182Os核yrast带结构SU(3)→U(5)→SU(3)形状相变的有序性研究

对于发生在同一个原子核中的转动诱导发生基准态结构的量子相变,可以理解为一种从高有序激发模式向着低有序激发模式的演化：被布居到高角动量态的高有序激发核,以E2跃迁的方式先行退耦到yrast带,再退耦到共存区(或临界点)时释放了有序的结构能,诱发价核子对耦合强度改变,重新组合出低有序的激发模式基准态,实现了基准态结构的过渡.对核量子相变的这种描述,与朗道经典热相变理论之间有了某些相似的术语和物理内涵.本文把这种理解推广到了相继的二次相变中.以¹⁸²Os 核为例作了说明,并展 关键词： 量子相变 基态结构演化 F_max方案')" href="#">微观sdIBM-F_max方案 182Os核')" href="#">¹⁸²Os核     

金属间化合物DyMn2Ge2的自发磁相变和场诱导的磁相变

在10—800K的温度范围内用X射线衍射方法测量了DyMn₂Ge₂化合物的晶格常数与温度的变化关系,观察到高温时DyMn₂Ge₂由顺磁状态到反铁磁状态的自发磁相变伴随着晶格常数a的负的磁弹性异常现象.在4.2K—200K的温度范围内测量了DyMn₂Ge₂的交流磁化率.在交换相互作用的分子场模型近似下,从理论上分析讨论了DyMn₂Ge₂的低温自发磁相变和场诱导的磁相变.计算了DyMn₂Ge₂单晶的磁化强度与温度的变化关系以及不同温度下外磁场沿晶轴c方向时的磁化曲线.理论分析和计算结果表明,温度低于33K时在DyMn₂Ge₂中观察到的场诱导的一级磁相变为由亚铁磁状态(Fi)到中间态(IS)相变. 关键词： 稀土-过渡族金属间化合物 磁结构 磁相变     

静水压下锆锡钛酸铅铁电陶瓷相变和介电性能研究

研究了铌掺杂锆锡钛酸铅铁电陶瓷Pb_0.99Nb_0.02[(Zr_0.90Sn_0.10)_0.96Ti_0.04]_0.98O₃(PZST 90/10-4-2Nb)在静水压(0-300 MPa)下的电荷释放量和介电性能. 对压力诱导的低温铁电三方(F_R(LT))→反铁电正交(A_O)相变进行了研究. PZST 90/10-4-2Nb铁电陶瓷分为未极化、极化和压力去极化三种. 极化PZST 90/10-4-2Nb陶瓷F_R(LT)→A_O相变过程中,电荷释放量为29.3 μC/cm²,相变压力为140 MPa. 介电性能表明:极化PZST 90/10-4-2Nb陶瓷相变压力为136 MPa,而未极化陶瓷相变压力为104 MPa,压力去极化陶瓷未表现出明显的相变特征. 关键词： 静水压 铁电陶瓷 相变 介电     

182Os 核yrast带相继SU(3)–U(5)–SU(3)结构相变势能曲面的一种可能理解

基于联合实施微观相互作用玻色子模型的最大F旋方案 (sdIBM-F_max)与γ射线能量-自旋曲线 (γ-ray energy over spin curves, E-GOS)方案, 成功描述了¹⁸²Os核yrast带相继的SU(3)–U(5)–SU(3)结构相变, 由于缺少直观解释而显得抽象. 本文借助微观sdIBM-F_max的微观参数与Bohr哈密顿量的势能曲面方程之间存在的泛函关系, 几何地给出了对这种相继相变途径的另外一种可能理解; 并阐述了在完全变形核的高角动量态中, 由于量子效应在高激发态与低激发态之间生成高简并的临界区, 提供了γ振动能量会变得低于转动能量的一个可能途径, 从而实现了SU(3)–U(5)的相变. 关键词： yrast带结构演化 势能曲面 相变临界区 182Os核')" href="#">¹⁸²Os核     

基于透射光谱确定溶胶凝胶ZrO2薄膜的光学常数

基于溶胶凝胶ZrO₂薄膜的紫外/可见/近红外透射实验光谱,采用Swanepoel方法结合Wemple-DiDomenico色散模型,方便地导出了ZrO₂薄膜在200—1200nm波长范围内的光学常数,包括折射率、色散常数、膜层厚度、吸收系数及能量带隙.研究发现,溶胶凝胶ZrO₂薄膜具有高折射率(1.63—1.93,测试波长为632.8nm)、低吸收和直接能量带隙(4.97—5.63eV) 等光学特性,而且其光学常数对薄膜制备过程中的重要工艺 关键词： 光学常数 Swanepoel方法 2薄膜')" href="#">ZrO₂薄膜 热处理     

自旋为1的双层平方晶格阻挫模型的相变

采用双时格林函数方法研究了自旋为1的双层平方晶格阻挫模型的相变行为.详细探讨了层间耦合相互作用J_c和单离子各向异性参数D对奈尔态(AF1)和共线态(AF2)之间相转换的影响.结果显示:只要参数J_c和D不同时为零,奈尔态和共线态在J₂=J₁/2(这里J₁和J₂分别描述的是系统自旋间最近邻和次近邻交换作用)时的相变温度相等,两个态共存.在低于相变点的温度范围内,AF1-AF2态之间可以发生相转换,其相变类型为一阶相变.当J₂≠J₁/2时,尽管AF1-AF2态有不同相变温度,但它们也可以共存.如果AF1(AF2)态的相变温度大,在低温,AF1(AF2)态更稳定;在高温,AF2(AF1)态更稳定;在中间温度范围内,AF1-AF2态之间也可以发生一阶相转换.     

PLZST反铁电陶瓷电场诱导相变与相稳定性的研究

在三方铁电(FE)-四方反铁(AFE)的准同型相界附近制备了一系列组份为(Pb_0.97La_0.02)(Zr_1-x-ySn_yTi_x)O₃(x=0.09或0.1;0.16≤y≤0.38)的反铁电陶瓷.研究了Sn含量y对电场诱导AFE→FE相变电场E_c、反铁电双电滞回线损耗ΔE、以及温度诱导FE→AFE相变温度T_FE，AFE→顺电(PE)相变温度T_c的影响.沿AFE-FE相界Ti含量一定的条件下，E_c随着Sn含量y的增加而增大，ΔE减小，T_FE与T_c均降低.场诱相变的回线参量E_c，ΔE与相变温度T_FE和T_c相关联.在直流偏压下用原位X-射线衍射表征了相变时晶格结构的变化，结果表明，当电场达到AFE→FE相变临界场时，伴随相变的发生，晶格结构由四方相转变为三方相，晶胞体积增大. 关键词：     

哈斯勒合金Ni-Mn-Ga的马氏体相变和磁增强双向形状记忆效应

通过研究铁磁性金属间化合物Ni_2+xMn_1-xGa(x=-0.1,0,0.08,0.13,0.18,0.2)和Ni_2-xMn_1+x/2Ga_1+x/2(x=-0.1,0,0.04,0.06,0.1)两个系列多晶样品的交流磁化率随温度的变化行为,得到了化合物在不同组分下的马氏体相变温度TM和居里温度T_C.发现随着Ni成分的增加,前者的马氏体相变温度T_m增加,而居里温度T_C降低,后者的马氏体相变温度T_m和居里温度T_C均是先增大后减小.报道了T_m在室温附近的单晶样品Ni₅₂Mn₂₄Ga₂₄的磁场增强双向形状记忆效应.发现伴随着马氏体相变,样品在[001]方向可产生1.2%的收缩.如果在该方向施加1.2T的偏磁场可以使该应变值增大到4.0%.而垂直于[001]方向施加1.2T的偏磁场时,在[001]方向产生1.6%的膨胀.阐明了产生大应变的原因并非相界移动,而是单晶的杂散内应力小和外加磁场通过孪晶界移动使马氏体变体重组的共同结果. 关键词： 形状记忆效应 马氏体相变 2MnGa')" href="#">Ni₂MnGa     

ZrO2／SiO2多层膜中膜厚组合周期数及基底材料对残余应力的影响

ZrO₂／SiO₂多层膜由相同沉积条件下的电子束蒸发方法制备而成， 通过改变多层膜中高(ZrO₂)、低(SiO₂)折射率材料膜厚组合周期数的方法，研究了沉积 在熔石英和BK7玻璃 基底上多层膜中残余应力的变化. 用ZYGO光学干涉仪测量了基底镀膜前后曲率半径的变化， 并确定了薄膜中的残余应力. 结果发现，该多层膜中的残余应力为压应力，随着薄膜中膜厚 组合周期数的增加，压应力值逐渐减小. 而且在相同条件下，石英基底上所沉积多层膜中的 压应力值要小于BK7玻璃基底上所沉积多层膜中的压应力值. 用x射线衍射技术测量分析了膜 厚组合周期数不同的ZrO₂／SiO₂多层膜微结构，发现随着周期数增 加，多层膜的结晶程 度增强. 同时多层膜的微结构应变表现出了与所测应力不一致的变化趋势，这主要是由多层 膜中，膜层界面之间复杂的相互作用引起的. 关键词： 2／SiO₂多层膜')" href="#">ZrO₂／SiO₂多层膜 残余应力 膜厚组合周期数     

Ln(Ⅲ)-Ni(Ⅱ)与双水杨醛缩乙二胺席夫碱异核配合物的合成与波谱

合成了双水杨醛缩乙二胺席夫碱(SALEN)与镍的配合物Ni₃(SALEN)₂(NO₃)₆·H₂O及镧系镍的异核配合物Ln₂Ni₃(SALEN)₆(NO₃)₁₂·H₂O(Ln=La,Nd,Sm,Gd,Yb,Y).以紫外、红外光谱、磁化率,特别是¹H NMR及EPR波谱等方法研究了它们在组成、结构和配位等方面的异同.Gd-Ni-SALEN配合物的EPR谱表明其在低温THF中呈"单峰效应".文中讨论了配合物在不同溶剂中峰宽的相对关系、配合物晶体场强度及Gd³⁺周围局部对称性问题.     

Stress-induced cubic-tetragonal transformation in partially stabilized ZrO2: Raman spectroscopy study

Regularities of the cubic-tetragonal transformation (C→t′) in partially stabilized zirconia were studied with Raman spectroscopy and high-temperature Raman spectroscopy techniques. New ‘low temperature’ mechanism of tetragonal nanoparticles formation in a volume of cubic solid solution was revealed in ZrO₂-Gd₂O₃ (Eu₂O₃) (6-8 mol%) single crystals. This mechanism includes nucleation of the tetragonal nanoparticles due to diffusionless C→t′ phase transformation at the first stage and gradual decrease of the stabilizer concentration inside t′-domains after subsequent low-temperature annealing. Predominant orientation of tetragonal domains due to the stress-induced C→t′ transformation was registered in ZrO₂-Gd₂O₃ (8 mol%) single crystals.     

Modeling of thermomechanical fracture of functionally graded materials with respect to multiple crack interaction

Different aspects of thermomechanical fracture of functionally graded materials (FGMs) are considered. Among them are the crack interaction problems in a functionally graded coating on a homogeneous substrate (FGM/H). The interaction between systems of edge cracks is investigated, as well as, how this mutual interaction influences the fracture process and the formation of crack patterns. The problem is formulated with respect to singular integral equations which are referred to the boundary equation methods. The FGM properties are modeled by exponential functions. The main fracture characteristics are calculated, namely, the stress intensity factors, the angles of deviation of the cracks from their initial propagation direction and the critical stresses when the crack starts to propagate. The last two characteristics are calculated using an appropriate fracture criterion. The problem contains different parameters, such as the geometry (location and orientation of cracks, their lengths, and the width of the FGM layer) and material parameters, i.e. the inhomogeneity parameters of elastic and thermal coefficients of the functionally graded material. The influence of these parameters on the thermo-mechanical fracture of FGM/H is investigated. As examples the following real material combinations are discussed: TiC/SiC, Al₂O₃/MoSi₂, MoSi₂/SiC, ZrO₂/nickel and ZrO₂/steel.     

Influence of yttrium on EPR characteristics of chromium ions in nanoscale particles of zirconium dioxide

The EPR and proton magnetic resonance methods were applied to study zirconium hydroxide samples which transformed to nanoscale ZrO₂ powders upon annealing. The samples were obtained from solutions with mixture compositions (ZrO₂ + 0.5 mol % Cr₂O₃) and (ZrO₂ + 3 mol % Y₂O₃ + 0.5 mol % Cr₂O₃). The influence of yttrium on the recharging of the chromium ion upon annealing of samples was studied in the temperature range 100–950°C. A significant influence of yttrium on internal stresses caused by heating and cooling in the lattice of nanoscale ZrO₂ particles was detected using the EPR method. It was shown that the typical features of the influence of yttrium on total (over the entire crystallite) and local (near chromium ions) lattice distortions depend on the sample heating temperature and are different for various annealing temperatures.     

Microstructure characterization and phase transformation kinetic study of ball-milled m-ZrO2–30 mol% a-TiO2 mixture by Rietveld method

High-energy ball milling of monoclinic ZrO₂–30 mol% anatase TiO₂ mixture at different durations results in the formation of m-ZrO₂–a-TiO₂ solid solution from which the nucleation of nanocrystalline cubic (c) ZrO₂ polymorphic phase sets in. Post-annealing of 12 h ball-milled sample at different elevated temperatures for 1 h results in almost complete formation of c-ZrO₂ phase. Microstructure of the unmilled, all the ball milled and annealed samples has been characterized by Rietveld's X-ray powder structure refinement method. Particle size, rms lattice strain, change in lattice parameters and phase content of individual phases have been estimated from Rietveld analysis, and are utilized to interpret the results. In course of milling, (1 1 1) of cubic lattice became parallel to () plane of monoclinic lattice due to the orientation effect and cubic phase may have been formed on the (0 0 1) of the m-ZrO₂–a-TiO₂ solid solution lattice. A comparative study of microstructure and phase transformation kinetics of ZrO₂–10, 20 and 30 mol% a-TiO₂ ball-milled and post-annealed samples reveals that rate of phase transformation m→c-ZrO₂ increases with increasing a-TiO₂ concentration and 30 mol% of nanocrystalline c-ZrO₂ phase can be obtained within 4 h of milling time in the presence of 30 mol% of a-TiO₂. The post-annealing treatment at 773, 873 and 973 K for 1 h duration each reveals that rate of c-ZrO₂ formation with increasing temperature is retarded with increasing a-TiO₂ concentration but the amount of c-ZrO₂ becomes almost equal (95 mol%) at 973 K. It suggests that almost fully stabilized nanocrystalline c-ZrO₂ can be formed by adding a tetravalent solute to m-ZrO_2.     

Phase transformation of ZrO2 nanoparticles produced from zircon

This article focuses on the phase transformation of zirconia (ZrO₂) nanoparticles produced from zircon using a bottom-up approach. The influence of mechanical milling and thermal annealing on crystalline phase transformation of ZrO₂ nanoparticles was explored. It was found that the iron oxide, as an inherent impurity present in ZrO₂ nanoparticles, produced from zircon stabilises the cubic phase after calcination at 600°C. The stabilised cubic phase of ZrO₂ nanoparticles was disappeared and transformed into partial tetragonal and monoclinic phases after mechanical milling. The phase transformation occurred on account of the crystal defect induced by high-energy mechanical milling. The destabilisation of cubic phase into monoclinic phase was observed after the thermal annealing of ZrO₂ nanoparticles at 1000°C. The phase transitions observed are correlated to the exclusion of iron oxide from the zirconia crystal structure.     

Texture development and magnetic properties of [ZrO2/CoPt]n/Ag nanocomposite films

The L1₀ CoPt films with (0 0 1) preferred orientation are achieved by fabricating on the glass substrates and post annealing at 600° C for 30 min. The preferred orientation of [ZrO₂/CoPt]_n/Ag films dependence of the Ag underlayer thickness, ZrO₂ and CoPt interlayer thickness is investigated. A large perpendicular magnetic anisotropy and a nearly perfect L1₀ CoPt (0 0 1) texture are obtained in the [ZrO₂ (3 nm)/CoPt (5 nm)]₃/Ag (10 nm) film. The existence of ZrO₂ plays an important role in reducing the intergranular interactions and in determining the size of CoPt grains. Magnetic reversal in textured CoPt films are close to a Stoner-Wolfarth rotation.     

Phase composition and structure of nanocrystalline powders based on ZrO<Subscript>2</Subscript>(Y) and Al<Subscript>2</Subscript>O<Subscript>3</Subscript> obtained by plasma spray pyrolysis

It is shown that a nonequilibrium solid solution ZrO₂(3Y, Al) with tetragonal structure is formed in systems based on ZrO₂(3Y) with Al₂O₃ as a second component. A delay in the γ → α Al₂O₃ transformation and a reduction in the size of the coherently scattering domain of modifications are observed in systems based on Al₂O₃ with ZrO₂(Y) as a second component.     

Mesoporous silica templated zirconia nanoparticles

Nanoparticles of zirconium oxide (ZrO₂) were synthesized by infiltration of a zirconia precursor (ZrOCl₂·8H₂O) into a SBA-15 mesoporous silica mold using a wet-impregnation technique. X-ray diffractometry and high-resolution transmission electron microscopy show formation of stable ZrO₂ nanoparticles inside the silica pores after a thermal treatment at 550 °C. Subsequent leaching out of the silica template by NaOH resulted in well-dispersed ZrO₂ nanoparticles with an average diameter of ~4 nm. The formed single crystal nanoparticles are faceted with 110 surfaces termination suggesting it to be the preferred growth orientation. A growth model of these nanoparticles is also suggested.     

Effect of calcination temperature on phase transformation,structural and optical properties of sol–gel derived ZrO2 nanostructures

Zirconia (ZrO₂) nanostructures of various sizes have been synthesized using sol–gel method followed by calcination of the samples from 500 to 700 °C. The calcined ZrO₂ powder samples were characterized by X-ray diffraction (XRD), transmission electron microscopy (TEM), Fourier-transform infra-red spectroscopy (FT-IR), UV–visible spectroscopy (UV–vis.), Raman spectroscopy (RS) and thermogravimetric analysis (TGA). The phase transformation from tetragonal (t) to monoclinic (m) was observed. The average diameter of the ZrO₂ nanostructures calcined at 500, 600 and 700 °C was calculated to be 8, 17 and 10 nm, respectively. The ZrO₂ sample calcined at 500 °C with tetragonal phase shows a direct optical band gap of 5.1 eV. The value of optical band gap is decreased to 4.3 eV for the ZrO₂ calcined at 600 °C, which contains both tetragonal (73%) and monoclinic (27%) phases. On further calcination at 700 °C, where the ZrO₂ nanostructures have 36% tetragonal and 64% monoclinic phases, the optical band gap is calculated to be 4.8 eV. The enhancement in optical band gap for ZrO₂ calcined at 700 °C may be due to the rod like shape of ZrO₂ nanostructures. The tetragonal to monoclinic phase transformation was also confirmed by analyzing Raman spectroscopic data. The TG analysis revealed that the ZrO₂ nanostructure with dominance of monoclinic phase is found to be more stable over the tetragonal phase. In order to confirm the phase stability of the two phases of ZrO₂, single point energy is calculated corresponding to its monoclinic and tetragonal structures using density functional theory (DFT) calculations. The results obtained by theoretical calculations are in good agreement with the experimental findings.