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Experimentally, it was shown that rivets same by design, but produced by different manufacturers, have a significant difference in the fatigue life-time; this difference was clearly identified with the proposed correction to the linear damage-accumulation estimation.
It was also found that the difference in the fatigue lives between the different stress levels was much higher at higher loading frequencies than that at lower loading frequencies for both temperatures.
In addition, the rate of increase in the fatigue life with the loading frequency was exponential, and the difference in the fatigue life (Nf) between the different loading frequencies was found to be higher at lower stress levels than that at higher strain levels at the two temperatures.
The slight difference in the fatigue behaviour of the FSW specimens whose process parameters differed form those of the unwelded composite was explained by the different microstructural homogeneity in the transition from the base to the FSW zone.
No statistically significant difference in the fatigue life between the 'as-cast' and machined surfaces was observed.
The in situ fatigue tests and the fracture surface analyses revealed a difference in the fatigue crack propagation mechanisms between the closed-cell foam and the hollow sphere structure: in the closed-cell foam a contiguous fatigue crack can be found, where in the case of the hollow sphere structure the fatigue crack propagation is concentrated in the vicinities of the sintering necks.
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The analysis of crack path roughness helped to understand those differences in the fatigue crack growth rate.
The specimen section and fracture surface observations revealed fatigue damage mechanisms in both the TBC-coated and uncoated specimens, and that finding helps explain the differences in the fatigue behaviour of both materials.
Investigations of Surface cracks after fatigue failure lead to the assumption of different crack types under φ="0° and φ= 180° loading according to [1] which cause the differences in the fatigue lives.
It appears therefore that a large proportion of the differences in the fatigue crack growth rate of metallic alloys can be explained in terms of the macroscopic tensile properties of the material rather than the details of the microstructure and chemical composition.
Strain-controlled fatigue tests were carried out in CrMn-alloyed austenitic steels with different sums (C + N: 0.65 1.2) and ratios (C/N: 0.13 ∞) of C and N. Manson Coffin analyses revealed distinct differences in the fatigue behaviour to CrNi-alloyed C + N steels investigated earlier.
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