Abstract
In this paper, a novel approach was proposed to increase the confidence of active slip system identification in polycrystalline metals. The approach takes advantage of microscale deformation tracking via Digital Image Correlation (DIC) combined with scanning electron microscopy (SEM). The experimentally-obtained high-resolution deformation fields were mapped to an undeformed configuration, which gives slip traces suitable for comparison with undeformed crystal orientation data. A metric, named herein as the ‘relative displacement ratio’ (RDR), is calculated from the displacement fields near slip traces to characterize the localized deformation due to slip. In validation cases, the experimentally-measured RDRs matched well with RDRs theoretically-calculated from active slip systems. In test cases, active slip system identification by incorporating RDR as an additional constraint was demonstrated to be preferable to using Schmid factor alone as a constraint. The proposed approach supplements existing techniques for slip system identification with increased confidence.
Similar content being viewed by others
References
Abuzaid WZ, Sangid MD, Carroll JD et al (2012) Slip transfer and plastic strain accumulation across grain boundaries in Hastelloy X. J Mech Phys Solids 60:1201–1220. doi:10.1016/j.jmps.2012.02.001
Aust KT, Chen NK (1954) Effect of orientation difference on the plastic deformation of aluminum bicrystals. Acta Metall 2:632–638. doi:10.1016/0001-6160(54)90199-6
Bieler TR, Eisenlohr P, Zhang C et al (2014) Grain boundaries and interfaces in slip transfer. Curr Opin Solid State Mater Sci 18:212–226. doi:10.1016/j.cossms.2014.05.003
Hosford WF (2009) Mechanical behavior of materials, second. Cambridge University Press, Cambridge
Koike J, Ohyama R (2005) Geometrical criterion for the activation of prismatic slip in AZ61 Mg alloy sheets deformed at room temperature. Acta Mater 53:1963–1972. doi:10.1016/j.actamat.2005.01.008
Luster J, Morris MA (1995) Compatibility of deformation in two-phase Ti-Al alloys: dependence on microstructure and orientation relationships. Metall Mater Trans A 26:1745–1756. doi:10.1007/BF02670762
Schmid E, Boas W (1968) Plasticity of crystals, with special reference to metals. Chapman & Hall, London
Bowen DK, Christian JW, Taylor G (1967) Deformation properties of niobium single crystals. Can J Phys 45:903–938. doi:10.1139/p67-069
Gröger R, Vitek V (2008) Breakdown of the Schmid law in bcc molybdenum related to the effect of shear stress perpendicular to the slip direction. Mater Sci Forum 482:123–126
Qin Q, Bassani JL (1992) Non-schmid yield behavior in single crystals. J Mech Phys Solids 40:813–833. doi:10.1016/0022-5096(92)90005-M
Šesták B, Zárubová N (1965) Asymmetry of slip in Fe-Si alloy single crystals. Phys Status Solidi 10:239–250. doi:10.1002/pssb.19650100124
Taylor GI (1928) The deformation of crystals of beta-brass. Proc R Soc London A Math Phys Eng Sci 118:1–24
Ball A, Smallman RE (1966) The operative slip system and general plasticity of NiAl-II. Acta Metall 14:1517–1526. doi:10.1016/0001-6160(66)90173-8
Boehlert CJ, Chen Z, Gutiérrez-Urrutia I et al (2012) In situ analysis of the tensile and tensile-creep deformation mechanisms in rolled AZ31. Acta Mater 60:1889–1904. doi:10.1016/j.actamat.2011.10.025
Keshavarz Z, Barnett MR (2006) EBSD analysis of deformation modes in Mg–3Al–1Zn. Scr Mater 55:915–918. doi:10.1016/j.scriptamat.2006.07.036
Lall C, Chin S, Pope DP (1979) The orientation and temperature dependence of the yield stress of Ni3(Al, Nb) single crystals. Metall Trans A 10:1323–1332
Loretto MH, Wasilewski RJ (1971) Slip systems in NiAl single crystals at 300°K and 77°K. Philos Mag 23:1311–1328. doi:10.1080/14786437108217004
Maurice C, Driver JH (1993) High temperature plane strain compression of cube oriented aluminium crystals. Acta Metall Mater 41:1653–1664. doi:10.1016/0956-7151(93)90185-U
Zaefferer S (2003) A study of active deformation systems in titanium alloys: dependence on alloy composition and correlation with deformation texture. Mater Sci Eng A 344:20–30. doi:10.1016/S0921-5093(02)00421-5
Chen Z, Boehlert CJ (2013) Evaluating the plastic anisotropy of AZ31 using microscopy techniques. JOM 65:1237–1244. doi:10.1007/s11837-013-0672-6
Chu TC, Ranson WF, Sutton MA (1985) Applications of digital-image-correlation techniques to experimental mechanics. Exp Mech 25:232–244. doi:10.1007/BF02325092
Peters WH, Ranson WF (1982) Digital imaging techniques in experimental stress analysis. Opt Eng 21:427–431
Sutton MA (1988) Effects of subpixel image restoration on digital correlation error estimates. Opt Eng 27:870–877. doi:10.1117/12.7976778
Sutton M, Wolters W, Peters W et al (1983) Determination of displacements using an improved digital correlation method. Image Vis Comput 1:133–139. doi:10.1016/0262-8856(83)90064-1
Sutton MA, Orteu JJ, Schreier H (2009) Image correlation for shape, motion and deformation measurements. Springer, New York. doi:10.1007/978-0-387-78747-3
Sutton MA, Li N, Garcia D et al (2006) Metrology in a scanning electron microscope: theoretical developments and experimental validation. Meas Sci Technol 17:2613–2622. doi:10.1088/0957-0233/17/10/012
Sutton MA, Li N, Joy DC et al (2007a) Scanning electron microscopy for quantitative small and large deformation measurements part I: SEM imaging at magnifications from 200 to 10,000. Exp Mech 47:775–787. doi:10.1007/s11340-007-9042-z
Sutton MA, Li N, Garcia D et al (2007b) Scanning electron microscopy for quantitative small and large deformation measurements part II: experimental validation for magnifications from 200 to 10,000. Exp Mech 47:789–804. doi:10.1007/s11340-007-9041-0
Kammers AD, Daly S (2013a) Digital image correlation under scanning electron microscopy: methodology and validation. Exp Mech 53:1743–1761. doi:10.1007/s11340-013-9782-x
Kammers AD, Daly S (2013b) Self-assembled nanoparticle surface patterning for improved digital image correlation in a scanning electron microscope. Exp Mech 53:1333–1341. doi:10.1007/s11340-013-9734-5
Callister WD, Rethwisch DG (2014) Materials science and engineering: an introduction. Wiley, Hoboken
Livingston JD, Chalmers B (1957) Multiple slip in bicrystal deformation. Acta Metall 5:322–327. doi:10.1016/0001-6160(57)90044-5
Shen Z, Wagoner RH, Clark WAT (1988) Dislocation and grain boundary interactions in metals. Acta Metall 36:3231–3242. doi:10.1016/0001-6160(88)90058-2
Werner E, Prantl W (1990) Slip transfer across grain and phase boundaries. Acta Metall Mater 38:533–537. doi:10.1016/0956-7151(90)90159-E
Bieler TR, Eisenlohr P, Roters F et al (2009) The role of heterogeneous deformation on damage nucleation at grain boundaries in single phase metals. Int J Plast 25:1655–1683. doi:10.1016/j.ijplas.2008.09.002
Guo Y, Britton TB, Wilkinson a J (2014) Slip band-grain boundary interactions in commercial-purity titanium. Acta Mater 76:1–12. doi:10.1016/j.actamat.2014.05.015
Li H, Mason DE, Bieler TR et al (2013) Methodology for estimating the critical resolved shear stress ratios of α-phase Ti using EBSD-based trace analysis. Acta Mater 61:7555–7567. doi:10.1016/j.actamat.2013.08.042
Aoki K, Izumi O (1978) Flow stress and work hardening in Ni3(Al·Ti) single crystals. Acta Metall 26:1257–1263. doi:10.1016/0001-6160(78)90010-X
Christian JW (1983) Some surprising features of the plastic-deformation of body-centered cubic metals and alloys. Metall Trans A-Physical Metall Mater Sci 14:1237–1256
Agnew SR, Duygulu Ö (2005) Plastic anisotropy and the role of non-basal slip in magnesium alloy AZ31B. Int J Plast 21:1161–1193. doi:10.1016/j.ijplas.2004.05.018
Obara T, Yoshinga H, Morozumi S (1973) {11-22} < −1-123 > Slip system in magnesium. Acta Metall 21:845–853. doi:10.1016/0001-6160(73)90141-7
Agnew SR, Tomé CN, Brown DW et al (2003) Study of slip mechanisms in a magnesium alloy by neutron diffraction and modeling. Scr Mater 48:1003–1008. doi:10.1016/S1359-6462(02)00591-2
Barnett MR (2003) A Taylor model based description of the proof stress of magnesium AZ31 during hot working. Metall Mater Trans A 34:1799–1806. doi:10.1007/s11661-003-0146-5
Acknowledgments
We gratefully acknowledge the funding provided to University of Michigan by the Office of Naval Research (Award Number: N00014-12-1-0013).
Author information
Authors and Affiliations
Corresponding author
Appendices
Appendix A
This appendix describes the procedure of calculating the predicted slip trace direction and theoretical RDR values for a given slip system based on crystal orientation data.
-
(1)
Express the slip plane normal and slip direction as a unit vector in a Cartesian coordinate system. For example, for basal slip system (0 0 0 1) [2–1 -1 0], the slip plane normal is expressed as a vector n’ = (0, 0, 1), and the slip direction is expressed as a vector m’ = (1, 0, 0). This Cartesian coordinate system is referred to as the ‘lattice coordinate system’.
-
(2)
Generate the transformation matrix (Q) between the lattice coordinate system (x’-y’-z’) to the sample coordinate system (x-y-z). Here, the sample coordinate system is a Cartesian coordinate system, with the x, y, and z axis along the longitudinal (loading direction), transverse, and normal direction of the sample. The transformation matrix Q between two coordinate systems, × 1 ’-× 2 ’-× 3 ’ and × 1 -× 2 -× 3 , is defined in a way such that the element on the ith row and jth column of Q is written as Q ij = cos(x i ’, x j ), where cos(x i ’, x j ) is the cosine of the angle between the x i ’-axis and the x j -axis. Based on this definition, a vector v ’ = [v 1’, v 2’, v 3’] in the x’-y’-z’ coordinate system can be expressed as v = v’Q in the x-y-z coordinate system. The crystal orientation is determined by EBSD and can be described by a set of Euler angles which represents a sequence of rotations about the coordinate axes, and through which the sample coordinate system becomes aligned with the lattice coordinate system. Therefore, for a given crystal orientation, a transformation matrix Q can be constructed.
-
(3)
Convert the slip plane normal and slip direction into the sample coordinate system, using the relationship n = n’Q, and m = m’Q.
-
(4)
The theoretical slip trace direction is calculated by taking the cross product of the slip plane normal n and the sample surface normal (0, 0, 1).
-
(5)
Let m = (m x , m y , m z ), the theoretical RDR is calculated as the ratio: m x /m y .
Appendix B
This appendix provides an analysis on the RDR measurement error due to lattice rotation.
As shown in Fig. 10, assume the black solid line is the slip trace line with an inclination of α degrees (we define the ‘inclination’ of a straight line to be the angle between x-direction and this line). The blue solid line is one of the lines along which the eleven data points were taken for RDR measurement. Because the blue line is perpendicular to the slip trace line, its inclination is (α˗90°). For simplicity, consider only the two data points at the ends of the blue line, and take one of them, in this case the left point, as the reference point, so its coordinate is (0, 0). Assume the length of the data line is L, then the coordinate of the right point is (L·cos(α˗90°), L·sin(α˗90°)). Next, assume slip occurs, and the displacement of the left point is (0, 0). Then, the displacement of the right point should be written in the form (u, u/r), where r is the theoretical RDR value:
Therefore, the coordinate of the right point is (L·cos(α˗90°) + u, L·sin(α˗90°) + u/r) after slip. Next, assume there is a lattice rotation of θ degrees around the left point, the final position of the right point can be calculated as (× 1, y 1) = (L·cos(α˗90°) + u, L·sin(α˗90°) + u/r) G ( θ ), where G is the transformation matrix and is a function of θ :
Therefore, the experimentally-measured RDR value is determined from the relative displacement between the right point and the left point, which is (× 1, y 1) – (L·cos(α˗90°), L·sin(α˗90°)). So,
It can be seen from this analysis that, even under such simple assumption, the measured RDR value affected by lattice rotation is a function of several variables instead of the lattice rotation alone. These variables include the: (1) theoretical RDR value; (2) inclination of the slip trace line, α; (3) lattice rotation angle, θ; (4) relative u-displacement, u. In general, θ and u are correlated, and both of them increase with increasing strain. For the current study, a rough approximation with u = 2θ could be used based on observation, where θ is in degrees and u is in pixels; and (5) the length of the data line, L. However, in our current study this value does not significantly change, and can be approximated as a constant, e.g., 20 pixels. As an example, quantitative assessment was performed on the slip traces in grains 125 and 136 to illustrate how the RDR measurement was affected by the aforementioned parameters, and the result is shown in Fig. 11. The rotation of each labeled slip trace, measured by tracking the displacement of the data points on the slip trace, was used to estimate the lattice rotation. The relative u-displacement was estimated by the range of centered-u values on the centered-u versus centered-v plot, such as the plot in Fig. 6d.
The simple model here provides an evaluation of the effect of lattice rotation. However, it should be noted that the experimentally-measured RDR is affected by many sources of error. Even limited to the effect of rotation, there are additional factors. For example, the sample could have rigid body rotation that is independent of slip activity. In addition, lattice rotation actually occurs in 3D, which is not considered in the above evaluation.
Rights and permissions
About this article
Cite this article
Chen, Z., Daly, S.H. Active Slip System Identification in Polycrystalline Metals by Digital Image Correlation (DIC). Exp Mech 57, 115–127 (2017). https://doi.org/10.1007/s11340-016-0217-3
Received:
Accepted:
Published:
Issue Date:
DOI: https://doi.org/10.1007/s11340-016-0217-3