Application of texture simulation to understanding mechanical behavior of Mg and solid solution alloys containing Li or Y

The viscoplastic self-consistent model was used to interpret differences in the mechanical behavior of hexagonal close packed magnesium alloys. There are only subtle differences in the compression textures of magnesium and its solid solution alloys containing lithium or yttrium. However, the plane strain compression textures of the alloys showed an increasing tendency for the basal poles to rotate away from the “normal direction” towards the “rolling direction”. Texture simulations enabled these distinctions to be attributed to the increased activity of the non-basal c+a slip mode. The alloys had improved compressive ductilities compared to pure magnesium, and the increased c+a slip mode activity provides a satisfying explanation for this improvement, since it can accommodate c-axis compression within individual grains. Accounting for individual deformation mode hardening enabled the flow curves to be simulated and the anisotropic plastic response of textured wrought alloys to be mechanistically understood and predicted.     

Orthorhombic Mg4IrD5 with disordered deuterium distribution

Mg₄IrH₅ and its deuteride was synthesized by the reaction of magnesium and iridium powders with hydrogen (deuterium) at high pressure (41–100 bar) and high temperature (723–783 K). The structure was determined by X-ray and neutron powder diffraction. This compound crystallizes with a new structure type with orthorhombic symmetry (space group Imma, cell parameters a = 4.8110(3) Å, b = 8.9624(6) Å, c = 10.8970(8) Å, Z = 4, hydride, T = 298 K). It contains two deuterium sites: one is disordered with an occupancy of 75% and surrounds iridium in a distorted square planar configuration with distances [Ir---D] = 1.69 Å; the other is ordered and is coordinated by magnesium in a distorted tetrahedral configuration.     

α-Al2O3 sapphire and rubies deformed by dual basal slip at intermediate temperatures (900–1300 °C): II. Dissociation and stacking faults

Sapphire and rubies (undoped and Cr-doped α-Al₂O₃ single crystals) have been deformed in compression at temperatures lower than those previously used in studies of dislocations in the basal slip plane. Above 1400 °C, several features associating stacking faults out of the basal planes and partial dislocations (dissociation and faulted dipoles) have been observed in previous transmission electron microscopy investigations. The formation of these features involves climb controlled by atomic diffusion. Properties of climb-dissociated dislocations are discussed in relation to dislocation dynamics. Transmission electron microscopy examination of dislocation structures at lower deformation temperatures (1000–1100 °C) shows that similar features are formed but that they often imply cross-slip. A new mechanism for the formation of faulted dipole by glide is presented and an explanation for the 30° Peierls valley orientation is proposed. The presence of chromium has a small influence on stacking fault energies on planes perpendicular to the basal plane.     

Slip patterns and preferred dislocation boundary planes

The planes of deformation induced extended planar dislocation boundaries are analysed in two different co-ordinate systems, namely the macroscopic system defined by the deformation axes and the crystallographic system given by the crystallographic lattice. The analysis covers single and polycrystals of fcc metals in three deformation modes (rolling, tension and torsion). In the macroscopic system, boundaries lie close to the macroscopically most stressed planes. In the crystallographic system, the boundary plane depends on the grain/crystal orientation. The boundary planes in both co-ordinate systems are rationalised based on the slip. The more the slip is concentrated on a slip plane, the closer the boundaries lie to this. The macroscopic preference arises from the macroscopic directionality of the slip. The established relations are applied to (a) prediction of boundary planes from slip patterns and (b) prediction of slip patterns from boundary planes.     

New Zr6CoAs2-type compounds: Y6CoBi2, Ho6CoBi2 and Tm6CoBi2

Results of a powder X-ray diffraction investigation of new ternary compounds are reported. The compounds Y₆CoBi₂ [a=0.8312(1) nm, c=0.4144(1) nm], Ho₆CoBi₂ [a=0.8246(2) nm, c=0.4095(1) nm], and Tm₆CoBi₂ [a=0.8155(2) nm, c=0.4066(1) nm] crystallize in the hexagonal Zr₆CoAs₂-type structure (space group P6b2m No. 189). The Zr₆CoAs₂-type structure is a superstructure of the Fe₂P-type structure.     

Dependency of c-lattice parameter, activation energy and its magnetic power constant on x in Y1−xYbx/2Gdx/2Ba2Cu3O7−y superconductors

To investigate the effect of x on c-lattice parameter, the activation energy, and the magnetic power constant of activation energy, the nominal composition of Y_1−xYb_x/2Gd_x/2Ba₂Cu₃O_7−y superconducting samples for x = 0.0, 0.2, 0.4, 0.6, 0.8 and 1.0 were prepared by solid-state reaction technique. c-Lattice parameters of the samples were calculated using XRD data. From the resistivity curves which were obtained under 11 different magnetic fields from 0 up to 5 T in the temperature range from 70 to 100 K steps by 0.25 K in zero field cooling regime, the activation energies of the samples were determined using Arrhenius activation energy law. The magnetic power constants of activation energy of the samples were calculated from the slopes of the plots ln U versus ln H. The results showed that the value of c-lattice parameters of samples x = 0 (Y123), and x = 1.0 (YbGd123) are in good agreement with the reported works. It was found that c-lattice parameter decreased with the increasing the content x except samples of x = 0.4 and 1.0. It was thought that the origin of the separation from the linearity comes from the lack of Y in nominal composition for x = 1.0. As for the sample x = 0.4, it was thought to be due to the fact that Y, Yb and Gd atoms affect the superconductivity properties dominantly. On the other hand, there is a similarity among U(0 T), U(1 T), its magnetic power constant and the c-lattice parameter with increasing content x. The desired activation energy and its magnetic field dependency constant can be controlled with x and then this can be useful for the superconducting applications.     

Single crystal preparation and crystal structure of the Cu2Zn/Cd,Hg/SnSe4 compounds

Single crystals of Cu₂Zn/Cd/SnSe₄ were grown using a solution-fusion method. The crystal structure of the Cu₂Zn/Cd,Hg/SnSe₄ compounds were investigated using X-ray powder diffraction. These compounds crystallize in the stannite structure (space group I 2m) with the lattice parameters: a=0.56882(9), c=1.13378(9) nm, c/a=1.993 (Cu₂ZnSnSe₄), a=0.58337(2), c=1.14039(4) nm, c/a=1.955 (Cu₂CdSnSe₄) and a=0.58288(1), c=1.14179(2) nm, c/a=1.959 (Cu₂HgSnSe₄). Atomic parameters were refined in the isotropic approximation (R_I=0.0517, R_I=0.0511 and R_I=0.0695 for Cu₂ZnSnSe₄, Cu₂CdSnSe₄ and Cu₂HgSnSe₄, respectively).     

有效介质理论计算He原子在金属钒中的扩散行为

采用有效介质理论，并考虑晶格驰豫的影响计算He原子在金属钒中的嵌入能，通过能量分析推测He原子在金属钒中可能的扩散路径和扩散势垒。计算结果表明，He原子在金属钒bcc结构的四面体间隙位置有能量的最低点，为4.37eV，在八面体间隙位置嵌入能比四面体间隙位置的稍大，He原子在金属钒的bcc结构中最有可能在(100)面内沿着由位置(1，1／4，1／2)，(1，1／2，1／2)，(1，3／4，1／2)联成的直线(或其等价晶面相应联线)向外扩散。     

AZ31镁合金蠕变初期的变形特征

通过蠕变曲线的测定和TEM的形貌观察,研究了AZ31镁合金在蠕变初期的变形特征及组织演化规律．结果表明,蠕变初期的变形特征是：大量形变产生的(α)位错在合金的基面和非基面滑移,(α c)位错在锥面滑移．其中(α)位错通过位错分解反应可由一非基面交滑移至另一非基面．随蠕变进行,高密度的形变位错发生动态回复,可进一步束集形成位错胞和位错墙．蠕变初始阶段,在应力的作用下,适当取向的晶体发生孪生,并作为一种附加的变形机制而改善合金的韧性．     

单晶硅裂纹尖端的位错发射行为

利用透射电镜原位观察了单晶硅压痕裂纹尖端位错及位错偶沿滑移面的发射行为,考察了滑移面取向,外荷对发射位错及塑性区的影响,结果表明：在I型载荷作用下,滑移面与裂纹面夹角要影响从裂纹尖端发射的位错数量及塑性区,发射出的位错可沿最大切应力方向改变运动方向或交换滑移面运动,实验观察的位错宽度平均值为22．0nm,与Peierls位移框架模型计算的23．6nm相近。     

Phase field model of dislocation networks

In phase field model of dislocations, the short-range, non-linear core–core interactions are characterized through the crystalline energy and the gradient energy. In this article we extend and generalize the approximations of these energies employed in previous phase field models to account for dislocation reactions leading to network formation. In order to characterize dislocation activities involving all slip planes, we suggest the crystalline energy to be a function of a general plastic strain tensor produced by arbitrary linear combinations of simple shears associated with each slip system. For the four {111} slip planes in an fcc crystal, a particular form of such a crystalline energy is formulated by simple linear superposition of the interplanar potential of each individual slip plane. A more detail and general form of the gradient energy is derived from the consideration of the total Burgers vector dependence of dislocation line energy. Examples of applications are presented for interactions between two dislocation loops expanding on either a single slip plane or two intersecting slip planes, as well as for more complex reactions taking place in dislocation networks. It is shown that the generalized expressions are able to handle self-consistently reactions among dislocations of all slip systems in accord with Frank’s rule. These extensions are necessary steps toward advanced applications of the phase field method to dislocation substructure formation and coarsening.     

Investigating deformation processes in AM60 magnesium alloy using the acoustic emission technique

Microstructure changes in an AM60 magnesium alloy were monitored using the acoustic emission (AE) technique during tensile tests in the temperature range from 20 to 300 °C. The correlation of the AE signal and the deformation processes is discussed. It is shown, using transmission electron and light microscopy, that the character of the AE response is associated with various modes of mechanical twinning at lower temperatures, whereas at higher temperatures also the influence of c + a non-basal dislocations on the AE response must be taken into account.     

New RRh5Ge3 compounds of the new SmRh5Ge3 structure type and their magnetic properties (R=Sm, Gd, Tb)

Powder X-ray diffraction results and macroscopic magnetic properties of new ternary RRh₅Ge₃ compounds (R=Sm, Gd, Tb) are reported. The compounds SmRh₅Ge₃ (a=2.2744(4) nm, c=0.3888(1) nm), GdRh₅Ge₃ (a=2.2711(5) nm, c=0.3872(1) nm) and TbRh₅Ge₃ (a=2.2628(7) nm, c=0.3851(1) nm) crystallize in the hexagonal SmRh₅Ge₃-type structure (space group P6₃/m; No. 176). The GdRh₅Ge₃ and TbRh₅Ge₃ compounds are Curie–Weiss paramagnets down to 5 K.     

镁及镁合金阻尼特性的研究进展

综述了镁及镁合金阻尼特性的研究进展及阻尼镁合金材料的研究现状,介绍了其阻尼性能的评价方法,阐明了其阻尼机制符合G-L位错钉扎模型、基面(0001)上的位错脱钉运动是造成镁合金在室温具有高应变振幅阻尼性能的主要原因,概述了应变振幅、温度、变形工艺、热处理、晶粒尺寸和取向以及合金元素对镁合金阻尼性能的影响.     

γ′-cutting as rate-controlling recovery process during high-temperature and low-stress creep of superalloy single crystals

In the present study the pairwise cutting of the γ′-phase after high-temperature and low-stress shear creep deformation of superalloy single crystals was investigated using weak-beam and high-resolution transmission electron microscopy. Recently, a cutting process in the single-crystal superalloy CMSX-6 was observed [Acta mater., 45 (1997) 4251] where two γ-channel dislocations with different Burgers' vectors (b) jointly shear the γ′-phase in forming a superdislocation with an overall Burgers' vector of a[010]. This type of high-temperature and low-stress γ′-phase cutting mechanism was also observed for CMSX-4 in the present work, indicating that this mechanism is relevant for superalloy single crystals in general. Two different configurations have been observed associated with the pure edge a010 and the 45° a001 dislocations. The cores of these superdislocations are not compact, but rather are composed of two different a/2110 dislocations. The distance between the leading and the trailing superpartial dislocation for the pure edge a010 configuration is of the order of 25 Å. In all cases observed in the present study, the common superpartial is associated with the crystallographic slip system that is directly loaded (Schmid factor 1). The striking feature of the movement of the superdislocations in the γ′-phase is that the two superpartials need to move by a combined process of glide and climb. This requires diffusional exchange of atoms/vacancies between the leading and the trailing superpartial, in which case the process is self-fed and the overall vacancy equilibrium is not disturbed. It is also possible that one dislocation pair produces or absorbs vacancies so that its movement must be coupled to events which maintain overall vacancy equilibrium. Minimum creep rates can be rationalized on the basis of the fluxes associated with the movement of superdislocations in the γ′-phase.     

Zur Kenntnis von RbBa3Ca4Cu3V7O28

Single crystals of RbBa₃Ca₄Cu₃V₇O₂₈ were prepared above the melting point of the reaction mixture. It crystallizes with hexagonal symmetry, space group C_6V⁴-P6₃mc, a 11.1751, c 12.434 Å, Z = 2. RbBa₃Ca₄Cu₃V₇O₂₈ is the second member of a new structure type of the copper-oxovanadates. Ba²⁺ shows an unusual 12-fold coordination. The two calcium positions are coordinated by trigonal prisms and octahedra respectively. The copper coordination is characterized by a stretched square pyramid. The Cu²⁺ ions are outside the centre nearly in plane of the pyramids.

Zusammenfassung

Einkristalle von RbBa₃Ca₄Cu₃V₇O₂₈ wurden oberhalb des Schmelzpunktes der Reaktionsmischung erhalten. Die Verbindung kristallisiert hexagonal, Raumgruppe C_6V⁴-P6₃mc, a 11.1751, c 12.434 Å, Z = 2. RbBa₃Ca₄Cu₃V₇O₂₈ ist das zweite Beispiel für einen neuen Strukturtyp der Kupfer-Oxovanadate, mit 12-fach koordinierten Ba²⁺ -Ionen. Die zwei Calciumpositionen sind trigonal prismatisch bzw. oktaedrisch koordiniert. Die Koordination der Cu²⁺-Ionen ist durch eine gestreckte Pyramide charakterisiert. Cu²⁺ ist auβerhalb des Polyederzentrums nahezu in der quadratischen Fläche der Pyramide angeordnet.     

High Strength and Ductility of a MgAg/MgGdYAg/MgAg Sandwiched Plate Produced by High-Pressure Torsion

Due to their unique precipitation behavior, magnesium-rare earth (Mg-RE) alloys exhibit excellent strength and high thermal stability. However, owing to the negative blocking effect of precipitation on dislocation slipping, the plasticity and ductility of Mg-RE alloys become deteriorate after aging treatment. In this work, a novel strategy to improve the combination of strength and ductility by designing a laminate heterostructured Mg alloy is proposed. High-pressure torsion (HPT) processing is employed to fabricate a clean and well-bonded interface between MgGdYAg and MgAg alloys. The two alloys have huge differences in precipitation hardening, and ductility is improved due to two facts. For one thing, the density of the second phases in the MgAg alloy is much lower than that of MgGdYAg alloy; for another, the non-basal 〈c + a〉 slipping is continuously activated during deformation. Through this mechanism, the uniform elongation of the heterostructured MgAg/MgGdYAg/MgAg alloy is improved to 7.1%.     

位错和位错偶沿单─滑移系从裂纹尖端的发射

采用计算机模拟了位错和位错偶沿单一滑移系从裂纹尖端的发射,考察了滑移面取向、外加载荷、晶格摩擦力以及位错发射的临界应力强度因子对所发射的位错数量、塑性区与无位错区大小以及裂关残余应力强度因子的影响研究表明,位错从裂纹尖端发射的临界应力强度因子对无位错区的存在和其大小起决定作用,而外加载荷与晶格摩擦力主要影响位错发射的数量以及塑性区大小．在Ｉ型载荷作用下,滑移面与裂纹面的夹角越大,从裂尖发射出的位错数量越多,位错对裂纹的屏蔽效应也越大当裂纹发射位错后的残余应力强度因子仍然较大时,位错偶就有可能在裂纹尖端附近产生井沿着几个滑移面发射,但发射出的位错偶对裂纹没有明显的屏蔽作用在滑移面不垂直于裂纹面时,发射出的位错或位错偶关于裂纹面呈不对称分布     

双相不锈钢中裂纹尖端塑性变形行为的透射电镜原位观察

在透射电子显微镜下对铁素体-奥氏体双相不锈钢薄膜试样进行了动态拉伸试验,原位观察了裂纹尖端塑性变形过程和位错分布,发现在铁素体相和奥氏体相中,裂尖位错组态有明显差异。在铁素体相中,裂尖无位错区较大,且让错易发生交滑移,在裂纹前端形成较大的塑性区。在奥氏体相中,裂尖无位错区较小,发射的位错在其滑移面内逆塞积。两相中裂尖滑移系的选择都与裂尖Schmid因子有关。但当形变较大时,奥氏体相中裂尖二次滑移系的选择不再为裂尖Schmid因子所支配。     

X-ray investigations of ternary R3Pd4Ge4 samples

Ternary R₃Pd₄Ge₄ samples (R=Nd, Eu, Er) were investigated by means of X-ray single crystal (four circle diffractometer Philips PW1100, MoK radiation) and powder diffraction (MX Labo diffractometer, CuK radiation). The Er₃Pd_3.68(1)Ge₄ compound belongs to the Gd₃Cu₄Ge₄ structure type, space group Immm, a=4.220(2) Å, b=6.843(2) Å, c=14.078(3) Å, R₁=0.0484 for 598 reflections with F_o>4σ(F_o) from X-ray single crystal diffraction data. No ternary R₃Pd₄Ge₄ compound when R is Nd or Eu was observed. The Nd and Eu containing samples appeared to be multiphase. Ternary phases observed in the Nd₃Pd₄Ge₄ and Eu₃Pd₄Ge₄ alloys and their crystallographic characteristics are the following: NdPd₂Ge₂, CeGa₂Al₂ structure type, space group I4/mmm, a=4.3010(2) Å, c=10.0633(2) Å (X-ray powder diffraction data); NdPd_0.6Ge_1.4, AlB₂ structure type, space group P6/mmm, a=4.2305(2) Å, c=4.1723(2) Å (X-ray powder diffraction data); Nd(Pd_0.464(1)Ge_0.536(1))₂, KHg₂ structure type, space group Imma, a=4.469(2) Å, b=7.214(2) Å, c=7.651(3) Å, R₁=0.0402 for 189 reflections with F_o>4σ(F_o) (X-ray single crystal diffraction data); Eu(Pd,Ge)₂, AlB₂ structure type, space group P6/mmm, a=4.311(2) Å, c=4.235(2) Å; EuPdGe, EuNiGe structure type, space group P2₁/c, and ternary compound with unknown structure (X-ray powder diffraction data).