TAN Mengting1, ZHANG Xianfeng1, †, , BAO Kuo1, WU Yang2, WU Xue1
1 Ministerial Key Laboratory of ZNDY, Nanjing University of Science and Technology, Nanjing 210094, China2 Science and Technology on Transient Impact Laboratory,Beijing 102202, China
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2019 中国力学学会 This is an open-access article distributed under the terms of the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original author and source are credited.
Interface Defeat, which can effectively defeat the long-rod projectile (LRP), is a specific phenomenon of ceramic armor. Studies on this area have been conducted for the last three decades both at home and abroad proving that delaying dwell time or increasing interface defeat/penetration transition velocity can defeat projectile and enhance the ballistic performance of ceramic armor. Related researches on the experimental techniques, theoretical models and numerical simulations of interface defeat are introduced, including the study of interface defeat at the micro and macro scale, a method for the design of the ceramic composite armor, etc. According to the insufficient work of interface defeat, some suggestions are proposed in this paper.
现阶段研究表明界面击溃现象是一个多因素(陶瓷材料、约束条件、预应力、射弹材料、形状、交汇条件、盖板和背板的设计以及尺寸效应等)作用下的复杂动力学问题,与弹靶破坏的时间效应、靶中破坏波和陶瓷中裂纹与损伤的演化紧密相关.界面击溃的重要科学意义和广阔应用前景主要体现在:界面击溃过程中陶瓷材料的损伤演化及吸能机制、界面击溃形成机理与发展规律的深入研究将为丰富我国的终点毁伤和防护力学研究领域理论和技术突破奠定坚实基础,为我国弹道国防新材料的研究和制备提供科学依据,并促进我国新概念攻防武器和装备的研制. 在宏观尺度上,国内外学者在不同因素对陶瓷界面击溃效应的作用研究已取得了阶段性成果.在微观尺度上,国际上主要基于陶瓷内部裂纹扩展、损伤演化、塑性变形等机理分析界面击溃向侵彻转变的过程.国内学者对陶瓷界面击溃现象的研究起步较晚,关于陶瓷界面击溃综述性文献(陈小伟和陈裕泽 2006, 杨江丽和宋顺成 2007, Hu et al. 2009)对界面击溃的研究现状与发展进行了展望.理论方面的研究主要有李继承开展的界面击溃过程中弹靶参数变化(李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017)和高举斌等对背板对界面击溃的影响规律研究和陶瓷基复合材料弹靶表面驻留行为的分析(高举斌等 2013, 2017). 实验方面, 胡欣等(2010)通过对约束的AD95陶瓷进行弹击实验,获得了驻留现象. 未来可研究的方向主要有:
In the last decade, the dynamic response of ceramicmaterials and the penetration/perforation of targets of ceramics,ceramic/metal, ceramic/composite and layered ceramics is an activeresearch area. It has applications, especially, in the military field. Relatively little work in thisarea is conducted in China. The present paper introduces therecent advances in this area.Theexperimental techniques, penetration/perforation mechanisms and theoreticalmodels are reviewed. The cavity expansion model in ceramics penetration andthe effect of failure wave are specially addressed. Some research proposalsare made at the end of the paper.
(Chen XW, Chen YZ.2006.
Review on the penetration/perforation of ceramics targets
In the last decade, the dynamic response of ceramicmaterials and the penetration/perforation of targets of ceramics,ceramic/metal, ceramic/composite and layered ceramics is an activeresearch area. It has applications, especially, in the military field. Relatively little work in thisarea is conducted in China. The present paper introduces therecent advances in this area.Theexperimental techniques, penetration/perforation mechanisms and theoreticalmodels are reviewed. The cavity expansion model in ceramics penetration andthe effect of failure wave are specially addressed. Some research proposalsare made at the end of the paper.
We have conducted impact experiments using gold long rods into borosilicate glass and the measured the penetration velocity as a function of impact velocity. At sufficiently low-impact velocities, the glass target resists penetration and there is dwell; dwell is observed to approximately 450 m/s for bare glass. If a copper buffer is placed over the glass to eliminate the impact shock, significant dwell can be seen at impact velocities as high as 890 m/s. These impact velocities correspond to Bernoulli stresses of approximately 2.0 and 7.6 GPa, respectively. The paper describes the experimental data, and summarizes the results and our findings.
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Anderson Jr CE, Gooch WA.2011.
Numerical simulations of dynamic X-ray imaging experiments of 7.62-mm Apm2 projectiles penetrating B4C//19th International Symposium of Ballistics,
The penetration of aluminum oxide tiles inserted into a 4340-steel block that also serves as a emi-infinite steel substrate is investigated for two length-to-diameter projectiles at a nominal impact velocity of 1.5 km/s. The experimental observable is the depth of penetration of the projectile into the backup steel. These data are compared with the total penetration into semi-infinite steel. The data are analysed and displayed as normalized depth of penetration as a function of areal density and tile thickness. Data from Woolsey et al. ( Fifth Annual TACOM Armor Coordinating Conference , Monterey, CA, 1989) are in good agreement with data from this study, and are used to extend the range of tile thicknesses. A methodology, assuming quasi-steady-state penetration, provides an estimate of the penetration resistance R 1 of the ceramic tile; R 1 is then used to estimate the erosion rate and length of projectile eroded as it penetrates the ceramic. A second approach that does not rely as heavily on the assumption of steady-state penetration is also developed and applied to the data to estimate the length of projectile eroded. It is found that the various measures of ceramic performance, for a well-confined target, are relatively constant as tile thickness is varied.
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Anderson Jr CE, Orphal DL.2003.
Analysis of the terminal phase of penetration
. International Journal of Impact Engineering, 29: 69-80.
ABSTRACT The terminal phase, or Phase 3, of penetration is investigated using numerical simulations. Results of the first set of simulations, for zero-strength tungsten-alloy projectiles into armor steel at velocity of 1.5, 3.0, and 6.0 km/s are reported here. For these simulations, the mechanisms for Phase 3 penetration are limited to the transient deceleration of the eroding projectile and "afterflow," the extension of penetration after the projectile has fully eroded. It is found that for projectile L/D less than or equal to similar to2, there is effectively no steady-state penetration (Phase 2) and penetration is dominated by Phase 3. For projectiles of L/D greater than or equal to 3, steady-state penetration is achieved. For L/D greater than or equal to 3, the deceleration of both the nose and tail of the projectile are essentially independent of LID. For LID greater than or equal to 3, the target penetration associated with Phase 3 is found to increase with impact velocity approximately as P-3/D proportional to V (1.0). "After-flow" as a separate, identifiable mechanism could not be discerned in the results. We therefore question whether the phenomenon of "after-flow," as usually defined, exists; rather, projectile deceleration and crater depth growth are intimately coupled.
[19]
Anderson Jr CE, Royal-Timmons SA.1997.
Ballistic performance of confined 99.5%-Al$_{2}$O$_{3}$ ceramic tiles
. International Journal of Impact Engineering, 19: 703-713.
The one-dimensional modified Bernoulli theory of Tate [ J. Mech. Phys. Solids 15 , 287 399 (1967)] is often used to examine long-rod penetration into semi-infinite targets. The theory is summarized and the origins of the target resistance term examined. Numerical simulations were performed of a tungsten-alloy, long-rod projectile into a semi-infinite hardened steel target at three impact velocities sufficiently high to result in projectile erosion. The constitutive responses of the target and projectile were varied parametrically to assess the effects of strain hardening, strain-rate hardening, and thermal softening on penetration response. The results of one of the numerical simulations were selected to compare and contrast in detail with the predictions of the Tate model.
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Anderson Jr CE, Walker JD.2005.
An analytical model for dwell and interface defeat
. International Journal of Impact Engineering, 31: 1119-1132.
An analytical model that captures the essential mechanics of dwell and interface defeat—the phenomenon where an impacting projectile flows radially outward (erodes) along the surface of the target (usually ceramic) with no significant penetration—is presented. During dwell, the projectile loses kinetic energy due to mass loss and deceleration. It is shown that model predictions are in very good agreement with experimental data.
[22]
Anderson Jr CE, BehnerT, Templeton DW, Holmquist TJ, WickertM, HohlerV.2006.
Interface defeat of long rods impacting borosilicate glass
We have conducted a series of experiments to examine projectile penetration of cylindrical hot-pressed silicon carbide (SiC) ceramic targets that are pre-damaged to varying degrees under controlled laboratory conditions prior to ballistic testing. SiC was thermally shocked to introduce non-contiguous cracks. Another set of targets was thermally shocked and then additional damage was induced by load nload cycling in an MTS machine while the ceramic specimen was confined in a 7075-T6 aluminum sleeve. Finally, targets were made by compacting SiC powder into a 7075-T6 aluminum sleeve. For each of these target types, long gold rod penetration was measured as a function of impact velocity v p over the approximate range of 1 3 km/s, with most data between 1.5 and 3 km/s. Penetration as a function of time was measured using multiple independently timed flash X-rays. Results are compared with previous results for non-damaged (intact) SiC targets. Key results from these experiments include the following: (1) penetration is nominally steady state for v p>1.5 km/s; (2) for all target types, the penetration velocity u is a linear function of v p (except for the lowest impact velocities); and (3) it is found that u intact< u pre-damaged< u in-situ comminuted< u powder< u hydrodynamic.
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Anderson Jr CE, BehnerT, Holmquist TJ, Orphal DL, WickertM.2009.
Dwell, interface defeat, and penetration of long rods impacting silicon carbide
Reverse ballistic experiments were used to investigate confinement, pre-damaged and intact, and rod size effects on penetration of long, gold rods into silicon carbide (SiC-N). Rod diameters were 1.002mm and 0.7502mm, and lengths were 7002mm and 5002mm, respectively. Within data scatter, penetration velocity was the same for intact (bare or sleeved), pre-damaged (thermally shocked with non-contiguous cracks), and Highlights? Penetration rate of long Au rods into SiC determined as function of impact velocity. ? Intact, pre-damaged, in situ comminuted, sleeved, and bare SiC tested. ? Two different rod diameters tested. ? Penetration function of impact velocity but independent of other variables examined. ? Failure front predamages ceramic in front of rod, so rod penetrates failed material.
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Anderson Jr CE, Burkins MS, Walker JD, Gooch WA.2005.
Time-resolved penetration of B4C tiles by the APM2 bullet
. CMES, 8: 91-104.
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Anderson Jr CE, Littlefield DL, Walker JD.1993a.
Long-rod penetration, target resistance, and hypervelocity impact
. International Journal of Impact Engineering, 14: 1-12.
A computational study was performed to quantify the effects of strain rate on replica-model (scaled) experiments of penetration and perforation. The impact of a tungsten-alloy, long-rod projectile into an armor steel target at 1.5 km s 1 was investigated. It was found that over a scale factor of 10, strain-rate effects change the depth of penetration, for semi-infinite targets, and the residual velocity and length of the projectile, for finite-thickness targets, by an order of 5%. Although not modeled explicitly in the present study, the time-dependence of damage was examined. Damage accumulation is a strong function of absolute time, not scaled time. At homologous times, a smaller scale will have less accumulated damage than a larger scale; therefore, the smaller scale will appear stronger, particularly in situations where the details of damage evolution are important.
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Anderson Jr CE, Orphal DL, Franzen RR, Walker JD.1999.
On the hydrodynamic approximation for long-rod penetration
. International Journal of Impact Engineering, 22: 23-43.
Steady-state hydrodynamic theory, or variations thereof, has been applied to long-rod penetration since the 1940s. It is generally believed that projectile strength is of little consequence at high velocities, and that hydrodynamic theory is applicable to long-rod penetration when penetration pressures are much greater than the target flow stress. Substantiating this belief is the observation that at approximately 2.5 km/s, for tungsten alloy projectiles into armor steel, normalized penetration (P/L) nominally saturates to the classical hydrodynamic limit of the square root of the ratio of the projectile to target densities. Experimental data herein, however, show penetration velocities and instantaneous penetration efficiencies fall below that expected from hydrodynamic theory, even at impact velocities as high as 4.0 km/s. Numerical simulations, using appropriate strength values, are in excellent agreement with the experimental data. Parametric studies demonstrate that both projectile and target strength have a measurable effect even at such high impact velocities.
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Anderson Jr CE, Walker JD, LankfordJ.1995.
Investigation of the ballistic response of brittle materials
Brittle materials (ceramics, rocks and ice are examples) may contain a distribution of small, grain-sized, cracks. When loaded in compression, these cracks propagate stably until they interact to give final failure. A model is developed for the growth and interaction of cracks in brittle solids under compressive stress states. A critical stress is required to initiate crack growth: it depends on the initial crack length and orientation, on the coefficient of friction and on the stress state. The cracks then grow in a stable way until they start to interact; interaction increases the stress intensity driving crack growth and leads to instability and final failure. This chain of events is modelled, and the framework of a theory of damage mechanics is suggested.
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Ashby MF, Sammis CG.1990.
The damage mechanics of brittle solids in compression
The development of microcrack damage in brittle solids in compression is analyzed, using a simple model. The model is developed from recent detailed analysis of the initiation, propagation and linkage of microfractures from pre-existing cracks, voids, or other inhomogeneities. It describes the evolution of damage with strain and from it a criteria for failure can be established. The results are used to construct failure surfaces in stress space which combine information about brittle failure with data describing the onset of plastic yielding. Such failure surfaces are constructed for a number of rocks and are compared with previously published experimental data.
[35]
AydelotteB, SchusterB.2015.
Impact and penetration of SiC: The role of rod strength in the transition from dwell to penetration
The phenomenon of dwell during projectile impact on ceramics has been an active area of research for several decades. Dwell in confined ceramics has received much attention, particularly the role of cover plates and their influence over the dwell to penetration transition. Dwell during long rod impact on unconfined ceramics has received relatively less attention. The present work will compare and contrast the results of two series of long rod impacts on hot pressed silicon carbide targets. One series utilized gold wire rods. The other series utilized rods fabricated from tungsten carbide with 10% cobalt matrix. A novel ten-flash X-ray system captured spatially resolved images of the penetration events. The experimental results are compared with simulations and predictions from the Alekseevskii-Tate equation to explore the role of shock pressure, the effects of the strength of the rod material in dwell to penetration transition behavior, and the behavior of defects within silicon carbide.
[36]
BehnerT, Anderson Jr CE, Holmquist TJ, et al.2008.
Interface defeat for unconfined SiC ceramics. Army Tank-Automotive and
To determine the behavior of silicon carbide (SiC) against long rod impact a detailed study with experiments in the velocity range from 0.8 to 3 km/s at normal impact conditions was performed in recent years. Interest ranged from penetration performance of intact and pre-damaged SiC to interface defeat capability of SiC. Together with impact data in the hypervelocity regime this paper provides a comprehensive overview of the penetration dynamics of SiC over a wide velocity range and during different phases of the penetration process.
[38]
BehnerT, HeineA, WickertM.2013.
Protective properties of finite-extension ceramic targets against steel and copper projectiles//27th International Symposium on Ballistics,
Impact experiments with a tungsten heavy alloy long rod projectile against silicon carbide tiles were performed to study the transition from dwell to penetration and to compare against earlier investigations which focused either on small scale semi-infinite set-ups or on finite thickness set-ups with confinement. A depth-of-penetration configuration consisting of a ceramic tile and an extended steel backing was used to assess the impact response of the unconfined finite-thickness ceramic. The ceramic tile was either bare or had a cover plate attached to the front. The cover plate thickness has been varied and gives best results for a thickness of about half the projectile diameter used in the experiments. For the bare ceramic, a long dwell phase can be maintained up to impact velocities of around 900 /s. For the buffered ceramic, partial dwell can be achieved up to around 1700 /s. The results corroborate those of earlier investigations mentioned above. More importantly, the present results show that it is possible to substantially erode a heavy alloy long-rod penetrator at the surface of a finite thickness ceramic element without lateral confinement in direct impact experiments even at high impact velocities.
This Work Brings Together The Experience Of Specialists In The Behaviour Of Concrete And Metal Structures, Both Above And Below The Ground, To Actions Of Blast, Penetration And High Speed Collisions. From The Second International Conference, "structures Under Shock And Impact", This Volume Aims To Help Stimulate Future Research Analysis.
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BourneN.2010.
On kinetics of failure in, and resistance to penetration of metals and ceramics
The performance of armour materials depends upon the deformation mechanisms operating during the penetration process. The critical mechanisms determining the behaviour of armour ceramics have not been isolated using traditional ballistics. It has recently become possible to measure strength histories in materials under shock. The data gained for the failed strength of the armour are shown to relate directly to the penetration measured. Furthermore, it has been demonstrated in one-dimensional strain that the material can be loaded and recovered for post-mortem examination. Failure is by microfracture, which is a function of the defects and then cracking activated by plasticity mechanisms within the grains and failure at grain boundaries in the amorphous intergranular phase. Thus, it appears that the shock induced plastic yielding of grains at the impact face that determines the later time penetration through the tile.
[42]
ChenW.1995.
Dynamic failure behavior of ceramics under multiaxial compression
. California Institute of Technology//Joint Applied Mechanics and Materials Summer Meeting, Los Angeles, CA.
An experimental technique has been developed that is capable of (1) dynamically loading the specimen in multiaxial compression; (2) controlling the stress state in the specimen in the range from uniaxial stress to uniaxial strain; and (3) allowing the recovery of the sample after loaded by a single, well defined pulse for the characterization of the failure mode. In this technique, cylindrical ceramic specimens were loaded in the axial direction using a split Hopkinson pressure bar modified to apply a single loading pulse, and were confined laterally either by shrink fit sleeves, or by eletro-magnetic force. Quasi-static and dynamic multiaxial compression experiments have been performed on a machinable glass ceramic, Macor, and a monolithic engineering ceramic, sintered aluminum nitride (A1N). The cylindrical ceramic specimens were confned laterally by shrink fit sleeves: the amount of confining pressure (0-230 MPa) was varied by using different sleeve materials. The quasi-static axial load was applied by a hydraulic driven Material Test System (MTS), whereas the dynamic axial load was provided by a modified split Hopkinson (Kolsky) pressure bar (SHPB). Under both quasi-static and dynamic loading conditions, the experimental results for both materials showed that the failure mode changed from fragmentation by axial splitting under conditions of uniaxial stress (without lateral confinement) to localized deformation on faults under moderate lateral confinement. The fault initiation process was studied experimentally in detail. Based on the experimental results, a compressive brittle failure process was summarized. A transition from brittle to ductile behavior was observed in Macor under high confinement pressure which was achieved using a second sleeve around the inner sleeve. The compressive failure strengths of both materials increased with increasing confinement pressure under both quasi-static and dynamic loading conditions. The highest dynamic compressive strengths of Macor and A1N measured in the experiments were 1.35 GPa and 5.40 GPa, respectively, whereas their quasi-static compressive strength were measured to be 0.43 GPa and 2.5 GPa, respectively. Based on the experimental results on A1N together with available data in the literature, a failure/flow criterion was developed for ceramic materials under multiaxial loading. A Mohr-Coulomb criterion and an improved Johnson-Holmquist model were found to fit the experimental data for brittle failure, whereas the materials exhibited pressure insensitive plastic flow at high pressures. Observations made in other types of dynamic experiments (e.g., shock wave loading) were rationalized based on the postulated failure mechanisms and the possibility of plastic flow beyond the Hugoniot elastic limit (HEL). The effect of various material properties on the failure behavior was investigated using the proposed failure criterion. The applicability of the present model to a range of ceramics was also explored and the limitations of the model were outlined.
[43]
ChiR, SerjoueiA, SridharI, Tan G EB.2013.
Ballistic impact on bi-layer alumina/aluminium armor: A semi-analytical approach
. International Journal of Impact Engineering, 52: 37-46.
This paper presents a semi-analytical approach on the performance of ceramic/metal armor under ballistic impact. Numerical simulations for alumina/aluminum armor impacted by 20 mm APDS in AUTODYN were carried out and verified against the experimental data. Comprehensive numerical simulations were performed using the verified numerical model material parameters providing corroborative data for ensuing discussions. A semi-analytical model relating projectile residual velocity, impact velocity and armor ballistic limit velocity (BLV) is presented for impact of hard projectile against ceramic/metal armor. It is shown that the projectile residual velocity and BLV satisfy the replica scaling laws. Based on the replica scaling laws of projectile residual velocity and BLV, an empirical equation for BLV is obtained and used for armor optimization applications giving reasonable results similar to experiments available in the literature. [All rights reserved Elsevier].
[44]
ChiR, SerjoueiA, SridharI, Geoffrey T EB.2015.
Pre-stress effect on confined ceramic armor ballistic performance
. International Journal of Impact Engineering, 84: 159e70.
61Numerical modeling of pre-stressed confined SiC is performed and validated against the experimental measurements.61Effect of different pre-stress types on ballistic behavior of armor is explored.61Effect of “pressure at initial failure point” on ballistic behavior of SiC is studied.61Dwell–penetration transition velocity for different pre-stressed SiC targets is found.
[45]
Crouch IG, Appleby-ThomasG, Hazell PJ.2015.
A study of the penetration behavior of mild-steel-cored ammunition against boron carbide ceramics armours
. International Journal of Impact Engineering, 80: 203-211.
61Stripping the jacket and filler material from AK47 MSC rounds appears to make a difference to its penetrating ability when impacting a boron carbide ceramic target.61The magnitude of this effect is much greater than previously reported for high-strength steel-cored rounds and for tungsten carbide-cored rounds.61The penetration event appears to be a two-stage process: mushrooming of the mild steel core on, or near, the surface of the ceramic, followed by a linear erosion process.61The second step has not been reported previously for MSC rounds.
It is possible to erode completely certain projectiles at the face of a ceramic block, provided the ceramic is confined suitably and is considerably stronger than the projectile. Lower projectile speeds, densities and length-to-diameter ratios favor this phenomenon. Heavy ceramic confinement and the use of shock attenuators also favor projectile interface defeat. In this paper we report on our use of the wave code HULL to study some of the factors which govern this phenomenon.
A mechanism-based constitutive model is presented for the inelastic deformation and fracture of ceramics. The model comprises four essential features: (i) micro-crack extension rates based on stress-intensity calculations and a crack growth law, (ii) the effect of the crack density on the stiffness, inclusive of crack closure, (iii) plasticity at high confining pressures, and (iv) initial flaws that scale with the grain size. Predictions of stress/strain responses for a range of stress states demonstrate that the model captures the transition from deformation by micro-cracking at low triaxiality to plastic slip at high triaxialities. Moreover, natural outcomes of the model include dilation (or bulking) upon micro-cracking, as well as the increase in the shear strength of the damaged ceramic with increasing triaxiality. Cavity expansion calculations are used to extract some key physics relevant to penetration. Three domains have been identified: (i) quasi-static, where the ceramic fails due to the outward propagation of a compression damage front, (ii) intermediate velocity, where an outward propagating compression damage front is accompanied by an inward propagating tensile (or spallation) front caused by the reflection of the elastic wave from the outer surface and (iii) high velocity, wherein plastic deformation initiates at the inner surface of the shell followed by spalling within a tensile damage front when the elastic wave reflects from the outer surface. Consistent with experimental observations, the cavity pressure is sensitive to the grain size under quasi-static conditions but relatively insensitive under dynamic loadings.
The objective of the article is to present a unified model for the dynamic mechanical response of ceramics under compressive stress states. The model incorporates three principal deformation mechanisms: (i) lattice plasticity due to dislocation glide or twinning; (ii) microcrack extension; and (iii) granular flow of densely packed comminuted particles. In addition to analytical descriptions of each mechanism, prescriptions are provided for their implementation into a finite element code as well as schemes for mechanism transitions. The utility of the code in addressing issues pertaining to deep penetration is demonstrated through a series of calculations of dynamic cavity expansion in an infinite medium. The results reveal two limiting behavioral regimes, dictated largely by the ratio of the cavity pressure p to the material yield strength Y. At low values of p/ Y, cavity expansion occurs by lattice plasticity and hence its rate diminishes with increasing Y. In contrast, at high values, expansion occurs by microcracking followed by granular plasticity and is therefore independent of Y. In the intermediate regime, the cavity expansion rate is governed by the interplay between microcracking and lattice plasticity. That is, when lattice plasticity is activated ahead of the expanding cavity, the stress triaxiality decreases (toward more negative values) which, in turn, reduces the propensity for microcracking and the rate of granular flow. The implications for penetration resistance to high-velocity projectiles are discussed. Finally, the constitutive model is used to simulate the quasi-static and dynamic indentation response of a typical engineering ceramic (alumina) and the results compared to experimental measurements. Some of the pertinent observations are shown to be captured by the present model whereas others require alternative approaches (such as those based on fracture mechanics) for complete characterization.
[50]
Espinosa HD, Zavattieri PD, Dwivedi SK.1998a.
A finite deformation continuum/discrete model for the description of fragmentation and damage in brittle materials
. Journal of the Mechanics and Physics of Solids, 46: 1909-1942.
A dynamic finite element analysis of large displacements, high strain rate deformation behavior of brittle materials is presented in total Lagrangian coordinates. A continuum discrete damage model capable of capturing fragmentation at two size scales is derived by combining a continuum damage model and a discrete damage model for brittle failure, It is assumed that size and distribution of potential fragments are known a priori, through either experimental findings or materials properties, and that macrocracks can nucleate and propagate along the boundaries of these potential fragments. The finite deformation continuum multiple-plane microcracking damage model accounts for microcracks within fragments. Interface elements, with cohesive strength and reversible unloading before debonding, between potential fragments describe the initiation of macrocracks, their propagation, and coalescence leading to the formation of discrete fragments. A surface-defined multibody contact algorithm with velocity dependent friction is used to describe the interaction between fragments and large relative sliding between them. The finite element equations of motion are integrated explicitly using a variable time step. Outputs are taken at discrete time intervals to study material failure in detail. The continuum discrete damage model and the discrete fragmentation model, employing interface elements alone, are used to simulate a ceramic rod on rod impact. Stress wave attenuation, fragmentation pattern, and overall failure behavior, obtained from the analyses using the two models, are compared with the experimental result and photographs of the failing rod. The results show that the continuum discrete model captures the stress attenuation and rod pulverization in agreement with the experimental observations while the pure discrete model underpredicts stress attenuation when the same potential fragment size is utilized. Further analyses are carried out to study the effect of potential fragment size and friction between sliding fragments It is found that compared with the continuun discrete damage model, the discrete fragmentation model is more sensitive to the multi-body discretization.
[51]
Espinosa HD, DwivediS, ZavattieriP, YuanG.1998b.
A numerical investigation of penetration in multilayered material/structure systems
. International Journal of Solids and Structures, 35: 2975-3001.
ABSTRACT The response of multilayered ceramic/steel targets to high velocity impact and penetration has been investigated through finite element simulations. A multiple-plane microcracking model has been used to describe the inelastic constitutive behavior of ceramics in the presence of damage. The model has been integrated into the finite element code EPIC95, which possesses contact and erosion capabilities particularly suitable for ballistic simulations. The integrated code has been used to analyze the depth of penetration (DOP) and interface defeat (ID) ceramic target configurations. Parametric analyses have been carried out to establish the effect of ceramic materials, target configuration design for ceramic confinement, diameter/length (d/L) ratio of the penetrator, material erosion threshold levels and the use of a shock attenuator on the response of multilayered targets subjected to high velocity impact. The response characteristics are established in terms of the parameters which can be measured experimentally. The analyses show that the integrated code is able to predict the response of ceramic targets in confirmation with experimental findings reported in the literature. The penetration process is found to be less dependent on the ceramic materials as usually assumed by most investigators. By contrast, the penetration process is highly dependent on the multilayered configuration and the target structural design (geometry, and boundary conditions). From a simulation standpoint, it has been found that the erosion parameter plays an important role in predicting the deformation history and interaction of the penetrator with the target. These findings show that meaningful lightweight armor design can only be accomplished through a combined experimental/numerical study in which relevant ballistic materials and structures are simultaneously investigated.
[52]
FeliS, AsgariM.2011.
Finite element simulation of ceramic/composite armor under ballistic impact
In this paper, based on LS-Dyna code, a new finite element (FE) simulation of the ballistic perforation of the ceramic/composite targets, which impacted by cylindrical tungsten projectiles, has been presented. Research on this method has been conducted by a few research groups in recent years. The ceramic material, which is the front plate, has been made of Alumina 99.5% and composite back-up plate composed of Twaron fibers. The 2-dimensional (2D), axi-symmetric, dynamic-explicit, Lagrangian model has been considered in this simulation. The Johnson-Cook, Johnson-Holmquist and Composite-Damage materials behaviors have been used for projectile, ceramic and composite materials respectively. The brittle fracture and fragmentation of ceramic conoid, the failure criteria based on fracture of fibers or matrixes of composite materials and erosion or flattening of projectile during perforation have been considered. The residual velocity and perforation time has been obtained and compared with the available analytical models. The results show that when the ceramic is impacted by a projectile, a fragmented ceramic conoid breaks from ceramic tile and the semi-angle of ceramic conoid with increasing initial velocity decreases. Furthermore, the dishing of composite layers at high impact velocities and the delamination of layers near the ballistic limit velocity decrease. [All rights reserved Elsevier].
Silicon carbide, with single-edge precracked beam (SEPB) toughness greater than 7 MPa·m 1/2 , was made by hot-pressing using Al–B–C (ABC) or Al–Y 2 O 3 (YAG) as additives. The hardness of SiC processed with a liquid phase was always less than SiC densified without a liquid phase despite having a similar or finer grain size. With increasing Al content, the ABC system changed from trans- to intergranular fracture with a drop in hardness and a two- to threefold increase in SEPB toughness. Strength and Weibull modulus for materials processed with a liquid phase were higher than those of solid-state densified SiC. Ballistic testing, however, did not show any improvement over SiC densified with B and C additives. Depth of penetration was controlled by hardness of the SiC-based materials, while V 50 values for 14.5 mm WC–Co cored projectiles were in the range of 720–750 m/s for all materials tested.
[55]
FountzoulasC, CheesemanB, LaSalviaJ.2009.
Simulation of ballistic impact of a tungsten carbide sphere on a confined silicon carbide target//Proceedings of the 23rd International Symosium on Balllistics, Tarragona, Spain
LaSalvia et al. (LaSalvia presentation (2010) Ballistic impact damage in hot- pressed boron carbide 34 ICACC, Daytona Beach, 25 29 Jan 2010) studied experimentally the interaction of confined hot-pressed boron carbide (B 4 C) targets impacted by laboratory-scale tungsten-based long-rod penetrators. To better understand the physics involved, Fountzoulas et al. (Fountzoulas CG, LaSalvia JC (2011) Simulation of the ballistic impact of tungsten-based penetrators on confined hot-pressed boron carbide targets. In: Proceedings of 35th ICACC, Advances in Ceramic Armor VII, p 261) studied by modeling and simulation the ballistic behavior of these targets. To satisfactorily replicate the experimental damage of the targets during impact, the material strength and failure models were iteratively modified. Despite numerous iterations, the damage replication of the target was only partially successful. The fracture of B 4 C was able to be replicated to some extent but without being able to stop its penetration by the projectile, a disagreement with the experimental observations. The current effort reports on the sensitivity and modification of the existing strength and failure B 4 C material models of the ANSYS/AUTODYN library to predict the tensile failure to accurately simulate the ballistic response of ceramics.
[59]
FranzenR, OrphalD, AndersonC.1997.
The influence of experimental design on depth-of-penetration (DOP) test results and derived ballistic efficiencies
. International Journal of Impact Engineering, 19: 727-737.
Abstract Experimental data for ceramic armor materials from two test methods, small-scale reverse ballistic tests and depth-of-penetration (DOP) tests, are reviewed and compared. Results from reverse ballistic tests can be used to estimate the length of rod erosion in the ceramic tiles of DOP tests. The outcome of a given DOP test can then be predicted by using recently published data bases on RHA penetration to determine the residual penetration into the steel back-up of the DOP test. Results of this methodology, compared to experimental DOP-test results, agree reasonably well for aluminum nitride and silicon carbide, even though scale sizes, impact velocities and experimental procedures varied considerably between investigators. The methodology was then applied to single-valued performance criteria for ceramic armor materials, for example, mass efficiency. This analysis demonstrates that in certain cases, test parameters, like the ratio of penetrator length to ceramic tile thickness, affect test results considerably more than differences between ceramic types. Thus, DOP tests must be properly designed and interpreted in order to assess correctly the ballistic performance of ceramics.
[60]
Gama BA, Bogetti TA, Fink BK, Yu CJ, Claar TD, Eifert HH, et al.2001.
Aluminum foam integral armor: A new dimension in armor design
Closed-cell aluminum foam offers a unique combination of properties such as low density, high stiffness, strength and energy absorption that can be tailored through design of the microstructure. During ballistic impact, the foam exhibits significant non-linear deformation and stress wave attenuation. Composite structural armor panels containing closed-cell aluminum foam are impacted with 20-mm fragment-simulating projectiles (FSP). One-dimensional plane strain finite element analysis (FEA) of stress wave propagation is performed to understand the dynamic response and deformation mechanisms. The FEA results correlate well with the experimental observation that aluminum foam can delay and attenuate stress waves. It is identified that the aluminum foam transmits an insignificant amount of stress pulse before complete densification. The ballistic performance of aluminum foam-based composite integral armor (CIA) is compared with the baseline integral armor of equivalent areal-density by impacting panels with 20-mm FSP. A comparative damage study reveals that the aluminum foam armor has finer ceramic fracture and less volumetric delamination of the composite backing plate as compared to the baseline. The aluminum foam armors also showed less dynamic deflection of the backing plate than the baseline. These attributes of the aluminum foam in integral armor system add a new dimension in the design of lightweight armor for the future armored vehicles.
[61]
Garcia-AvilaM, PortanovaM, RabieiA.2014.
Ballistic performance of a composite metal foam-ceramic armor system
Composite Metal Foam is a low-weight, high-strength porous material capable of absorbing great amounts of energy under loading. In this report, Composite Metal Foam panels are manufactured using powder metallurgy technique and 2mm steel hollow spheres in a steel matrix and used in conjunction with a ceramic plate to fabricate a new light-weight composite armor system. This armor system is tested under ballistic loading using 7.62x51mm M80 and 7.62x63mm M2 AP projectiles at varying impact velocities for single and multi-impact scenarios. The material behavior, failure mechanism, and ballistic performance of the armor system are studied for optimization.
[62]
GroveD, RajendranA.2001.
Modeling the interface defeat phenomenon using a physically-based ceramic damage model
. APS Shock Compression of Condensed Matter Meeting Abstracts, 46.
This paper presents results from simulations of metallic rods impacting confined ceramic targets. If the ceramic target is properly confined, a phenomenon known as "interface defeat" may occur at a critical impact velocity. When this happens, the projectile is defeated at the ceramic surface, with no penetration into the ceramic. Due to the severe deformations that the projectile experiences during interface defeat, this phenomenon has been traditionally impossible to numerically simulate using conventional Lagrangian finite element algorithms. However, recent advances in particle method techniques have eliminated some of the numerical problems associated with such large deformations. Employing a new generalized particle algorithm option that is now available in the Lagrangian hydrocode EPIC, we simulated several "interface defeat" experimental configurations using the Rajendran-Grove (RG) ceramic model to describe the ceramic material's response to dynamic impact. The purpose of this effort was to evaluate the ability of the RG model to reproduce and predict the phenomenon of interface defeat.
[63]
HallamD, HeatonA, JamesB, SmithP, YeomansJ.2015.
The correlation of indentation behavior with ballistic performance for spark plasma sintered armour ceramics.
Abstract The Knoop and Vickers indentation behaviour of spark plasma sintered SiC–5 wt.% B4C, B4C and SiC–2.5 wt.% AlN–3 wt.% C armour ceramics have been investigated and observations correlated with ballistic performance. Surface and sub-surface indentation-induced damage has been characterised via cross-sectioning and serial ceramographic polishing techniques. The nature of the damage appears to be less influential than hardness in relation to ballistic performance, but variability in indentation behaviour appears to correlate with variability in ballistic performance. Examination of the indentation size effect curves shows that both Knoop hardness and predicted transition velocities correlate with V50 ballistic performance against an armour-piercing threat, further supporting the importance of hardness and the potential for indentation to be used as a screening method for armour materials.
It has long been known that a relation exists between a material's hardness and its gross impact performance; however, the nature of this relationship has not been understood to a degree useful in materials development. Many studies have shown that harder ceramics tend to display better ballistic performance. In addition, some research has suggested that a material's potential for inelastic deformation (or its “quasi-plasticity” – a bulk property) may also play an important role in its resistance to penetration. Methods of quantifying the bulk plasticity of a ceramic material are, however, extremely limited. The current study continues an investigation into a recently proposed technique to (1) quantify bulk quasi-plasticity in SiC materials, and (2) use the “plasticity” value along with a hardness value to predict the transition velocity of potential armor ceramics. The transition velocity values predicted by this approach generally show excellent agreement (within 5% in most cases) with experimentally determined velocities. In addition, the robustness of this predictive technique is demonstrated through the use of multiple operators and multiple hardness testing units.
[69]
Holmquist TJ, Templeton DW, Bishnoi KD.2001.
Constitutive modeling of aluminum nitride for large strain, high-strain rate, and high-pressure applications
. International Journal of Impact Engineering, 25: 211-231.
This paper presents constitutive modeling of aluminum nitride (AlN) for severe loading conditions that produce large strains, high-strain rates, and high pressures. The Johnson olmquist constitutive model (JH-2) for brittle materials is used. Constants are obtained for the model using existing test data that include both laboratory and ballistic experiments. Due to the wide range of experimental data the majority of constants are determined explicitly. The process of determining constants is provided in detail. The model and constants are used to perform computations of many of the experiments including those not used to generate the constants. The computational results are used to validate the model, provide insight into the response of AlN, and to demonstrate that one set of constants can provide reasonable results over a broad range of experimental data.
[70]
Holmquist TJ, Johnson GR.2002a.
Response of silicon carbide to high velocity impact
This article presents an analysis of the response of silicon carbide to high velocity impact. This includes a wide range of loading conditions that produce large strains, high strain rates, and high pressures. Experimental data from the literature are used to determine constants for the Johnson olmquist constitutive model for brittle materials (JH-1). It is possible to directly determine the strength and pressure response of the intact material from test data in the literature. After the ceramic has failed, however, there are not adequate experimental data to directly determine the response of the failed material. Instead, the response is inferred from a comparison of computational results to ballistic penetration test results. After the constants have been obtained for the JH-1 model, a wide range of computational results are compared to experimental data in the literature. Generally, the computational results are in good agreement with the experimental results. Included are computational results that model interface defeat, which occurs when a high velocity projectile impacts a ceramic target and then dwells on the surface of the ceramic with no significant penetration.
This work presents computed results for the responses of ceramic targets, with and without prestress, subjected to projectile impact. Also presented is a computational technique to include prestress. Ceramic materials have been considered for armor applications for many years because of their high strength and low density. Many researchers have demonstrated that providing confinement enhances the ballistic performance of ceramic targets. More recently, prestressing the ceramic is being considered as an additional enhancement technique. This work investigates the effect of prestressing the ceramic for both thin and thick target configurations subjected to projectile impact. In all cases the targets with ceramic prestress provided enhanced ballistic performance. The computed results indicate that prestressed ceramic reduces and/or delays failure, resulting in improved ceramic performance and ballistic efficiency.
[73]
Holmquist TJ, Johnson GR.2005a.
Characterization and evaluation of silicon carbide for high-velocity impact
This article presents a characterization and evaluation of silicon carbide for high-velocity impact. This includes a wide range of loading conditions that produce large strains, high strain rates, and high pressures. Experimental data from the literature are used to determine constants for the Johnson olmquist eissel (JHB) constitutive model for brittle materials. A previous article by the authors presented a characterization of silicon carbide for high-velocity impact using an earlier version of the model (JH-1). The previous work provided good agreement with a broad range of experimental data with the exception of high-velocity penetration data. The current work uses the more recently developed JHB constitutive model, a target geometry that more closely matches the experimental design, and a computational technique that allows for target prestress. These recent developments (primarily the prestress) produce computed results that agree with all the experimental data, including the high-velocity penetration data. The computed results also provide a detailed analysis of the penetration process into a prestressed target and show why it is necessary to include the target prestress. A specific result is the ability to reproduce the nonsteady penetration rate that occurs in the prestressed target.
[74]
Holmquist TJ, Johnson GR.2005b.
Modeling prestressed ceramic and its effect on ballistic performance
. International Journal of Impact Engineering, 31: 113-127.
This article presents computed results for the responses of ceramic targets, with and without prestress, subjected to projectile impact. Also presented is a computational technique to include prestress. Thin and thick ceramic target configurations are used to understand the effect prestressing has on ballistic performance. For both targets two prestress levels (small and large), and two prestress states (radial and hydrostatic) are investigated. The small prestress is similar in magnitude to values obtained experimentally and the large prestress is approximately the maximum prestress the confinement can produce (determined computationally). The targets are subjected to projectile impact and the resulting ballistic responses are evaluated. In all cases prestressing the ceramic enhanced the ballistic performance, although the effect of the different prestress conditions on the ballistic response was not always obvious.
[75]
Holmquist TJ, Johnson GR.2008.
Response of boron carbide subjected to high-velocity impact
. International Journal of Impact Engineering, 35: 742-752.
This article presents an evaluation of the response of boron carbide (BC) subjected to impact loading under three different conditions. Condition A is produced by plate-impact experiments where the loading condition is uniaxial strain and the stresses and pressures are high. Under plate-impact loading the material fails at the Hugoniot Elastic Limit (HEL) and the failed material undergoes high confining pressures and relatively small inelastic strains. Condition B is produced by projectile impact onto thick targets where the stresses and pressures are dependent on impact velocity, but they are generally lower than those from plate impact. Under thick-target impact/penetration most of the material fails under compression, the inelastic strains are large and the material appears to exhibit more ductility than under condition A. Lastly, condition C is produced by projectile impact and perforation of thin targets where the stresses and pressures are a combination of compression and tension. Under thin-target perforation the material fails in both tension and compression. The Johnson olmquist eissel (JHB) constitutive model is used to evaluate the material behavior for each of the three conditions, but it is not possible to accurately reproduce the experimental results of the three conditions with a single set of constants. Instead, three different sets of constants are required to accurately model the three impact conditions. These three models/constants are used to provide insight into the complex response of BC, and to identify possible mechanisms that are not included in the JHB model.
[76]
Holmquist TJ, Johnson GR.2011.
A computational constitutive model for glass subjected to large strains, high strain rates and high pressures
This article presents a computational constitutive model for glass subjected to large strains, high strain rates and high pressures. The model has similarities to a previously developed model for brittle materials by Johnson, Holmquist and Beissel (JHB model), but there are significant differences. This new glass model provides a material strength that is dependent on the location and/or condition of the material. Provisions are made for the strength to be dependent on whether it is in the interior, on the surface (different surface finishes can be accommodated), adjacent to failed material, or if it is failed. The intact and failed strengths are also dependent on the pressure and the strain rate. Thermal softening, damage softening, time-dependent softening, and the effect of the third invariant are also included. The shear modulus can be constant or variable. The pressure-volume relationship includes permanent densification and bulking. Damage is accumulated based on plastic strain, pressure and strain rate. Simple (single-element) examples are presented to illustrate the capabilities of the model. Computed results for more complex ballistic impact configurations are also presented and compared to experimental data. [DOI: 10.1115/1.4004326]
[77]
Holmquist TJ, Anderson Jr CE, BehnerT.2008.
The effect of a copper buffer on interface defeat//Proceedings of the 24th international symposium on ballistics
, Lancaster. 721-728.
[78]
Holmquist TJ, Anderson Jr CE, BehnerT, Orphal DL.2010.
Ceramic material with high hardness and light quality is wildly used to protect the light armored vehicles against the threat of small-bore armor-piercing projectile.However,the ability for anti-striking many times of ceramic armour needs to be stronger.During the amour-piericing process,the hardness and intensity of ceramic under confinement condition are increased effectively by the dwell phenomene,then the ability for anti-striking many times of ceramic armour is improved.In this text the definition,microcosmic mechanism,influencing factors of the dwell phenomena and the trends and hotpoint of research are introduced.Finally,the research direction to be focused on numerical simulation and the questions needing to be solved are pointed out.
[81]
Iyer KA.2007.
Relationships between multiaxial stress states and internal fracture patterns in sphere-impacted silicon carbide
Internal fracture patterns developed in silicon carbide cylindrical targets as a result of dynamic indentation (63 500 m/s) by tungsten carbide spheres are defined. Microscopy of recovered and sectioned targets delineate into three regions, each associated with distinct cracking modes, i.e., shallow cone macrocracking at and near the impact surface, steep interior cone macrocracks that radiate into the target from the impact region and local grain-scale microcracking directly underneath the impact region. The observed fracture patterns are found to maintain a noticeable degree of self-similarity upto the impact velocity of 500 m/s. Linear elastic analysis of the full (surface and interior) stress field developed under static (Hertz) contact loading delineate the target into four regions, based on the number of principal stresses that are tensile (none, 1, 2 or all 3). A strong correlation is found between the principal stress conditions within each region and the forms of cracking, their locations and orientations present therein. This correlation has a number of implications, including non-interaction of crack systems, which are discussed. Illustrative linear elastic fracture mechanics analyses are performed for three regions, and calculated and observed macrocrack lengths are found to be in reasonable agreement.
[82]
Jaansalu KM.2013.
Material properties and interface defeat
//27th International Symposium on Ballistics Freiburg, Germany. 1277-1288.
[83]
Johnson GR, Holmquist TJ.1992.
A computational constitutive model for brittle materials subjected to large strains, high strain rates and high pressures
. Shock Wave and High-Strain-Rate Phenomena in Materials, 1075-1081.
This article presents a computational constitutive model for glass subjected to large strains, high strain rates and high pressures. The model has similarities to a previously developed model for brittle materials by Johnson, Holmquist and Beissel (JHB model), but there are significant differences. This new glass model provides a material strength that is dependent on the location and/or condition of the material. Provisions are made for the strength to be dependent on whether it is in the interior, on the surface (different surface finishes can be accommodated), adjacent to failed material, or if it is failed. The intact and failed strengths are also dependent on the pressure and the strain rate. Thermal softening, damage softening, time-dependent softening, and the effect of the third invariant are also included. The shear modulus can be constant or variable. The pressure-volume relationship includes permanent densification and bulking. Damage is accumulated based on plastic strain, pressure and strain rate. Simple (single-element) examples are presented to illustrate the capabilities of the model. Computed results for more complex ballistic impact configurations are also presented and compared to experimental data. [DOI: 10.1115/1.4004326]
[84]
Johnson GR, Holmquist TJ.1994.
An improved computational constitutive model for brittle materials
. High-Pressure Science and Technology—993: AIP Publishing. 981-984.
An improved computational constitutive model for brittle materials is presented. It is applicable for brittle materials subjected to large strains, high strain rates and high pressures, and is well锕晆ited for computations in both Lagrangian and Eulerian codes. The equivalent strength is dependent on the intact strength, fractured strength, strain rate, pressure, and damage. The pressure includes the effect of bulking, which is introduced through the transfer of internal energy from decreased shear and deviator stresses to potential internal energy associated with increased hydrostatic pressure. Examples are presented to illustrate the model.
[85]
Johnson GR, HolmquistTJ.1999.
Response of boron carbide subjected to large strains, high strain rates, and high pressures
This article presents an analysis of the response of boron carbide (B 4C) to severe loading conditions that produce large strains, high strain rates, and high pressures. Experimental data from the literature are used to determine and/or estimate constants for the JH-2 constitutive model for brittle materials. Because B 4C is a very strong material, it is not always possible to determine the constants explicitly. Instead they must sometimes be inferred from the limited experimental data that are available. The process of determining constants provides insight into the constitutive behavior for some loading conditions, but it also raises questions regarding the response under other loading conditions. Several Lagrangian finite element and Eulerian finite difference computations are provided to illustrate responses for a variety of impact and penetration problems
[86]
Johnson GR, Holmquist TJ, Beissel SR.2003.
Response of aluminum nitride (including a phase change) to large strains, high strain rates, and high pressures
This article contains a description of a computational constitutive model for brittle materials subjected to large strains, high strain rates, and high pressures. The focus of this model is to determine the response of aluminum nitride under high velocity impact conditions that produce large strains, high strain rates, and high pressures. The strength is expressed as a function of the pressure, strain rate, and accumulated damage; and it allows for strength of both intact and failed material. The pressure is primarily expressed as a function of the volumetric strain, but it also includes the effect of bulking for the failed material. For materials without a phase change this model is an extension of the previous Johnson olmquist models for brittle materials. The primary new feature of this model is the capability to include a phase change, and this is required for aluminum nitride. Computations are performed to illustrate the capabilities of the model, to compare computed results to experimental results,...
[87]
Johnson KL.1987. Contact Mechanics. Cambridge University Press.
Armor systems made of ceramic and composite materials are widely used in ballistic applications to defeat armor piercing (AP) projectiles. Both the designers and users of body armor face interesting choices – how best to balance the competing requirements posed by weight, thickness and cost of the armor package for a particular threat level. A finite element model with a well developed material model is indispensible in understanding the various nuances of projectile–armor interaction and finding effective ways of developing lightweight solutions. In this research we use the explicit finite element analysis and explain how the models are built and the results verified. The Johnson–Holmquist material model in LS-DYNA is used to model the impact phenomenon in ceramic material. A user defined material model is developed to characterize the ductile backing made of ultra high molecular weight polyethylene (UHMWPE) material. An ad hoc design optimization is carried out to design a thin, light and cost-effective armor package. Laboratory testing of the prototype package shows that the finite element predictions of damage are excellent though the back face deformations are under predicted.
[90]
LaSalvia JC.2002a.
A physically-based model for the effect of microstructure and mechanical properties on ballistic performance//26th Annual Conference on Composites, Advanced Ceramics, Materials,
Summary Recovery of ceramics from ballistic experiments in which impacting ductile long-rod projectiles failed to penetrate has led to the observation and understanding of the localized damage mechanisms beneath the region of impact. The shape of the damaged region indicates that these mechanisms are shear-assisted. Based upon these observations, a model for the transition between no penetration and penetration was formulated by combining a micromechanics -based compressive failure model with Hertz's theory for frictionless contact between axisymmetric linear-elastic bodies. The resulting model indicates the relative significance of a ceramic's grain size, short-crack fracture toughness, yield strength, Poisson's ratio, coefficient of friction, and critical crack-length on the dwell/penetration transition. A brief review of the derivation and predictions of the model are presented.
[91]
LaSalvia JC.2002b.
Recent progress on the influence of microstructure and mechanical properties on ballistic performance
An analytical prediction for the effect of ceramic thickness and mechanical properties on the dwell/penetration transition velocity//20th International Symposium on Ballistics
The inelastic deformation mechanisms and damage features observed in structural ceramics subjected to nonpenetrating, high-velocity impacts are similar to those seen in quasistatic Hertzian indentation, albeit more severe. For impacts on large ceramic bodies (relative to impactor diameter), cone cracking is the primary mechanism in regions of high tensile stresses. In regions of nonhydrostatic compressive stresses, depending on the material characteristics, elasticity, grain-boundary microcracking, or plasticity are the primary mechanisms, and depending on their associated energetics, may be able to compete with the initiation and growth of cone cracks. In this regard, a new model is presented that examines the effect of grain-boundary microcracking on cone cracking through shear-induced dilatancy (i.e., bulking) within the quasiplastic zone that forms just underneath the impact site. Depending on the size of the quasiplastic zone and bulking pressure, it is shown that the bulking phenomenon has the potential to suppress cone cracking. Lastly, examples of other shear-driven inelastic deformation mechanisms are presented.
ABSTRACT Armor-grade B4C and WC cylinders (25.4 mm 25.4 mm) were impacted with WC-6Co (6 wt.% Co) spheres (6.35 mm diameter) at velocities between 100 m/s and 400 m/s. The recovered cylinders were subsequently sectioned and metallographically-prepared to reveal the dominant sub-surface damage types and change in damage severity as a function of impact velocity. In general, both ceramics exhibited radial, ring, Hertzian cone, and lateral cracks which increased in number and length as the impact velocity increased. The cracking was predominately transgranular for B4C and intergranular for WC. However, unlike SiC and TiB2 (reported in the part I[1]), no evidence of a comminuted region directly beneath the impact center was observed in either ceramic. B4C exhibited severe spallation of material surrounding the impact center. In addition, evidence of shear localization beneath the impact center was also observed. This observation may in part explain the sharp drop in shear strength that B4C exhibits in plate impact experiments when shocked above 20 GPa. In contrast, WC was almost unremarkable in its response to being impact with the WC spheres in that it exhibited a nice spherical crater that is more typical of the response of a metal. The effect of impact velocity on the observed damage and differences in damage between these two armor-grade ceramics will be presented.
[98]
LaSalvia JC, McCuiston RC, FanchiniG, McCauley JW, ChhowallaM, Miller HT, et al.2007.
Shear localization in a sphere-impacted armor-grade boron carbide
//23rd International Symposium on Ballistics Tarragona, Spain, 1329-1337.
ballistic impact damage observations in a hot-pressed boron carbidercial hot-pressed boron carbide (B4C) impacted ballistically are reported. The ballistic targets con
[101]
LaSalvia JC, CampbellJ, SwabJ, McCauleyJ.2010b.
Beyond hardness: Ceramics and ceramic-based composites for protection
Because of their lightweight and high hardness, ceramics have been successfully used in protection technologies for over 40 years. The high hardness of a ceramic enables it to break, fragment, and deform impacting projectiles. This paper deals with a number of issues connected to the application of ceramics to ballistic protection, including ceramic hardness, inelastic deformation mechanisms, basic ballistic phenomenology and experimentation, ceramic damage due to ballistic impact, performance/failure maps based upon specific damage/failure mechanisms, and what possible future types of ceramics the suppression of these damage/failure mechanisms guide us to.
[102]
LeavyB, RickterB, Normandia MJ.2008.
Modeling dynamically impacted ceramic material experiments
//Advances in Ceramic Armor: A Collection of Papers Presented at the 29th International Conference on Advanced Ceramics and Composites, January 23-28, 2005, Cocoa Beach, Florida, Ceramic Engineering and Science Proceedings: Wiley-American Ceramic Society. 11.
ABSTRACT SummaryA number of new experimental techniques were developed to simplify the process of calibrating ceramic constitutive models. Current ceramic model calibration techniques for the Johnson-Holmquist One (JH1) model require the use of complicated penetration experiments to tune the damage evolution to a specific experiment Application of these ceramic models to different experiments often illustrates discrepancies in the results.This paper will illustrate the use of data from these new experimental methods to simplify the calibration process for hot-pressed silicon carbide (SiC), and thus more accurately capture the behavior of different ceramic materials. Dynamic sphere impacts as well as kinetic energy rod penetration rate study programs have been established. Comparison of the experimental data with the corresponding simulation results will highlight areas for improvement in ceramic modeling. Specifically, the macroscopic behavior the constitutive model attempts to encompass and its relation to relevant static and dynamic properties.
[103]
Li JC, Chen XW.2017.
Theoretical analysis of projectile-target interface defeat and transition to penetration by long rods due to oblique impacts of ceramic targets
. International Journal of Impact Engineering, 106: 53-63.
61Three deformation modes of the long rod and the ceramic target are summarized.61The critical impact velocity range for the transition is further identified.61Critical transition time is analyzed and an analytical expression is formulated.61The analytical formula is convenient for the engineering application.
[106]
LiuT, Fleck NA, Wadley H NG, Deshpande VS.2013.
The impact of sand slugs against beams and plates: Coupled discrete particle/finite element simulations
. Journal of the Mechanics and Physics of Solids, 61: 1798-1821.
The impact of a slug of dry sand particles against a metallic sandwich beam or circular sandwich plate is analysed in order to aid the design of sandwich panels for shock mitigation. The sand particles interact via a combined linear-spring-and-dashpot law whereas the face sheets and compressible core of the sandwich beam and plate are treated as rate-sensitive, elastic–plastic solids. The majority of the calculations are performed in two dimensions and entail the transverse impact of end-clamped monolithic and sandwich beams, with plane strain conditions imposed. The sand slug is of rectangular shape and comprises a random loose packing of identical, circular cylindrical particles. These calculations reveal that loading due to the sand is primarily inertial in nature with negligible fluid–structure interaction: the momentum transmitted to the beam is approximately equal to that of the incoming sand slug. For a slug of given incoming momentum, the dynamic deflection of the beam increases with decreasing duration of sand-loading until the impulsive limit is attained. Sandwich beams with thick, strong cores significantly outperform monolithic beams of equal areal mass. This performance enhancement is traced to the “sandwich effect” whereby the sandwich beams have a higher bending strength than that of the monolithic beams. Three-dimensional (3D) calculations are also performed such that the sand slug has the shape of a circular cylindrical column of finite height, and contains spherical sand particles. The 3D slug impacts a circular monolithic plate or sandwich plate and we show that sandwich plates with thick strong cores again outperform monolithic plates of equal areal mass. Finally, we demonstrate that impact by sand particles is equivalent to impact by a crushable foam projectile. The calculations on the equivalent projectile are significantly less intensive computationally, yet give predictions to within 5% of the full discrete particle calculations for the monolithic and sandwich beams and plates. These foam projectile calculations suggest that metallic foam projectiles can be used to simulate the loading by sand particles within a laboratory setting.
[107]
LundbergP.2004.
Interface defeat and penetration: Two modes of interaction between metallic projectiles and ceramic targets
Summary This chapter contains sections titled: Introduction Dwell and Interface Defeat Experimental Techniques Projectile and Target Materials Used Modelling and Analyses Transition Velocity Versus Material Properties and Confinement Transition Velocity Versus Projectile Geometry Discussion Conclusions Future Research Acknowledgments
[109]
LundbergP, LundbergB.2005.
Transition between interface defeat and penetration for tungsten projectiles and four silicon carbide materials
. International Journal of Impact Engineering, 31: 781-792.
As ballistic tests are often performed in reduced geometrical scale, the scaling laws are important for the interpretation of the results. In this study, we tested the validity of replica scaling, by which we mean that all geometrical dimensions are scaled uniformly, while the materials and the impact velocity are kept the same. Long tungsten projectiles with length-to-diameter ratio 15 were fired against unconfined alumina targets with steel backing. The tests were carried out with impact velocities 1500 m sand 2500 m s, and in three different scales with projectile lengths 30, 75 and 150 mm (diameters 2, 5 and 10 mm). The alumina targets were photographed by means of a high-speed camera, and the tungsten projectiles were photographed inside the alumina targets by means of flash radiography. Also, the residual penetrations in the steel backings were measured. The Johnson-Holmquist model for ceramic materials was implemented into the AUTODYN code, which was used for simulation of the experiments. The agreement between results of experiment and simulation was fair, and over the tested interval of scales replica scaling was found to be valid with reasonable accuracy.
[111]
LundbergP, RenströmR, LundbergB.2000.
Impact of metallic projectiles on ceramic targets transition between interface defeat and penetration
. International Journal of Impact Engineering, 24: 259-275.
Armour systems capable of defeating an incoming projectile on the surface of a ceramic have been reported by several authors. This capability, called interface defeat, signifies that the projectile material is forced to flow radially outwards on the surface of the ceramic without penetrating significantly. In order to investigate the conditions for interface defeat, two models for the interaction of a metallic projectile and a ceramic target were established. With the aid of them, upper and lower bounds for the transition impact velocity between interface defeat and normal penetration were estimated for a given combination of metallic projectile and ceramic target. These approximate bounds were found to be consistent with transition velocities determined experimentally for two projectile materials (tungsten and molybdenum) and five target materials (two types of silicon carbide, boron carbide, titanium diboride and a polycrystalline diamond composite).
[112]
LundbergP, RenströmR, HolmbergL.2001.
An experimental investigation of interface defeat at extended interaction time
//19th International Symposium of Ballistics Interlaken, Switzerland, 1463-1469.
Normal impact of conical tungsten projectiles on flat silicon carbide targets was studied experimentally and numerically for half apex angles 5 and 5 15 , respectively, and comparisons were made with cylindrical projectiles. A 30 mm powder gun and two 150 kV and four 450 kV X-ray flashes were used in the impact tests. The numerical simulations were run with the Autodyn code in two steps. In the first, the surface loads were determined for different impact velocities under assumed condition of interface defeat. In the second, these surface loads were applied to the targets in order to obtain critical states of damage and failure related to the transition between interface defeat and penetration, and the corresponding critical velocities. In the impact tests, interface defeat occurred below a transition velocity, which was significantly lower for the conical than for the cylindrical projectiles. Above the transition velocity, the initial penetration of conical projectiles differed markedly from that usually observed for cylindrical projectiles. It occurred along a cone-shaped surface crack, qualitatively corresponding to surface failure observed in the simulations. The transition velocity for the conical projectile was found to be close to the critical velocity associated with this surface failure.
[114]
LundbergP, RenströmR, AnderssonO.2013.
Influence of length scale on the transition from interface defeat to penetration in unconfined ceramic targets
One observation from interface defeat experiments with thick ceramic targets is that confinement and prestress becomes less important if the test scale is reduced. A small unconfined target can show similar transition velocity as a large and heavily confined target. A possible explanation for this behavior is that the transition velocity depends on the formation and growth of macro cracks. Since the crack resistance increases with decreasing length scale, the extension of a crack in a small-scale target will need a stronger stress field, viz., a higher impact velocity, in order to propagate. An analytical model for the relation between projectile load, corresponding stress field, and the propagation of a cone-shaped crack under a state of interface defeat has been formulated. It is based on the assumption that the transition from interface defeat to penetration is controlled by the growth of the cone crack to a critical length. The model is compared to experimentally determined transition velocities for ceramic targets in different sizes, representing a linear scale factor of ten. The model shows that the projectile pressure at transition is proportional to one over the square root of the length scale. The experiments with small targets follow this relation as long as the projectile pressure at transition exceeds the bound of tensile failure of the ceramic. For larger targets, the transition will become independent of length scale and only depend on the tensile strength of the ceramic material. Both the experiments and the model indicate that scaling of interface defeat needs to be done with caution and that experimental data from one length scale needs to be examined carefully before extrapolating to another.
[115]
LundbergP, RenströmR, AnderssonO.2016.
Influence of confining prestress on the transition from interface defeat to penetration in ceramic targets
Replica scaled impact experiments with unconfined ceramic targets have shown that the transition velocity, i.e., the impact velocity at which interface defeat ceases and ceramic penetration occurs, decreased as the length scale increased. A possible explanation of how this scale effect is related to the formation of a cone crack in the ceramic has been presented by the authors in an earlier paper. Here, the influence of confinement and prestress on cone cracking and transition velocity is investigated. The hypothesis is that prestress will suppress the formation and growth of the cone crack by lowering the driving stress. A set of impact experiments has been performed in which the transition velocity for four different levels of prestress has been determined. The transition velocities as a function of the level of confining prestress is compared to an analytical model for the influence of prestress on the formation and extension of the cone crack in the ceramic material. Both experiments and model indicate that prestress has a strong influence on the transition from interface defeat to penetration, although the model underestimates the influence of prestress.
Adequate confinement of a ceramic block can lead to its impenetrability against long rod penetrators. New ballistic experiments (encapsulated rod experiments) enabling a pressurization of the front face of the ceramic block (dynamic confinement) have been performed and compared to results obtained from standard unconfined configurations (DOP tests). Impenetrability of the ceramic block is obtained with the encapsulated rod configuration. A modeling approach based on a description of the fragmentation process of the ceramic is proposed. In particular, effects of the void content of the fragmented ceramic on its shear resistance are taken into account. Comparisons between Eulerian computation and the experiments show that conditions for rod dwell are linked to immobilizing fragments of ceramic in front of the projectile.
[117]
McCauley JW, Wilantewicz TE.2009.
Using plasticity values determined from systematic hardness indentation measurements for predicting impact behavior in structural ceramics: A new, simple screening technique
. Army Research Lab Aberdeen Proving Ground Md Weapons and Materials Research Directorate.
[118]
McGlaun MJ, Thompson SL, Elrick MG.1990.
CTH: A three-dimensional shock wave physics code
. International Journal of Impact Engineering, 10: 351-360.
Several hot-pressed and sintered SiC variants were impacted with tungsten-carbide (WC) spheres at velocities up to 1700 m/s. Ballistic response curves of areal density penetrated as a function of impact velocity were generated to compare ceramics for ballistic applications. Observed response curve features are shown to be similar to those observed for metal impacts. Ballistics penetration models that captured these features for metal targets were utilized to analyze the ceramic data. Visual examination of damage type and extent suggested that cavity expansion expressions for target resistance might help to quantify the strength of fully confined, damaged, comminuted ceramics. The experimental results, visual observations, and preliminary analysis using a ballistics penetration model are presented.
[122]
Orphal DL.1997.
Phase three penetration
. International Journal of Impact Engineering, 20: 601-616.
A series of 27 terminal ballistics experiments were performed to measure the penetration of long tungsten rods against confined silicon carbide targets. Impact velocities ranged from 1.5 to about 4.6 km/s. The experiments were performed in the reverse ballistic mode using a two-stage light-gas gun. Penetrator diameter, D , was 0.762 mm (0.030 in). The length to diameter ratio for the penetrator was LD = 20 for nearly all the tests and never less than LD = 15. Primary instrumentation for these experiments was four independently timed, 450 kV flash X-rays. These X-rays provided four views of the penetrator-target interaction during the penetration event from which the following data were determined: p = penetration depth as a function of time , L r = remaining length of penetrator as a function of time, as well as target hole geometry, spatial distribution of the eroded rod material, etc. From these data u = dpdt = speed of penetration into the target, vc = d(L 61 Lr)dt = speed of “consumption” of the long rod, were obtained, as well as final penetration depth.
Forty terminal ballistics experiments were performed to measure the penetration of simple confined boron carbide targets by long tungsten rods. Impact velocities ranged from 1.5 to about 5.0km/s. The experiments were performed in the reverse ballistic mode using a two-stage light-gas gun. For tests with velocities 1.493≤v≤2.767km/s, the penetrator diameter was 1.02mm (0.040inch). For tests with impact velocities v≥2.778km/s the penetrator diameter was 0.762mm (0.030 inch). For tests in the velocity range 2.335 < v< 2.761 km/s both penetrator sizes were used. The length-to-diameter ratio for the penetrator was L/D = 20 for all but the three highest velocity tests; in these three tests L/D = 15. Primary instrumentation for these experiments was four independently timed, 450 kV flash X-rays. These X-rays provided four views of the penetrator-target interaction during the penetration event from which he following data were determined: p = penetration depth as a function of time, L
[126]
PartomY.2011.
Modeling interface defeat and dwell in long rod penetration into ceramic
. Shock Compression of Condensed Matter, 1426: 76-79.
When a long rod projectile hits a ceramic target, the projectile may sometimes dwell at the target boundary and flow radially. This dwell or interface defeat phenomenon has to do with the dynamic failure process of the ceramic target material. As ceramics are brittle materials, what is needed to model dwell, is a realistic model for dynamic failure of brittle materials. A "standard" such model is the so called JH model (which has several versions). According to JH the material accumulates damage as a function of the effective plastic strain, which is a ductile response feature. Brittle materials are not supposed to accumulate plastic strain before they're fully failed. To model dwell we therefore propose here a different failure model. We call it BSF (= Brittle Shear Failure), and it is based on the Overstress (or overload) principle. Our BSF model is rather simple, has a small number of adjustable parameters, and is readily calibrated. We implement the model in a hydro-code and demonstrate how it works for a typical example of dwell situation. In the example, a long steel rod impacts an AD995 alumina target with and without a copper buffer.
[127]
PickeringE, O'MastaM, WadleyH, DeshpandeV.2016.
Effect of confinement on the static and dynamic indentation response of model ceramic and cermet materials
. International Journal of Impact Engineering, 110: 123-137.
The effect of confinement on the localized impact response of ceramic and cermet tiles is investigated. A scoping study was first conducted using alumina and TiC/Ni cermet tiles encased in a metal matrix composite (MMC) and impacted by high velocity steel balls. The investigation revealed that increasing the MMC casing thickness reduced the cracking in the ceramic (alumina) tile but had a much smaller effect on the cermet tile. This motivated a detailed experimental investigation of the effect of lateral confining pressure on the static and dynamic indentation response of granite and Corian ; tiles that serve as model ceramic and cermet materials, respectively. Quasi-static indentation resulted in comminution under the indenter and the formation of radial cracks in the granite tiles, with the number of radial cracks decreasing with increasing confining pressure. By contrast, the plastic indentation and small shallow radial cracks observed in the Corian ; tiles were unaffected by variations in the confining pressure. The loading imposed by the high velocity impact of a steel ball resulted in conical and lateral cracks as well as radial cracks and comminution in the granite tiles. Intriguingly, while the cone and radial cracks were suppressed by confining pressure, the lateral cracks appeared only at the higher confining pressures. By contrast, the strain rate sensitivity of the yield strength of the Corian ; reduced the plastic indentation under dynamic loading, but this in turn promoted the formation of radial cracks which decreased in number with increasing confining pressure. No lateral cracks, conical cracks or comminution was observed in the Corian ; . The study shows that confining pressure has a less significant effect on cermets compared to ceramics. Since confinement systems add considerable weight to ceramic-based ballistic protection systems, this study suggests that the use of lightly confined cermets could reduce the overall weight of ballistic protection systems.
[128]
PickupI, BarkerA, ChenariR, JamesB, HohlerV, WeberK, et al.2002.
Aspects of geometry affecting the ballistic performance of ceramic targets
The Johnson–Holmquist model for simulating impact and penetration into ceramic and glass materials is commonly used in continuum hydrocodes. There are two forms of the Johnson–Holmquist ceramic model: JH-1 using a segmented linear approximation to the strength envelope with instantaneous failure; JH-2 using a smooth analytic approximation to the strength envelope with damage-induced strength reduction. Both these models are now implemented in the AUTODYN 03 software. The validation of the JH-1 model is presented in this paper by comparing numerical predictions with experimental data. The failure parameters of the JH-1 model are also validated in the current numerical approach. Good agreement between numerical predictions and experimental measurements is shown for the behavior of silicon carbide in various impact situations. Time histories of particle velocity in compressive and tensile spall plate impact, interface dwell in confined impact, and total penetration depth in oblique impact are used in the comparison. The JH-1 model in AUTODYN is shown to be a powerful numerical tool in the design and analysis of ceramic armor systems.
[131]
RabieiA.2014.
Materials with Improved Absorption of Collision Forces for Railroad Cars
The purpose of this project is to develop and perform an extensive experimental and numerical investigation and evaluate the dynamic properties of composite metal foams (CMF) at various impact speeds. This will include different speeds mimicking those of railroad car collisions, at different speeds, including high speeds. This investigation will provide the fundamental understanding of the behavior of CMF that is of critical importance before composite metal foams can be implemented effectively to increase protection against hazards and damage in potential railroad car collisions. The outcome of this work could lead to safer and more efficient railroad car safety structures along with less weight. The reduced weight of these components could also help to lower costs for production and operation and improve fuel economy.
[132]
RajendranA.1994.
Modeling the impact behavior of AD85 ceramic under multiaxial loading
. International Journal of Impact Engineering, 15: 749-768.
This report presents an advanced constitutive model to describe the complex behavior of ceramic materials under impact loading conditions. The governing equations utilize a set of microphysically based constitutive relationships to model deformation and damage processes in a ceramic. The total strain is decomposed into elastic, plastic, and microcracking components. The model parameters for AD85 ceramic were determined using the data from split Hopkinson bar (SHB) and bar-on-bar experiments under uniaxial stress state and plate impact experiment under uniaxial strain state. To further validate the generality of the model parameters, modeling of a diagnostic ballistic experiment in which a steel projectile impacted an AD85 ceramic front-faced thick aluminum plate was considered. In this experiment, stress histories were measured in the target by embedded manganin and carbon stress gauges. The results from the numerical simulations of the ballistic experiment using a shock wave propagation based finite element code successfully matched the measured stress history.
[133]
RajendranA, GroveD.1996. Determination of Rajendran-Grove ceramic constitutive model constants//Pro- ceedings of the Conference of the American Physical Society Topical Group on Shock Compression of Condensed Matter: AIP Publishing. 539-542.
Armour systems capable of defeating an incoming projectile on the surface of a ceramic target have been reported. This capability, called interface defeat or dwell, signifies that the projectile material is forced to flow radially on the surface of the target without penetrating significantly. Under such flow conditions, the hydrodynamic pressure is normally the most important part of the normal load on the target surface. Therefore, projectile properties such as yield strength and compressibility are commonly ignored or assumed to contribute only marginally. In order to investigate the effects of these properties, an analytical expression was derived for the normal load from a cylindrical metallic projectile impacting on a flat, rigid and friction-free surface, which includes the contributions from yield strength and compressibility in addition to that of inertia. At an impact velocity representative of today's ordinance velocities, the contributions to load intensity on the axis from yield strength and compressibility were found to be 15% and 3.4%, respectively, of that of inertia. The analytical results and Autodyn-2D numerical simulations show good agreement within a projectile radius from the axis.
[135]
RenströmR, LundbergP, LundbergB.2009.
Self-similar flow of a conical projectile on a flat target surface under conditions of dwell
. International Journal of Impact Engineering, 36: 352-362.
In order to investigate the state of stress in a target material under conditions of interface defeat or dwell it is necessary to determine the load intensity at the interface of the flowing projectile material and the target. Previous studies for a cylindrical projectile geometry at normal impact under stationary conditions show that the load can be considered to be composed of three components, viz., those of inertia, compressibility and yield strength of the projectile material. In order to determine the influence of projectile shape, a conical projectile in axi-symmetric impact on a ridged, friction-free surface is studied by use of an analytical model for self-similar flow and numerical Autodyn simulations. It is shown how the maximum load intensity, and the position of the maximum, depends on the apex angle. Both the self-similar model and the Autodyn simulations show that the contribution to the load intensity from compressibility is positive below and negative above apex angles 80 . The influence of yield strength on the load intensity depends only weakly on the apex angle and therefore corresponds to that for a cylindrical projectile.
[136]
RobersonC, HazellP.2003.
Resistance of different ceramic materials to penetration by a tungsten carbide cored projectile
The penetration of ceramic tiles by long rod penetrators is discussed in terms of the modified hydrodynamic theory of A. Tate which was developed for thick metallic targets. The resistance of the tile to penetration is determined with the threshold velocity for the penetration of a very large ceramic block. According to Tate's theory, the threshold impact velocity for a given projectile (with a well defined strength) depends only on the tile's resistance to penetration. We show here that using three different projectiles (copper, steel and tungsten) resulted in the same value for this parameter for thick alumina tiles. This fact strongly enhances the idea of applying Tate's theory to ceramics. A different set of experiments, with relatively thin tiles bonded to thick steel plates, was performed determining penetration depths of the long rods into the steel backing. These were compared with predictions based on Tate's model using the values for the penetration resistance, which were determined by thick tile experiments. The good agreement can be considered as a further confirmation of our main thesis. Resistance of penetration parameters ( R t) were determined for other ceramics (silicon carbide, titanium diboride, etc.) by measuring the penetration depths of the long rod projectile into the thick backing and using Tate's model with R t as a parameter.
[138]
SavioS, RamanjaneyuluK, MadhuV, BhatTB.2011.
An experimental study on ballistic performance of boron carbide tiles
. International Journal of Impact Engineering, 38: 535-341.
Boron carbide is an attractive candidate for use as armour material because of its lower density combined with high hardness. The ballistic performance of boron carbide tiles were evaluated using standard Depth of Penetration (DOP) test method against hard steel 7.6202mm armour piercing (AP) projectiles. The effect of variation in thickness of tile and the projectile velocity on the ballistic efficiency of the material was studied. It has been found that the differential efficiency factor (DEF) increases with increase in projectile velocity from 600 to 82002m/s. And an insignificant or marginal increase in efficiency was observed for increase in tile thickness from 5.202mm up to 7.302mm. The effect of the type of radial confinement on the residual DOP was also studied. It was found that the steel radial confinement produces lower residual DOP values compared to aluminium alloy and with no radial confinement. Results along with photographs have been presented.
[139]
SerjoueiA.2014.
Modelling and analysis of bi-layer ceramic-metal protective structures
. [PhD Thesis]. Singapore:Nanyang Technological University (NTU).
This paper investigates experimentally and numerically methods to enhance the ballistic performance of ceramic armor. Initially we demonstrate an experimental set-up to impose pre-stress to ceramic-metal bi-layer armor and study the depth of penetration to measure the ballistic efficiency as a function of pre-stress intensity validating our previous numerical studies on effect of pre-stress on the ballistic limit of ceramic armor (Int. Journal of Impact Engineering, 2015(84)159-170). Secondly, a module is designed and tested to achieve interface defeat in ceramic armor with multiple interface layers. Finally, influence of thickness of the steel cover plate (CP) on ballistic performance of SiC ceramic is studied through AUTODYN finite element simulations for normal and oblique (NATO 60 ) against long rod projectile (LRP) with a conical tip. The LRP and CP are modeled using smooth particle hydrodynamic (SPH) particles and rest of the component is modeled using Lagrangian domain. The numerical analyses of armor modules are compared via depth of penetration (DOP) and LRP residual length for varying cover plate thicknesses.
[141]
Simha C HM, BlessS, BedfordA.2002.
Computational modeling of the penetration response of a high-purity ceramic
. International Journal of Impact Engineering, 27: 65-86.
This paper describes computational modeling of the penetration response of a high-purity ceramic, namely the AD-99.5 alumina. This material is the most widely investigated ceramic, and extensive materials testing and ballistic data are available. The model development is based on constitutive relationships inferred from bar impact and plate impact data. The model is then incorporated into the EPIC Lagrangian finite element code. A novel element removal scheme for ceramics is presented, and the code is then used to investigate the penetration response of AD-99.5 alumina in the depth of penetration and semi-infinite configurations. The computations are found to be in excellent agreement with the experimental results. The interface defeat problem is also investigated numerically, and the results are used to suggest an explanation for interface defeat.
[142]
SternbergJ.1989.
Material Properties Determining the resistance of ceramics to high velocity penetration
The relationships between target material properties and the target strength term in the analytic representation of impact is examined. For ductile materials hardness is closely related to the magnitude of the strength term. It is shown that the key parameters correlating microhardness measurements in ceramics are similar to those for ductile materials. However, the strength terms that have been measured in ballistic tests are much lower than the values that would be predicted on the basis of the indentation measurements. It is found that the penetration resistance depends on the fracture toughness, where the ratio of the measured target strength term to the hardness increases with the fracture toughness of the target.
[143]
Steinhauser MO, GrassK.
2005. Failure and plasticity models of ceramics—A numerical study. The 11th Int Symposium on Plasticity and Current Applications, (PLASTICITY 2005), Kauai, Hawaii,
January2005. 03-08.
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StrassburgerE, BauerS, WeberS, GedonH.2016.
Flash X-ray cinematography analysis of dwell and penetration of small caliber projectiles with three types of SiC ceramics
In order to improve the performance of ceramic composite armor it is essential to know the mechanisms during each phase of the projectile–target interaction and their influence on the penetration resistance. Since the view on the crater zone and the tip of a projectile penetrating a ceramic is rapidly getting obscured by damaged material, a flash X-ray technique has to be applied in order to visualize projectile penetration. For this purpose, usually several flash X-ray tubes are arranged around the target and the radiographs are recorded on film. At EMI a flash X-ray imaging method has been developed, which provides up to eight flash radiographs in one experiment. A multi-anode 45065kV flash X-ray tube is utilized with this method. The radiation transmitted through the target is then detected on a fluorescent screen. The fluorescent screen converts the radiograph into an image in the visible wavelength range, which is photographed by means of a high-speed camera. This technique has been applied to visualize and analyze the penetration of 7.6265mm AP projectiles into three different types of SiC ceramics. Two commercial SiC grades and MICASIC (Metal Infiltrated Carbon derived SiC), a C-SiSiC ceramic developed by DLR, have been studied. The influences, not only of the ceramic but also the backing material, on dwell time and projectile erosion have been studied. Penetration curves have been determined and their relevance to the ballistic resistance is discussed.
[145]
SubramanianR, Bless SJ.1995.
Penetration of semi-infinite AD995 alumina targets by tungsten long rod penetrators
. International Journal of Impact Engineering, 17: 807-816.
In tests in which the ratio of target diameter to penetrator diameter was reduced to 15, R t , dropped by 30% to 50%. When a steel coverplate was used, total interface defeat occurred at 1.5 km/s.
[146]
TateA.1967.
A theory for the deceleration of long rods after impact
. Journal of the Mechanics and Physics of Solids, 15: 387-399.
A modified hydrodynamic theory which takes some account of strength effects is used to predict the deceleration of a long rod after striking a target. The results are then compared with experimental data from X-ray observations.
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Templeton DW, Holmquist TJ, LeavyB.2002.
Computational simulations of interface defeat//The 2nd International Conference on Structural Stability and Dynamics Singapore
Light metal sandwich panel structures with cellular cores have attracted interest for multifunctional applications which exploit their high bend strength and impact energy absorption. This concept has been explored here using a model 6061-T6 aluminum alloy system fabricated by friction stir weld joining extruded sandwich panels with a triangular corrugated core. Micro-hardness and miniature tensile coupon testing revealed that friction stir welding reduced the strength and ductility in the welds and a narrow heat affected zone on either side of the weld by approximately 30%. Square, edge clamped sandwich panels and solid plates of equal mass per unit area were subjected to localized impulsive loading by the impact of explosively accelerated, water saturated, sand shells. The hydrodynamic load and impulse applied by the sand were gradually increased by reducing the stand-off distance between the test charge and panel surfaces. The sandwich panels suffered global bending and stretching, and localized core crushing. As the pressure applied by the sand increased, face sheet fracture by a combination of tensile stretching and shear-off occurred first at the two clamped edges of the panels that were parallel with the corrugation and weld direction. The plane of these fractures always lay within the heat affected zone of the longitudinal welds. For the most intensively loaded panels additional cracks occurred at the other clamped boundaries and in the center of the panel. To investigate the dynamic deformation and fracture processes, a particle-based method has been used to simulate the impulsive loading of the panels. This has been combined with a finite element analysis utilizing a modified Johnson ook constitutive relation and a Cockcroft atham fracture criterion that accounted for local variation in material properties. The fully coupled simulation approach enabled the relationships between the soil-explosive test charge design, panel geometry, spatially varying material properties and the panel's deformation and dynamic failure responses to be explored. This comprehensive study reveals the existence of a strong instability in the loading that results from changes in sand particle reflection during dynamic evolution of the panel's surface topology. Significant fluid tructure interaction effects are also discovered at the sample sides and corners due to changes of the sand reflection angle by the edge clamping system.
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Walker JD, Anderson Jr CE.1991.
The Wilkins' computational ceramic model for CTH
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WesterlingL, LundbergP, LundbergB.2001.
Tungsten long-rod penetration into confined cylinders of boron carbide at and above ordnance velocities
. International Journal of Impact Engineering, 25: 703-714.
The purpose was to investigate the influence of impact velocity and confinement on the resistance of boron carbide targets to the penetration of tungsten long-rod projectiles. Experimental tests with impact velocities from 1400 to 2600 m/s were performed using a two-stage light-gas gun and a reverse impact technique. The targets consisted of boron carbide cylinders confined by steel tubes of various thicknesses. Simulations were carried out using the AUTODYN-2D code and Johnson olmquist's constitutive model with and without damage evolution. The experimental results show that the penetration process had different character in three different regions. At low-impact velocities, no significant penetration occurred. At high-impact velocities, the relation between penetration velocity and impact velocity was approximately linear, and the penetration was steady and symmetrical. In between, there was a narrow transition region of impact velocities with intermittent and strongly variable penetration velocity. In the lower part of this region, extended lateral flow of the projectile took place on the surface of the target. The influence of confinement on penetration velocity was found to be small, especially at high-impact velocities. The simulated results for penetration velocity versus impact velocity agreed fairly well with the experimental results provided damage evolution was suspended below the transition region.
An analytical model for dwell and interface defeat
6
2005
... 半个世纪以来,陶瓷界面击溃效应的研究工作从最初的获得界面击溃效应(Wilkins 1963;Hauver et al. 1993, 1994, 2005; Rosenberg & Tsaliah 1990;Anderson & Walker 1991; Anderson & Morris 1992;Anderson & Royal-Timmons 1997; Anderson et al. 1993a, 1995, 1999, 2005; Den Reijer 1991; Bless et al. 1992; Lundberg et al. 1996; Westerling et al. 2001)转为研究界面击溃过程中弹、靶动态力学响应(Lundberg 2004, 2007;Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016; LaSalvia & McCauley 2010; LaSalvia 2002a, 2002b, 2005a, 2005b; LaSalvia et al. 2001, 2005, 2007, 2009, 2010a, 2010b; LaSalvia & Normandia 2002; Deshpande & Evans 2008; Deshpande et al. 2011; Anderson & Orphal 2003;Pickering et al. 2016), 以明确界面击溃效应作用机理,为界面击溃效应在工程上的应用奠定基础. 在实验方法和技术方面,主要围绕陶瓷材料、弹体形状、尺寸效应等影响因素开展撞击实验,获得不同弹靶条件下的界面击溃效应(Lundberg 2004, 2007; Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016). 一方面国内外学者加强了实验观测技术,宏观观测界面击溃过程并对回收后的靶体材料破坏情况进行细观观测,以了解界面击溃效应对弹靶破坏的作用(Anderson et al. 2005, 2008, 2009, 2011a, 2011b; Anderson 2009, 2010; Anderson & Gooch 2011; Lundberg et al. 2000, 2001; Thoma et al. 2007; Strassburgeret al. 2016; Behner et al. 2008, 2016). 另一方面,通过不同影响因素下的界面击溃效应实验,获得界面击溃/侵彻转变速度等参数,以深入探索界面击溃/侵彻转变过程的作用机理(Lundberg 2004; Lundberget al. 2005, 2006). 在界面击溃效应理论研究方面,陶瓷的锥裂纹(Lundberg 2007; Lundberg et al. 2013, 2016)和微观翼型裂纹理论 (LaSalvia 2002a, 2002b, 2005a, 2005b;LaSalvia et al. 2001, 2005, 2007, 2010a, 2010b; LaSalvia & Normandia 2002;LaSalvia & McCauley 2010)是通过靶体的破坏解释界面击溃效应的重要模型.弹体在界面击溃效应中的参数变化主要依靠修正的AT模型获得(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017).数值模拟作为辅助实验和理论研究界面击溃效应的手段,其关键问题是确定可靠的陶瓷本构模型.学者们采用不同的陶瓷本构模型及参数对影响界面击溃效应的因素进行了数值模拟(Anderson 2006; Anderson et al. 1993b;Holmquist & Johnson 2002a, 2002b, 2003, 2005a, 2005b, 2008, 2011; Holmquist et al. 2001, 2008; Quan et al. 2006; Fountzoulas et al. 2009; Fountzoulas & LaSalvia 2013; Chi et al. 2013, 2015; Serjouei 2014; Yuan et al. 2016; 谈梦婷等 2016). 此外, 从陶瓷的微观结构入手,对界面击溃效应进行数值模拟研究是当今的一大热点. ...
... ). 一方面国内外学者加强了实验观测技术,宏观观测界面击溃过程并对回收后的靶体材料破坏情况进行细观观测,以了解界面击溃效应对弹靶破坏的作用(Anderson et al. 2005, 2008, 2009, 2011a, 2011b; Anderson 2009, 2010; Anderson & Gooch 2011; Lundberg et al. 2000, 2001; Thoma et al. 2007; Strassburgeret al. 2016; Behner et al. 2008, 2016). 另一方面,通过不同影响因素下的界面击溃效应实验,获得界面击溃/侵彻转变速度等参数,以深入探索界面击溃/侵彻转变过程的作用机理(Lundberg 2004; Lundberget al. 2005, 2006). 在界面击溃效应理论研究方面,陶瓷的锥裂纹(Lundberg 2007; Lundberg et al. 2013, 2016)和微观翼型裂纹理论 (LaSalvia 2002a, 2002b, 2005a, 2005b;LaSalvia et al. 2001, 2005, 2007, 2010a, 2010b; LaSalvia & Normandia 2002;LaSalvia & McCauley 2010)是通过靶体的破坏解释界面击溃效应的重要模型.弹体在界面击溃效应中的参数变化主要依靠修正的AT模型获得(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017).数值模拟作为辅助实验和理论研究界面击溃效应的手段,其关键问题是确定可靠的陶瓷本构模型.学者们采用不同的陶瓷本构模型及参数对影响界面击溃效应的因素进行了数值模拟(Anderson 2006; Anderson et al. 1993b;Holmquist & Johnson 2002a, 2002b, 2003, 2005a, 2005b, 2008, 2011; Holmquist et al. 2001, 2008; Quan et al. 2006; Fountzoulas et al. 2009; Fountzoulas & LaSalvia 2013; Chi et al. 2013, 2015; Serjouei 2014; Yuan et al. 2016; 谈梦婷等 2016). 此外, 从陶瓷的微观结构入手,对界面击溃效应进行数值模拟研究是当今的一大热点. ...
... )是通过靶体的破坏解释界面击溃效应的重要模型.弹体在界面击溃效应中的参数变化主要依靠修正的AT模型获得(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017).数值模拟作为辅助实验和理论研究界面击溃效应的手段,其关键问题是确定可靠的陶瓷本构模型.学者们采用不同的陶瓷本构模型及参数对影响界面击溃效应的因素进行了数值模拟(Anderson 2006; Anderson et al. 1993b;Holmquist & Johnson 2002a, 2002b, 2003, 2005a, 2005b, 2008, 2011; Holmquist et al. 2001, 2008; Quan et al. 2006; Fountzoulas et al. 2009; Fountzoulas & LaSalvia 2013; Chi et al. 2013, 2015; Serjouei 2014; Yuan et al. 2016; 谈梦婷等 2016). 此外, 从陶瓷的微观结构入手,对界面击溃效应进行数值模拟研究是当今的一大热点. ...
... 为了清晰地观测侵彻过程中弹体头部和靶表面破坏情况,学者们采用了高速录像、X光摄影等设备和技术观测了陶瓷靶的界面击溃效应作用过程.Anderson等(2005, 2008, 2011a),采用X光摄影技术对不同角度斜置靶体撞击弹体过程进行了研究.Lundberg等(2000)和Westerling等(2001)利用X光摄影技术观测了直径为2mm、长径比分别为40和75的钨合金射弹撞击SiC等陶瓷的界面击溃作用过程,获取了不同陶瓷的界面击溃/侵彻转变速度. 结果表明,陶瓷材料强度及韧性均对界面击溃过程有显著的影响.对陶瓷材料界面击溃现象研究较多的另一团队是来自德国的Ernst-Mach-Institut(EMI)的研究小组(Thoma et al. 2007, Strassburger et al. 2016,Behner et al. 2016), 他们利用先进的多通道X光摄影设备研究了7.62mmAPM2 子弹撞击陶瓷材料时的界面击溃效应(如图5所示),研究了背板材料的影响规律、界面驻留时间以及弹体侵蚀现象,并进行了相关的数值模拟. 实验观测结果表明背板材料强度越大,界面驻留持续时间越长,但该部分工作未能将侵彻速度变化与陶瓷材料力学性能相关联. ...
Simulation of ballistic impact of a tungsten carbide sphere on a confined silicon carbide target//Proceedings of the 23rd International Symosium on Balllistics, Tarragona, Spain
2
2009
... 半个世纪以来,陶瓷界面击溃效应的研究工作从最初的获得界面击溃效应(Wilkins 1963;Hauver et al. 1993, 1994, 2005; Rosenberg & Tsaliah 1990;Anderson & Walker 1991; Anderson & Morris 1992;Anderson & Royal-Timmons 1997; Anderson et al. 1993a, 1995, 1999, 2005; Den Reijer 1991; Bless et al. 1992; Lundberg et al. 1996; Westerling et al. 2001)转为研究界面击溃过程中弹、靶动态力学响应(Lundberg 2004, 2007;Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016; LaSalvia & McCauley 2010; LaSalvia 2002a, 2002b, 2005a, 2005b; LaSalvia et al. 2001, 2005, 2007, 2009, 2010a, 2010b; LaSalvia & Normandia 2002; Deshpande & Evans 2008; Deshpande et al. 2011; Anderson & Orphal 2003;Pickering et al. 2016), 以明确界面击溃效应作用机理,为界面击溃效应在工程上的应用奠定基础. 在实验方法和技术方面,主要围绕陶瓷材料、弹体形状、尺寸效应等影响因素开展撞击实验,获得不同弹靶条件下的界面击溃效应(Lundberg 2004, 2007; Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016). 一方面国内外学者加强了实验观测技术,宏观观测界面击溃过程并对回收后的靶体材料破坏情况进行细观观测,以了解界面击溃效应对弹靶破坏的作用(Anderson et al. 2005, 2008, 2009, 2011a, 2011b; Anderson 2009, 2010; Anderson & Gooch 2011; Lundberg et al. 2000, 2001; Thoma et al. 2007; Strassburgeret al. 2016; Behner et al. 2008, 2016). 另一方面,通过不同影响因素下的界面击溃效应实验,获得界面击溃/侵彻转变速度等参数,以深入探索界面击溃/侵彻转变过程的作用机理(Lundberg 2004; Lundberget al. 2005, 2006). 在界面击溃效应理论研究方面,陶瓷的锥裂纹(Lundberg 2007; Lundberg et al. 2013, 2016)和微观翼型裂纹理论 (LaSalvia 2002a, 2002b, 2005a, 2005b;LaSalvia et al. 2001, 2005, 2007, 2010a, 2010b; LaSalvia & Normandia 2002;LaSalvia & McCauley 2010)是通过靶体的破坏解释界面击溃效应的重要模型.弹体在界面击溃效应中的参数变化主要依靠修正的AT模型获得(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017).数值模拟作为辅助实验和理论研究界面击溃效应的手段,其关键问题是确定可靠的陶瓷本构模型.学者们采用不同的陶瓷本构模型及参数对影响界面击溃效应的因素进行了数值模拟(Anderson 2006; Anderson et al. 1993b;Holmquist & Johnson 2002a, 2002b, 2003, 2005a, 2005b, 2008, 2011; Holmquist et al. 2001, 2008; Quan et al. 2006; Fountzoulas et al. 2009; Fountzoulas & LaSalvia 2013; Chi et al. 2013, 2015; Serjouei 2014; Yuan et al. 2016; 谈梦婷等 2016). 此外, 从陶瓷的微观结构入手,对界面击溃效应进行数值模拟研究是当今的一大热点. ...
Numerical simulation of ceramic composite armor subjected to ballistic impact
2010
A physically-based model for the effect of microstructure and mechanical properties on ballistic performance//26th Annual Conference on Composites, Advanced Ceramics, Materials,
7
2002
... 半个世纪以来,陶瓷界面击溃效应的研究工作从最初的获得界面击溃效应(Wilkins 1963;Hauver et al. 1993, 1994, 2005; Rosenberg & Tsaliah 1990;Anderson & Walker 1991; Anderson & Morris 1992;Anderson & Royal-Timmons 1997; Anderson et al. 1993a, 1995, 1999, 2005; Den Reijer 1991; Bless et al. 1992; Lundberg et al. 1996; Westerling et al. 2001)转为研究界面击溃过程中弹、靶动态力学响应(Lundberg 2004, 2007;Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016; LaSalvia & McCauley 2010; LaSalvia 2002a, 2002b, 2005a, 2005b; LaSalvia et al. 2001, 2005, 2007, 2009, 2010a, 2010b; LaSalvia & Normandia 2002; Deshpande & Evans 2008; Deshpande et al. 2011; Anderson & Orphal 2003;Pickering et al. 2016), 以明确界面击溃效应作用机理,为界面击溃效应在工程上的应用奠定基础. 在实验方法和技术方面,主要围绕陶瓷材料、弹体形状、尺寸效应等影响因素开展撞击实验,获得不同弹靶条件下的界面击溃效应(Lundberg 2004, 2007; Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016). 一方面国内外学者加强了实验观测技术,宏观观测界面击溃过程并对回收后的靶体材料破坏情况进行细观观测,以了解界面击溃效应对弹靶破坏的作用(Anderson et al. 2005, 2008, 2009, 2011a, 2011b; Anderson 2009, 2010; Anderson & Gooch 2011; Lundberg et al. 2000, 2001; Thoma et al. 2007; Strassburgeret al. 2016; Behner et al. 2008, 2016). 另一方面,通过不同影响因素下的界面击溃效应实验,获得界面击溃/侵彻转变速度等参数,以深入探索界面击溃/侵彻转变过程的作用机理(Lundberg 2004; Lundberget al. 2005, 2006). 在界面击溃效应理论研究方面,陶瓷的锥裂纹(Lundberg 2007; Lundberg et al. 2013, 2016)和微观翼型裂纹理论 (LaSalvia 2002a, 2002b, 2005a, 2005b;LaSalvia et al. 2001, 2005, 2007, 2010a, 2010b; LaSalvia & Normandia 2002;LaSalvia & McCauley 2010)是通过靶体的破坏解释界面击溃效应的重要模型.弹体在界面击溃效应中的参数变化主要依靠修正的AT模型获得(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017).数值模拟作为辅助实验和理论研究界面击溃效应的手段,其关键问题是确定可靠的陶瓷本构模型.学者们采用不同的陶瓷本构模型及参数对影响界面击溃效应的因素进行了数值模拟(Anderson 2006; Anderson et al. 1993b;Holmquist & Johnson 2002a, 2002b, 2003, 2005a, 2005b, 2008, 2011; Holmquist et al. 2001, 2008; Quan et al. 2006; Fountzoulas et al. 2009; Fountzoulas & LaSalvia 2013; Chi et al. 2013, 2015; Serjouei 2014; Yuan et al. 2016; 谈梦婷等 2016). 此外, 从陶瓷的微观结构入手,对界面击溃效应进行数值模拟研究是当今的一大热点. ...
... , 2002b, 2005a, 2005b; LaSalvia et al. 2001, 2005, 2007, 2009, 2010a, 2010b; LaSalvia & Normandia 2002; Deshpande & Evans 2008; Deshpande et al. 2011; Anderson & Orphal 2003;Pickering et al. 2016), 以明确界面击溃效应作用机理,为界面击溃效应在工程上的应用奠定基础. 在实验方法和技术方面,主要围绕陶瓷材料、弹体形状、尺寸效应等影响因素开展撞击实验,获得不同弹靶条件下的界面击溃效应(Lundberg 2004, 2007; Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016). 一方面国内外学者加强了实验观测技术,宏观观测界面击溃过程并对回收后的靶体材料破坏情况进行细观观测,以了解界面击溃效应对弹靶破坏的作用(Anderson et al. 2005, 2008, 2009, 2011a, 2011b; Anderson 2009, 2010; Anderson & Gooch 2011; Lundberg et al. 2000, 2001; Thoma et al. 2007; Strassburgeret al. 2016; Behner et al. 2008, 2016). 另一方面,通过不同影响因素下的界面击溃效应实验,获得界面击溃/侵彻转变速度等参数,以深入探索界面击溃/侵彻转变过程的作用机理(Lundberg 2004; Lundberget al. 2005, 2006). 在界面击溃效应理论研究方面,陶瓷的锥裂纹(Lundberg 2007; Lundberg et al. 2013, 2016)和微观翼型裂纹理论 (LaSalvia 2002a, 2002b, 2005a, 2005b;LaSalvia et al. 2001, 2005, 2007, 2010a, 2010b; LaSalvia & Normandia 2002;LaSalvia & McCauley 2010)是通过靶体的破坏解释界面击溃效应的重要模型.弹体在界面击溃效应中的参数变化主要依靠修正的AT模型获得(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017).数值模拟作为辅助实验和理论研究界面击溃效应的手段,其关键问题是确定可靠的陶瓷本构模型.学者们采用不同的陶瓷本构模型及参数对影响界面击溃效应的因素进行了数值模拟(Anderson 2006; Anderson et al. 1993b;Holmquist & Johnson 2002a, 2002b, 2003, 2005a, 2005b, 2008, 2011; Holmquist et al. 2001, 2008; Quan et al. 2006; Fountzoulas et al. 2009; Fountzoulas & LaSalvia 2013; Chi et al. 2013, 2015; Serjouei 2014; Yuan et al. 2016; 谈梦婷等 2016). 此外, 从陶瓷的微观结构入手,对界面击溃效应进行数值模拟研究是当今的一大热点. ...
... )和微观翼型裂纹理论 (LaSalvia 2002a, 2002b, 2005a, 2005b;LaSalvia et al. 2001, 2005, 2007, 2010a, 2010b; LaSalvia & Normandia 2002;LaSalvia & McCauley 2010)是通过靶体的破坏解释界面击溃效应的重要模型.弹体在界面击溃效应中的参数变化主要依靠修正的AT模型获得(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017).数值模拟作为辅助实验和理论研究界面击溃效应的手段,其关键问题是确定可靠的陶瓷本构模型.学者们采用不同的陶瓷本构模型及参数对影响界面击溃效应的因素进行了数值模拟(Anderson 2006; Anderson et al. 1993b;Holmquist & Johnson 2002a, 2002b, 2003, 2005a, 2005b, 2008, 2011; Holmquist et al. 2001, 2008; Quan et al. 2006; Fountzoulas et al. 2009; Fountzoulas & LaSalvia 2013; Chi et al. 2013, 2015; Serjouei 2014; Yuan et al. 2016; 谈梦婷等 2016). 此外, 从陶瓷的微观结构入手,对界面击溃效应进行数值模拟研究是当今的一大热点. ...
... Hauver等(1994)通过大量实验发现TiB$_{2}$在界面击溃过程中,撞击区域的正下方出现大片粉碎区域, 另有锥形裂纹从陶瓷表面开始扩展,如图11所示. 目前关于陶瓷界面击溃理论的研究工作可分为三类:一是从宏观陶瓷锥入手研究界面击溃/侵彻转变速度与弹靶表面压力的关系(Lundberg 2004, 2007; Lundberg et al. 2000, 2013, 2016; Renström et al. 2004, 2009; Andersson et al. 2007)以及撞击表面下锥裂纹的形成和扩展对界面击溃的影响;二是基于微观翼型裂纹扩展模式研究轴向应力与界面击溃/侵彻转变速度的关系(LaSalvia 2002a, 2002b, 2005a, 2005b; LaSalvia et al. 2001, 2010b; LaSalvia & McCauley 2010),结合翼型微裂纹与塑性区域的产生对界面击溃现象进行研究;三是基于AT模型研究不同头部形状长杆弹在界面击溃条件下的动能变化(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017). ...
Recent progress on the influence of microstructure and mechanical properties on ballistic performance
1
2002
... 半个世纪以来,陶瓷界面击溃效应的研究工作从最初的获得界面击溃效应(Wilkins 1963;Hauver et al. 1993, 1994, 2005; Rosenberg & Tsaliah 1990;Anderson & Walker 1991; Anderson & Morris 1992;Anderson & Royal-Timmons 1997; Anderson et al. 1993a, 1995, 1999, 2005; Den Reijer 1991; Bless et al. 1992; Lundberg et al. 1996; Westerling et al. 2001)转为研究界面击溃过程中弹、靶动态力学响应(Lundberg 2004, 2007;Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016; LaSalvia & McCauley 2010; LaSalvia 2002a, 2002b, 2005a, 2005b; LaSalvia et al. 2001, 2005, 2007, 2009, 2010a, 2010b; LaSalvia & Normandia 2002; Deshpande & Evans 2008; Deshpande et al. 2011; Anderson & Orphal 2003;Pickering et al. 2016), 以明确界面击溃效应作用机理,为界面击溃效应在工程上的应用奠定基础. 在实验方法和技术方面,主要围绕陶瓷材料、弹体形状、尺寸效应等影响因素开展撞击实验,获得不同弹靶条件下的界面击溃效应(Lundberg 2004, 2007; Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016). 一方面国内外学者加强了实验观测技术,宏观观测界面击溃过程并对回收后的靶体材料破坏情况进行细观观测,以了解界面击溃效应对弹靶破坏的作用(Anderson et al. 2005, 2008, 2009, 2011a, 2011b; Anderson 2009, 2010; Anderson & Gooch 2011; Lundberg et al. 2000, 2001; Thoma et al. 2007; Strassburgeret al. 2016; Behner et al. 2008, 2016). 另一方面,通过不同影响因素下的界面击溃效应实验,获得界面击溃/侵彻转变速度等参数,以深入探索界面击溃/侵彻转变过程的作用机理(Lundberg 2004; Lundberget al. 2005, 2006). 在界面击溃效应理论研究方面,陶瓷的锥裂纹(Lundberg 2007; Lundberg et al. 2013, 2016)和微观翼型裂纹理论 (LaSalvia 2002a, 2002b, 2005a, 2005b;LaSalvia et al. 2001, 2005, 2007, 2010a, 2010b; LaSalvia & Normandia 2002;LaSalvia & McCauley 2010)是通过靶体的破坏解释界面击溃效应的重要模型.弹体在界面击溃效应中的参数变化主要依靠修正的AT模型获得(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017).数值模拟作为辅助实验和理论研究界面击溃效应的手段,其关键问题是确定可靠的陶瓷本构模型.学者们采用不同的陶瓷本构模型及参数对影响界面击溃效应的因素进行了数值模拟(Anderson 2006; Anderson et al. 1993b;Holmquist & Johnson 2002a, 2002b, 2003, 2005a, 2005b, 2008, 2011; Holmquist et al. 2001, 2008; Quan et al. 2006; Fountzoulas et al. 2009; Fountzoulas & LaSalvia 2013; Chi et al. 2013, 2015; Serjouei 2014; Yuan et al. 2016; 谈梦婷等 2016). 此外, 从陶瓷的微观结构入手,对界面击溃效应进行数值模拟研究是当今的一大热点. ...
Effect of ceramic thickness on the dwell/penetration transition phenomenon
3
2005
... 半个世纪以来,陶瓷界面击溃效应的研究工作从最初的获得界面击溃效应(Wilkins 1963;Hauver et al. 1993, 1994, 2005; Rosenberg & Tsaliah 1990;Anderson & Walker 1991; Anderson & Morris 1992;Anderson & Royal-Timmons 1997; Anderson et al. 1993a, 1995, 1999, 2005; Den Reijer 1991; Bless et al. 1992; Lundberg et al. 1996; Westerling et al. 2001)转为研究界面击溃过程中弹、靶动态力学响应(Lundberg 2004, 2007;Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016; LaSalvia & McCauley 2010; LaSalvia 2002a, 2002b, 2005a, 2005b; LaSalvia et al. 2001, 2005, 2007, 2009, 2010a, 2010b; LaSalvia & Normandia 2002; Deshpande & Evans 2008; Deshpande et al. 2011; Anderson & Orphal 2003;Pickering et al. 2016), 以明确界面击溃效应作用机理,为界面击溃效应在工程上的应用奠定基础. 在实验方法和技术方面,主要围绕陶瓷材料、弹体形状、尺寸效应等影响因素开展撞击实验,获得不同弹靶条件下的界面击溃效应(Lundberg 2004, 2007; Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016). 一方面国内外学者加强了实验观测技术,宏观观测界面击溃过程并对回收后的靶体材料破坏情况进行细观观测,以了解界面击溃效应对弹靶破坏的作用(Anderson et al. 2005, 2008, 2009, 2011a, 2011b; Anderson 2009, 2010; Anderson & Gooch 2011; Lundberg et al. 2000, 2001; Thoma et al. 2007; Strassburgeret al. 2016; Behner et al. 2008, 2016). 另一方面,通过不同影响因素下的界面击溃效应实验,获得界面击溃/侵彻转变速度等参数,以深入探索界面击溃/侵彻转变过程的作用机理(Lundberg 2004; Lundberget al. 2005, 2006). 在界面击溃效应理论研究方面,陶瓷的锥裂纹(Lundberg 2007; Lundberg et al. 2013, 2016)和微观翼型裂纹理论 (LaSalvia 2002a, 2002b, 2005a, 2005b;LaSalvia et al. 2001, 2005, 2007, 2010a, 2010b; LaSalvia & Normandia 2002;LaSalvia & McCauley 2010)是通过靶体的破坏解释界面击溃效应的重要模型.弹体在界面击溃效应中的参数变化主要依靠修正的AT模型获得(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017).数值模拟作为辅助实验和理论研究界面击溃效应的手段,其关键问题是确定可靠的陶瓷本构模型.学者们采用不同的陶瓷本构模型及参数对影响界面击溃效应的因素进行了数值模拟(Anderson 2006; Anderson et al. 1993b;Holmquist & Johnson 2002a, 2002b, 2003, 2005a, 2005b, 2008, 2011; Holmquist et al. 2001, 2008; Quan et al. 2006; Fountzoulas et al. 2009; Fountzoulas & LaSalvia 2013; Chi et al. 2013, 2015; Serjouei 2014; Yuan et al. 2016; 谈梦婷等 2016). 此外, 从陶瓷的微观结构入手,对界面击溃效应进行数值模拟研究是当今的一大热点. ...
... , 2005b;LaSalvia et al. 2001, 2005, 2007, 2010a, 2010b; LaSalvia & Normandia 2002;LaSalvia & McCauley 2010)是通过靶体的破坏解释界面击溃效应的重要模型.弹体在界面击溃效应中的参数变化主要依靠修正的AT模型获得(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017).数值模拟作为辅助实验和理论研究界面击溃效应的手段,其关键问题是确定可靠的陶瓷本构模型.学者们采用不同的陶瓷本构模型及参数对影响界面击溃效应的因素进行了数值模拟(Anderson 2006; Anderson et al. 1993b;Holmquist & Johnson 2002a, 2002b, 2003, 2005a, 2005b, 2008, 2011; Holmquist et al. 2001, 2008; Quan et al. 2006; Fountzoulas et al. 2009; Fountzoulas & LaSalvia 2013; Chi et al. 2013, 2015; Serjouei 2014; Yuan et al. 2016; 谈梦婷等 2016). 此外, 从陶瓷的微观结构入手,对界面击溃效应进行数值模拟研究是当今的一大热点. ...
... Hauver等(1994)通过大量实验发现TiB$_{2}$在界面击溃过程中,撞击区域的正下方出现大片粉碎区域, 另有锥形裂纹从陶瓷表面开始扩展,如图11所示. 目前关于陶瓷界面击溃理论的研究工作可分为三类:一是从宏观陶瓷锥入手研究界面击溃/侵彻转变速度与弹靶表面压力的关系(Lundberg 2004, 2007; Lundberg et al. 2000, 2013, 2016; Renström et al. 2004, 2009; Andersson et al. 2007)以及撞击表面下锥裂纹的形成和扩展对界面击溃的影响;二是基于微观翼型裂纹扩展模式研究轴向应力与界面击溃/侵彻转变速度的关系(LaSalvia 2002a, 2002b, 2005a, 2005b; LaSalvia et al. 2001, 2010b; LaSalvia & McCauley 2010),结合翼型微裂纹与塑性区域的产生对界面击溃现象进行研究;三是基于AT模型研究不同头部形状长杆弹在界面击溃条件下的动能变化(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017). ...
A predictive model for the dwell/penetration transition phenomenon//Proceeding of the 22th International Symposium on
3
2005
... 半个世纪以来,陶瓷界面击溃效应的研究工作从最初的获得界面击溃效应(Wilkins 1963;Hauver et al. 1993, 1994, 2005; Rosenberg & Tsaliah 1990;Anderson & Walker 1991; Anderson & Morris 1992;Anderson & Royal-Timmons 1997; Anderson et al. 1993a, 1995, 1999, 2005; Den Reijer 1991; Bless et al. 1992; Lundberg et al. 1996; Westerling et al. 2001)转为研究界面击溃过程中弹、靶动态力学响应(Lundberg 2004, 2007;Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016; LaSalvia & McCauley 2010; LaSalvia 2002a, 2002b, 2005a, 2005b; LaSalvia et al. 2001, 2005, 2007, 2009, 2010a, 2010b; LaSalvia & Normandia 2002; Deshpande & Evans 2008; Deshpande et al. 2011; Anderson & Orphal 2003;Pickering et al. 2016), 以明确界面击溃效应作用机理,为界面击溃效应在工程上的应用奠定基础. 在实验方法和技术方面,主要围绕陶瓷材料、弹体形状、尺寸效应等影响因素开展撞击实验,获得不同弹靶条件下的界面击溃效应(Lundberg 2004, 2007; Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016). 一方面国内外学者加强了实验观测技术,宏观观测界面击溃过程并对回收后的靶体材料破坏情况进行细观观测,以了解界面击溃效应对弹靶破坏的作用(Anderson et al. 2005, 2008, 2009, 2011a, 2011b; Anderson 2009, 2010; Anderson & Gooch 2011; Lundberg et al. 2000, 2001; Thoma et al. 2007; Strassburgeret al. 2016; Behner et al. 2008, 2016). 另一方面,通过不同影响因素下的界面击溃效应实验,获得界面击溃/侵彻转变速度等参数,以深入探索界面击溃/侵彻转变过程的作用机理(Lundberg 2004; Lundberget al. 2005, 2006). 在界面击溃效应理论研究方面,陶瓷的锥裂纹(Lundberg 2007; Lundberg et al. 2013, 2016)和微观翼型裂纹理论 (LaSalvia 2002a, 2002b, 2005a, 2005b;LaSalvia et al. 2001, 2005, 2007, 2010a, 2010b; LaSalvia & Normandia 2002;LaSalvia & McCauley 2010)是通过靶体的破坏解释界面击溃效应的重要模型.弹体在界面击溃效应中的参数变化主要依靠修正的AT模型获得(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017).数值模拟作为辅助实验和理论研究界面击溃效应的手段,其关键问题是确定可靠的陶瓷本构模型.学者们采用不同的陶瓷本构模型及参数对影响界面击溃效应的因素进行了数值模拟(Anderson 2006; Anderson et al. 1993b;Holmquist & Johnson 2002a, 2002b, 2003, 2005a, 2005b, 2008, 2011; Holmquist et al. 2001, 2008; Quan et al. 2006; Fountzoulas et al. 2009; Fountzoulas & LaSalvia 2013; Chi et al. 2013, 2015; Serjouei 2014; Yuan et al. 2016; 谈梦婷等 2016). 此外, 从陶瓷的微观结构入手,对界面击溃效应进行数值模拟研究是当今的一大热点. ...
... Hauver等(1994)通过大量实验发现TiB$_{2}$在界面击溃过程中,撞击区域的正下方出现大片粉碎区域, 另有锥形裂纹从陶瓷表面开始扩展,如图11所示. 目前关于陶瓷界面击溃理论的研究工作可分为三类:一是从宏观陶瓷锥入手研究界面击溃/侵彻转变速度与弹靶表面压力的关系(Lundberg 2004, 2007; Lundberg et al. 2000, 2013, 2016; Renström et al. 2004, 2009; Andersson et al. 2007)以及撞击表面下锥裂纹的形成和扩展对界面击溃的影响;二是基于微观翼型裂纹扩展模式研究轴向应力与界面击溃/侵彻转变速度的关系(LaSalvia 2002a, 2002b, 2005a, 2005b; LaSalvia et al. 2001, 2010b; LaSalvia & McCauley 2010),结合翼型微裂纹与塑性区域的产生对界面击溃现象进行研究;三是基于AT模型研究不同头部形状长杆弹在界面击溃条件下的动能变化(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017). ...
... , 2005b; LaSalvia et al. 2001, 2010b; LaSalvia & McCauley 2010),结合翼型微裂纹与塑性区域的产生对界面击溃现象进行研究;三是基于AT模型研究不同头部形状长杆弹在界面击溃条件下的动能变化(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017). ...
An analytical prediction for the effect of ceramic thickness and mechanical properties on the dwell/penetration transition velocity//20th International Symposium on Ballistics
2
2002
... 半个世纪以来,陶瓷界面击溃效应的研究工作从最初的获得界面击溃效应(Wilkins 1963;Hauver et al. 1993, 1994, 2005; Rosenberg & Tsaliah 1990;Anderson & Walker 1991; Anderson & Morris 1992;Anderson & Royal-Timmons 1997; Anderson et al. 1993a, 1995, 1999, 2005; Den Reijer 1991; Bless et al. 1992; Lundberg et al. 1996; Westerling et al. 2001)转为研究界面击溃过程中弹、靶动态力学响应(Lundberg 2004, 2007;Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016; LaSalvia & McCauley 2010; LaSalvia 2002a, 2002b, 2005a, 2005b; LaSalvia et al. 2001, 2005, 2007, 2009, 2010a, 2010b; LaSalvia & Normandia 2002; Deshpande & Evans 2008; Deshpande et al. 2011; Anderson & Orphal 2003;Pickering et al. 2016), 以明确界面击溃效应作用机理,为界面击溃效应在工程上的应用奠定基础. 在实验方法和技术方面,主要围绕陶瓷材料、弹体形状、尺寸效应等影响因素开展撞击实验,获得不同弹靶条件下的界面击溃效应(Lundberg 2004, 2007; Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016). 一方面国内外学者加强了实验观测技术,宏观观测界面击溃过程并对回收后的靶体材料破坏情况进行细观观测,以了解界面击溃效应对弹靶破坏的作用(Anderson et al. 2005, 2008, 2009, 2011a, 2011b; Anderson 2009, 2010; Anderson & Gooch 2011; Lundberg et al. 2000, 2001; Thoma et al. 2007; Strassburgeret al. 2016; Behner et al. 2008, 2016). 另一方面,通过不同影响因素下的界面击溃效应实验,获得界面击溃/侵彻转变速度等参数,以深入探索界面击溃/侵彻转变过程的作用机理(Lundberg 2004; Lundberget al. 2005, 2006). 在界面击溃效应理论研究方面,陶瓷的锥裂纹(Lundberg 2007; Lundberg et al. 2013, 2016)和微观翼型裂纹理论 (LaSalvia 2002a, 2002b, 2005a, 2005b;LaSalvia et al. 2001, 2005, 2007, 2010a, 2010b; LaSalvia & Normandia 2002;LaSalvia & McCauley 2010)是通过靶体的破坏解释界面击溃效应的重要模型.弹体在界面击溃效应中的参数变化主要依靠修正的AT模型获得(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017).数值模拟作为辅助实验和理论研究界面击溃效应的手段,其关键问题是确定可靠的陶瓷本构模型.学者们采用不同的陶瓷本构模型及参数对影响界面击溃效应的因素进行了数值模拟(Anderson 2006; Anderson et al. 1993b;Holmquist & Johnson 2002a, 2002b, 2003, 2005a, 2005b, 2008, 2011; Holmquist et al. 2001, 2008; Quan et al. 2006; Fountzoulas et al. 2009; Fountzoulas & LaSalvia 2013; Chi et al. 2013, 2015; Serjouei 2014; Yuan et al. 2016; 谈梦婷等 2016). 此外, 从陶瓷的微观结构入手,对界面击溃效应进行数值模拟研究是当今的一大热点. ...
... ; LaSalvia & Normandia 2002;LaSalvia & McCauley 2010)是通过靶体的破坏解释界面击溃效应的重要模型.弹体在界面击溃效应中的参数变化主要依靠修正的AT模型获得(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017).数值模拟作为辅助实验和理论研究界面击溃效应的手段,其关键问题是确定可靠的陶瓷本构模型.学者们采用不同的陶瓷本构模型及参数对影响界面击溃效应的因素进行了数值模拟(Anderson 2006; Anderson et al. 1993b;Holmquist & Johnson 2002a, 2002b, 2003, 2005a, 2005b, 2008, 2011; Holmquist et al. 2001, 2008; Quan et al. 2006; Fountzoulas et al. 2009; Fountzoulas & LaSalvia 2013; Chi et al. 2013, 2015; Serjouei 2014; Yuan et al. 2016; 谈梦婷等 2016). 此外, 从陶瓷的微观结构入手,对界面击溃效应进行数值模拟研究是当今的一大热点. ...
Inelastic deformation mechanisms and damage in structural ceramics subjected to high-velocity impact
5
2010
... 半个世纪以来,陶瓷界面击溃效应的研究工作从最初的获得界面击溃效应(Wilkins 1963;Hauver et al. 1993, 1994, 2005; Rosenberg & Tsaliah 1990;Anderson & Walker 1991; Anderson & Morris 1992;Anderson & Royal-Timmons 1997; Anderson et al. 1993a, 1995, 1999, 2005; Den Reijer 1991; Bless et al. 1992; Lundberg et al. 1996; Westerling et al. 2001)转为研究界面击溃过程中弹、靶动态力学响应(Lundberg 2004, 2007;Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016; LaSalvia & McCauley 2010; LaSalvia 2002a, 2002b, 2005a, 2005b; LaSalvia et al. 2001, 2005, 2007, 2009, 2010a, 2010b; LaSalvia & Normandia 2002; Deshpande & Evans 2008; Deshpande et al. 2011; Anderson & Orphal 2003;Pickering et al. 2016), 以明确界面击溃效应作用机理,为界面击溃效应在工程上的应用奠定基础. 在实验方法和技术方面,主要围绕陶瓷材料、弹体形状、尺寸效应等影响因素开展撞击实验,获得不同弹靶条件下的界面击溃效应(Lundberg 2004, 2007; Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016). 一方面国内外学者加强了实验观测技术,宏观观测界面击溃过程并对回收后的靶体材料破坏情况进行细观观测,以了解界面击溃效应对弹靶破坏的作用(Anderson et al. 2005, 2008, 2009, 2011a, 2011b; Anderson 2009, 2010; Anderson & Gooch 2011; Lundberg et al. 2000, 2001; Thoma et al. 2007; Strassburgeret al. 2016; Behner et al. 2008, 2016). 另一方面,通过不同影响因素下的界面击溃效应实验,获得界面击溃/侵彻转变速度等参数,以深入探索界面击溃/侵彻转变过程的作用机理(Lundberg 2004; Lundberget al. 2005, 2006). 在界面击溃效应理论研究方面,陶瓷的锥裂纹(Lundberg 2007; Lundberg et al. 2013, 2016)和微观翼型裂纹理论 (LaSalvia 2002a, 2002b, 2005a, 2005b;LaSalvia et al. 2001, 2005, 2007, 2010a, 2010b; LaSalvia & Normandia 2002;LaSalvia & McCauley 2010)是通过靶体的破坏解释界面击溃效应的重要模型.弹体在界面击溃效应中的参数变化主要依靠修正的AT模型获得(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017).数值模拟作为辅助实验和理论研究界面击溃效应的手段,其关键问题是确定可靠的陶瓷本构模型.学者们采用不同的陶瓷本构模型及参数对影响界面击溃效应的因素进行了数值模拟(Anderson 2006; Anderson et al. 1993b;Holmquist & Johnson 2002a, 2002b, 2003, 2005a, 2005b, 2008, 2011; Holmquist et al. 2001, 2008; Quan et al. 2006; Fountzoulas et al. 2009; Fountzoulas & LaSalvia 2013; Chi et al. 2013, 2015; Serjouei 2014; Yuan et al. 2016; 谈梦婷等 2016). 此外, 从陶瓷的微观结构入手,对界面击溃效应进行数值模拟研究是当今的一大热点. ...
... ;LaSalvia et al. 2001, 2005, 2007, 2010a, 2010b; LaSalvia & Normandia 2002;LaSalvia & McCauley 2010)是通过靶体的破坏解释界面击溃效应的重要模型.弹体在界面击溃效应中的参数变化主要依靠修正的AT模型获得(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017).数值模拟作为辅助实验和理论研究界面击溃效应的手段,其关键问题是确定可靠的陶瓷本构模型.学者们采用不同的陶瓷本构模型及参数对影响界面击溃效应的因素进行了数值模拟(Anderson 2006; Anderson et al. 1993b;Holmquist & Johnson 2002a, 2002b, 2003, 2005a, 2005b, 2008, 2011; Holmquist et al. 2001, 2008; Quan et al. 2006; Fountzoulas et al. 2009; Fountzoulas & LaSalvia 2013; Chi et al. 2013, 2015; Serjouei 2014; Yuan et al. 2016; 谈梦婷等 2016). 此外, 从陶瓷的微观结构入手,对界面击溃效应进行数值模拟研究是当今的一大热点. ...
... ;LaSalvia & McCauley 2010)是通过靶体的破坏解释界面击溃效应的重要模型.弹体在界面击溃效应中的参数变化主要依靠修正的AT模型获得(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017).数值模拟作为辅助实验和理论研究界面击溃效应的手段,其关键问题是确定可靠的陶瓷本构模型.学者们采用不同的陶瓷本构模型及参数对影响界面击溃效应的因素进行了数值模拟(Anderson 2006; Anderson et al. 1993b;Holmquist & Johnson 2002a, 2002b, 2003, 2005a, 2005b, 2008, 2011; Holmquist et al. 2001, 2008; Quan et al. 2006; Fountzoulas et al. 2009; Fountzoulas & LaSalvia 2013; Chi et al. 2013, 2015; Serjouei 2014; Yuan et al. 2016; 谈梦婷等 2016). 此外, 从陶瓷的微观结构入手,对界面击溃效应进行数值模拟研究是当今的一大热点. ...
... Hauver等(1994)通过大量实验发现TiB$_{2}$在界面击溃过程中,撞击区域的正下方出现大片粉碎区域, 另有锥形裂纹从陶瓷表面开始扩展,如图11所示. 目前关于陶瓷界面击溃理论的研究工作可分为三类:一是从宏观陶瓷锥入手研究界面击溃/侵彻转变速度与弹靶表面压力的关系(Lundberg 2004, 2007; Lundberg et al. 2000, 2013, 2016; Renström et al. 2004, 2009; Andersson et al. 2007)以及撞击表面下锥裂纹的形成和扩展对界面击溃的影响;二是基于微观翼型裂纹扩展模式研究轴向应力与界面击溃/侵彻转变速度的关系(LaSalvia 2002a, 2002b, 2005a, 2005b; LaSalvia et al. 2001, 2010b; LaSalvia & McCauley 2010),结合翼型微裂纹与塑性区域的产生对界面击溃现象进行研究;三是基于AT模型研究不同头部形状长杆弹在界面击溃条件下的动能变化(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017). ...
Effects of a dynamic confinement on the penetration resistance of ceramics against long rods
2000
Using plasticity values determined from systematic hardness indentation measurements for predicting impact behavior in structural ceramics: A new, simple screening technique
2005. Failure and plasticity models of ceramics—A numerical study. The 11th Int Symposium on Plasticity and Current Applications, (PLASTICITY 2005), Kauai, Hawaii,
2005
Flash X-ray cinematography analysis of dwell and penetration of small caliber projectiles with three types of SiC ceramics
3
2016
... 半个世纪以来,陶瓷界面击溃效应的研究工作从最初的获得界面击溃效应(Wilkins 1963;Hauver et al. 1993, 1994, 2005; Rosenberg & Tsaliah 1990;Anderson & Walker 1991; Anderson & Morris 1992;Anderson & Royal-Timmons 1997; Anderson et al. 1993a, 1995, 1999, 2005; Den Reijer 1991; Bless et al. 1992; Lundberg et al. 1996; Westerling et al. 2001)转为研究界面击溃过程中弹、靶动态力学响应(Lundberg 2004, 2007;Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016; LaSalvia & McCauley 2010; LaSalvia 2002a, 2002b, 2005a, 2005b; LaSalvia et al. 2001, 2005, 2007, 2009, 2010a, 2010b; LaSalvia & Normandia 2002; Deshpande & Evans 2008; Deshpande et al. 2011; Anderson & Orphal 2003;Pickering et al. 2016), 以明确界面击溃效应作用机理,为界面击溃效应在工程上的应用奠定基础. 在实验方法和技术方面,主要围绕陶瓷材料、弹体形状、尺寸效应等影响因素开展撞击实验,获得不同弹靶条件下的界面击溃效应(Lundberg 2004, 2007; Lundberg P & Lundberg B 2005; Lundberg et al. 2000, 2001, 2006, 2013, 2016). 一方面国内外学者加强了实验观测技术,宏观观测界面击溃过程并对回收后的靶体材料破坏情况进行细观观测,以了解界面击溃效应对弹靶破坏的作用(Anderson et al. 2005, 2008, 2009, 2011a, 2011b; Anderson 2009, 2010; Anderson & Gooch 2011; Lundberg et al. 2000, 2001; Thoma et al. 2007; Strassburgeret al. 2016; Behner et al. 2008, 2016). 另一方面,通过不同影响因素下的界面击溃效应实验,获得界面击溃/侵彻转变速度等参数,以深入探索界面击溃/侵彻转变过程的作用机理(Lundberg 2004; Lundberget al. 2005, 2006). 在界面击溃效应理论研究方面,陶瓷的锥裂纹(Lundberg 2007; Lundberg et al. 2013, 2016)和微观翼型裂纹理论 (LaSalvia 2002a, 2002b, 2005a, 2005b;LaSalvia et al. 2001, 2005, 2007, 2010a, 2010b; LaSalvia & Normandia 2002;LaSalvia & McCauley 2010)是通过靶体的破坏解释界面击溃效应的重要模型.弹体在界面击溃效应中的参数变化主要依靠修正的AT模型获得(Anderson & Walker 2005; 李继承和陈小伟 2011a, 2011b; Li et al. 2014, 2015; Li & Chen 2017).数值模拟作为辅助实验和理论研究界面击溃效应的手段,其关键问题是确定可靠的陶瓷本构模型.学者们采用不同的陶瓷本构模型及参数对影响界面击溃效应的因素进行了数值模拟(Anderson 2006; Anderson et al. 1993b;Holmquist & Johnson 2002a, 2002b, 2003, 2005a, 2005b, 2008, 2011; Holmquist et al. 2001, 2008; Quan et al. 2006; Fountzoulas et al. 2009; Fountzoulas & LaSalvia 2013; Chi et al. 2013, 2015; Serjouei 2014; Yuan et al. 2016; 谈梦婷等 2016). 此外, 从陶瓷的微观结构入手,对界面击溃效应进行数值模拟研究是当今的一大热点. ...
... 为了清晰地观测侵彻过程中弹体头部和靶表面破坏情况,学者们采用了高速录像、X光摄影等设备和技术观测了陶瓷靶的界面击溃效应作用过程.Anderson等(2005, 2008, 2011a),采用X光摄影技术对不同角度斜置靶体撞击弹体过程进行了研究.Lundberg等(2000)和Westerling等(2001)利用X光摄影技术观测了直径为2mm、长径比分别为40和75的钨合金射弹撞击SiC等陶瓷的界面击溃作用过程,获取了不同陶瓷的界面击溃/侵彻转变速度. 结果表明,陶瓷材料强度及韧性均对界面击溃过程有显著的影响.对陶瓷材料界面击溃现象研究较多的另一团队是来自德国的Ernst-Mach-Institut(EMI)的研究小组(Thoma et al. 2007, Strassburger et al. 2016,Behner et al. 2016), 他们利用先进的多通道X光摄影设备研究了7.62mmAPM2 子弹撞击陶瓷材料时的界面击溃效应(如图5所示),研究了背板材料的影响规律、界面驻留时间以及弹体侵蚀现象,并进行了相关的数值模拟. 实验观测结果表明背板材料强度越大,界面驻留持续时间越长,但该部分工作未能将侵彻速度变化与陶瓷材料力学性能相关联. ...
... EMI侵彻实验观测装置(Strassburger et al. 2016) ...
Penetration of semi-infinite AD995 alumina targets by tungsten long rod penetrators
1
1995
... Uth 和 Deshpande(2013)综合分析了现有的界面击溃理论模型,认为其存在的缺陷有: (1)当SiC, WC和B$_{4}$C都存在界面击溃效应时,SiC中存在微裂纹导致的粉碎区域, 但在WC和B$_{4}$C中并不存在该区域.因此, 现有的界面击溃理论模型无法适用于所有陶瓷材料; (2)微裂纹产生的时间较短, 在1$\mu $s左右(Bourne 2010),界面击溃时间可能达几百微秒, 推测微裂纹的形成阶段可以忽略(Lundberg 2004, Andersson et al. 2007); (3) 研究中一般认为界面击溃过程中,弹体侵彻速度为0, 实验表明在界面击溃过程中, 侵彻速度不为0,靶板会被侵彻或推动(Subramanian & Bless 1995). Renström等(2004)通过研究发现在高速冲击下, 弹体可视为流体对陶瓷靶产生冲击,借鉴流固耦合机制在三明治靶板中的成功应用(Wadley et al. 2013, Liu et al. 2013),可以将弹靶界面击溃问题演变成流体弹与变形体靶之间的流固耦合问题.文中采用了水流撞击柔软透明的高真空润滑脂材料类比观察陶瓷与弹体之间的界面击溃与侵彻现象,如图15所示.采用尺寸相似模型的优点是可以清楚地观测界面击溃效应. ...
A theory for the deceleration of long rods after impact
, 包阔
