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| Naji, M. |
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| Motta, Antonella |
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| Aletan, Dirar |
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| Mohamed, Tarek |
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| Ertürk, Emre |
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| Taccardi, Nicola |
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| Kononenko, Denys |
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| Petrov, R. H. | Madrid |
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| Alshaaer, Mazen | Brussels |
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| Bih, L. |
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| Casati, R. |
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| Muller, Hermance |
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| Kočí, Jan | Prague |
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| Šuljagić, Marija |
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| Kalteremidou, Kalliopi-Artemi | Brussels |
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| Azam, Siraj |
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| Ospanova, Alyiya |
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| Blanpain, Bart |
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| Ali, M. A. |
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| Popa, V. |
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| Rančić, M. |
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| Ollier, Nadège |
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| Azevedo, Nuno Monteiro |
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| Landes, Michael |
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| Rignanese, Gian-Marco |
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Manno, Riccardo
University of Bristol
in Cooperation with on an Cooperation-Score of 37%
Topics
Publications (6/6 displayed)
- 2023Tensile Failure of Bio-inspired Lattices with Different Base Topologies
- 2022Fracture of Honeycombs Produced by Additive Manufacturingcitations
- 2021Mode I and Mode II interfacial fracture energy of SiC/BN/SiC CMCscitations
- 2020An investigation into the fracture behaviour of honeycombs with density gradientscitations
- 2018A Computational Study on Crack Propagation in Bio-Inspired Latticescitations
- 2018Engineering the crack path in lattice cellular materials through bio-inspired micro-structural alterationscitations
Places of action
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article
Mode I and Mode II interfacial fracture energy of SiC/BN/SiC CMCs
Abstract
Quantifying the mixed mode fracture toughness of interfaces in ceramic matrix composites (CMCs) is crucial for understanding their failure. In this work we use in situ micromechanical testing in the scanning electron microscope to achieve stable interfacial crack propagation in Mode I (Double Cantilever Beam) and Mode II (Push out) and measure the corresponding fracture resistances. We use this approach to measure the interfacial fracture resistance in SiC/BN/SiC CMCs and compare it to the fracture energy of the fibres. During in-situ testing, fracture paths can be observed while data is acquired simultaneously. We clearly observe debonding at the BN-fibre interface (i.e. inside adhesive debonding). The critical energy release rate of the BN-fibre interface for Mode I and II (G I c ≈ 2.1 ± 1.0 J/m 2 and G II c ≈ 1.2 ± 0.5 J/m 2 ) are equivalent and is lower than that measured for the fibre using microscopic DCB tests (G I c ≈ 6.0 ± 2.0 J/m 2 ). These results explain the generalized fibre debonding and pull out observed in the fracture of these CMCs. By enabling direct observation of crack paths and quantifying the corresponding fracture energies, we highlight possible routes for the optimisation and modelling of the new generation of CMC interphases.