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 共查询到19条相似文献,搜索用时 78 毫秒
1.
屈少华  曹万强 《物理学报》2014,63(4):47701-047701
基于球形无规键无规场模型和电场作用下弛豫铁电体微畴-宏畴机理,利用模糊畴界观点以及电场对极化的分数维效应,分析了电场对畴的作用机理.研究结果表明:电场对畴的诱导偶极子增量的极化效应导致了电滞回线的不饱和及相关的大的电致伸缩效应;而畴的偶极子增量耦合时结合能的变化对低电场的电滞回线略有影响,但基本不会改变高电场时的极化状态.初始微畴大小对电滞回线非常重要,细小的微畴会导致细长的电滞回线及电场与电致伸缩良好的线性关系.  相似文献   

2.
铁电体中偶极子的滞后对剩余极化的影响   总被引:1,自引:0,他引:1       下载免费PDF全文
曹万强  刘培朝  陈勇  潘瑞琨  祁亚军 《物理学报》2016,65(13):137701-137701
铁电体的剩余极化强度随温度降低而下降的特性引起了人们对铁电体存储数据失效的担心.运用铁电体的唯象理论和偶极子对交变电场的响应,提出了在电滞回线测量中偶极子的滞后冷冻效应模型,对极化的低温退化现象做了合理解释:温度下降导致吉布斯自由能势垒增大,致使偶极子对交变电场的响应时间延长.引入响应的滞后因子发现,极化强度随温度降低会出现峰值,在低温下降直至为零,可用偶极子的滞后与冻结效应描述.详细研究结果表明:因材料组份变化导致热力学参量的变化是重要因素:铁电-顺电相变中软模系数的增大会导致剩余极化峰移向高温;铁电性的增强,温度极化系数的增大和耐压强度或饱和电场的增强均会抑制滞后效应,从而使低温滞后效应移向低温.运用导出的公式数值模拟Ba Ti O_3/Bi Sc O_3复合陶瓷剩余极化强度的实验结果发现,Bi Sc O3含量的增加,使居里温度略有减小,但导致了软模系数较大幅度的增加,其结果是使偶极子的滞后效应发生在较高的温度.软模系数与铁电体的极化特性、铁电性、介电性和力学性均密切相关.研究结论表明:在低温下铁电体的铁电性没有失效,偶极子的低温冻结效应更有利于铁电体长久地保存数据.  相似文献   

3.
一、引 言 电滞回线是铁电体的主要特征之一,电滞回线的测量是检验铁电体的一种主要手段,常见的电滞回线如图1所示.通过电滞回线的测量,可测定铁电体的剩余极化强度Pr和矫顽场强Ec,对材料的研制和应用都有很大的意义. 测量电滞回线的基本电路是Sawyer-Tower回路,近年来测量频率已由50Hz向低频方面发展,其原因是铁电体的电滞回线与温度有密切关系.在50Hz的频率测量时,由于介电损耗而使试样发热,因此,测量结果不能反映真实的温度关系.尤其重要的是,就所测电滞回线来说,50Hz的频率太高,既不能测量铁电体的起始回线,也无法用函数记录仪记录.…  相似文献   

4.
铌锰锆钛酸铅铁电陶瓷电滞回线的温度和频率响应   总被引:1,自引:0,他引:1       下载免费PDF全文
研究了Pb[(Zr052Ti048)095(Mn1/3Nb2/3)005]O3 (PMnN_PZT) 铁电陶瓷电滞回线的温度和频率响应,结果显示在高频和室温条件下测试铁电特性时,电滞回线呈现“束腰”形状,而不是通常所看到的方形回线 . 在低频和高温条件下测试时才能观察到正常的方形回线,同时,诸如矫顽场、极化强度、 内偏场这些重要的铁电参数也会随频率和温度发生显著的变化. 剩余极化强度随频率和温度 的大幅增长表明“束腰” 电滞回线有可能是由于缺陷偶极子引起的. 电滞回线形状与温度 和频率存在较强的相关性说明缺陷偶极子存在一特征弛豫时间,缺陷偶极子反转响应速度由 此弛豫时间决定. 关键词: 电滞回线 氧空位 频率响应 温度响应  相似文献   

5.
利用电滞回线发生器,通过信号测量电路及计算机接口技术,描绘电滞回线,计算出待测铁电体(压电陶瓷片)的电特性参量.  相似文献   

6.
比较了电介质物理学和铁电物理学对介电常数定义的差异.这种差异导致了解释实验结果方面相反的结论:铁电体物理学能够很好地解释极化强度增大导致介电常数减小的实验结果和外加直流电场下铁电体的介电可调行为,而电介质物理学得到的却是相反的结论.其原因是铁电材料介电常数在顺电相仅来源于横光学模的贡献,在铁电相来源于横光学模和偶极子极化,且偶极子极化会引起损耗.数学推导证实弛豫铁电行为的成份分布不是高斯分布函数.  相似文献   

7.
弛豫铁电体材料在通讯、传感、超声、能量转换、航空航天等领域具有重要的应用.与正常铁电体不同,弛豫铁电体在冷却过程中出现弥散相变,体系的宏观极化不会突然产生,而是出现纳米极性微区,体系的宏观晶体对称性没有明显的变化.如何理解弥散相变及其与内部机制之间的相互影响是一个重要的问题.本研究基于伊辛模型(Ising model),对自旋变量(在研究中视为电偶极子)引入能量势阱的作用,并计算了这一系统的相变过程.结果表明这一改进的伊辛模型使极化率的相变曲线显著变缓,呈现出具有弥散相变的弛豫体特性.研究显示,弛豫体现象出现的一个重要原因是系统内部偶极子受到势阱限制而出现反转受阻,从而使极化率偏离常规铁电体.利用这一改进的伊辛模型进一步研究了弛豫铁电体的热滞效应,分析了热滞的起源,并与实验结果进行了对比分析,明确了弛豫体弥散相变和热滞的物理机制.  相似文献   

8.
电滞回线的精确测量和分析   总被引:1,自引:0,他引:1  
人们通常用 Sawyer和 Tower[1]提出的方法测量铁电体的电滞回线.Diamant[2]考虑了样品的漏电电阻R和剩余电容Cr的影响对此方法作了改进.图1描述了这种改进后的方法.被测样品在图中用R和C并联的电路等效地代替.C是样品的微分电容,其中Q为样品的电极在电压E作用下积存的电荷.若电  相似文献   

9.
外延PbZr0.4Ti0.6O3薄膜厚度对其铁电性能的影响   总被引:2,自引:0,他引:2       下载免费PDF全文
从Landau-Devonshire唯象理论出发,考虑到晶格失配导致的NFDA3位错应力场与极化场的耦合,研究了在SrTiO3衬底上外延生长的PbZr0.4Ti0.6O3薄膜厚度对其自发极化强度、电滞回线的影响. 结果表明,产生刃位错的PbZr0.4Ti0.6O3薄膜临界厚度为~1.27nm,当薄膜厚度大于临界厚度时,在所形成的位错附近,极化强度出现急剧变化,形成自发极化强度明显减弱的“死层”;随着薄膜厚度的减小,位错间距增大,“死层”厚度与薄膜总厚度之比增加. 由薄膜电滞回线的变化情况可知,其剩余极化强度随着薄膜厚度的减小而逐渐减小. 关键词: 铁电薄膜 自发极化强度 电滞回线 位错  相似文献   

10.
PZT铁电材料的总剂量辐照效应实验研究   总被引:1,自引:0,他引:1       下载免费PDF全文
 采用传统固相反应法制备PZT铁电材料,并制作成平行平板无源电容器结构,在ELV-8电子直线加速器上进行了总剂量效应辐照实验。结果表明:样片经过不同强度高能高速直流电子束辐照后的电滞回线随着辐照强度的增加,电滞回线所包围的面积逐渐减小,饱和极化强度、剩余极化强度和矫顽场呈线性减小。其中当辐照剂量为1×108rad(Si)时,饱和极化强度、剩余极化强度和矫顽场的衰减幅度分别为14.1%,15.0%和2.7%,样片抗总剂量辐照能力可达1×108rad(Si)。  相似文献   

11.
Simulations of the kinetics of polarization switching at first-order ferroelectric phase transitions are carried out within the framework of Ishibashi dipole lattice model. We consider the influence of the dipole–dipole interaction between polar units on the polarization switching taking into account the existence of metastable states. We also examine the size effect on the switching kinetics. We calculate hysteresis loops and switching rates in the systems in which the continuum approximation is not valid. We show that in the case of hundreds of polar units our equations give the known analytical expressions for the switching rate.  相似文献   

12.
Polarization switching and retention of each of the two polarized states in Langmuir—Blodgett (LB) ferroelectric films are studied using nonlinear dielectric spectroscopy. It is found that polarized states can be preserved for a long time, but the polarization dynamics in 10–40-nm-thick LB films is characterized by a considerable switching-time dispersion. In addition, ferroelectric LB films exhibit clearly manifested asymmetry of switching to states with opposite directions of polarization. To explain the experimental results, a polarization-switching model is proposed that takes into account the energy of interaction of a ferroelectric polymer with boundary surfaces. The effect of inhomogeneity of the LB film structure on the ferroelectric switching dynamics is also discussed.  相似文献   

13.
We report on the results of experiments on polarization switching in a ferroelectric TGS crystal during injection of electron beams from a scanning electron microscope under a surface layer. A series of models reflecting the polarization switching dynamics of a ferroelectric crystal under the action of an injected charge is constructed. The implementation of these models is based on the principles of evolution of domain structures taking into account analysis of possible polarization switching mechanisms for ferroelectric samples. A mathematical model developed using these principles demonstrates qualitative similarity of model current pulses and those obtained experimentally in the injection mode.  相似文献   

14.
We investigated domain kinetics by measuring the polarization switching behaviors of (111)-preferred polycrystalline Pb(Zr,Ti)O3 films, which are widely used in ferroelectric memories. Their switching behaviors at various electric fields and temperatures could be explained by assuming the Lorentzian distribution of logarithmic domain-switching times. We suggested that the local field variation due to dipole defects at domain pinning sites could explain the Lorentzian distribution.  相似文献   

15.
The low-frequency quadratic electro-optical effect with a maximum electro-optical coefficient of g = 8 × 10?19 m2/V2 (i.e., four orders of magnitude greater than the standard high-frequency value) has been studied in thin films of ferroelectric polymer PVDF(70%)-TrFE(30%). The observed effect is related to the process of spontaneous polarization switching, during which the electron oscillators of C-F and C-H dipole groups rotate to become parallel to the applied field. As a result, the ellipsoid of the refractive index exhibits narrowing in the direction perpendicular to the field. The field dependence of the electro-optical coefficient g correlates with that of the apparent dielectric permittivity, which can be introduced under the condition of ferroelectric polarization switching. The observed electro-optical effect strongly decreases when the frequency increases up to several hundred hertz. The temperature dependence of the effect exhibits clearly pronounced hysteresis in the region of the ferroelectric phase transition.  相似文献   

16.
Ferroelectric properties of copolymers of vinylidene fluoride with trifluoroethylene and tetrafluoroethylene are described with special interest in their polarization reversal and phase transition behavior. The ferroelectric phase consists of all-trans molecules packed in a parallel fashion while molecules adopt irregular TT, TG, T[Gbar] conformations in the paraelectric phase. In the ferroelectric phase, polarization reversal occurs at very high fields (> 100 MV/m) as a result of eventual 180° rotations of individual chain molecules around their axes. The switching time ranges from sec to nsec depending upon the strength of the applied field according to an exponential law with a particularly large activation field (~ 1 GV/m). The value of the observed remnant polarization is consistent with prediction from a simple dipole sum implying a minor contribution from the Coulomb interaction. The ferroelectric-to-paraelectric transition appears most clearly for copolymers containing 50-80 mol% vinylidene fluoride at temperatures from 70 to 140°C. The transition accompanies cooperative dipole motions associated with elementary trans-gauche transformations. Changes in various properties as well as in structures in the vicinity of the Curie point are consistent with an order-disorder transition of first order. Detailed characteristics specifying their ferroelectricity are summarized and discussed in relation to the molecular, crystalline, and higher-order structures inherent to ferroelectric polymers.  相似文献   

17.
18.
An optical probe is suggested that allows measurements of the local field and Lorentz factor (L) in ferroelectric medium. The copolymer poly (vinylidene fluoride/trifluoroethylene) is mixed with Pd-tetraphenylporphyrin (TPP-Pd) that has a very narrow absorption band. Thus, TPP-Pd serves as a molecular optical probe of the local field. During the switching of the electric field lower than the coercive one the factor L of an unpolarized ferroelectric mixture is found to be of about 1/3 that corresponds to the random distribution of molecular dipoles in the ferroelectric. With increasing field, the dipole orientation acquires a lower symmetry and L tends to zero as predicted by lattice sum calculations for vinylidene fluoride. The knowledge of the field dependence of L and the usage of the optical probe makes it possible to measure directly the local and macroscopic fields in the individual elements of various ferroelectric-dielectric heterostructures.  相似文献   

19.
The ferroelectric specimen is considered as an aggregation of many randomly oriented domains. According to this mechanism, a multi-domain mechanical model is developed in this paper. Each domain is represented by one element. The applied stress and electric field are taken to be the stress and electric field in the formula of the driving force of domain switching for each element in the specimen. It means that the macroscopic switching criterion is used for calculating the volume fraction of domain switching for each element. By using the hardening relation between the driving force of domain switching and the volume fraction of domain switching calibrated, the volume fraction of domain switching for each element is calculated. Substituting the stress and electric field and the volume fraction of domain switching into the constitutive equation of ferroelectric material, one can easily get the strain and electric displacement for each element. The macroscopic behavior of the ferroelectric specimen is then directly calculated by volume averaging. Meanwhile, the nonlinear finite element analysis for the ferroelectric specimen is carried out. In the finite element simulation, the volume fraction of domain switching for each element is calculated by using the same method mentioned above. The interaction between different elements is taken into account in the finite element simulation and the local stress and electric field for each element is obtained. The macroscopic behavior of the specimen is then calculated by volume averaging. The computation results involve the electric butterfly shaped curves of axial strain versus the axial electric field and the hysteresis loops of electric displacement versus the electric field for ferroelectric specimens under the uniaxial coupled stress and electric field loading. The present theoretical prediction agrees reasonably with the experimental results. Supported by the National Natural Science Foundation of China (Grant No. 10572138)  相似文献   

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