Residual Strength and Fatigue Lifetime of ... - Solid Mechanics
Residual Strength and Fatigue Lifetime of ... - Solid Mechanics Residual Strength and Fatigue Lifetime of ... - Solid Mechanics
Figure 5.14: Kinking of the crack into the face sheet in an STT specimen with H250 core. Figure 5.15: Fiber bridging in the rear side of an STT specimen with H250 core. A 4 Mpix Digital Image Correlation (DIC) measurement system (ARAMIS 4M) was utilized to monitor 2D surface major strains and locate the crack tip position by the strain concentration at the crack tip in the measured 2D strain contours. To ensure the accuracy of the measurement a tape ruler was glued to the bottom side of the specimens to locate the crack tip as well and measure the crack length by a calliper with an accuracy of ±0.05 mm. Figure 5.16 shows a majore strain contour from an STT specimen with H45 core used to locate the crack tip position by the DIC system. Fatigue crack growth length vs. load cycle diagrams for the STT specimens from both the visual measurements and the measurements using the DIC system are presented in Figure 5.17. The crack length measurements by the DIC system agree well with the physical crack measurements, as shown in Figure 5.17. Crack growth length vs. load cycle results from the two repetitions of each type of STT specimens are shown in Figure 5.18. It is seen that for all core densities the crack initially grows fast, but the crack growth rate decreases as the crack propagates further. This can be attributed to increasing membrane forces and subsequent decreasing energy release rates for the H100 and H45 specimens and fully developed fibre bridging resisting the crack growth for the H250 specimens. For both STT specimens with H45 core, unstable crack propagation was observed during the initial load cycles where the crack propagated unstably 100
around 150 mm. After the unstable crack propagation, the crack continued to propagate in a stable manner. A small deviation between the two test repetitions is observed for the H45 and H100 specimens. However, Figure 5.18 (c) illustrates a large deviation between the two test repetitions for the STT specimens with H250 core, which can be attributed to the different scales of fibre bridging in H250 specimens. Crack length [mm] Figure 5.16: Surface major strain contour of the STT specimens from the DIC system. 250 200 150 100 50 0 Strain concentration at the crack tip 200 (a) (b) 0 20000 40000 60000 80000 Cycles, N Visual DIC 101 Crack length [mm] 160 120 80 40 0 Visual DIC 0 20000 40000 60000 80000 100000 Cycles, N
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Figure 5.14: Kinking <strong>of</strong> the crack into the face sheet in an STT specimen with H250 core.<br />
Figure 5.15: Fiber bridging in the rear side <strong>of</strong> an STT specimen with H250 core.<br />
A 4 Mpix Digital Image Correlation (DIC) measurement system (ARAMIS 4M) was utilized to<br />
monitor 2D surface major strains <strong>and</strong> locate the crack tip position by the strain concentration at<br />
the crack tip in the measured 2D strain contours. To ensure the accuracy <strong>of</strong> the measurement a<br />
tape ruler was glued to the bottom side <strong>of</strong> the specimens to locate the crack tip as well <strong>and</strong><br />
measure the crack length by a calliper with an accuracy <strong>of</strong> ±0.05 mm. Figure 5.16 shows a<br />
majore strain contour from an STT specimen with H45 core used to locate the crack tip position<br />
by the DIC system.<br />
<strong>Fatigue</strong> crack growth length vs. load cycle diagrams for the STT specimens from both the visual<br />
measurements <strong>and</strong> the measurements using the DIC system are presented in Figure 5.17. The<br />
crack length measurements by the DIC system agree well with the physical crack measurements,<br />
as shown in Figure 5.17. Crack growth length vs. load cycle results from the two repetitions <strong>of</strong><br />
each type <strong>of</strong> STT specimens are shown in Figure 5.18. It is seen that for all core densities the<br />
crack initially grows fast, but the crack growth rate decreases as the crack propagates further.<br />
This can be attributed to increasing membrane forces <strong>and</strong> subsequent decreasing energy release<br />
rates for the H100 <strong>and</strong> H45 specimens <strong>and</strong> fully developed fibre bridging resisting the crack<br />
growth for the H250 specimens. For both STT specimens with H45 core, unstable crack<br />
propagation was observed during the initial load cycles where the crack propagated unstably<br />
100