均匀分布;而某公司原工艺生产的25 mm厚2024预拉伸铝板,内部残余应力高达100 MPa左右,其内部晶粒取向沿板厚分布很不均匀。结论源自于轧制的内部织构沿板厚分布的不均匀性,使得以消减残余应力为目的的预拉伸处理中的铝板塑性变形不均匀,导致某公司国产预拉伸铝板内部残余应力的消减效果差,在其后续加工中容易产生加工变形超差的问题,需要抑制强剪切织构的产生,减小织构在整个板材厚度上的不均匀分布程度。     

镀锡钢板分条翘曲的残余应力分析

使用X-350A型X射线应力测试仪对分条翘曲的镀锡钢板残余应力进行测定,发现镀锡钢板的分条剪切过程对原有残余应力有一定的释放,但是并没有产生新的残余应力。对镀锡钢板生产过程中的各阶段取样进行残余应力测定,结果表明:连续退火和平整之前冷轧态的带钢存在较大的表面残余压应力;平整之后的带钢表面残余压应力明显较冷轧态带钢的要小,但仍然存在一定的残余压应力;而在镀锡之后,镀锡板表面依然存在一定的残余应力,且与平整后带钢的残余应力在数值上接近;镀锡钢板发生翘曲的根本原因是平整轧制过程中带钢上下表面的纵向延伸不相等。本研究工作对解决镀锡钢板分条翘曲行为,改善镀锡钢板生产工艺有借鉴作用。     

不同焊接参数下CT70连续钢管高频电阻焊残余应力分布的数值模拟

目的研究CT70连续油管高频电阻焊接后的残余应力值和分布规律,以及焊接速度和挤压量等焊接参数对残余应力的影响。方法通过有限元计算的方法施加移动面热源和移动挤压辊,来模拟高频电阻焊的加热和加压过程,并用小孔法测量了高频电阻焊后连续钢管的残余应力值。结果对比计算的和实际的焊缝尺寸,均是内壁处为0.2 mm,壁厚中间部位为0.1 mm,内壁凸起高度为1.0 mm,宽度为2.1 mm,验证了有限元模型的准确性。计算得到的高频电阻焊后在焊缝处的轴向残余应力较大,在400～500MPa之间;环向残余应力较小,在-100～200MPa之间,与小孔法测量的残余应力一致。结论焊缝附近的残余应力主要由不均匀加热引起,远离焊缝处的残余应力主要由挤压引起。热源与挤压辊间距离和焊接速度增加会导致焊缝附近的残余应力增加;挤压量增加和焊接功率增加会导致焊缝附近的残余应力降低。     

冷轧带钢板形分段接触式检测过程的力学建模与仿真

建立了冷轧带钢板形应力分段接触式检测过程的ANSYS有限元模型,引入欧式距离方法表征检测误差,分析了在不同板形缺陷模式下,板形辊弯曲变形、板形辊分段区域宽度、板形辊直径、带钢包角、带钢厚度、卷取张力、带钢张力横向分布不对度等因素对板形检测精度的影响。仿真结果表明:随着板形辊弯曲变形程度的增大,板形应力检测精度大幅度降低。随着板形辊分段区域宽度的增大,板形检测精度大幅度降低;而随着板形辊分段区域宽度的减小,板形检测精度提高,但提高的幅度随着分段区域宽度的减小而越来越小。卷取工艺张力越低,板形检测精度越低;且当卷取张力增大到某一值时,再继续增大卷取张力对板形检测精度影响甚小。随着卷取张力横向分布不对称度的增大,板形检测精度降低。板形检测辊直径大小、带钢包角的变化以及带钢厚度的变化对板形检测精度没有影响。     

六辊轧机扭振动态建模及与板带钢质量关系研究

考虑轧机扭振与辊系沿轴向动态特性和板带材质量的关系,基于连续体动力学建立了六辊轧机扭振动力学模型,包括轧机辊系等效模型和辊身与辊径过渡部分等效模型。根据轧制速度与轧辊角速度的关系,建立了板带钢前后张力、轧制力等参数与辊系扭振的关系模型。基于所建模型对某六辊轧机施加位移激励模拟扭振情况,仿真分析了轧机辊系和板带钢在扭振激励下的三维动态响应。仿真结果表明,轧辊角位移和角速度沿辊身长度方向波动较小;轧辊扭振使轧制压力、前张应力和后张应力横向分布发生不同程度的波动,扭振对前张应力分布影响较大,即对板带钢板形产生影响,且传动侧的波动幅值大于操作侧。     

Q355钢板对接接头裂纹扩展所致焊接残余应力重分布研究

目的 定量研究裂纹扩展导致的焊接残余应力重分布效应,得到残余应力随裂纹扩展的变化规律。方法 首先采用盲孔法测试了Q355钢板对接接头的初始残余应力;其次利用线切割技术模拟了平行以及垂直于焊缝的裂纹扩展情况,并测试了裂纹扩展导致的残余应力变化量;最后根据测试数据提出了残余应力释放量Δσ与裂纹长度a之间的函数关系式,进一步得到了基于裂纹扩展的应力重分布计算公式。结果 Q355钢板对接焊的焊缝区纵向(沿焊缝方向)存在较大的残余拉应力,拉应力峰值出现在焊趾处,为屈服强度的1.13倍。焊缝区横向存在梯度较大、拉压交替变化的残余应力,压应力峰值出现在焊趾处,大小为52.6 MPa,拉应力峰值出现在距焊缝中心线17 mm处,大小为63.5 MPa。裂纹扩展能显著释放残余拉应力:裂纹沿焊缝中心扩展,横向残余拉应力峰值降低了45.8%;裂纹沿垂直于焊缝方向扩展,焊趾处的拉应力峰值降低了63.3%。结论 裂纹扩展会显著影响焊接构件的残余应力分布,根据实测数据提出的裂纹扩展应力重分布计算公式能够较好地反映残余应力重分布情况。     

薄壁管壳体环矢挤压缩径工艺仿真分析与研究

目的 针对空心薄壁件在缩径成形工序中力学性质难以观测且缩径成形加工效率较低的问题,提出一种使用18瓣环矢挤压模具进行环矢挤压一次性成形的缩径工艺,并研究了该工艺下薄壁管壳体的弹塑性变形规律。方法 以外径6.3 mm、壁厚2 mm、颈缩宽度1 mm的小尺寸薄壁管壳体（Q255材料）为研究对象,基于Barlat''96屈服准则和M–K沟槽理论,结合L.H.Donnell理论,建立管壳体环矢挤压缩径的塑性微元应力模型,通过ANSYS软件建立环矢挤压缩径工艺有限元模型,并进行数值模拟分析,获得管壳体环矢挤压过程中内壁面和颈缩区厚度方向的应力分布规律;最后进行实验验证,利用千分尺测量外径,采用应力测定仪测量中心位点应力,验证了该工艺下仿真结果的准确性。结论 颈缩区域宽径比越大,缩径成形越远离弹性区;内壁面的应力整体呈凸状分布;卸载后,壁厚方向的残余应力呈从外壁到内壁逐渐增大的线性分布趋势,缩径区中心点最大残余等效应力为319.76 MPa,分布在挤压部位的内表面;经实验验证,内壁面中心位点的最大残余应力为183 MPa,其与仿真分析结果（202.5 MPa）的吻合度高达91.5%,验证了仿真结果的准确性。该环矢挤压模具能够有效进行空心薄壁管壳体的一次性缩径成形,提高制造效率,该研究结果可为薄壁管件环矢挤压缩径成形的工艺设计及工程应用提供参考。     

短波长特征X射线衍射法无损测定孔挤压强化A100钢内部径向残余应力分布

工件表层残余压应力场直接影响其疲劳性能。为研究孔挤压强化试样的内部残余应力状态,利用自主研发的短波长X射线衍射仪,无损地测定了2.4mm厚A100钢孔挤压件板厚中心层的内部径向残余应力场的分布。结果表明:孔挤压强化使工件内部引入了残余压应力,最大压应力位于距孔表面4.6mm处,为-302MPa;残余压应力场深度达30mm左右。     

四辊平整机轧制过程多体接触耦合变形有限元模拟

为了提高四辊平整机的板型控制精度,采用非线性大变形弹塑性有限元法,考虑辊系弹性变形和轧件弹塑性变形的耦合关系,建立辊系与带钢多体接触的平整过程三维分析模型.利用该模型对不同轧制工艺条件进行的模拟计算,得到了平整小压下量时的接触压扁及应力状态分布规律和工艺参数对辊系弯曲变形及辊缝形状分布的影响规律.所建模型和分析结果可用于现场轧制过程离线分析和指导在线模型的设定.     

6.8级冷镦螺栓的表层残余应力分布

利用X射线衍射残余应力分析仪测定了6.8级螺栓热处理前后表层轴向和切向残余应力及其分布,分析了冷镦和缩径对螺杆与螺栓头部过渡圆角处残余应力的影响。结果表明:热处理前螺栓表层残余应力分布不均匀,最大残余拉应力为155.8MPa,热处理后残余应力降低幅度可达50%;半径方向上,残余应力随深度的增加由压应力向着拉应力转变。     

6061-T6 铝合金激光焊接接头腐蚀疲劳裂纹扩展

目的研究6061-T6铝合金激光焊接接头的腐蚀疲劳裂纹扩展特性,并分析裂纹扩展的影响因素。方法利用光纤激光器,焊接尺寸为150 mm×100 mm×4 mm(焊接方向、横向、熔深方向)的6061-T6铝合金,采用SE(B)三点弯曲疲劳裂纹扩展试验并利用连续降K法,分别在空气和人工海水中进行疲劳裂纹扩展试验,通过使用金相显微镜(OE)和扫描电子显微镜(SEM),对金相结构进行观测分析。结果同样工艺参数的焊接接头,在海水中疲劳裂纹门槛值(4.063 016 MPa·m~(0.5))大于空气中的门槛值(3.479 166 MPa·m~(0.5));在疲劳裂纹扩展中速区(da/dN10~(-5) mm/cycle)时,海水焊接接头疲劳裂纹扩展速率大于空气中的,低速区(da/d N10~(-5) mm/cycle)则小于在空气中的。结论成形良好的焊缝、晶粒细小的焊缝组织有助于接头疲劳裂纹扩展性能的提高;中速区,海水中疲劳裂纹扩展速率偏大,主要是由腐蚀条件下焊缝裂纹尖端阳极溶解和交变载荷共同作用导致;低速区,海水中疲劳裂纹扩展速率偏小,主要原因是腐蚀产物堆积于疲劳裂纹扩展尖端,产生较强裂纹闭合效应。     

Fatigue properties of arc-welded lap joints with weld start and end points

Fatigue properties of arc‐welded lap joints with weld start and end points were investigated through experiments with 2.3‐mm and 3.2‐mm thick 440 MPa‐class steel sheets. Macroscopic fatigue crack‐initiation sites depended on the length of the weld bead to the specimen width. In joints with shorter weld beads, cracks mainly initiated at the toe of the weld start points, while joints with longer beads had initial cracks at the toe of the bead centre. Crack‐propagation analyses, taking stress distribution around the weld toe and residual stress into account, suggested that residual stress distribution could move crack‐initiation sites from the weld start point to the bead centre, although the applied stress at the toe of the weld start point remains the highest.     

Evaluation of local fatigue strength in spot weld by small specimen

It has been reported that high strength steel sheet cannot improve fatigue strength of components with a spot weld. The purpose of this study is to discuss the dominant factors on the fatigue strength of spot weld in order to clarify the reasons. A new fatigue testing technique is developed for a small specimen with a total length of less than 3 mm, and the local fatigue strength of heat‐affected zone (HAZ), which is the crack initiation site in the joint, in a mild steel sheet (270MPa‐grade) and a high strength steel sheet (590MPa‐grade) are evaluated by this technique. The fatigue strength of HAZ is almost equal in both steels although the tensile strength of the 590MPa steel is higher than that of the mild steel. The stress in the tensile‐shear spot‐welded joint under cyclic loading and the residual stress by the spot‐welding are evaluated by finite element analyses. The residual stress is tensile in both steels. However, the plastic deformation takes place in the joint of the mild steel and this releases the residual stress. On the other hand, the stress in the 590MPa steel is elastic and the residual stress decreases the allowable alternating stress. The stress under the condition of the experimental fatigue limit of the joint considering the residual stress coincides well with the fatigue limit diagram of HAZ, which means that the fatigue limit of the joint is determined by the fatigue limit of HAZ and the residual stress.     

Residual stress field analysis of Al/steel butt joint using laser welding–brazing

The objective of this study is to analyse residual stress of the Al/steel butt joint using the laser welding–brazing. The welding parameters were a laser power of 1200?W, a welding speed of 600?mm min^?1, thickness of 150×150×2?mm and 150×150×1?mm, respectively. The residual stress was measured by the hole-drilling methods. Then, a finite-element model of the welding process was established, and it was verified by experiments. The results show that the calculated results are in conformity with the experimental results. The longitudinal residual stress on the galvanised steel (329?MPa) is larger than that on the aluminium alloy (293?MPa). At the location of the fixture, the longitudinal residual stress is substantially zero.     

Thermal Generation of Residual Stress Fields for Purpose of Distortion Minimization

Thermal treatments of steel components with the goal of hardening often result in distortion by releasing the residual stresses which were brought into the specimen during the preceding processing steps. The goal of the presented work is the minimization of this distortion. By generating definite residual stress fields and investigating the resulting distortion, the distortion mechanism can be observed in detail. A flexible and reproducible way to generate such residual stress fields inside a specimen is by means of local thermal treatment with a laser beam. Computer simulations as well as experiments were carried out using an idealized tooth of a gearwheel (finger sample) as a model system. The deformation of the samples due to the laser heat treatment and the stress fields generated inside the samples were determined with respect to different process parameters.     

Investigation on cracking mechanism of austenite stainless steel during in situ tension in transmission electron microscope

Twin-roll strip casting technology is a new one to produce austenite stainless steel strip directly. However, during this process, the cracking occurs usually on the surface of the steel strip. The technique of in situ tension in transmission electron microscope was used to observe and analyze the crack initiation and propagation in austenite stainless steel produced by twin-roll strip casting technology in this work. The results show that the crack initiates in dislocation free-zone firstly and then propagates along the direction vertical to the tensile force. The crack may propagate in continuous propagation way and discontinuous one respectively. When the shear stress on the close-packing face and the normal stress on the secondary close-packing face are at the same side of the tensile force, the cracks propagate continuously. However, when the shear stress on the close-packing face and the normal stress on the secondary close-packing face are in two sides, the cracks propagate discontinuously.     

Research on fatigue behavior and residual stress of large-scale cruciform welding joint with groove

Fatigue fracture behavior of the 30 mm thick Q460C-Z steel cruciform welded joint with groove was investigated. The fatigue test results indicated that fatigue strength of 30 mm thick Q460C-Z steel cruciform welded joint with groove can reach fatigue level of 80 MPa (FAT80). Fatigue crack source of the failure specimen initiated from weld toe. Meanwhile, the microcrack was also found in the fusion zones of the fatigue failure specimen, which was caused by weld quality and weld metal integrity resulting from the multi-pass welds. Two-dimensional map of the longitudinal residual stress of 30 mm thick Q460C-Z steel cruciform welded joint with groove was obtained by using the contour method. The stress nephogram of Two-dimensional map indicated that longitudinal residual stress in the welding center is the largest.     

热处理对TC4-DT钛合金组织性能的影响

研究了Ф300mm的TC4-DT钛合金几种热处理工艺参数对显微组织和室温性能的影响。研究表明α＋β区锻造Ф300mm的棒材晶粒较大,低倍呈现模糊晶,局部区域有明显的清晰晶,表明大规格棒材锻造均匀性较差。大规格的棒材＋双重退火热处理后,拉伸性能和断裂韧性均能达到Rm≥825MPa,RP0.2≥750MPa,A（纵向）≥8％,Z≥15％;KIC（T—L）≥90MPa·m1/2,具有良好的强度塑性匹配性能。α＋β相区锻造的Ф300mm棒材经965℃／1h Ac十550℃／6h AC和940℃／1h AC＋570℃／6h AC处理后,疲劳裂纹扩展速率在△K=11MPa·m1/2时,分别达到2．833036×10^-6mm／cycle和7．294209×10^-6mm／cyele。     

The stress-strain behaviour of a porous unidirectional ceramic matrix composite

The stress-strain behaviour of a porous unidirectional ceramic matrix composite is investigated. The fibres are SiC (Nicalon) and the matrix is an aluminium phosphate based system. Microscopic observations indicate that pores and microcracks break up the continuity of the matrix to create an irregular array of discontinuities or ‘matrix cracks’. Load/unload tensile test results indicate an increase in compliance, permanent strain and hysteresis as the peak stress is increased. These features are attributed to sliding at the fibre-matrix interface. In the model developed, the product of the crack spacing and interfacial sliding stress, l_cτ, completely defines the stress-strain response provided the constituent properties, residual stresses and initial crack spacing are known. For the material investigated, the product l_cτ maintains a value of about 1.0 mm MPa throughout the tensile test. This result is corroborated by optical measurements of the pore/microcrack spacing and push-out test results.     

Fretting fatigue behaviour of shot-peened Ti-6Al-4V at room and elevated temperatures

Fretting fatigue behaviour of shot‐peened titanium alloy, Ti‐6Al‐4V was investigated at room and elevated temperatures. Constant amplitude fretting fatigue tests were conducted over a wide range of maximum stresses, σ_max= 333 to 666 MPa with a stress ratio of R= 0.1 . Two infrared heaters, placed at the front and back of specimen, were used to heat and maintain temperature of the gage section of specimen at 260 °C. Residual stress measurements by X‐ray diffraction method before and after fretting test showed that residual compressive stress was relaxed during fretting fatigue. Elevated temperature induced more residual stress relaxation, which, in turn, decreased fretting fatigue life significantly at 260 °C. Finite element analysis (FEA) showed that the longitudinal tensile stress, σ_xx varied with the depth inside the specimen from contact surface during fretting fatigue and the largest σ_xx could exist away from the contact surface in a certain situation. A critical plane based fatigue crack initiation model, modified shear stress range parameter (MSSR), was computed from FEA results to characterize fretting fatigue crack initiation behaviour. It showed that stress relaxation during test affected fretting fatigue life and location of crack initiation significantly. MSSR parameter also predicted crack initiation location, which matched with experimental observations and the number of cycles for crack initiation, which showed the appropriate trend with the experimental observations at both temperatures.