COMP．B复合炸药动态力学性能和塑性流动本构关系的研究

利用自制的含能材料动态变温三轴压缩实验装置，采用准静态应变速率（１０－４／ｓ）和中等应变速率（３／ｓ），对国产复合炸药Ｃｏｍｐ．Ｂ进行了三轴压缩实验．测试了Ｃｏｍｐ．Ｂ在不同温度、不同应变速率条件下的杨氏模量Ｅ，泊松比ν和屈服强度Ｙ．实验结果表明，Ｃｏｍｐ．Ｂ具有明显的应变率相关和热软化效应．基于热激活模型，作了适当的改进，根据实验数据建立了含能材料塑性流动模型，分析表明该模型能合理地描述率相关材料的塑性流动，同时考虑了应变率和温度对塑性流动的影响．这些基础研究为含能材料动态力学性能的研究和炸药早爆机理的理论分析提供了依据     

含能材料在低温条件下冲击压缩力学性能的实验研究

采用自制的含能材料动态变温压缩实验装置，在低温环境下，对国产复合炸药Ｃｏｍｐ．Ｂ和单质炸药ＴＮＴ进行了动静态压缩实验，测试了压缩模量、压缩强度等材料性能参数。实验结果表明:在低温条件下，Ｃｏｍｐ，Ｂ和ＴＮＴ材料具有明显的应变率效应和温度效应，复合炸药Ｃｏｍｐ．Ｂ的压缩模量和压缩强度都高于ＴＮＴ炸药，Ｃｏｍｐ．Ｂ对温度效应更为敏感。还讨论了惯性效应对动态实验波形的影响，通过引入柔度系数，使测试波形趋于光滑。所介绍的实验方法为研究含能材料在低温条件下的冲击压缩性能，提供了一套较完整的技术和手段。     

高能材料动态力学性能的研究

采用自制的高能材料动静态变温三轴、单轴压缩试验装置、在熔点以下温度,以及在中等应变速率（２～４／ｓ）和准静态（３１０￣（－３）／ｓ）条件下测试了ＴＮＴ材料三轴、单轴压缩力学性能参数。试验结果表明,ＴＮＴ材料具有明显的应变率相关和热软化效应。在单轴压缩条件下,ＴＮＴ材料是脆性破坏,断裂强度小于屈服极限;在三轴压缩条件下,试件有较大的塑性变形。根据试验结果拟合了ＴＮＴ材料随着加载速率和环境温度变化的本构关系,分析表明该本构关系可以很好地描述材料的应变率、温度效应。     

Al基含能结构材料的Johnson-Cook本构模型及失效参数研究

利用万能实验机和Hopkinson杆装置测试了Al基含能结构材料在不同温度下的静动态力学性能,分析实验结果得到了温度效应和应变率效应对材料力学性能的影响及该合金的Johnson-Cook本构模型参数.结合二维数字图像相关(DIC)方法,研究了Al基含能结构材料的失效应变与应力三轴度及温度之间的关系,得到了该合金的Johnson-Cook失效模型参数.通过平面撞击实验获得了Al基含能结构材料粒子速度和应力波波速之间的经验线性关系和该合金的Grüneisen系数.基于实验获得的材料本构关系和状态方程参数,完成了Al基含能结构材料超高速撞击多层间隔薄钢板的数值模拟,结果表明,数值模拟中靶板的毁伤模式、破孔直径及弹坑主要散布区和实验结果吻合.     

冲击载荷下盐岩的力学性能和本构关系研究

利用直径75mm的大尺寸SHPB实验装置开展盐岩的动态压缩性能实验研究,得到了其动态应力应变曲线。分析表明,在冲击压缩载荷作用下,盐岩材料有明显的损伤软化现象和应变率效应。针对实验曲线,通过引入描述材料强度随应变率强化的应变率增强因子和随不可逆变形发展而弱化的损伤因子,提出了含损伤率的相关动态本构模型,拟合得到的本构方程形式比较简单,能够较好地反映盐岩动态实验加载过程的主要特征,具有一定的工程应用价值。     

异种不锈钢激光焊缝材料的动态本构关系

利用等应变测试法获取了304及316L激光焊接焊缝材料的准静态应力应变曲线,发现焊缝材料 具有明显的细晶硬脆化趋势。利用SHTB技术对304、316L及焊接构件材料高温动态力学性能进行了研究。 根据动态实验数据对不锈钢304及316L母材应变率及温度相关的Johnson-Cook本构方程参数进行了拟合。 利用LS-DYNA建立了SHTB动态拉伸实验数值模型,发现了在应力波加载初始阶段由于结构效应及材料 阻抗不匹配引起的应力不平衡现象。通过动态实验与数值模拟相结合的方法确定了焊缝材料的应变率相关 本构参数。     

软质聚氨酯泡沫的动态压缩力学性能和本构模型

采用Instron 9350落锤试验机研究了中低应变率下软质聚氨酯泡沫的动态压缩力学性能,分析了其应力-应变响应特征和应变率敏感性,讨论了应变率对材料应变率敏感性指数和能量吸收特性的影响,并基于实验结果建立了可准确描述其压缩力学响应的率相关本构模型。结果表明,软质聚氨酯泡沫的静动态压缩应力-应变响应具有典型的三阶段特征,且呈现出明显的应变率强化效应。准静态加载下,材料具有较高的吸能效率但能量吸收值较小,应变率对最大吸能效率和比吸能的影响较小;动态加载下,随着应变率的增加,最大吸能效率显著减小而比吸能明显增大。考虑应变率影响的修正Sherwood-Frost模型和修正Avalle模型都能够很好地表征软质聚氨酯泡沫的静动态压缩应力-应变响应,但修正Avalle模型的参数较少,更便于工程应用。研究结果可为软质聚氨酯泡沫抗冲击结构的设计和优化提供指导。     

NEPE推进剂低高应变率下改进的黏-超弹本构模型

为研究低高应变率条件下NEPE推进剂的力学特性,通过电子万能试验机和分离式霍普金森杆装置,对NEPE推进剂进行了准静态和冲击实验,得到了不同应变率下（1.667×10?4～4 500 s?1）的应力-应变曲线。实验结果表明NEPE推进剂具有明显的非线性弹性和应变率敏感性,随着应变率的增加,材料的强度、屈服应力和弹性模量显著增加,与低应变率相比,高应变率条件下材料的应变率敏感性更高。在高速冲击下材料内部瞬间产生大量热量无法及时散发出去,使得材料内部温度升高,导致材料出现软化效应,力学性能降低。本文建立了一个非线性黏超弹本构模型,其中采用Rivlin应变能函数来描述稳态超弹响应部分,采用积分型本构模型来描述材料的动态黏弹性响应部分,考虑到松弛时间具有应变率相关性,本文采用了一个率相关松弛函数来替代传统的Prony级数形式。使用极慢速压缩实验数据对本构模型中的超弹部分进行拟合获得超弹参数,然后用准静态和动态实验数据对本构模型进行拟合得出其他参数。不同应变率下的预测曲线与实验曲线具有较好的重合度,证明了该模型可以很好地描述低高应变率下NEPE推进剂的力学特性。     

YB-2航空有机玻璃的应变率和温度敏感性及其本构模型

为了理解和评价YB-2航空有机玻璃在极端环境下的动态力学性能,采用电子万能试验机和分离式Hopkinson压杆对YB-2航空有机玻璃在218~373 K温度范围、10^-3~3 000 s^-1应变率范围内的压缩力学行为进行了研究,得到了材料的应力应变曲线。结果表明：随着温度的升高,材料的流动应力逐渐减小而破坏应变呈现增大的趋势;温度相同时,材料的流动应力随应变率的增加而增大,破坏应变随应变率的增加而减小。随着应变率的提高,材料的应变软化效应更加剧烈。基于朱-王-唐(ZWT)本构模型,得到了考虑温度效应的本构参数。结果显示,在8%应变范围内,改进的考虑温度效应的本构模型可以较为理想地表征该材料的应力应变响应。

     

应用MS材料试验机对高能材料进行快速加载的试验研究

介绍了开发ＭＴＳ材料试验机应用于快速加载的高能材料动态力学的试验方法，研究了方波信号的频率对加载速率的影响，开发了低周疲劳试验机在冲击载荷下用于固体炸药在不同温度下的单轴，三轴材料动态力学性能研究的功能，得出了应变速率达到４／ｓ。     

铀合金动态力学性能的研究

本文利用分离式霍布金生压杆研究了四种国产铀合金的动态力学性能,给出了这些材料随应变率和环境温度变化的本构关系。实验结果表明,国产铀合金具有与钨合金相当的动态强度,是钨穿甲弹中弹芯材料的极好替代物。     

高强混凝土动态压缩试验分析

准确测量混凝土动态压缩性能及其应变率强化效应一直是冲击动力学研究领域的重点和难点之一。针对混凝土大口径SHPB实验,分析探讨了其中几个主要问题:应力均匀性问题、恒应变率问题和端面接触问题。研究表明:对于此次试验中混凝土试件而言,应力均匀性假设限制试验最大应变率小于166 s^-1;杆和试件端面接触不平和接触不良使得测算出的杨氏模量和屈服强度明显小于实际值;在此基础上,给出了五步测试法和预应力法;利用复合整形技术实现了近似恒应变率加载。利用以上所发展和改进的技术得到了C110混凝土动静态应力应变曲线,结果显示,在试验范围内混凝土杨氏模量并没有应变率效应,其单轴压缩屈服强度与应变率对数呈线性正比关系,其唯象应变率强化因子为0.10。理论分析表明,大口径SHPB试验所得混凝土应变率效应是一种唯象效应,对于混凝土类压力敏感屈服材料而言,应该根据其屈服面方程对其进行校正,从而得到其本构方程中材料的应变率强化因子,分别利用Tresca屈服准则和K&C本构中屈服面方程对其进行校正,得到C110材料的真实应变率强化因子分别为0.015和0.038。     

SnAgCu焊料的动态力学性能

对SnAgCu焊锡材料在应变率0.001、600、1 200、1 800 s-1下的拉伸和压缩力学性能进行了测试,得到了不同应变率下的应力应变曲线。结果表明,该材料不仅具有明显的应变率效应,而且其动、静态的塑性硬化模量差异很大。金相分析显示:准静态压缩时,塑性变形主要由晶粒的转动、变形和晶界的滑移控制;而动态压缩时,可观察到材料内部的枝状晶粒被折断为大量次级晶枝,呈现出明显不同于准静态情况下的变形机制。     

Dynamic Experiments using Simultaneous Compression and Shear Loading

Material characterization at high strain rates under simultaneous compression and shear loading has been a challenge due to the differing normal and shear wave speeds. An experimental technique utilizing the compression Kolsky bar apparatus was developed to apply dynamic compression and shear loading on a specimen nearly simultaneously. Synchronization between the compression and shear loading was realized by generating the torsion wave near the specimen which minimizes the time difference between the arrival of the compression and torsion waves. This modified Kolsky bar makes it possible to characterize the dynamic response of a material to combined compression and shear impact loading. This method can also be applied to study dynamic friction behavior across an interface under controlled loading conditions. The feasibility of this method is demonstrated in the dynamic characterization of a simulant polymer bonded explosive material.     

Shear band formation in thermo-viscoplastic solids under plane strain compression

The plane strain compression of a rectangular block is numerically investigated for the study of dynamic shear band development in thermo-elasto-viscoplastic materials from an internal inhomogeneity. As expected, it plays an important role in triggering the onset of shear, localization as well as thermal softening. And the competition between the strain, strain-rate hardening and thermal softening exists throughout the process. It is found that shear band develops at a 45-degree angle to the compression axis. In the light of given patterns of deformation and temperature, shear band evolution accelerated by thermal softening is retarded by the inertial effects. Interestingly, a similar temperature band is also formed along the trajectory of the localized deformation band. The calculations also show the energy evolution during the coupled thermo-mechanical process of shear band propagation. Finally, the mesh effect is discussed in terms of the numerical results from two different meshes. The project is supported by the National Natural Sciences Foundation of China.     

The effect of strain rate and heat developed during deformation on the stress-strain curve of plastics

Polymethylmethacrylate, cellulose acetate butyrate, polypropylene and nylon 6–6 have been characterized in compression at various strain rates from 10^?4 s^?1 to 10³ s^?1 at room temperature. A medium strain-rate machine and a split-Hopkinson-bar apparatus are used in conducting the experiments. The temperature rise developed during deformation is also measured by using a thermocouple. All four materials tested definitely show a viscous effect at the beginning of the deformation and a plastic flow follows thereafter. Test results also indicate that the temperature rise developed during deformation cannot be neglected in determining the dynamic response of those materials investigated in this study.     

SHPB实验中端面摩擦效应研究

选取硅橡胶、聚氨酯泡沫、Comp.B炸药、PBX-HMX(97%)炸药以及6061-T6铝合金五种材料试样,对分离式霍普金森压杆（SHPB）实验技术中的端面摩擦效应进行了研究。实验结果表明,SHPB实验技术中的端面摩擦效应与材料的性质相关。另外,基于各向同性弹性理论,运用能量守恒法对SHPB实验中的端面摩擦效应进行了机理分析,研究表明,材料泊松比、端面摩擦系数、试样长径比、轴向应变是SHPB实验中影响端面摩擦效应的四个因素。     

A secant-viscosity composite model for the strain-rate sensitivity of nanocrystalline materials

In order to address the strain-rate sensitivity of nanocrystalline solids, a secant-viscosity composite model is developed in this article. The microgeometry of the composite is taken to consist of the grain-interior phase and the grain-boundary affected zone (GBAZ) as suggested by Schwaiger et al. [Schwaiger, R., Moser, B., Dao, M., Chollacoop, N., Suresh, S., 2003. Some critical experiments on the strain-rate sensitivity of nanocrystalline nickel. Acta Mater. 51, 5159–5172], while the constituent properties are modeled by a unified viscoplastic constitutive law. The drag stress of the grain interior is assumed to follow the Hall–Petch relation, but that of the GBAZ is independent of grain size, d. Then in terms of the secant viscosity of the constituent phases, the strain-rate sensitivity of the nanocrystalline solid is determined with the help of a linear viscous comparison composite and a field-fluctuation approach. To test the applicability of the developed model, it is applied to predict the strain-rate effect of a nanocrystalline Ni, and the grain-size dependence of its stress–strain relations. Our theoretical calculations indicate that the tensile strength of a nanocrystalline Ni with d = 40 nm is about five times that of a microcrystalline one with d = 10 μm under the same strain rate of , and that the nanocrystalline Ni exhibits a much stronger strain-rate effect. These predictions are found to be consistent with the experimental data of Schwaiger et al. Possible grain-size softening with further grain-size reduction such as reported in molecular dynamic simulations is also demonstrated.     

Strain-rate history and temperature effects on the torsional-shear behavior of a mild steel

Previous investigations on the effects of strain-rate and temperature histories on the mechanical behavior of steel are briefly reviewed. A study is presented on the influence of strain rate and strain-rate history on the shear behavior of a mild steel, over a wide range of temperature Experiments were performed on thin-walled tubular specimens of short gage length, using a torsional split-Hopkinson-bar apparatus adapted to permit quasi-static as well as dynamic straining at different temperatures. The constant-rate behavior was first measured at nominal strain rates of 10^?3 and 10³ s^?1 for ?150, ?100, ?50, 20, 200 and 400°C. Tests were then carried out, at the same temperatures, in which the strain rate was suddenly increased during deformation from the lower to the higher rate at various large values of plastic strain. The increase in rate occurred in a time of the order of 20 μs so that relatively little change of strain took place during the jump. The low strain-rate results show a well-defined elastic limit but no yield drop, a small yield plateau is found at room temperature. The subsequent strain hardening shows a maximum at 200°C, when serrated flow occurs and the ductility is reduced. The high strain-rate results show a considerable drop of stress at yield. The post-yield flow stress decreases steadily with increasing temperature, throughout the temperature range investigated. At room temperature and below, the strain-hardening rate becomes negative at large strains. The adiabatic temperature rise in the dynamic tests was computed on the assumption that the plastic work is entirely converted to heat. This enabled the isothermal dynamic stress-strain curves to be calculated, and showed that considerable thermal softening took place. The initial response to a strain-rate jump is approximately elastic, and has a magnitude which increases with decrease of testing temperature; it is little affected by the amount of prestrain. At 200 and 400° C, a yield drop occurs after the initial stress increment. The post-jump flow stress is always greater than that for the same strain in a constant-rate dynamic test, the strain-hardening rate becoming negative at large strains or low testing temperature. This observed effect of strain-rate history cannot be explained by the thermal softening accompanying dynamic deformation. These and other results concerning total ductility under various strain-rate and temperature conditions show that strain-rate history strongly affects the mechanical behavior of the mild steel tested and, hence, should be taken into account in the formulation of constitutive equations for that material.