Transversal compression fracture of unidirectional fibre-reinforced plastics

Баженов, С. Л.; Kozey, V. V.

doi:10.1007/bf02387736

Cited by 14 publications

(6 citation statements)

References 14 publications

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“…Inspection of recovered specimens loaded under confinement and/or at high-strain-rates shows that neither confining pressure nor the strain rate has any significant effect on the angle of failure planes, at least for the range of confining pressures and strain rates applied. These findings are consistent with other observations made for a variety of fiber-reinforced polymeric composites [23] where it is reported that the orientation of failure planes in transversely compressed composites are highly scattered in the range from 49 to 55 . Therefore, based on the orientation of localization bands, transverse failure can be defined to occur when the shear stress at Transverse Failure in S2-Glass/Epoxy FRCs a particular plane reaches a critical value which is a function of normal stress acting on the plane, i.e.,…”

Section: Failure Modessupporting

confidence: 93%

Transverse Failure in Thick S2-Glass/ Epoxy Fiber-Reinforced Composites

Vural

Ravichandran

2004

Journal of Composite Materials

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The transverse mechanical and failure behavior of unidirectional S2-glass/epoxy composites are investigated and reported for a wide range of strain rates from 10-4to 10 4s-1under multiaxial compressive loading conditions. The effect of stress multiaxiality is explored using the confining sleeve technique to impose varying degrees of lateral confinement. The lateral confinement has been found to significantly increase both the maximum attainable stress level and the strain to failure. Scanning electron microscopy (SEM) observations on recovered specimens reveal that the transverse failure occurs within localized shear bands through multiple fiber–matrix interface failure at the micro-scale. Based on theorientation of shear bands a Mohr–Coulomb type failure criterion is suggested to represent the transverse failure of unidirectional S2-glass/epoxy composites.

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Section: Failure Modessupporting

confidence: 93%

Transverse Failure in Thick S2-Glass/ Epoxy Fiber-Reinforced Composites

Vural

Ravichandran

2004

Journal of Composite Materials

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“…It can be seen that the crack in shear mode occurred on the plane orientated around 36 40 with respect to the loading direction propagating transverse to the fiber direction. Similar failure behaviors were also observed in other polymeric composites systems [13]. Based on the experimental investigations, it was found that the compressive failure mechanism basically was not altered by the contents of silica nanoparticles and the loading rates.…”

Section: Failure Mechanismsupporting

confidence: 78%

Investigating Silica Nanoparticle Effect on Dynamic and Quasi-static Compressive Strengths of Glass Fiber/Epoxy Nanocomposites

Tsai

Cheng

2009

Journal of Composite Materials

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The research is aimed to investigate the compressive strengths of glass/epoxy nanocomposites, containing various loadings of spherical silica nanoparticles. Through a sol—gel technique, the silica particles with a diameter of 25 nm were exfoliated uniformly into the epoxy resin. Subsequently, by inserting the silica—epoxy mixture into the unidirectional glass fiber through a vacuum hand lay-up process, the glass fiber/epoxy composite laminates with 10, 20, and 30 wt% of silica nanoparticles were fabricated. Quasi-static and dynamic compression tests were conducted on the brick composite specimens with fiber orientations of 0°, 5°, 10°, 15°, and 90° using a hydraulic MTS machine and a split Hopkinson pressure bar, respectively. Observations on the failure specimens indicated that for fiber orientations less than 15°, the fiber microbuckling is the dominant failure mechanism. On the other hand, for the 90° samples, the out-of-plane shear failure is the main failure mechanism. In addition, it was denoted that as the silica contents increase, the compressive strengths of the glass/epoxy composites are improved accordingly. The enhancing mechanism in the compressive strengths can be properly explicated using the microbuckling model.

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“…There are dents on them, which suggest the plastic deformation in compression of two neighboring fila ments oriented at a small angle because of yarn twist. The transverse compressive yield strength of aramid filaments is ≈60 MPa [10]. In this work, the transverse stress was an order of magnitude higher; therefore, the filaments were plastically deformed [11].…”

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confidence: 63%

Effect of transverse compression on the tensile strength of aramid yarns

2015

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Fabrics based on aramid fibers have a high ability to dissipate the energy of a ballistic impact. For this rea son, they are used in helmets and flexible armor vests, as well as internal layers of hard armor [1]. A transverse ballistic impact gives rise to a longitudinal wave travel ing along a fiber at the speed of sound in both direc tions away from the point of impact. By high speed photography, Rakhmatulin has detected that a trans verse impact on a rubber fiber initiates a transverse wave in the form of a triangle the sides of which increase with time while preserving angles with the impactor at the upper vertex [2,3].Behind the front of the longitudinal wave, the fiber is uniformly stretched. The tensile stress rises with impactor velocity [5,6]. At a certain (critical) impac tor velocity, the tensile stress reaches the ultimate strength of the fiber and the fiber breaks at the moment of the impact [7]. By high speed photography, the experimental value of the critical velocity of impact by a ball on a single SVM yarn was determined as ≈670 m/s [7]. The experimental values of the critical velocities of impact by a fragment simulating projectile on single yarns of PBO, Kevlar KM2, and ultra high molecular weight polyethylene Dyneema are within the ranges 517-583, 523-610, and 621-634 m/s, respectively [8]. For PBO and Kevlar KM2, these val ues are ≈50% of the corresponding theoretical values. The loss of strength on impact was explained by non linear relaxation behavior of polymer [7], and also by doubling of stress in elastic reflection of the yarn from the impactor surface [8]. However, the reduction in the longitudinal strength of the yarns can also be caused by their transverse damage in transverse com pression.The purpose of this work was to study the effect of preliminary transverse compression of fabric on the residual longitudinal strength of Rusar aramid yarns. It was shown for the first time that transverse compres sion leads to reduction in the longitudinal strength of yarns and, at a certain compressive stress, the fabric bursts. The reduction in the longitudinal strength was explained by plastic deformation of filaments under transverse compression, whereas the cause of the burst failed to be determined.The tests were performed on Rusar 56319 filament yarns and twilled fabrics. From the fabric, 100 × 100 mm rectangular specimens were cut. Fabric layers were placed between non sharp edged steel cylinders 12 mm PHYSICAL CHEMISTRY4 0 1 . 0 σ t , GPa 0.5 1.5 σ*, GPa 3 2 1 Fig. 1. Dependence of the residual longitudinal tensile strength σ* of the Rusar yarns on the transverse stress σ t applied to the aramid fabric.

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Transversal compression fracture of unidirectional fibre-reinforced plastics

Cited by 14 publications

References 14 publications

Transverse Failure in Thick S2-Glass/ Epoxy Fiber-Reinforced Composites

Transverse Failure in Thick S2-Glass/ Epoxy Fiber-Reinforced Composites

Investigating Silica Nanoparticle Effect on Dynamic and Quasi-static Compressive Strengths of Glass Fiber/Epoxy Nanocomposites

Effect of transverse compression on the tensile strength of aramid yarns

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