Issue 35

S. Barter et alii, Frattura ed Integrità Strutturale, 35 (2016) 132-141; DOI: 10.3221/IGF-ESIS.35.16 134 rates of small cracks being faster and having lower thresholds than long cracks, as will be shown. From this figure, it is clear that part of the reason that these bands are visible is that during the application of a spectrum block the fatigue crack path is changing while the fracture surface texture from each spectrum block is relatively consistent (at this scale). Path changes produced by load changes have been often observed, particularly with the application of underloads as reported in [16]. Abelkis [19] noted similar features on the fatigue cracks produced in other 7XXX aluminium alloys as well as the 2XXX alloys. Krkoska et al. [21] notes this effect in AA2024-T3, although it was not as strongly defined as found here with AA7050- T7451. From a practical point of view, this leads to one possible method of marking fracture surfaces at growth rates below those where striations are visible: i.e., the use of high R sequences with underloads [3] or sequences with bands of different R. Figure 1 : Origin region of cracks grown with repeated applications of the complex wing root bending moment loading sequence shown (left). The cracking started from multiple sites (shallow etch pits) on the ion vapour deposited aluminium coated surface: bottom of the view. G ENERAL CRACK PATHS IN AA7050-T7451 or stage two fatigue crack growth [15], it is commonly assumed when applying linear elastic fracture mechanics for predictions, that the crack path plane is flat and perpendicular to the loading direction. In this context, flat is a relative term since high magnification microscopic examination will usually reveal that this is not the case –roughness is present and this implies that the microscopic crack path is not always perpendicular to the loading direction. The degree of this path roughness, as the fatigue crack grows, is dependent on: the crack tip stress intensity variation (∆ K ) associated with the cyclic loading; the influence of the microstructure; the influence of the environment, etc. [11]. For example, in AA7050-T7451, the surface is generally faceted for CA loading where ∆ K and maximum K ( K max ) are below ~5MPa√m 3 . Crack surfaces produced by such loading are shown in Fig. 2A and B that were produced with very simple spectra approximating CA since they consisted of large blocks of CA of R =0.5 with occasional single loads of a different R . (Fig. 2A was taken at a high angle of tilt to highlight the meandering faceted growth of the crack and Fig. 2B was imaged in the scanning electron microscope (SEM) using only one quadrant of the four piece backscatter electron detector to give a shadowed view of the surface: bright facets are tilted towards the detector and dark ones away from the detector). These views clearly indicate that the surfaces are not consistently perpendicular to the loading direction. Additionally, in Fig. 2B, features labelled as ridges and fissures on the fracture surface, suggest the crack is locally sampling multiple paths around the crack front as it progresses through the material. The ridges and fissures seen in Fig. 2B coincide with the single low to negative R cycles that were applied occasionally in the R=0.5 loading. The ridges are on the facets facing away from the crack origin (the growth direction) and the fissures are on those facets facing the origin and are therefore alternate crack paths. 3 This is a somewhat arbitrary point and may vary from material to material F