用广义胞元法研究弱界面复合材料偏轴拉伸强度

本文用广义胞元法结合应力集中系数模型,从细观、宏观力学结合的角度,预测了弱界面复合材料偏轴拉伸强度值．用广义胞元法/高精度广义胞元法计算复合材料开裂前和开裂后的应力场,引入基体应力集中系数以得到基体真实应力．在计算真实应力时根据宏观试验现象考量是否对界面开裂后的复合材料进行刚度衰减,最终形成4种方案计算出复合材料的偏轴拉伸强度．通过对比芳纶纤维和亚麻纤维两种弱界面复合材料的偏轴拉伸强度试验值,找到了最可靠的预报方案并具有良好的预报精度．     

基体的真实应力理论

连续介质力学中,各向同性材料的力学理论已基本成熟,即,对任何一个各向同性材料的力学问题,人们几乎总能从现有理论中找到有效解决方案,但对各向异性材料暨复合材料而言,只有线弹性理论才基本成熟,复合材料的塑性变形、破坏和强度等问题,都还缺少成熟分析方法。根本原因是,现有理论只能得到纤维和基体中的均值应力,复合材料的塑性、破坏和强度分析,都必须基于基体的真实应力。本文对作者创建和发展的基体真实应力理论进行了综述介绍,并简要指出了真实应力理论在复合材料破坏和强度分析中所起的作用。     

短纤维金属基复合材料应力传递的有限元分析

基于短纤维增强金属基复合材料的单纤维轴对称和三维细观力学模型,利用弹塑性有限元分析方法对该复合材料中基体与纤维间的应力传递进行研究,研究中主要讨论了基体、纤维和界面的力学性能以及纤维位向的变化对应力传递和应力分布的影响。研究表明,复合材料微结构参数的变化将显著影响基体与纤维间的应力传递和复合材料中的应力分布,复合材料设计过程中必须考虑合理的微结构特征。     

侧向受拉脆性岩石压缩本构及蠕变失效研究

轴向压缩作用下,脆性岩石侧向应力严重影响岩石力学特性。侧向压应力影响下的轴向压缩岩石力学行为已经得到广泛研究,然而侧向拉应力对轴向压缩岩石力学行为影响研究很少。本文基于脆性岩石翼型裂纹扩展模型中,初始裂纹面法向应力与剪切应力的正负方向为判断依据,研究了侧向拉应力对轴向压缩力学行为的影响。发现恒定的侧向拉应力作用下,轴向压缩应力渐进变化过程中,脆性岩石内部细观初始裂纹面的法向应力只能为压缩应力,不存在拉应力情况。分析了从侧向压应力到拉应力转化过程中,脆性岩石轴向压应力与细观裂纹扩展长度关系、轴向压应力与轴向应变关系、岩石峰值强度、裂纹启裂应力及初始弹性模量的变化规律。并分析了侧向拉应力对岩石蠕变裂纹长度、裂纹速率、轴向应变及应变率演化曲线,以及对蠕变失效时间及稳态蠕变应变率的影响。讨论了侧向拉压应力突变转化以及侧向拉应力分级增大对轴向压缩岩石蠕变演化行为影响。该研究为深部地下工程围岩稳定性评价提供了一定理论依据。     

具有界面相的球形粒子在无限大基体中的应力集中分析

研究了无限大基体内具有界面相的球形粒子在轴对称载荷作用下的应力场,并与线弹簧界面模型的情形进行了比较,对粒子／界面相以及界面相／基体两个界面的应力集中系数以及粒子内部的应力集中系数进行了分析．研究了应力二轴度、界面相厚度以及三相的模量对应力集中系数的影响．结果表明,对给定的模量和界面相厚度值,存在一个临界应力三轴度值．若应力二轴度小于此临界值,则界面相／基体界面的应力集中系数大于粒子／界面相界面的应力集中系数;否则,前者会小于后者．所做的应力分析可以为颗粒增强复合材料的强韧化设计提供一定参考．     

复合材料内由纤维断裂引起的应力集中

在研究复合材料的断裂和强度时,由纤维断裂引起的应力集中是必须首先知道的.在纤维断点附近的应力集中己有不少研究.本文着重研究当应力波沿纤维方向传播时,离纤维断点有一定距离处的动应力集中系数.     

纤维复合材料横向荷载下的应力分析研究

单向加劲的纤维复合材料,在正交纤维方向的均布荷载作用下,基体内将出现超过外载集度的局部应力集中.本文先扼要介绍已有有关研究工作,总结出这种应力集中系数的范围,此外,为便于一般计算,文中另提出一种近似的模型和算式.1.Schulz 的工作设纤维方向与x_1轴平行,如图1.Schulz 取宽度等于一个纤维直径和两个纤维间基体的薄片(如图1的阴线部分)来分析.假定在横向荷载作用下,纤维并基体内各具有均匀的应力、应变,如图2.令基体和纤维的弹性系数分别为E_m,μ_m,G_m 及E_f,μ_f,G_f,     

具有中心孔的正交复合材料板在双轴载荷下的应力分析

本文研究了具有中心孔的正交复合材料板在双向载荷下的应力,建立了有限校核系数和双轴率以及之间板宽率的关系,并得到孔边的应力集中系数.这些结果对研究具有中心孔的正交复合材料板在双向载荷下的强度预测和应力分析具有重要的作用.     

纤维增强陶瓷基复合材料疲劳迟滞回线模型研究

纤维增强陶瓷基复合材料初始加载到疲劳峰值应力时, 基体出现裂纹, 纤维/基体界面发生脱粘. 在疲劳载荷作用下, 纤维相对基体在界面脱粘区往复滑移使得陶瓷基复合材料出现疲劳迟滞现象. 建立了纤维陶瓷基复合材料疲劳迟滞回线细观力学模型, 采用断裂力学方法确定了初始加载纤维/基体界面脱粘长度、卸载界面反向滑移长度与重新加载新界面滑移长度, 分析了4种不同界面滑移情况的疲劳迟滞回线. 假设正交铺设与编织陶瓷基复合材料疲劳迟滞回线主要受0°铺层、轴向纱线内纤维/基体界面滑移的影响, 预测了单向、正交铺设与编织陶瓷基复合材料在不同峰值应力与不同循环的疲劳迟滞回线, 与试验结果吻合.      

INVESTIGATION ON FATIGUE HYSTERESIS LOOPS MODELS OF FIBRE-REINFORCED CERAMIC-MATRIX COMPOSITES

纤维增强陶瓷基复合材料初始加载到疲劳峰值应力时, 基体出现裂纹, 纤维/基体界面发生脱粘. 在疲劳载荷作用下, 纤维相对基体在界面脱粘区往复滑移使得陶瓷基复合材料出现疲劳迟滞现象. 建立了纤维陶瓷基复合材料疲劳迟滞回线细观力学模型, 采用断裂力学方法确定了初始加载纤维/基体界面脱粘长度、卸载界面反向滑移长度与重新加载新界面滑移长度, 分析了4种不同界面滑移情况的疲劳迟滞回线. 假设正交铺设与编织陶瓷基复合材料疲劳迟滞回线主要受0°铺层、轴向纱线内纤维/基体界面滑移的影响, 预测了单向、正交铺设与编织陶瓷基复合材料在不同峰值应力与不同循环的疲劳迟滞回线, 与试验结果吻合.     

Assessment of composite failure and ultimate strength without experiment on composite

This paper attempts to estimate the ultimate strength of a laminated composite only based on its con- stituent properties measured independently. Three important issues involved have been systematically addressed, i.e., stress calculation for the constituent fiber and matrix materials, failure detection for the lamina and laminate upon the internal stresses in their constituents, and input data determination of the constituents from monolithic measurements. There are three important factors to influence the accuracy of the strength prediction. One is the stress concentration factor （SCF） in the matrix. Another is matrix plasticity. The third is thermal residual stresses in the constituents. It is these three factors, however, that have not been sufficiently well realized in the composite community. One can easily find out the elastic and strength parameters of a great many laminae and laminates in the current literature. Unfortunately, necessary information to determine the SCF, the matrix plasticity, and the thermal residual stresses of the composites is rare or incomplete. A useful design methodology is demonstrated in the paper.     

In situ strengths of matrix in a composite

A major obstacle to achieving reasonable strength prediction of a composite only from its constituent infor-mation is in the determination of in situ strengths of the matrix. One can measure only the original strengths of the pure matrix, on the basis of which the predicted transverse strengths of a unidirectional (UD) composite are far from reality. It is impossible to reliably measure matrix in situ strengths. This paper focuses on the correlation between in situ and original strengths. Stress concentrations in a matrix owing to the introduction of fibers are attributed to the strength variation. Once stress concentration factors (SCFs) are obtained, the matrix in situ strengths are assigned as the original counterparts divided by them. Such an SCF can-not be defined following a classical approach. All of the relevant issues associated with determining it are system-atically addressed in this paper. Analytical expressions for SCFs under transverse tension, transverse compression, and transverse shear are derived. Closed-form and compact for-mulas for all of the uniaxial strengths of a UD composite are first presented in this paper. Their application to strength pre-dictions of a number of typical UD composites demonstrates the correctness of these formulas.     

Residual strength of a fiber reinforced metal matrix composite with a crack

The residual strength of a cracked unidirectional fiver reinforced metal matrix composite is studied. We propose a bridging model based on the Dugdale strip yielding zones in the matrix ahead of the crack tips that accounts for ductile deformations of the matrix and fiber debonding and pull-out in the strip yielding zone. The bridging model is used to study the fracture of an anisotropic material and its residual strength is calculated numerically. The predicted results for a SiC/titanium composite agree well with the existing experimental data. It is found that a higher fiber bridging stress and a larger fiber pull-out length significantly contribute to the composite's residual strength. The composite's strength may be more notch-insensitive than the corresponding matrix material's strength depending on several factors such as fiber-matrix interface properties and the ratio of the matrix modulus to an ‘effective modulus’ of the composite.     

用Eshelby理论研究复合材料线粘弹性本构关系

本文用Eshelby微力学理论分析,得到短纤维增强材料(SFRC)和基体材料两者的粘弹性本构方程之间存在简单的正比关系。发现体积含量为f的短纤维无序取向SFRC一维力学行为,等效于体积含量为F的短纤维单轴取向SFRC在取向轴上的力学行为。     

含弧形裂纹复合陶瓷强度的尺度效应

认为含弧形裂纹复合陶瓷由随机方向的三相胞元与有效介质构成,用细观力学的方法研究了复合陶瓷的损伤失效和强度。首先确定三相胞元的外载应变,再依据复合陶瓷在损伤过程中的细观应力场和广义热力学力,计算出三相胞元内基体和颗粒的损伤等效应力,当基体和颗粒的损伤等效应力分别等于两者的极限应力时,得到基体和颗粒的破坏应力。然后,根据混合型应力强度因子计算弧形裂纹扩展时的能量释放率,进而得到界面的破坏应力。最后综合考虑基体、颗粒和和界面损伤影响,获得含弧形裂纹复合陶瓷的宏观强度及其尺度效应。     

Prestressing effect of twisted fiber yarn in composites

By utilizing the behavior of twisted fiber yarn, prestressing composites can be made. In unloading, the matrix of the prestressing composite is applied in compression. If tensile load acts on the composite, the value of the tensile stress acting on the materials may decrease greatly. By twisted fiber yarn, therefore, the tensile strength of the composites can be improved. An analysis for extension of continuous fiber yarns is made here and residual stress after curing is taken into account. The prestressing intensity in the composite depends on the twist of fiber yarn. The photoelastic test and the analysis of electron micrograph are performed, and the theoretical method for calculating prestressing effect is presented in this paper.     

纵向剪切三相共焦点椭圆模型的精确解及其应用

推广夹杂问题的三相同心圆模型,提出了三相共焦点椭圆模型,从而计及了夹杂形状变化的重要因素。利用保角变换结合罗朗级数展开技术获得了纵向剪切载荷下的封闭形式解。本模型和解答对夹杂、界面层附近的细观应力场分析、对复合材料和含缺陷材料的有效弹性模量预测有重要实用价值,获得了比经典公式更精确的结果。对特殊模型,可以得到许多有意义的问题（如二相模型）的解答。     

Spall strength of glass fiber reinforced polymer composites

In the present paper results of a series of plate impact experiments designed to study spall strength in glass–fiber reinforced polymer composites (GRP) are presented. Two GRP architectures are investigated—S2 glass woven roving in Cycom 4102 polyester resin matrix and a balanced 5-harness satin weave E-glass in a Ciba epoxy (LY564) matrix. The GRP specimens were shock loaded using an 82.5 mm bore single-stage gas-gun. A velocity interferometer was used to measure the particle velocity profile at the rear (free) surface of the target plate. The spall strength of the GRP was obtained as a function of the normal component of the impact stress and the applied shear-strain by subjecting the GRP specimens to normal shock compression and combined shock compression and shear loading, respectively. The spall strengths of the two GRP composites were observed to decrease with increasing levels of normal shock compression. Moreover, superposition of shear-strain on the normal shock compression was found to be highly detrimental to the spall strength. The E-glass reinforced GRP composite was found to have a much higher level of spall strength under both normal shock compression and combined compression and shear loading when compared to the S2-glass GRP composite. The maximum spall strength of the E-glass GRP composite was found to be 119.5 MPa, while the maximum spall strength for the S2 glass GRP composite was only 53.7 MPa. These relatively low spall strength levels of the S2-glass and the E-glass fiber reinforced composites have important implications to the design and development of GRP-based light-weight integral armor.