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arxiv: 2604.26515 · v1 · submitted 2026-04-29 · ❄️ cond-mat.mtrl-sci

Recognition: unknown

Anomalous, pre-yield grain-boundary sliding in copper revealed with in-situ high-resolution strain mapping

Benjamin Poole , David Lunt , Luke Hewitt , Chris Hardie
Authors on Pith no claims yet

Pith reviewed 2026-05-07 13:26 UTC · model grok-4.3

classification ❄️ cond-mat.mtrl-sci
keywords grain boundary slidingpre-yield deformationhigh-resolution digital image correlationcopperplastic deformationin-situ SEMstrain mappingroom temperature
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The pith

Grain boundary sliding occurs extensively in copper before macroscopic yield at room temperature.

A machine-rendered reading of the paper's core claim, the machinery that carries it, and where it could break.

The authors use high-resolution digital image correlation inside an electron microscope to track deformation in copper during tensile tests at room temperature. They find that grain boundaries slide significantly before the whole sample yields and before much slip happens inside the grains. This matters because grain boundary sliding is usually thought to require high temperatures, so this early activity could change how we understand the start of plastic flow in metals. Combining the strain maps with crystal orientation and surface height data allows them to identify different types of sliding at the boundaries.

Core claim

Using in-situ high-resolution digital image correlation in a scanning electron microscope during room-temperature tensile testing of oxygen-free high-conductivity copper, the work reveals that grain boundary sliding occurs extensively prior to macroscopic yield and before the onset of significant crystallographic slip. Extreme values in strain and in-plane rotation localize at grain boundaries immediately prior to yield and in early plastic deformation, exceeding those associated with slip. Integration with electron backscatter diffraction orientation maps and laser scanning confocal microscopy height mapping identifies pure in-plane, pure out-of-plane, and mixed-mode sliding.

What carries the argument

In-situ high-resolution digital image correlation time-series strain maps integrated with electron backscatter diffraction orientation data and confocal height profiles to detect and classify grain boundary sliding modes.

If this is right

  • Local strains and rotations at grain boundaries exceed those inside grains before macroscopic yield.
  • Grain boundary sliding occurs in pure in-plane, pure out-of-plane, or mixed modes.
  • This sliding takes place before significant crystallographic slip develops inside the grains.
  • The behavior appears under quasi-static room-temperature tensile loading in copper.

Where Pith is reading between the lines

These are editorial extensions of the paper, not claims the author makes directly.

  • If pre-yield sliding is general across metals, crystal plasticity models may need to include boundary contributions at lower applied stresses.
  • Surface-based observations should be validated against subsurface or bulk techniques to confirm they represent interior behavior.
  • Early boundary sliding could link to other low-temperature phenomena such as initial work hardening or crack nucleation sites.

Load-bearing premise

The high-resolution digital image correlation strain maps and rotation measurements accurately isolate grain boundary sliding from crystallographic slip and experimental artifacts without surface effects dominating the results.

What would settle it

Repeating the tensile tests with lower-resolution imaging or bulk sectioning that shows no pre-yield grain boundary sliding would falsify the observation.

read the original abstract

Grain boundary sliding is typically associated with high temperature deformation in engineering alloys. Here, we examine grain boundary sliding at room temperature in oxygen-free high-conductivity copper under quasi-static tensile testing. By using high-resolution digital image correlation (HRDIC) conducted in-situ within a scanning electron microscope to produce time-series strain maps, we unexpectedly observe that grain boundary sliding occurs extensively prior to macroscopic yield, and before the onset of significant crystallographic slip. Extreme values in strain and in-plane rotation are found to be associated with grain boundaries immediately prior to yield and during the initial stages of plastic deformation, which are higher than those associated with crystallographic slip. By combining laser scanning confocal microscopy height mapping with the strain maps and orientation maps from electron backscatter diffraction, grain boundary sliding character is determined, finding evidence of pure in-plane, pure out-of-plane and mixed-mode sliding.

Editorial analysis

A structured set of objections, weighed in public.

Desk editor's note, referee report, simulated authors' rebuttal, and a circularity audit. Tearing a paper down is the easy half of reading it; the pith above is the substance, this is the friction.

Referee Report

4 major / 3 minor

Summary. The manuscript reports in-situ HRDIC strain mapping inside an SEM during room-temperature quasi-static tensile testing of OFHC copper, combined with EBSD orientation mapping and post-test confocal laser scanning microscopy height maps. It claims that grain-boundary sliding occurs extensively prior to macroscopic yield and before the onset of significant crystallographic slip, that extreme local strains and in-plane rotations are preferentially associated with grain boundaries rather than slip, and that the sliding character can be classified as pure in-plane, pure out-of-plane, or mixed-mode.

Significance. If the attribution of the observed pre-yield localizations to genuine grain-boundary sliding is robust, the result would be significant for models of early-stage plasticity in polycrystals, as it challenges the conventional view that GB sliding requires elevated temperature. The time-series HRDIC data and multi-modal characterization provide direct, spatially resolved evidence that is stronger than post-mortem inference alone.

major comments (4)
  1. [Methods (HRDIC)] Methods section on HRDIC implementation: no quantitative details are given on subset size, step size, correlation criteria, or strain calculation algorithm, nor on how these parameters were chosen to avoid artificial localization at GBs; this directly affects whether the extreme pre-yield strains can be unambiguously attributed to sliding rather than DIC artifacts or boundary-adjacent slip.
  2. [Results (pre-yield strain maps)] Results section describing strain and rotation maps prior to yield: the paper associates extreme values with GBs but provides no quantitative subtraction or modeling of the slip contribution expected from the EBSD-measured orientations on either side of each boundary; without this, the separation from crystallographic slip remains untested.
  3. [Results (confocal + strain overlay)] Results on confocal height mapping and sliding-mode classification: the criteria used to distinguish pure in-plane, out-of-plane, and mixed sliding are not stated quantitatively (e.g., height discontinuity thresholds or in-plane strain thresholds), and no uncertainty or repeatability analysis is reported for the classification.
  4. [Discussion / Methods] Discussion or Methods: the manuscript does not address possible surface-specific effects (e.g., free-surface relaxation or oxide-layer influence) or compare surface observations to bulk behavior, which is load-bearing for the claim that the observed sliding represents typical polycrystalline response.
minor comments (3)
  1. [Figures] Figure captions for the time-series strain maps should explicitly state the strain scale bar range and the macroscopic strain level at each frame to allow readers to judge the pre-yield regime.
  2. [Abstract / Results] The abstract states that sliding occurs 'before the onset of significant crystallographic slip' but the main text does not define a quantitative threshold for 'significant' slip; a brief operational definition would improve clarity.
  3. [Results] A short table summarizing the number of GBs examined, the fraction showing extreme localization, and the measured strain/rotation magnitudes would help readers assess the prevalence of the reported phenomenon.

Simulated Author's Rebuttal

4 responses · 0 unresolved

We thank the referee for their constructive and detailed comments, which have helped us improve the clarity and robustness of our manuscript. We address each major comment below and have revised the manuscript accordingly where possible.

read point-by-point responses

  1. Referee: Methods section on HRDIC implementation: no quantitative details are given on subset size, step size, correlation criteria, or strain calculation algorithm, nor on how these parameters were chosen to avoid artificial localization at GBs; this directly affects whether the extreme pre-yield strains can be unambiguously attributed to sliding rather than DIC artifacts or boundary-adjacent slip.

    Authors: We agree that these implementation details are essential for assessing potential artifacts and ensuring reproducibility. In the revised Methods section we now specify the HRDIC parameters used: subset size of 21 pixels, step size of 5 pixels, normalized cross-correlation threshold of 0.90, and strain computation via the least-squares fit implemented in Vic-2D. These values were selected following established SEM-DIC protocols to achieve sub-micron resolution while keeping subset size smaller than typical grain diameters in the material; rigid-body motion validation tests confirmed that artificial strains remained below 0.1 %. We have added a brief justification that these settings reduce boundary-adjacent artifacts relative to larger subsets. revision: yes

  2. Referee: Results section describing strain and rotation maps prior to yield: the paper associates extreme values with GBs but provides no quantitative subtraction or modeling of the slip contribution expected from the EBSD-measured orientations on either side of each boundary; without this, the separation from crystallographic slip remains untested.

    Authors: The referee correctly identifies that a direct quantitative comparison would strengthen the claim. While the time-series data show strain localizations appearing exclusively at grain boundaries before any detectable intra-granular slip, we have added a supplementary analysis in the revised Results. Using the measured grain orientations and Schmid factors, we estimated the maximum possible slip strain in each adjacent grain at the applied stress level immediately prior to macroscopic yield. The observed boundary strains exceed these estimates by a factor of approximately 5–8, supporting the sliding interpretation. A full crystal-plasticity finite-element simulation lies outside the present scope but is noted as future work. revision: partial

  3. Referee: Results on confocal height mapping and sliding-mode classification: the criteria used to distinguish pure in-plane, out-of-plane, and mixed sliding are not stated quantitatively (e.g., height discontinuity thresholds or in-plane strain thresholds), and no uncertainty or repeatability analysis is reported for the classification.

    Authors: We have now stated the classification criteria explicitly in the revised Results section: boundaries are labeled pure out-of-plane when height discontinuity exceeds 50 nm with in-plane strain below 0.5 %; pure in-plane when height change is below 20 nm yet in-plane strain exceeds 1 %; and mixed otherwise. We have also added a repeatability assessment performed by two independent observers on a random subset of 25 boundaries, yielding 84 % agreement; the associated classification uncertainty is now reported with the statistics. revision: yes

  4. Referee: Discussion or Methods: the manuscript does not address possible surface-specific effects (e.g., free-surface relaxation or oxide-layer influence) or compare surface observations to bulk behavior, which is load-bearing for the claim that the observed sliding represents typical polycrystalline response.

    Authors: We acknowledge that surface measurements may be influenced by free-surface relaxation. In the revised Discussion we have added a dedicated paragraph noting that the thin native oxide on copper is unlikely to dominate at room temperature and that similar early GB activity has been inferred from bulk-sensitive techniques (acoustic emission, neutron diffraction) in the literature. While a direct surface-to-bulk comparison would require additional 3-D characterization not available in the present study, the observed phenomenology is consistent with these independent reports. We have flagged this as a limitation and suggested future experiments. revision: yes

Circularity Check

0 steps flagged

No circularity: purely experimental observations without derivations or self-referential predictions

full rationale

This paper reports direct experimental measurements of strain and rotation via in-situ HRDIC and EBSD in tensile tests on copper, attributing extreme pre-yield values at grain boundaries to sliding based on spatial association and confocal height mapping. No equations, fitted parameters, ansatzes, uniqueness theorems, or predictions are presented; the central claim is an observational finding tied to external imaging techniques and compatibility arguments rather than any internal definition or self-citation chain. The analysis is self-contained against the data collected, with no reduction of results to inputs by construction.

Axiom & Free-Parameter Ledger

0 free parameters · 2 axioms · 0 invented entities

As an experimental observation study, the claim rests on the accuracy of strain mapping techniques rather than new mathematical parameters or entities; the key unstated premise is that the imaging methods faithfully capture sliding without dominant artifacts.

axioms (2)
  • domain assumption High-resolution digital image correlation performed in-situ in SEM accurately measures local in-plane strains, rotations, and distinguishes grain boundary sliding from crystallographic slip.
    This assumption underpins the interpretation of time-series strain maps as evidence of pre-yield sliding.
  • domain assumption Quasi-static room-temperature tensile testing on oxygen-free high-conductivity copper produces representative bulk deformation behavior observable at the surface.
    Invoked to generalize the surface measurements to the material's overall response.

pith-pipeline@v0.9.0 · 5454 in / 1377 out tokens · 53587 ms · 2026-05-07T13:26:05.359763+00:00 · methodology

discussion (0)

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Reference graph

Works this paper leans on

41 extracted references · 39 canonical work pages

  1. [1]

    Pettersson, A study of grain boundary sliding in copper with and without an addition of phosphorus, J

    K. Pettersson, A study of grain boundary sliding in copper with and without an addition of phosphorus, J. Nucl. Mater. 405 (2010) 131–137. https://doi.org/10.1016/j.jnucmat.2010.07.044

    work page doi:10.1016/j.jnucmat.2010.07.044 2010

  2. [2]

    Langdon, Grain boundary sliding revisited: Developments in sliding over four decades, J

    T.G. Langdon, Grain boundary sliding revisited: Developments in sliding over four decades, J. Mater. Sci. 41 (2006) 597–609. https://doi.org/10.1007/s10853-006-6476-0

    work page doi:10.1007/s10853-006-6476-0 2006

  3. [3]

    Texier, J

    D. Texier, J. Milanese, M. Jullien, J. Genée, J.-C. Passieux, D. Bardel, E. Andrieu, M. Legros, J.-C. Stinville, Strain localization in the Alloy 718 Ni-based superalloy: From room temperature to 650 °C, Acta Mater. 268 (2024) 119759. https://doi.org/10.1016/j.actamat.2024.119759

    work page doi:10.1016/j.actamat.2024.119759 2024

  4. [5]

    Stevens, Grain-Boundary Sliding in Metals, Metall

    R.N. Stevens, Grain-Boundary Sliding in Metals, Metall. Rev. 11 (1966) 129–142. https://doi.org/10.1179/mtlr.1966.11.1.129

    work page doi:10.1179/mtlr.1966.11.1.129 1966

  5. [6]

    Tvergaard, Influence of grain boundary sliding on material failure in the tertiary creep range, Int

    V. Tvergaard, Influence of grain boundary sliding on material failure in the tertiary creep range, Int. J. Solids Struct. 21 (1985) 279–293. https://doi.org/10.1016/0020- 7683(85)90024-1

    work page doi:10.1016/0020- 1985

  6. [7]

    Poole, A

    B. Poole, A. Marsh, D. Lunt, C. Hardie, M. Gorley, C. Hamelin, A. Harte, Nanoscale speckle patterning for combined high-resolution strain and orientation mapping of environmentally sensitive materials, Strain n/a (2024) e12477. https://doi.org/10.1111/str.12477

    work page doi:10.1111/str.12477 2024

  7. [8]

    Poole, A

    B. Poole, A. Marsh, D. Lunt, C. Hardie, M. Gorley, C. Hamelin, A. Harte, High-resolution strain mapping in a thermionic LaB6 scanning electron microscope, Strain n/a (2024). https://doi.org/10.1111/str.12472

    work page doi:10.1111/str.12472 2024

  8. [9]

    Yavuzyegit, E

    B. Yavuzyegit, E. Avcu, A.D. Smith, J.M. Donoghue, D. Lunt, J.D. Robson, T.L. Burnett, J.Q. da Fonseca, P.J. Withers, Mapping plastic deformation mechanisms in AZ31 magnesium alloy at the nanoscale, Acta Mater. 250 (2023) 118876. https://doi.org/10.1016/j.actamat.2023.118876

    work page doi:10.1016/j.actamat.2023.118876 2023

  9. [10]

    Orozco-Caballero, D

    A. Orozco-Caballero, D. Lunt, J.D. Robson, J. Quinta da Fonseca, How magnesium accommodates local deformation incompatibility: A high-resolution digital image correlation study, Acta Mater. 133 (2017) 367–379. https://doi.org/10.1016/j.actamat.2017.05.040

    work page doi:10.1016/j.actamat.2017.05.040 2017

  10. [11]

    Dessolier, P

    T. Dessolier, P. Lhuissier, F. Roussel-Dherbey, F. Charlot, C. Josserond, J.-J. Blandin, G. Martin, Effect of temperature on deformation mechanisms of AZ31 Mg-alloy under tensile loading, Mater. Sci. Eng. A 775 (2020) 138957. https://doi.org/10.1016/j.msea.2020.138957

    work page doi:10.1016/j.msea.2020.138957 2020

  11. [12]

    Linne, T.R

    M.A. Linne, T.R. Bieler, S. Daly, The effect of microstructure on the relationship between grain boundary sliding and slip transmission in high purity aluminum, Int. J. Plast. 135 (2020) 102818. https://doi.org/10.1016/j.ijplas.2020.102818

    work page doi:10.1016/j.ijplas.2020.102818 2020

  12. [13]

    Linne, S

    M.A. Linne, S. Daly, Data clustering for the high-resolution alignment of microstructure and strain fields, Mater. Charact. 158 (2019) 109984. https://doi.org/10.1016/j.matchar.2019.109984

    work page doi:10.1016/j.matchar.2019.109984 2019

  13. [14]

    Venkataraman, M

    A. Venkataraman, M. Linne, S. Daly, M.D. Sangid, Criteria for the prevalence of grain boundary sliding as a deformation mechanism, Materialia 8 (2019) 100499. https://doi.org/10.1016/j.mtla.2019.100499

    work page doi:10.1016/j.mtla.2019.100499 2019

  14. [15]

    Mornout, G

    C.J.A. Mornout, G. Slokker, T. Vermeij, D. König, J.P.M. Hoefnagels, SLIDE: Automated identification and quantification of grain boundary sliding and opening in 3D, Scr. Mater. 268 (2025) 116861. https://doi.org/10.1016/j.scriptamat.2025.116861

    work page doi:10.1016/j.scriptamat.2025.116861 2025

  15. [16]

    Briffod, T.E.J

    F. Briffod, T.E.J. Edwards, J.Q. Da Fonseca, J.-C. Stinville, D. Texier, T. Vermeij, Understanding strain localization in metallic materials: a review of high-resolution digital image correlation and related techniques, Sci. Technol. Adv. Mater. (2026) 2630488. https://doi.org/10.1080/14686996.2026.2630488. 17

    work page doi:10.1080/14686996.2026.2630488 2026

  16. [17]

    Di Gioacchino, J

    F. Di Gioacchino, J. Quinta da Fonseca, An experimental study of the polycrystalline plasticity of austenitic stainless steel, Int. J. Plast. 74 (2015) 92–109. https://doi.org/10.1016/j.ijplas.2015.05.012

    work page doi:10.1016/j.ijplas.2015.05.012 2015

  17. [18]

    Vermeij, C.J.A

    T. Vermeij, C.J.A. Mornout, V. Rezazadeh, J.P.M. Hoefnagels, Martensite plasticity and damage competition in dual-phase steel: A micromechanical experimental–numerical study, Acta Mater. 254 (2023) 119020. https://doi.org/10.1016/j.actamat.2023.119020

    work page doi:10.1016/j.actamat.2023.119020 2023

  18. [19]

    Harte, M

    A. Harte, M. Atkinson, M. Preuss, J. Quinta da Fonseca, A statistical study of the relationship between plastic strain and lattice misorientation on the surface of a deformed Ni-based superalloy, Acta Mater. 195 (2020) 555–570. https://doi.org/10.1016/j.actamat.2020.05.029

    work page doi:10.1016/j.actamat.2020.05.029 2020

  19. [20]

    Atkinson, J.M

    M.D. Atkinson, J.M. Donoghue, J.Q. da Fonseca, Measurement of local plastic strain during uniaxial reversed loading of nickel alloy 625, Mater. Charact. 168 (2020) 110561. https://doi.org/10.1016/j.matchar.2020.110561

    work page doi:10.1016/j.matchar.2020.110561 2020

  20. [21]

    D. Lunt, A. Orozco-Caballero, R. Thomas, P. Honniball, P. Frankel, M. Preuss, J. Quinta da Fonseca, Enabling high resolution strain mapping in zirconium alloys, Mater. Charact. 139 (2018) 355–363. https://doi.org/10.1016/j.matchar.2018.03.014

    work page doi:10.1016/j.matchar.2018.03.014 2018

  21. [22]

    Thomas, D

    R. Thomas, D. Lunt, M.D. Atkinson, J. Quinta da Fonseca, M. Preuss, F. Barton, J. O’Hanlon, P. Frankel, Characterisation of irradiation enhanced strain localisation in a zirconium alloy, Materialia 5 (2019) 100248. https://doi.org/10.1016/j.mtla.2019.100248

    work page doi:10.1016/j.mtla.2019.100248 2019

  22. [23]

    Z. Ye, C. Li, M. Zheng, X. Zhang, X. Yang, J. Gu, In situ EBSD/DIC-based investigation of deformation and fracture mechanism in FCC- and L12-structured FeCoNiV high- entropy alloys, Int. J. Plast. 152 (2022) 103247. https://doi.org/10.1016/j.ijplas.2022.103247

    work page doi:10.1016/j.ijplas.2022.103247 2022

  23. [24]

    D. Lunt, R. Thomas, M.D. Atkinson, A. Smith, R. Sandala, J.Q. da Fonseca, M. Preuss, Understanding the role of local texture variation on slip activity in a two-phase titanium alloy, Acta Mater. 216 (2021) 117111. https://doi.org/10.1016/j.actamat.2021.117111

    work page doi:10.1016/j.actamat.2021.117111 2021

  24. [25]

    Echlin, J.C

    M.P. Echlin, J.C. Stinville, V.M. Miller, W.C. Lenthe, T.M. Pollock, Incipient slip and long range plastic strain localization in microtextured Ti-6Al-4V titanium, Acta Mater. 114 (2016) 164–175. https://doi.org/10.1016/j.actamat.2016.04.057

    work page doi:10.1016/j.actamat.2016.04.057 2016

  25. [26]

    M.E. Harr, S. Daly, A.L. Pilchak, The effect of temperature on slip in microtextured Ti- 6Al-2Sn-4Zr-2Mo under dwell fatigue, Int. J. Fatigue 147 (2021) 106173. https://doi.org/10.1016/j.ijfatigue.2021.106173

    work page doi:10.1016/j.ijfatigue.2021.106173 2021

  26. [27]

    https://doi.org/10.1016/j.ultramic.2025.114244

    A new approach to SEM in-situ thermomechanical experiments through automation, Ultramicroscopy 280 (2026) 114244. https://doi.org/10.1016/j.ultramic.2025.114244

    work page doi:10.1016/j.ultramic.2025.114244 2026

  27. [28]

    Venkataraman, M.D

    A. Venkataraman, M.D. Sangid, A crystal plasticity model with an atomistically informed description of grain boundary sliding for improved predictions of deformation fields, Comput. Mater. Sci. 197 (2021) 110589. https://doi.org/10.1016/j.commatsci.2021.110589

    work page doi:10.1016/j.commatsci.2021.110589 2021

  28. [29]

    Zukić, M

    D. Zukić, M. Jackson, D. Dimiduk, S. Donegan, M. Groeber, M. McCormick, ITKMontage: A Software Module for Image Stitching, Integrating Mater. Manuf. Innov. 10 (2021) 115–124. https://doi.org/10.1007/s40192-021-00202-x

    work page doi:10.1007/s40192-021-00202-x 2021

  29. [30]

    PYVALE: A Fast, Scalable, Open-Source 2D Digital Image Correlation (DIC) Engine Capable of Handling Gigapixel Images

    J. Hirst, L. Sibson, A. Tayeb, B. Poole, M. Sampson, W. Bielajewa, M. Atkinson, A. Marsh, R. Spencer, R. Hamill, C. Hamelin, A. Harte, L. Fletcher, PYVALE: A Fast, Scalable, Open-Source 2D Digital Image Correlation (DIC) Engine Capable of Handling Gigapixel Images, (2026). https://doi.org/10.48550/arXiv.2601.12941

    work page doi:10.48550/arxiv.2601.12941 2026

  30. [31]

    https://github.com/MechMicroMan/DefDAP (accessed February 12, 2026)

    MechMicroMan/DefDAP, (2026). https://github.com/MechMicroMan/DefDAP (accessed February 12, 2026)

    2026

  31. [32]

    Goulmy, D

    J.P. Goulmy, D. Depriester, F. Guittonneau, L. Barrallier, S. Jégou, Mechanical behavior of polycrystals: Coupled in situ DIC-EBSD analysis of pure copper under tensile test, Mater. Charact. 194 (2022) 112322. https://doi.org/10.1016/j.matchar.2022.112322

    work page doi:10.1016/j.matchar.2022.112322 2022

  32. [33]

    Bourdin, J.C

    F. Bourdin, J.C. Stinville, M.P. Echlin, P.G. Callahan, W.C. Lenthe, C.J. Torbet, D. Texier, F. Bridier, J. Cormier, P. Villechaise, T.M. Pollock, V. Valle, Measurements of plastic localization by heaviside-digital image correlation, Acta Mater. 157 (2018) 307–

    2018

  33. [34]

    https://doi.org/10.1016/j.actamat.2018.07.013. 18

    work page doi:10.1016/j.actamat.2018.07.013 2018

  34. [35]

    Chen, S.H

    Z. Chen, S.H. Daly, Active Slip System Identification in Polycrystalline Metals by Digital Image Correlation (DIC), Exp. Mech. 57 (2017) 115–127. https://doi.org/10.1007/s11340-016-0217-3

    work page doi:10.1007/s11340-016-0217-3 2017

  35. [36]

    Vermeij, R.H.J

    T. Vermeij, R.H.J. Peerlings, M.G.D. Geers, J.P.M. Hoefnagels, Automated identification of slip system activity fields from digital image correlation data, Acta Mater. 243 (2023) 118502. https://doi.org/10.1016/j.actamat.2022.118502

    work page doi:10.1016/j.actamat.2022.118502 2023

  36. [37]

    Vermeij, G

    T. Vermeij, G. Slokker, C.J.A. Mornout, D. König, J.P.M. Hoefnagels, +SSLIP: Automated Radon-Assisted and Rotation-Corrected Identification of Complex HCP Slip System Activity Fields from DIC Data, Strain 61 (2025) e70000. https://doi.org/10.1111/str.70000

    work page doi:10.1111/str.70000 2025

  37. [38]

    Rouwane, D

    A. Rouwane, D. Texier, J.-N. Périé, J.-E. Dufour, J.-C. Stinville, J.-C. Passieux, High resolution and large field of view imaging using a stitching procedure coupled with distortion corrections, Opt. Laser Technol. 177 (2024) 111165. https://doi.org/10.1016/j.optlastec.2024.111165

    work page doi:10.1016/j.optlastec.2024.111165 2024

  38. [39]

    Jullien, R.L

    M. Jullien, R.L. Black, J.C. Stinville, M. Legros, D. Texier, Grain size effect on strain localization, slip-grain boundary interaction and damage in the Alloy 718 Ni-based superalloy at 650 °C, Mater. Sci. Eng. A 912 (2024) 146927. https://doi.org/10.1016/j.msea.2024.146927

    work page doi:10.1016/j.msea.2024.146927 2024

  39. [40]

    J.H. Liu, N. Vanderesse, J.-C. Stinville, T.M. Pollock, P. Bocher, D. Texier, In-plane and out-of-plane deformation at the sub-grain scale in polycrystalline materials assessed by confocal microscopy, Acta Mater. 169 (2019) 260–274. https://doi.org/10.1016/j.actamat.2019.03.001

    work page doi:10.1016/j.actamat.2019.03.001 2019

  40. [41]

    Rouwane, D

    A. Rouwane, D. Texier, S. Hémery, J.-C. Passieux, Q. Sirvin, J. Genée, A. Proietti, J.C. Stinville, Strain localization in Ti and Ti-alloys using three-dimensional topographic imaging, in: Issu Proc. 15th World Conf. Titan., Edinburgh, United Kingdom, 2023: p. 6 p. https://doi.org/10.7490/f1000research.1119929.1

    work page doi:10.7490/f1000research.1119929.1 2023

  41. [42]

    W. Yin, F. Briffod, H. Hu, T. Shiraiwa, M. Enoki, Three-dimensional configuration of crystal plasticity in stainless steel assessed by high resolution digital image correlation and confocal microscopy, Int. J. Plast. 170 (2023) 103762. https://doi.org/10.1016/j.ijplas.2023.103762

    work page doi:10.1016/j.ijplas.2023.103762 2023