Full length articleUsing architectured materials to control localized shear fracture
Graphical abstract
Introduction
One important mode of failure is by localized shear often at low overall strain. Localized shear fractures occur in a wide variety of materials including geological materials [1], bulk metallic Glasses [2], high strength steels [3], [4], heat treated aluminum alloys [5], [6] and magnesium alloys [7]. A variety of criteria have been developed to describe localized shear failure in terms of mechanics formulations [3], [8]. However the general formulation of the transition from general uniform plasticity to localized shear is complex because a variety of phenomena such as particle decohesion and void formation within the shear band, adiabatic heat leading to strain softening, or effects of negative rate sensitivity may arise depending on the specific material which is tested; Thus, it is difficult to delay the occurrence of localized shear fracture by changing the condition of a uniform microstructure. An alternative possibility is to limit the propagation of localized shear bands by introducing non-uniformities into the structure which prevent the growth of the localized shear bands. This is the concept of an architectured material in which a new length scale is introduced into the material in order to modify the mesoscopic non-uniformity of microstructure and properties in the material. In the current work, we have chosen to introduce this concept of an imposed architecture into a heat treated medium carbon steel which normally exhibits strain localization in its homogenous form. In the early literature, a seminal paper by Tanaka and Spretnak [3] analyzes the plastic instability in pure shear of a 4340 steel. We have chosen to perform tests on a steel of very similar composition in order to illustrate the benefits of the use of novel architectured materials to control this form of shear instability.
Section snippets
Experimental procedure
The starting material is a forged bar of aerospace-grade 300 M steel with homogenous composition, listed in Table 1 . Flat sheets with 3 mm thickness were machined. The samples were decarburized at 1075 °C under a CO/CO2 atmosphere of a given carbon activity for 90 min followed by oil quenching. The CO/CO2 ratio and decarburization time were adjusted to set the carbon content at the surface at 0.10 wt pct while the center remained at the nominal carbon content. A CO/CO2 ratio of 15.0 was
Initial structure
Fig. 1 shows the carbon and hardness profile of the as-quenched decarburized sample with an average carbon concentration of 0.3 wt pct. Hardness measurements show a two-fold increase in hardness from approximately 350 HV at the surface to 700 HV at the center. Experimental hardness data indicates a gradual increase in hardness from the surface to the center while carbon content gradually evolves from 0.1 to 0.4 wt pct, respectively. The hardness of the sample with homogenous composition
Discussion
To start, it is useful to summarize some of the key observations on the global deformation behaviour of martensite. Recent studies on the deformation of lath martensite confirm that slip is much easier within the plane of the lath and very difficult normal to it [14]. In addition, a small applied strain leads to the replacement of lath structure with a cell structure in ultra-low carbon martensite [15]. Increasing the carbon content stabilized the laths to higher strains. For a carbon content
Conclusions
In conclusion, the present study provides insights into the deformation of martensite and the development of shear localization in steels. It is shown that it is possible to deform as-quenched martensite in medium carbon steel to an equivalent strain in excess of 2.0, provided that the shear bands formed within the martensite are not allowed to reach the surface of the specimen. In this work, the shear bands were effectively contained by partial decarburization to create a compositionally
Acknowledgments
We would like to acknowledge Mr. Doug Colley for the help on experimental set up and execution. Dr. Vahid Tari is also acknowledged for his work on austenite grain reconstruction. Access to the Canadian Centre for Electron Microscopy, a national facility funded by NSERC and McMaster University is gratefully acknowledged.
References (21)
- et al.
Shear bands in metallic glasses
Mater. Sci. Eng. R Rep.
(2013) - et al.
Microstructural aspects of strain localization in Al-Mg alloys
Acta Metall.
(1986) - et al.
Mechanism of macroscopic shear band formation in plane strain compressed fine-grained aluminium
Mater. Sci. Eng. A
(2015) - et al.
On the role of non-basal deformation mechanisms for the ductility of Mg and Mg–Y alloys
Acta Mater.
(2011) - et al.
On critical conditions for shear band formation at high strain rates
Scr. Metall.
(1984) - et al.
Ultragrain refinement of plain low carbon steel by cold-rolling and annealing of martensite
Acta Mater.
(2002) - et al.
Effect of block size on the strength of lath martensite in low carbon steels
Mater. Sci. Eng. A
(2006) - et al.
An advanced approach to reconstructing parent orientation maps in the case of approximate orientation relations: application to steels
Acta Mater.
(2012) - et al.
Micro-tension behaviour of lath martensite structures of carbon steel
Mater. Sci. Eng. A
(2013) - et al.
The modes of deformation within an instability band in sheet tensile specimens
Scr. Metall.
(1974)