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REVIEW 3 major objections 3 minor 59 references

Strain heterogeneity and micro-damage nucleation under tensile stresses in an Mg-5Al-3Ca alloy with an intermetallic skeleton

T0 review · 3 major / 3 minor · reviewed 2026-08-14 · deepseek-v4-flash

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Pith's one-line read In Mg-5Al-3Ca, cracks nucleate in the Laves phase where slip lines or twins meet the α-Mg interface, then grow along the Laves network.

desk verdict A careful quasi in-situ DIC study of crack nucleation in Mg-Al-Ca that makes a good case but overreaches slightly in claiming bulk support for slip-interface cracks. read the letter →

arxiv 1908.08271 v1 pith:TEAZ3XTW submitted 2019-08-22 cond-mat.mtrl-sci

Muhammad Zubair , Stefanie Sandlöbes-Haut , Max A. Wollenweber , Katrin Bugelnig , Carl F. Kusche , Guillermo Requena , Sandra Korte-Kerzel This is my paper · ORCID
classification cond-mat.mtrl-sci
keywords μ-DICstrainheterogeneityEulernumbermicro-cracksMg-Al-CaalloyLavesphasehigh-temperaturetensiledeformationtwinning
verification ladder T0 review T1 audit T2 compute T3 formal

The pith

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

The reading

At 170 °C, the two-phase magnesium alloy AX53 fails not by uniform plastic flow but by a two-stage process documented here at sub-micrometer resolution. The α-Mg matrix carries nearly all of the imposed strain, deforming by basal slip and tensile twinning in grains well oriented for those modes, while the hard (Mg,Al)2Ca Laves skeleton remains almost undeformed. Strain then concentrates at the α-Mg/Laves interfaces, and micro-cracks nucleate inside the Laves phase precisely where slip lines or twins intersect those interfaces. With further straining, cracks propagate preferentially along the connected Laves network, so a more interconnected skeleton raises strength but lowers ductility. If this picture is right, it gives alloy designers a concrete lever: Laves-phase connectivity and basal-slip texture should control the strength–formability trade-off in creep-resistant Mg-Al-Ca alloys.

What carries the argument

The argument runs on two instruments. First, micro-digital image correlation (μ-DIC) on a polished surface speckled only by residual SiO2 nanoparticles from the final polish, stitched into panoramic images, turns the microstructure into a strain field with facet size 0.55 µm; this is what lets the authors see that strain is carried by α-Mg and accumulates at interfaces. Second, the Euler number $\chi = b_0 - b_1$ (objects minus holes) of the segmented Laves network is the topological quantity that measures skeleton connectivity; its increase from −1363 to −594 after 4% strain is the quantitative sign that deformation fragments the hard skeleton. These instruments are tied together by Schmid-factor mapping of basal slip and tensile twinning, which explains why only certain α-Mg grains carry strain and therefore host crack-nucleation sites at their interfaces with the Laves phase. The material-level mechanism is dislocation pile-up: basal slip and twins impinge on the hard Laves skeleton, concentrating stress at the interface and cracking the Laves phase.

What would settle it

Run in-situ tensile loading at 170 °C inside a synchrotron micro-tomography setup and reconstruct crack nucleation sites in 3D as a function of strain. If most cracks do not lie at intersections of basal slip traces or twins with α-Mg/Laves interfaces, or if the fracture path does not follow the Laves network, the proposed nucleation-and-growth mechanism fails.

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Extended reading notes

Core claim

The paper's central claim is that in as-cast AX53 the soft α-Mg matrix accommodates the imposed strain while the (Mg,Al)2Ca Laves phase concentrates stress at interfaces and determines failure. Using quasi in-situ micro-DIC maps with a facet size of 0.55 µm, the authors find that local von Mises strains remain low, around 0.5–1.5%, while the global strain reaches 4%, which they read as the Laves phase staying nearly elastic. Strain hot spots appear on basal slip traces, at tensile twins, along α-Mg/Laves interfaces, and between eutectic Laves lamellae. Crack nucleation in the Laves phase occurs preferentially at intersections of basal slip lines with the interfaces, at twin-interface intersections, and where twins transmit across the interface; bulk post-mortem samples show the same twin-related nucleation sites, indicating the surface observations are not purely a free-surface artifact. The Euler number of the segmented Laves network rises from −1363 to −594 after 4% strain, quantifying fragmentation of the skeleton, and final fracture follows the Laves network. The conclusion is that a highly connected Laves skeleton raises yield strength and creep resistance but provides a continuous crack path that limits ductility.

Load-bearing premise

The load-bearing premise is that strain and crack statistics gathered from a polished free surface, with residual SiO2 nanoparticles as speckles, faithfully represent bulk tensile behavior at 170 °C; the paper's bulk post-mortem images support this for twin-related cracks but do not fully test it for the DIC strain fields and Euler-number changes.

Editorial extensions

If this is right

  • In AX53, a highly interconnected Laves network should raise yield strength and creep resistance but lower tensile ductility, because the network supplies a continuous crack path.
  • Changing the Ca/Al ratio to reduce Laves-phase connectivity should trade some strength for improved formability, as the paper's comparison of alloys with different Ca/Al ratios already suggests.
  • Texture engineering that lowers the Schmid factor for basal slip and tensile twinning should reduce the number of crack-nucleation sites at α-Mg/Laves interfaces.
  • Euler-number analysis of the Laves skeleton can serve as a quantitative screening metric for cast Mg-Al-Ca alloys before mechanical testing.
  • Damage prediction in such alloys should treat slip-band and twin impingement on the Laves phase, not just average phase properties, as the nucleation criterion.

Reading between the lines

Editorial extensions of the paper, not claims the author makes directly.

  • Because the DIC strain fields became unusable at 5.5% strain due to surface topography, a synchrotron tomography version of this experiment could test whether the surface-observed crack sites and Laves-network fragmentation are statistically representative of the bulk in three dimensions.
  • The attribution of interface strain concentrations to grain and phase boundary sliding at 170 °C predicts a direct temperature contrast: the same alloy tested at room temperature should show less interface-localized strain and more slip-dominated damage, a comparison the paper does not make with DIC.
  • If the impingement criterion is transferable, then pre-straining to introduce a controlled twin density, or microstructural changes that shorten basal slip-band lengths, should shift crack nucleation to higher global strains in Mg-Al-Ca alloys.
  • The same μ-DIC plus Euler-number methodology could be applied to other skeleton-forming cast alloys, such as Al-Si eutectics, with the testable prediction that the rise in Euler number at failure scales with ductility loss.
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Editorial analysis

A structured set of objections, weighed in public.

Desk editor's note, referee report, and a circularity audit.

Referee Report

3 major / 3 minor

Summary. This paper investigates strain heterogeneity and micro-damage nucleation in an as-cast Mg-5Al-3Ca (AX53) alloy during tensile deformation at 170°C using quasi in-situ micro-DIC, EBSD, and Euler number analysis. The authors report that the α-Mg matrix carries most of the imposed strain, strain concentrates along basal slip traces, deformation twins, and α-Mg/Laves phase interfaces, and cracks nucleate in the (Mg,Al)2Ca Laves phase at intersections of basal slip lines and twins with the phase interfaces. They also report that the connectivity of the Laves phase network decreases with deformation and that cracks propagate preferentially along the Laves phase skeleton. The conclusions connect these observations to the trade-off between strength and ductility in Mg-Al-Ca alloys.

Significance. If the central mechanistic claims hold, this work provides a valuable microstructural explanation for the limited formability of Mg-Al-Ca alloys with a continuous intermetallic skeleton: the hard Laves phase acts as a crack nucleation site at localized strain concentrations and as a preferential crack path. The study combines several complementary techniques (SE/BSE imaging, EBSD, μ-DIC, Euler number analysis) and includes a quasi in-situ surface observation supplemented by a bulk post-mortem check, which is a strong feature. The Schmid factor correlation and the quantitative connectivity analysis are useful and go beyond purely descriptive observations. The main limitation, however, is that the dominant crack nucleation mechanism (slip-line/interface intersections) is only directly observed on the free surface, while the bulk validation covers only twin/interface intersections, leaving part of the central claim under-supported.

major comments (3)
  1. [§3.4, Fig. 9; Conclusions point 2] The bulk post-mortem analysis presented in Fig. 9 provides evidence of crack nucleation at twin–α-Mg/Laves phase interface intersections, but it does not show any slip-line–interface cracks. Since Fig. 11(e) reports that slip-interface cracks are the dominant crack type on the surface, and slip lines are surface topographic features that may produce stress concentrations not present in the bulk, the statement in the Abstract and Conclusions that 'quasi in-situ and bulk material analysis' supports crack nucleation at slip line–interface intersections is not supported by the shown bulk data. Please either provide bulk evidence for slip-induced nucleation (e.g., via EBSD trace analysis on samples where slip activity is retained, or serial sectioning to find slip-associated cracks), or explicitly restrict the bulk validation claim to twin-interface nucleation.
  2. [§3.3, Fig. 6; §4.2] The quantitative claim that the α-Mg phase carries most of the imposed strain and that local von Mises strains are about 0.5–1.5% at 4% global strain rests on a single panoramic DIC region with no uncertainty quantification. No replicate measurements, error bars, or DIC displacement/strain uncertainty estimates are reported. Since this single region is the basis for a central conclusion, please add a statement about DIC measurement error and ideally show that the qualitative strain partitioning pattern is reproducible across at least one additional region.
  3. [§3.3, Fig. 7; §2] The Euler number connectivity analysis relies on a global gray-value threshold for segmenting the Laves phase network (Section 2), but no sensitivity analysis of the threshold choice is presented. Because the Euler number is a topological metric that can be sensitive to segmentation details, a brief threshold variation test or a statement of the threshold selection criterion would increase confidence in the reported connectivity decrease from -1363 to -594.
minor comments (3)
  1. [§2] There is a typo: 'An a cceleration voltage' should be 'An acceleration voltage'.
  2. [§3.3, Fig. 5] The text refers to 'deformed image at a stage tilt of 70°' and to unit cells in panel (d), but the caption and surrounding sentences do not clearly map panels (a)–(e); please clarify the panel references.
  3. [§3.3, Fig. 6 caption] The caption lists red, yellow, white, black, and orange arrows but the corresponding legend in the text (Section 3.3) does not explicitly state which color corresponds to strain concentration 'in between the eutectic Laves lamellas' (orange arrows) until later; a direct mapping in the caption would improve readability.

Circularity Check

0 steps flagged · score 0.0 of 10

No circularity: the paper presents an observational microstructural study whose claims rest on independently measured images, strain maps, and topological parameters, not on definitions or fitted inputs.

full rationale

This paper is an experimental characterization study, not a derivation or modeling paper. Its central claims (strain carried mainly by the alpha-Mg phase, strain concentration at alpha-Mg/Laves interfaces, crack nucleation in the Laves phase at slip-line and twin intersections, and preferential crack growth along the Laves network) are established by quasi in-situ SEM imaging, mu-DIC strain maps, EBSD orientation/Schmid-factor analysis, segmented Laves-phase network images, and Euler-number counting. None of these results is computed from a model whose output equals its input. The Euler number is defined topologically, but the reported values are independently measured from segmented 2D images before and after deformation, so no fitted parameter is renamed as a prediction. The authors cite their own earlier work (Zubair et al. [16]) for microstructure comparison, mechanical-property context, and methodological precedent, and they cite Kruglova et al. [36] for the use of Euler numbers in Al-Si alloys; these citations are contextual and comparative, not load-bearing reductions of the present observations. The only notable weakness is that the bulk post-mortem validation (Fig. 9) shows cracks only at twin-interface intersections, while slip-interface cracks, which Fig. 11(e) reports as more numerous, are evidenced mainly on the free surface; this is a question of evidence completeness and surface-vs-bulk representativeness, not circularity. Since no step in the paper reduces a claimed result to a definition, a fitted input, or a self-citation chain, there is no circularity to report.

Assumptions & free parameters 2 free parameters · 4 assumptions · 0 invented entities

This is an experimental characterization paper with no mathematical derivation. The central claims rest on standard image-correlation and topology assumptions plus hand-set image analysis parameters, not on fitted mechanical constants or invented physical entities.

free parameters (2)
  • Global gray-value threshold for Laves phase segmentation
    Chosen by hand to segment the Laves network before Euler number analysis; the reported connectivity change (Euler -1363 to -594) depends on this threshold, and no sensitivity analysis is reported (Section 3.3, Fig. 7).
  • DIC facet size and step size = 0.55 um facet, 0.44 um step
    Chosen spatial resolution for strain maps; it affects the magnitude and localization of measured strain, and no uncertainty analysis is given (Section 3.3, Fig. 6).
assumptions (4)
  • standard math Euler number chi = b0 - b1, and a decrease in chi corresponds to an increase in connectivity.
    Standard topology result used to interpret Laves network connectivity changes (Eq. 1, refs 36, 38, 39).
  • domain assumption The CRSS hierarchy for magnesium makes basal slip and tensile twinning much easier than prismatic and pyramidal slip at 170 C.
    Used to explain why grains with high Schmid factors for basal slip or tensile twinning carry most strain and nucleate cracks (Section 4.2).
  • domain assumption Quasi in-situ surface measurements represent bulk deformation behavior, and the residual SiO2 speckle layer does not alter deformation.
    DIC is inherently a surface measurement; the authors partially validate crack observations in bulk samples (Fig. 9), but strain fields and surface topography remain 2D surface effects.
  • domain assumption Phase boundary sliding occurs at 170 C and contributes to interface strain localization.
    Inferred from lack of crystallographic orientation preference and supported by prior work (refs 7, 16, 40, 50); not directly measured in this study (Section 4.2).

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Pith. "Pith review of Strain heterogeneity and micro-damage nucleation under tensile stresses in an Mg-5Al-3Ca alloy with an intermetallic skeleton." pith.science (2026). https://pith.science/paper/TEAZ3XTW

@misc{pith2026190808271,
  author       = {Pith},
  title        = {Pith review of: Strain heterogeneity and micro-damage nucleation under tensile stresses in an Mg-5Al-3Ca alloy with an intermetallic skeleton},
  year         = {2026},
  howpublished = {\url{https://pith.science/paper/TEAZ3XTW}},
  note         = {Machine review of arXiv:1908.08271}
}
read the original abstract

Strain heterogeneity at the microstructural level plays a vital role in the deformation and fracture behaviour of dual or multi-phase materials. In the present work, the strain heterogeneity, localization and partitioning arising at the sub-micron scale during elevated temperature (170 {\deg}C) tensile deformation of an Mg-5Al-3Ca alloy was investigated using quasi in-situ {\mu}-DIC experiments. The results reveal that the strain is mainly carried by the {\alpha}-Mg phase, while the intermetallic Laves phase plays a critical role in that strain concentrations build up at the {\alpha}-Mg matrix and Laves phase interfaces, hence, reducing the overall deformability of the alloy. In quasi in-situ and bulk material analysis at elevated temperature, cracks were observed to nucleate in the Laves phase, at i) the intersection points of slip lines in the {\alpha}-Mg matrix with the Laves phase and ii) the twin intersections with {\alpha}-Mg/Laves phase interfaces and iii) twin transmissions across {\alpha}-Mg/Laves phase interfaces. Euler number analysis has shown that the (inter-)connectivity of the Laves phase decreases with deformation. Finally, cracks grow preferentially along the Laves phases until the material fractures.

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Reference graph

Works this paper leans on

59 extracted references · 59 canonical work pages

  1. [1]

    Mouritz, Editor

    Mouritz, A.P., Magnesium alloys for aerospace structures, in Introduction to Aerospace Materials, A.P. Mouritz, Editor. 2012, Woodhead Publishing Limited. p. 224-231

    work page 2012

  2. [2]

    Krajewski, and A.A

    Powell, B.R., P.E. Krajewski, and A.A. Luo, Magnesium alloys for lightweight powertrains and automotive structures, in Materials, Design and Manufacturing for Lightweight Vehicles, P.K. Mallick, Editor. 2010, Woodhead Publishing Limited. p. 114- 173

    work page 2010

  3. [3]

    Shuang-shou, and T

    Wei-chao, Z., L.I. Shuang-shou, and T. Bin, Microstructure and properties of Mg-Al binary alloys. China Foundry, 2006. 3(4): p. 270-274

    work page 2006

  4. [4]

    Kondori, B. and R. Mahmudi, Effect of Ca additions on the microstructure, thermal stability and mechanical properties of a cast AM60 magnesium alloy. Materials Science and Engineering a-Structural Materials Properties Microstructure and Processing, 2010. 527(7-8): p. 2014-2021. 27

    work page 2010

  5. [5]

    Mihriban O

    Kaya, A.A., Physical metallurgy of magnesium, in Fundamentals of Magnesium Alloy Metallurgy, K.U.K.a.A.A.K. Mihriban O. Pekguleryuz, Editor. 2013, Woodhead Publishing Limited. p. 33-84

    work page 2013

  6. [6]

    Maier-Kiener, and S

    Mathur, H.N., V. Maier-Kiener, and S. Korte-Kerzel, Deformation in the γ-Mg 17 Al 12 phase at 25–278 °C. Acta Materialia, 2016. 113: p. 221-229

    work page 2016

  7. [7]

    Watanabe, and K

    Nakaura, Y., A. Watanabe, and K. Ohori, Effects of Ca,Sr Additions on Properties of Mg- Al Based Alloys. Materials Transactions, 2006. 47(4): p. 1031-1039

    work page 2006

  8. [8]

    Kondori, B. and R. Mahmudi, Effect of Ca additions on the microstructure and creep properties of a cast Mg–Al–Mn magnesium alloy. Materials Science and Engineering: A,

    work page

Show all 59 references
  1. [9]

    Eisenlohr, and M

    Amberger, D., P. Eisenlohr, and M. Goken, Microstructural evolution during creep of Ca-containing AZ91. Materials Science and Engineering a-Structural Materials Properties Microstructure and Processing, 2009. 510-11: p. 398-402

    2009

  2. [10]

    Eisenlohr, and M

    Amberger, D., P. Eisenlohr, and M. Goken, On the importance of a connected hard- phase skeleton for the creep resistance of Mg alloys. Acta Materialia, 2012. 60(5): p. 2277-2289

    2012

  3. [11]

    Metallurgical and Materials Transactions A, 2004

    Terada, Y., et al., A Thousandfold Creep Strengthening by Ca Addition in Die-Cast AM50 Magnesium Alloy. Metallurgical and Materials Transactions A, 2004. 35A: p. 4

    2004

  4. [12]

    Materials Science and Engineering a-Structural Materials Properties Microstructure and Processing, 2017

    Li, Z.T., et al., Effect of Ca/Al ratio on microstructure and mechanical properties of Mg- Al-Ca-Mn alloys. Materials Science and Engineering a-Structural Materials Properties Microstructure and Processing, 2017. 682: p. 423-432

    2017

  5. [13]

    Materials Science and Engineering: A, 2018

    Chai, Y., et al., Role of Al content on the microstructure, texture and mechanical properties of Mg-3.5Ca based alloys. Materials Science and Engineering: A, 2018. 730: p. 303-316

    2018

  6. [14]

    Materials Science & Engineering A, 2015

    Zhang, L., et al., Microstructures and mechanical properties of Mg–Al–Ca alloysaffected by Ca/Al ratio. Materials Science & Engineering A, 2015. 636: p. 279-288

    2015

  7. [15]

    Acta Materialia, 2005

    Suzuki, A., et al., Solidification paths and eutectic intermetallic phases in Mg–Al–Ca ternary alloys. Acta Materialia, 2005. 53: p. 2823-2834

    2005

  8. [16]

    Materials Science and Engineering: A, 2019

    Zubair, M., et al., On the role of Laves phases on the mechanical properties of Mg-Al-Ca alloys. Materials Science and Engineering: A, 2019. 756: p. 272-283. 28

    2019

  9. [17]

    Metal Science and Heat Treatment, 2009

    Rokhlin, L.L., et al., Calcium-alloyed magnesium alloys. Metal Science and Heat Treatment, 2009. 51(3-4): p. 164-169

    2009

  10. [18]

    Rare Metal Materials and Engineering, 2008

    Wang, H.X., et al., Microstructure and properties of Mg-Al binary alloys. Rare Metal Materials and Engineering, 2008. 37(11): p. 2004-2007

    2008

  11. [19]

    Materials Science and Engineering: A, 2019

    Zehnder, C., et al., Plastic deformation of single crystalline C14 Mg2Ca Laves phase at room temperature. Materials Science and Engineering: A, 2019. 759: p. 754-761

    2019

  12. [20]

    Scripta Materialia, 2010

    Saddock, N.D., et al., Grain-scale creep processes in Mg–Al–Ca base alloys: Implications for alloy design. Scripta Materialia, 2010. 63(7): p. 692-697

    2010

  13. [21]

    Materialia, 2019

    Dutta, A., et al., Strain partitioning and strain localization in medium manganese steels measured by in situ microscopic digital image correlation. Materialia, 2019. 5

    2019

  14. [22]

    Acta Materialia, 2014

    Tasan, C.C., et al., Integrated experimental–simulation analysis of stress and strain partitioning in multiphase alloys. Acta Materialia, 2014. 81: p. 386-400

    2014

  15. [23]

    Materials (Basel, Switzerland), 2018

    Gao, P., et al., Characterization and Analysis of Strain Heterogeneity at Grain-Scale of Titanium Alloy with Tri-Modal Microstructure during Tensile Deformation. Materials (Basel, Switzerland), 2018. 11(11): p. 2194

    2018

  16. [24]

    Tasan, and D

    Yan, D., C.C. Tasan, and D. Raabe, High resolution in situ mapping of microstrain and microstructure evolution reveals damage resistance criteria in dual phase steels. Acta Materialia, 2015. 96: p. 399-409

    2015

  17. [25]

    Amini, S. and R.S. Kumar, A high-fidelity strain-mapping framework using digital image correlation. Materials Science and Engineering: A, 2014. 594: p. 394-403

    2014

  18. [26]

    Procedia Structural Integrity, 2016

    Li, Z., et al., Damage investigation in A319 aluminum alloy by digital image correlation during in-situ tensile tests. Procedia Structural Integrity, 2016. 2: p. 3415-3422

    2016

  19. [27]

    Wilkinson, and M

    Halim, H., D. Wilkinson, and M. Niewczas, The Portevin–Le Chatelier (PLC) effect and shear band formation in an AA5754 alloy. Acta Materialia, 2007. 55(12): p. 4151-4160

    2007

  20. [28]

    Mummery, and P.J

    Quinta, D.A.F.J., P.M. Mummery, and P.J. Withers, Full-field strain mapping by optical correlation of micrographs acquired during deformation. Journal of Microscopy, 2005. 218(Pt 1): p. 9-21

    2005

  21. [29]

    Di Gioacchino, F. and J. Quinta da Fonseca, Plastic Strain Mapping with Sub-micron Resolution Using Digital Image Correlation. Experimental Mechanics, 2013. 53(5): p. 743-754. 29

    2013

  22. [30]

    Measurement Science and Technology, 2009

    Pan, B., et al., Two-dimensional digital image correlation for in-plane displacement and strain measurement: a review. Measurement Science and Technology, 2009. 20(6)

    2009

  23. [31]

    Metallurgical and Materials Transactions A, 2009

    Tschopp, M.A., et al., Microstructure-Dependent Local Strain Behavior in Polycrystals through In-Situ Scanning Electron Microscope Tensile Experiments. Metallurgical and Materials Transactions A, 2009. 40(10): p. 2363-2368

    2009

  24. [32]

    Kammers, A.D. and S. Daly, Self-Assembled Nanoparticle Surface Patterning for Improved Digital Image Correlation in a Scanning Electron Microscope. Experimental Mechanics, 2013. 53(8): p. 1333-1341

    2013

  25. [33]

    Di Gioacchino, F. and J. Quinta da Fonseca, An experimental study of the polycrystalline plasticity of austenitic stainless steel. International Journal of Plasticity, 2015. 74: p. 92- 109

    2015

  26. [34]

    Acta Materialia, 2018

    Edwards, T.E.J., et al., Longitudinal twinning in a TiAl alloy at high temperature by in situ microcompression. Acta Materialia, 2018. 148: p. 202-215

    2018

  27. [35]

    Materials & Design, 2018

    Wu, Z., et al., Local mechanical properties and plasticity mechanisms in a Zn-Al eutectic alloy. Materials & Design, 2018. 157: p. 337-350

    2018

  28. [36]

    Computational Materials Science, 2016

    Kruglova, A., et al., 3D connectivity of eutectic Si as a key property defining strength of Al–Si alloys. Computational Materials Science, 2016. 120: p. 99-107

    2016

  29. [37]

    Available from: https://www.microsoft.com/en- us/research/product/computational-photography-applications/image-composite-editor/

    Image Composite Editor. Available from: https://www.microsoft.com/en- us/research/product/computational-photography-applications/image-composite-editor/

  30. [38]

    Aydogan, D.B. and J. Hyttinen, Characterization of microstructures using contour tree connectivity for fluid flow analysis. Journal of the Royal Society Interface, 2014. 11(95): p. 20131042

    2014

  31. [39]

    Lee, C.-N. and T. Poston, Winding and Euler Numbers for 2D and SD Digital Images. Graphical Models and Image Processing, 1991. 53(6): p. 522-537

    1991

  32. [40]

    Balogh, and B.R

    Luo, A.A., M.P. Balogh, and B.R. Powell, Creep and microstructure of magnesium- aluminum-calcium based alloys. Metallurgical and Materials Transactions a-Physical Metallurgy and Materials Science, 2002. 33(3): p. 567-574

    2002

  33. [41]

    Conrad, H. and W.D. Robertson, Effect of temperature on the flow stress and strain- hardening coefficient of magnesium single crystals. JOM, 1957. 9(4): p. 503-512. 30

    1957

  34. [42]

    Zhang, and Y

    Yu, Q., J. Zhang, and Y. Jiang, Direct observation of twinning–detwinning–retwinning on magnesium single crystal subjected to strain-controlled cyclic tension–compression in [0 0 0 1] direction. Philosophical Magazine Letters, 2011. 91(12): p. 757-765

    2011

  35. [43]

    Reed-Hill, R.E. and W.D. Robertson, Deformation of magnesium single crystals by nonbasal slip. JOM, 1957. 9(4): p. 496-502

    1957

  36. [44]

    Acta Materialia, 2014

    Sánchez-Martín, R., et al., Measuring the critical resolved shear stresses in Mg alloys by instrumented nanoindentation. Acta Materialia, 2014. 71: p. 283-292

    2014

  37. [45]

    Chapuis, A. and J.H. Driver, Temperature dependency of slip and twinning in plane strain compressed magnesium single crystals. Acta Materialia, 2011. 59(5): p. 1986- 1994

    2011

  38. [46]

    Scripta Materialia,

    Byer, C.M., et al., Microcompression of single-crystal magnesium. Scripta Materialia,

  39. [47]

    Materials Science Forum, 2000

    Miura, S., et al., Deformation Behavior of Mg Alloy Single Crystals at Various Temperatures. Materials Science Forum, 2000. 350-351: p. 183-190

    2000

  40. [48]

    Stanford, N. and M.R. Barnett, Solute strengthening of prismatic slip, basal slip and twinning in Mg and Mg–Zn binary alloys. International Journal of Plasticity, 2013. 47: p. 165-181

    2013

  41. [49]

    Philosophical Magazine, 2013

    Boehlert, C.J., et al., In situanalysis of the tensile deformation mechanisms in extruded Mg–1Mn–1Nd (wt%). Philosophical Magazine, 2013. 93(6): p. 598-617

    2013

  42. [50]

    China Foundry,

    Zhang, G., et al., Creep resistance of as-cast Mg-5Al-5Ca-2Sn alloy. China Foundry,

  43. [51]

    Materials Science and Engineering A, 2009

    Xu, S.W., et al., High temperature tensile properties of as-cast Mg–Al–Ca alloys. Materials Science and Engineering A, 2009. 509: p. 105-110

    2009

  44. [52]

    International Journal of Plasticity, 2009

    Bieler, T.R., et al., The role of heterogeneous deformation on damage nucleation at grain boundaries in single phase metals. International Journal of Plasticity, 2009. 25(9): p. 1655-1683

    2009

  45. [53]

    Metallurgical and Materials Transactions A, 2009

    Avramovic-Cingara, G., et al., Void Nucleation and Growth in Dual-Phase Steel 600 during Uniaxial Tensile Testing. Metallurgical and Materials Transactions A, 2009. 40(13): p. 3117-3127

    2009

  46. [54]

    Materials (Basel), 2017

    Pathak, N., et al., Damage Evolution in Complex-Phase and Dual-Phase Steels during Edge Stretching. Materials (Basel), 2017. 10(4). 31

    2017

  47. [55]

    PLOS ONE, 2019

    Kusche, C., et al., Large-area, high-resolution characterisation and classification of damage mechanisms in dual-phase steel using deep learning. PLOS ONE, 2019. 14(5): p. e0216493

    2019

  48. [56]

    Materials Science and Engineering: A, 2008

    Yang, F., et al., Crack initiation mechanism of extruded AZ31 magnesium alloy in the very high cycle fatigue regime. Materials Science and Engineering: A, 2008. 491(1-2): p. 131-136

    2008

  49. [57]

    JOM, 2009

    Bieler, T.R., et al., Strain heterogeneity and damage nucleation at grain boundaries during monotonic deformation in commercial purity titanium. JOM, 2009. 61(12): p. 45- 52

    2009

  50. [58]

    Intermetallics, 2004

    Ng, B.C., et al., The role of mechanical twinning on microcrack nucleation and crack propagation in a near-γ TiAl alloy. Intermetallics, 2004. 12(12): p. 1317-1323

    2004

  51. [59]

    Materials (Basel), 2018

    Bugelnig, K., et al., Revealing the Effect of Local Connectivity of Rigid Phases during Deformation at High Temperature of Cast AlSi12Cu4Ni(2,3)Mg Alloys. Materials (Basel), 2018. 11(8)

    2018

Pith tools

Reviewed August 14, 2026 · model on record in the stance chip above.