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although there has been a significant reduction in time and cost to generate an scc sample, there is still a cost associated with failure modelling. using this technique, low-cost sem imaging can be used to identify regions of interest in terms of depth of damage and corrosion. this provides a powerful tool to identify regions with tensile stresses. subsequent analysis of these regions by microscopy or scanning probe techniques on the surface of these regions is required to characterise damage within the bulk of the sample. 12

mumford et al. 13 found that the nature of the surface crack path was important to its rate of growth. to investigate this in the method described here, a primary focus of the research was to study the nature of the crack path and its effect on the crack rate and hence the rate of damage formation. the crack path was designed to favour the growth of the crack tip, thus favouring crack growth in the longitudinal direction. as shown in the figure below, the crack can be seen growing in length from a gb (bottom left). increasing the tensile load allows crack to grow at the crack tip and when the crack tip arrives at the apt tip position of a gb (bottom right), it forms a plane of crack propagation.

the continuous crack has caused the distortion of the top surface to increase, with an increased presence of a hazy, reflective region. this is shown in fig. 4a – d, where the cracks are observed to propagate underneath and outside of the eds region. in most cases, the crack appears to be similar in width to the eds results at the point of maximum height. this shows a clear relationship between the imaging system and the underlying sample, highlighting the importance of the sample preparation. we would also expect the cracks to vary in width across the frame, since the exact location of the crack tip may change. however, many of the cracks appear to be consistent in width, suggesting that they are caused by the same mechanism. figure 4a – d demonstrates the efficacy of the system, which can reveal interesting behaviour in an otherwise opaque medium.

crack 110s after fig. 4a has propagated to the top of the field of view, revealing a molten region at the tip of the crack. this is shown in fig. 4e and f and is located at a position coinciding with a gb carbide precipitate present on the cracked surface. the carbon fibre is seen to be pulled in some instances as the crack propagates deeper through the composite. we believe this is a result of deformation and to reduce stress concentration. this is supported by the observation of fib sectioning 23 (shown in fig. 4g ), which clearly shows that the crack has propagated through the carbon fibre, deforming it and deforming it again as the crack travels deeper through the sample. figure 4h shows the deformed surface revealing that the carbon fibre has been pulled deeper in a region. the deformation observed here is caused by multiple incipient cracks and is not induced by crack propagation. it is important to note that the effect observed here is not enough to cause delamination or complete failure of the carbon fibre. rather, the carbon fibre is simply moved deeper in some cases. the cleaving of the carbon fibre observed by cryo-sem imaging is shown in fig. 4i.
the high-resolution maps of the crack tip surface and subsurface cracking observed using hs-afm provided the first results from this work. in the morphology images, the crack tip was found to be discontinuous, which is consistent with propagating subsurface crack. fib milling and sem imaging revealed further surface subsurface cracks arising from the crack tip, which directly link to the cracks of the phase contrast image. cross-sections of these holes, obtained by fib and sem, demonstrated the embedded crack propagating through the crack tip and into the bulk of the sample. this substantiates the high-resolution crack tip mapping performed by hs-afm.
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