Issue 35

S. Barter et alii, Frattura ed Integrità Strutturale, 35 (2016) 132-141; DOI: 10.3221/IGF-ESIS.35.16 140 Measurement of the CA crack growth sub-block’ widths and assuming a centre semi-elliptical surface crack geometry factor [25] allowed da/dN vs  K data to be determined. These data are presented in Fig. 8B where power curves were fitted to the average growth of each type of CA band. It appears that the average da/dN or crack growth per cycle varies inversely with the number of cycles in the CA blocks below  K ~ 2.5 MPa√m or a rate of ~2x10 -8 m/cycle for this material. Comparing this data to the long crack data found in [26] indicated that  K ~ 2.5 MPa√m was about the region from which the Paris regime of the R =0.8 crack growth rate starts. The inverse decay suggests that growth rates will be faster with fewer CA cycles between the VA loading below this point (  K ~2.5 MPa√m), suggesting that when the cycles are applied as VA for small cracks, a more efficient crack grows. All of this growth is considerably faster with lower threshold than predicted by long crack CA data alone, for example that found in Reference [26]. C ONCLUSIONS y adjusting the pattern of loads involving sequences of high stress ratio CA cycles followed by; underloads, bands of different stress ratio cycles or bands of VA loading, distinct fracture surface features or progression marks can be produced at very low stress intensity factor range levels. Examination of the crack paths on the fracture surfaces produced by small cracks in AA7050-T7451 found that path changes were sensitive to the crystal orientation of the grain through which the crack was growing, and by using simple loading sequences the path could be changed. This observation facilitated the measurement of crack growth rates at very low  K levels. It was also observed that CA loads of varying stress ratios in bands could progressively cause retardation of further growth. Whereas changing the loading more often increased the rate of growth measured in the CA bands. This observation may help to explain why VA loading can often result in faster crack growth than is predicted from data developed from CA tests. Since for any sequence of CA loading the crack will prefer to grow on one particular plane in one direction through a grain, it was postulated that a decrease in crack growth rate could be expected particularly when the preferred local plane and direction is not aligned to the preferred average growth plane. Using VA loads results in growth that was less governed by this limitation and as such allowed growth closer to a preferred growth plain making the cracking more efficient in the small to intermediate crack regime where K max is < about 5MPa√m. A CKNOWLEDGMENTS . Jones, DSTO, and T. Hattenberg of NLR, are acknowledged for some of the fractography and measurement work. R EFERENCES [1] White, P., Barter, S. A., Molent, L. Observations of crack path changes caused by periodic underloads in AA7050-T7451. International Journal of Fatigue, 30 (2008) 1267-1278. [2] Dainty, R. V., The use of ‘marker-loads’ as an aid in quantitative fractography in full-scale aircraft fatigue testing – a case study. Technical Report LTR-ST-1374. National Research Council, Canada, (1982). [3] Barter, S. A., Wanhill, R. J. H. Marker Loads for Quantitative Fractography (QF) of Fatigue in Aerospace Alloys, NLR Client report NLR-TR-2008-644. National Aerospace Laboratory, NLR., Amsterdam The Netherlands, (2008). [4] Wanhill, R. J. H., Damage tolerance engineering property evaluation of aerospace aluminium alloys with emphasis on fatigue crack growth. Technical Report NLR TP 94177U, National Aerospace Laboratory NLR; (1995). [5] Wallbrink, C., Jackson, P. Hu, W., Crack growth rate curves: Which Part Dominates Life Prediction and When? In: International Committee on Aeronautical Fatigue, Montreal, Canada, (2011). [6] Blom, A. F., Relevance of short crack growth data for durability and damage tolerance analysis of aircraft. Proceedings of the Second Engineering Foundation International Conference/Workshop on Small Fatigue Cracks, Metallurgical Soc. Inc, (1996) 623-638. B M