On the role of Cu-Zr amorphous intergranular films on crack growth retardation in nanocrystalline Cu during monotonic and cyclic loading conditions

2019 ◽  
Vol 169 ◽  
pp. 109122 ◽  
Author(s):  
Snehanshu Pal ◽  
K. Vijay Reddy ◽  
Chuang Deng
2008 ◽  
Vol 23 (2) ◽  
pp. 190-190
Author(s):  
S. Y. Lee ◽  
H. Choo ◽  
P. K. Liaw ◽  
K. An ◽  
T. R. Watkins ◽  
...  

2019 ◽  
Vol 37 (5) ◽  
pp. 483-497
Author(s):  
A.K. Vasudevan ◽  
K. Sadananda ◽  
P.S. Pao

AbstractThe role of tensile overload superimposed on a constant amplitude cycling results in compressive residual stresses at the crack tip that cause crack growth retardation. The degree to which this effect manifests depends on whether the tests are done at a constant driving force (Kmax) or at a constant crack growth rate (da/dN). It is observed that depending on the magnitude of the overload at a given applied base stress intensity, these residual stresses can have significant effect on the crack growth in both the inert (vacuum) and the chemical (NaCl) environments. In general, cracks will grow only if the total crack tip driving force Ktotal exceeds the long crack intrinsic threshold ${\rm{K*}}_{{\rm{max,th}}}^{}.$ The crack growth retardation results can be attributed to the combined effects of the crack tip chemical reaction rates and the overload compressive residual stresses.


2004 ◽  
Vol 29 (4) ◽  
pp. 446-452 ◽  
Author(s):  
D.G. Pavlou ◽  
N.V. Vlachakis ◽  
M.G. Pavlou ◽  
V.N. Vlachakis

2014 ◽  
Vol 891-892 ◽  
pp. 948-954 ◽  
Author(s):  
Madeleine Burchill ◽  
Simon A. Barter ◽  
Michael Jones

It has often been observed that the growth of short fatigue cracks under variable amplitude (VA) cyclic loading is not well predicted when utilising standard constant amplitude (CA) crack growth rate/stress intensity data (da/dN v DK). This paper outlines a coupon fatigue test program and analyses, investigating a possible cause of crack growth retardation from CA-only testing. Various test loading spectra were developed with sub-blocks of VA and CA cycles, then using quantitative fractography (QF) the sub-block crack growth increments were measured. Comparison of these results found that, after establishing a consistent uniform crack front using a VA load sequence, the average crack growth rate then progressively slowed down with the number of subsequent CA load cycles applied. Further fractographic investigation of the fracture surface at the end of each CA and VA sub-block crack growth, identified significant crack front morphology differences. Thus it is postulated that a variation or deviation from an efficient crack path is a driver of local retardation in short crack growth during CA loading. This may be a source of error in analytical predictions of crack growth under VA spectra loading that may need to be considered in addition to other potential effects such asless closure whilst cracks are small. For aircraft designers, using solely CA data for fatigue life predictions this may result in non-conservative estimates of total crack fatigue life, producing unexpected failures or an increased maintenance burden.


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