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In this work, the applicability of the two most commonly used equations for calculating the fracture toughness by nanoindentation is discussed in terms of the indenter geometry and the indentation crack morphology. These equations are calibrated for Berkovich and cube-corner indenters taking into account the actual indentation crack morphology, aimed at attaining a more reliable estimation of fracture toughness in small material volumes by nanoindentation. Hill's expanding cavity solution for an elastic-plastic solid and assuming a half-penny crack configuration, suggested the following expression to calculate K IC [5]:

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When indenting a brittle material with a sharp indenter, cracks can be generated at the corners of the imprint. From the length of these cracks, the fracture resistance can be estimated. This technique is simple and allows characterizing small volumes of materials, especially if nanoindentation cube-corners tips are used. For evaluation of fracture resistance, a number of different models based on crack morphology have been proposed. However, the morphology of the cracks is difficult to determine due to the small scales involved. In this work, indentation fracture with a cube-corner nanoindentation tip on different materials is investigated by FIB tomography to obtain the generated crack morphology. Experimental observations are rationalized in terms of applied load, tip geometry and crystal anisotropy. Once the crack morphology is visualized, the two most commonly used equations for calculating the fracture resistance are discussed. Finally, guidelines for better estimation of fracture resistance are proposed. (C) 2015 Elsevier Ltd. All rights reserved.Peer ReviewedPostprint (author’s final draft

Crack nucleation mechanisms in two types of cold work tool steels were evaluated under monotonic and cyclic loading conditions. The effect of the microstructural constituents: the primary alloy carbides and the tempered martensite matrix, and their interaction, was identified through fractographic analysis and determination of mechanical properties such as the bending strength, σR, the fatigue limit, Δσfat, and the fracture strength of the primary carbides under static tensile stressing, σRC. The response under monotonic loading was found to be governed by the fracture of primary carbides. The cracks nucleated when the applied stresses were higher than the carbides fracture strength, accordingly depending on their properties, morphology and arrangement. Under cyclic loading, despite failure origins were located at the primary carbides and cracks emanating from them and propagating through the metallic matrix were evidenced, crack nucleation phenomena could not be explained as in monotonic loading since the applied stresses in fatigue were lower than the determined σRC. Carbides fracture was then probably caused by damage observed in the metallic matrix. Primary carbides acted as stress concentrators and strain localization was more likely occurring in the matrix around them. Thus, fatigue failure was attributed to the destabilization of the tempered martensite of the matrix, induced by the strain localization processes around carbides, which produced their breakage and gave rise to fatigue propagating cracks.Postprint (published version

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