钻井完井液浸泡弱化页岩脆性机制

页岩脆性是页岩地层钻井、水力压裂设计的关键参数之一,目前针对钻井过程中工作液浸泡对页岩脆性的影响还未引起关注.通过开展钻井完井液浸泡前后页岩三轴力学实验,利用脆性评价模型分析了页岩脆性变化特征.结果表明,延长组页岩脆性强于龙马溪组页岩;油基和水基钻井完井液浸泡均能导致页岩脆性降低,且油基钻井完井液浸泡后的页岩脆性降低幅度更大;龙马溪组页岩浸泡后脆性减弱幅度较延长组页岩大.页岩脆性弱化机制包括:(1)由层理面胶结强度不同引起的脆性强弱差异;(2)由毛管自吸作用导致的高孔压、高应力强度因子、低临界断裂韧性;(3)由碱液侵蚀导致的页岩溶蚀孔形成及矿物颗粒碎裂;(4)由黏土矿物水化膨胀产生的膨胀应力;(5)由钻井完井液滤液润滑导致的页岩破裂面摩擦系数降低.延长组页岩层理面强度较龙马溪组页岩低,导致延长组页岩脆性强于龙马溪组页岩.其次,和水基钻井完井液相比,油基钻井完井液具有更大的自吸量、更高的pH值、更强的润滑性,因此,油基钻井完井液浸泡降低页岩脆性幅度更大.另外,由于龙马溪组页岩具有更小的润湿角、更强的毛管自吸和碱液侵蚀作用,相同浸泡条件下,龙马溪组页岩脆性降低幅度更大.本研究可为页岩地层钻井液性能优化、井壁稳定控制、水力压裂设计等提供理论指导.      

晶粒取向和物相组成的电子背散射衍射测定

介绍了用扫描电镜中电子背散射衍射（ＥＢＳＤ）附件所进行的初步研究工作．这些工作表明,２Ｈ马氏体的基面由母相的一个｛２２０｝Ｐ面转变而来,一个自协作马氏体片群内的Ａ、Ｂ、Ｃ、Ｄ４个变体由母相的不同的｛１１０｝Ｐ面转变而来．用ＥＢＳＤ技术可测出它们之间的取向关系．ＥＢＳＤ技术所提供的结构信息与Ｘ射线能谱分析提供的化学成分信息相结合使微区物相鉴定的结果更为可靠．发现Ａｌ６２．５Ｃｕ２５Ｆｅ１２．５合金的铸态主要由λ－Ａｌ１３Ｆｅ４、二十面体准晶和β相３者组成．无间隙钢７５０℃再结晶后有两类晶粒,其中平坦晶粒具有有利于冷加工性的γ纤维显微织构．     

Large-Field EBSD Mapping: Application to the Microstructure of a Friction Stir Welding Nugget

A dedicated procedure has been carried out to enable EBSD orientation mapping of large-fields, by combining beam scanning and stage control in order to acquire a patchwork of overlapping areas, and by using specially developed software to reconstruct the EBSD file of the large-field from the individual files. This procedure has been successfully used to study the microstructure of a friction stir welding nugget in an aluminium alloy.     

Orientation sensitivity of focused ion beam damage in pure zirconium: direct experimental observations and molecular dynamics simulations

A high-purity predominantly single crystalline zirconium was subjected to controlled focused ion beam (FIB) damage. Damage estimates were obtained from electron backscattered diffraction (EBSD) and nano-indentation measurements on exactly the same area/orientation. The damage kinetics, between different crystallographic orientations, differed by one order of magnitude and a clear hierarchy of orientation sensitive ion damage emerged. Use of a simple geometric approach, linear density of atoms and corresponding scattering cross-sections to impinging gallium ions, could differentiate between extreme damage kinetics; but failed when such differences were relatively minor. Numerically intensive molecular dynamics (MD) simulations, on the other hand, were more effective. However, MD simulations or direct EBSD observations failed to justify anisotropic irradiation hardening (AIH): 3–8 times more hardening for near basal. Though explanation for AIH is indirect, evidence and rationalization for orientation-sensitive radiation damage appears clear and statistically reproducible.     

Magnetically tunable transparency for magnetorheological elastomer films consisting of polydimethylsiloxane and Fe3O4 nanoparticles

In this research, we demonstrate magnetically tunable transmittance for the magnetorheological elastomer films comprised of polydimethylsiloxane and Fe₃O₄ nanoparticles. The films bearing anisotropic and isotropic microtexture were prepared with and without magnetic field, respectively. The usage of toluene as diluent during the film preparation process leads to the increased tunable range of the magnetically induced transparency in comparison with our previous results. For the anisotropic film containing 1 wt% Fe₃O₄ nanoparticles, an increase of 23.01% in film transparency was observed at the wavelength of 600 nm with a magnetic field of B = ~ 80 mT applied, which is 2.67 times greater than the maximum change achieved in our previous research. The variation in transparency caused by the external magnetic field has been tentatively assigned to magnetostrictive effect. And the film microtexture might have a great influence upon the way an external magnetic field alters film transmittance.     

TEM Orientation Mapping Applied to the Study of Shear Band Formation

The formation of brass-type shear bands (SBs) in twinned microstructures of oriented copper single crystals, has been investigated after channel-die deformation at 77K. Setting up a system for making high-resolution orientation maps using transmission electron microscopy (TEM) has opened new advantageous circumstances for the analysis of orientation changes within SBs. This method with spatial resolution higher than 10nm allows an examination of microstructure images composed of nanoscale sub-cells forming SBs structure. The early stages of SBs formation are the result of equally effective operation of two slip systems operating on the {111} slip planes which could be represented by a resultant super-system of type. This process leads to the lattice rotation about axis and to the rise of Goss orientation within the band. A minor group of components is observed near , arising from the near primary matrix orientation. For well-developed SBs, a second rotation about direction is observed. This tendency, resulting from the type slip systems operation, is usually accompanied by activation of new slip systems. Hence the process of SBs formation is regarded as a strictly crystallographic one.     

Orientation Imaging in Scanning Electron and Transmission Electron Microscopy for Characterization of the Shear Banding Phenomenon

The texture evolution during deformation of high purity fcc single crystals with initial (112) [11 ] orientation has been characterised in detail by transmission (TEM) and scanning (SEM–FEG) electron microscopes. The channel-die deformed samples up to reduction of about 1–1.5, first developing strongly anisotropic layers of elongated cells or twin-matrix plates and then compact clusters of SB. Substantial progress in understanding the mechanism of the SB formation was possible thanks to systematic local orientation measurements (orientation mapping) using SEM and TEM. These two techniques of local orientation measurements have been compared with respect to their applicability for the study of shear banding phenomenon and for characterization of the specific nanostructure of SB in metals with fcc lattice. It was shown that well-developed SB exhibit large orientation spreads up to 35–40° with respect to the adjacent areas outside the band. Most of these misorientations occur by rotations about the TD‖〈110〉 axis with significant further rotations about 〈112〉 poles. This ultimately leads to the formation of the texture components whose occurrence cannot be explained by models homogeneous deformation.