Pith. sign in

REVIEW 4 major objections 4 minor 68 references

Dynamic Plastic Deformation Delocalization in FCC Solid Solution Metals

T0 review · 4 major / 4 minor · reviewed 2026-08-06 · deepseek-v4-flash

Challenge this review Re-run · record.json Download PDF Read on arXiv ↗ Review JSON

Pith's one-line read In FCC solid-solution alloys, nanometer-scale twins that form during deformation force dislocations onto closely spaced slip planes, spreading plastic strain evenly and raising very-high-cycle fatigue strength.

desk verdict Solid HR-DIC dataset showing a real delocalized-flow phenomenon in some FCC alloys; the causal twin-driven mechanism and SFE window are retrofits, but the paper deserves review. read the letter →

arxiv 2507.05293 v1 pith:VMQ5KRUF submitted 2025-07-05 cond-mat.mtrl-sci

Dhruv Anjaria , Milan Heczko , Daegun YoU , Mathieu Calvat , Shuchi Sanandiya , Maik Rajkowski , Aditya Srinivasan Tirunilai , Huseyin Sehitoglu
show 2 more authors
Guillaume Laplanche J.C. Stinville
This is my paper · ORCID
classification cond-mat.mtrl-sci
keywords PlasticdeformationdelocalizationFatigueSolidsolutionstrengtheningNanotwinningStackingfaultenergyHigh-resolutiondigitalimagecorrelationVeryhighcycleFCCalloys
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

The paper identifies a mechanism it calls dynamic plastic deformation delocalization, by which face-centered cubic solid-solution alloys spread plastic strain evenly across grains instead of concentrating it in intense slip bands. The driver is the formation, during loading, of nanometer-scale deformation twins and other planar defects that push dislocation glide onto many closely spaced crystallographic planes. The effect is confined to a narrow window of intermediate stacking fault energies, and the paper shows it coincides with a markedly higher fatigue ratio for CrCoNi in very high cycle fatigue. If correct, the mechanism gives metallurgists a design rule for fatigue-resistant alloys that does not trade away monotonic strength.

What carries the argument

The central object is the named mechanism of dynamic plastic deformation delocalization. Its load-bearing component is the nanometer-scale deformation twin: a thin slab of material with a mirror-symmetric stacking sequence, formed during plastic flow, that coexists with full dislocations inside each deformation event. The twins and associated planar defects are inferred to act as both obstacles and sources, deactivating existing dislocation sources and nucleating glide on successive closely spaced planes, so that each surface step is small and strain spreads over whole grains. The organizing design parameter is the stacking fault energy (SFE), the energy per unit area needed to create a stacking fault; the paper computes it with first-principles methods and shows that delocalization occurs only in an intermediate SFE range, with high-SFE alloys deforming by full-dislocation slip and very-low-SFE CrCoNi at 20 K forming long twins that localize strain.

What would settle it

Strain a CrCoNi specimen at 300 K inside an electron microscope or synchrotron beamline and record when nanotwins first appear relative to the onset of homogeneous slip: if homogeneous slip appears before the nanotwins, or if suppressing twinning (for example by prior deformation or a slight composition shift) leaves the homogeneous slip unchanged, the proposed causal mechanism would be falsified.

Watch

Extended reading notes

Core claim

The paper's central claim is that plastic deformation can be dynamically delocalized in FCC solid-solution metals through deformation-induced nanotwinning. In CrCoNi at 300 K and 77 K, FeNi36 at 300 K, and CrMnFeCoNi at 77 K, high-resolution digital image correlation shows strain spread uniformly across entire grains, with almost no discrete intense slip events, whereas CrMnFeCoNi at 300 K, VCoNi, 316L, and CrCoNi at 20 K localize strain in intense bands. Atomic-resolution STEM on the homogeneously deformed grains reveals dense nanometer-scale twins, intrinsic and extrinsic stacking faults, and HCP platelets inside thick deformation events, while localizing grains contain mostly full dislocations. The authors argue that the nanotwins form during deformation and force dislocations onto closely spaced planes, thickening every deformation event and homogenizing plasticity; plotting the measured localization against computed stacking fault energies places all delocalizing conditions inside a narrow intermediate-SFE window. In very high cycle fatigue, CrCoNi's delocalized response coincides with a fatigue ratio far above the usual strength-versus-fatigue-efficiency trend, which the paper attributes to the same dynamic mechanism.

Load-bearing premise

The mechanism's direction of causality—that nanotwins form during deformation and actively redirect dislocations onto closely spaced planes, rather than being a byproduct of already-homogeneous deformation or of a third factor such as short-range order—is inferred from post-mortem foils, not observed live.

Editorial extensions

If this is right

  • Alloys and temperatures that land in the intermediate SFE window should show low slip localization and higher fatigue ratios, making SFE a screening parameter for fatigue-resistant compositions.
  • CrCoNi at room temperature should remain a positive outlier in fatigue-ratio-versus-strength plots, with the delocalization mechanism explaining the outlier rather than high strength alone.
  • The mechanism should let engineers decouple fatigue strength from monotonic strength, analogous to how the dynamic Hall–Petch effect decouples strength from ductility.
  • Deformation events in delocalizing alloys should have a characteristic thick, multi-plane structure, so inspecting for nanotwin-rich thickened slip bands can identify other candidate alloys.
  • At temperatures or compositions far outside the SFE window, delocalization should disappear and conventional intense slip or long-twin localization should return.

Reading between the lines

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

  • Beyond the paper's direct measurements, if the causal ordering is confirmed by live straining experiments, the intermediate-SFE rule becomes a practical composition-screening criterion for other FCC solid solutions, since SFE can be tuned by chemistry and temperature.
  • The delocalization may also be linked to short-range order: in these concentrated alloys, SFE and fault energies depend on the local atomic environment, so tailoring short-range order could widen or sharpen the delocalization window.
  • A direct test would be to suppress twinning (for example by a slight composition shift or pre-deformation) while holding SFE fixed; if slip localization returns, the twins are causal rather than a byproduct.
  • The fatigue benefit probably extends to crack-initiation resistance in general, because homogenized slip removes the surface stress concentrations that nucleate fatigue cracks; the paper measures very-high-cycle fatigue life directly but does not isolate crack initiation from propagation.
Share X Bluesky LinkedIn Reddit HN

Signed reviews

No signed human review yet.

Editorial analysis

A structured set of objections, weighed in public.

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

Referee Report

4 major / 4 minor

Summary. The manuscript reports an experimental and computational study of plastic localization in several FCC solid-solution alloys (CrCoNi, CrMnFeCoNi, VCoNi, FeNi36, 316L) tested at 300 K, 77 K, and 20 K. HR-DIC strain mapping is combined with site-specific TEM and atomic-resolution HAADF-STEM/COS defect analysis, DFT/AIMD stacking fault energy calculations, and VHCF fatigue tests. The central claim is a new 'dynamic plastic deformation delocalization' mechanism: nanometer-scale deformation twins and related planar defects form during deformation and force dislocations onto closely spaced slip planes, homogenizing plasticity. This behavior is reported to occur in a narrow intermediate range of stacking fault energies and to improve fatigue strength, with CrCoNi at 300 K as the standout case.

Significance. If the causal mechanism were established, this would be a significant advance: it would identify a microstructural design principle for overcoming the strength-fatigue trade-off in FCC alloys and would connect nanoscale defect physics to macroscopic fatigue performance. The paper's strengths are the high-quality multi-alloy HR-DIC dataset, the atomically resolved STEM/COS defect identification, the independent DFT/AIMD stacking fault energy calculations, and the inclusion of VHCF fatigue data. The manuscript also provides reproducible analysis scripts. However, the central claim currently rests on post-mortem observations and a retrospective correlation, so the significance of the paper as a mechanistic demonstration is not yet at the level claimed.

major comments (4)
  1. [Fig. 1 caption; Fig. 2(a); Fig. 7(a)] The materials are not compared at equal macroscopic plastic strains. CrCoNi at 300 K was deformed to 1.66% plastic strain (Fig. 1c), whereas Fig. 2(a) and Fig. 7(a) state that the localization comparison was performed at about 0.8% plastic strain. CrCoNi at 77 K and FeNi36 at 300 K are shown in Fig. 3 and Fig. S11 with strains that are not all 0.8%. The average plastic localization metric is strain-dependent, and event segmentation at higher strains may fail when events overlap. The factor-of-two reduction claimed for CrCoNi at 300 K could therefore be partly an artifact of the different imposed strain. Please provide equal-strain comparisons, or explicitly demonstrate that the localization metric is independent of macroscopic strain over the range 0.8-1.7%.
  2. [High-resolution TEM; 'A dynamic delocalization mechanism' (Figs. 4, 5, 7c)] The causal ordering at the heart of the mechanism is not established. HAADF-STEM/COS images from unloaded foils show nanotwins inside deformation events in homogeneously deformed grains, but they cannot determine whether the twins formed before and caused the homogeneous slip, or whether they are a byproduct of it. The same observations are equally consistent with homogeneous deformation producing nanotwins as a consequence, or with a third factor (short-range order, local stress state, or texture) causing both. The paper explicitly offers two candidate mechanistic routes (double cross-slip promoted by planar defects, and source deactivation from ref. 46) but does not test either. In-situ straining experiments, sequential interrupted tests, or another direct time-ordering measurement are needed to support the word 'dynamic' in the proposed mechanism.
  3. [Fig. 7(d); Fig. S12; 'Quantitative measurement of plastic localization'] The intermediate-SFE design window is established retrospectively. The 'Low' and 'Lower' categories are defined by an arbitrary 20 nm threshold (stated in Fig. S12), and the alloys and temperatures that fall in the 'narrow range' of SFE are the same data used to draw the window. Although the SFE values themselves are computed independently and are not fitted to the localization data, the classification and the window boundaries are post hoc. CrMnFeCoNi at 77 K lies just below the threshold while still containing grains with high localization (Fig. S12c), which makes the boundary fragile. An out-of-sample prediction (an alloy or temperature not used to define the window) or a pre-registered threshold would be needed to convert this correlation into a mechanistic design rule.
  4. [Fig. 8 and 'A new design space for enhancing fatigue strength'] The fatigue demonstration is limited to room-temperature VHCF tests on CrCoNi, CrMnFeCoNi, and 316L, of which only CrCoNi exhibits the 'Lower' delocalized response. No fatigue data are provided for FeNi36 at 300 K or CrCoNi at 77 K, which are also claimed to exhibit the delocalization mechanism, so the claim that mechanism activation 'greatly enhances fatigue strength when it occurs' is supported by only one alloy condition. In addition, the fatigue ratio is normalized by yield strength, and alternative contributing factors (inclusion populations, crack initiation sites, internal defects, or differences in yield strength normalization) are not discussed. Please either extend the fatigue comparison to other delocalizing conditions or soften the general fatigue claim.
minor comments (4)
  1. [Methods, SFE calculation] The text contains a typo: 'V ASP' should be 'VASP' (Vienna Ab-initio Simulation Package). Also, the AIMD runs of 1.2-1.4 ps appear short for converged free-energy estimates; reporting error bars or convergence tests for the SFE values would strengthen Fig. 7(d).
  2. [Fig. 3 caption] The caption states that the SADP indicates 'a high density of deformation twins, which we do not observe spatially on the BF TEM images.' This is confusing; please clarify whether the twins are invisible in BF due to their nanoscale size and explain how the SADP contrast is interpreted.
  3. [Section 'Quantitative measurement of plastic localization'] The definition of the average plastic localization metric would benefit from more detail on event segmentation: how are events identified when the plasticity is so diffuse that 'individual deformation events cannot be resolved using HR-DIC'? The metric and the classification threshold (20 nm) both depend on the segmentation procedure.
  4. [Fig. 4(c) and Fig. S15] The statement that the nanotwin-containing structure 'was present in most of the deformation events within this foil' is qualitative. A simple count or quantitative fraction would make the association between nanotwins and thick deformation events more robust.

Circularity Check

0 steps flagged · score 0.0 of 10

No significant circularity: the SFE values are computed independently, the localization measurements are direct observations, and the proposed mechanism is presented as a post-hoc explanation rather than a prediction derived from its own inputs.

full rationale

The paper's central derivation chain is not circular. The plastic localization values are measured directly with HR-DIC and the stacking fault energies are computed with independent DFT/AIMD calculations, with no parameter fitted to the localization data. The identification of nanotwins and planar defects is made by post-mortem STEM/COS analysis, and the correlation between low localization and intermediate SFE is presented as an observed pattern, not as a quantity defined in terms of the outcome it explains. The fatigue comparison is likewise a direct measurement, and the connection to localization relies on a previously published correlation (ref. 10). Although refs. 10 and 26 are by overlapping authors, they are external published results and are not used as an unverified uniqueness or derivation step. The main weaknesses are evidential rather than circular: the causal ordering (nanotwins drive homogenization versus homogenization producing nanotwins) is inferred from post-mortem images, the intermediate-SFE design window is retrospective and not validated on a new alloy, and the paper explicitly acknowledges two alternative mechanisms. These are limitations of causal support and predictive scope, but none of the paper's predictions or classifications reduces to its inputs by construction or to a self-citation chain.

Assumptions & free parameters 1 free parameters · 4 assumptions · 0 invented entities

The central claims rest on domain assumptions rather than mathematical axioms. The most consequential are the causal interpretation of post-mortem microstructures, the microstructural comparability of the alloys, and the quantitative reliability of computed SFEs. One free parameter (the arbitrary classification threshold) directly shapes the qualitative conclusions. No new particles, fields, or conserved quantities are proposed.

free parameters (1)
  • Plastic localization classification thresholds = 20 nm and 45 nm
    Supplementary Fig. S12 defines thresholds, called arbitrary, that split alloys into 'High' vs 'Low'/'Lower' localization. The delocalization regime, the SFE window, and the 'new design space' are all defined relative to these thresholds.
assumptions (4)
  • domain assumption Post-mortem microstructures are representative of the deformation state at the end of loading, and nanotwins observed in TEM foils formed during deformation and are causally prior to the homogeneous slip distribution.
    Invoked throughout Sections 'TEM characterization' and 'A dynamic delocalization mechanism'; no in-situ observation is provided, so the time-ordering and causal direction are assumed.
  • domain assumption The five alloys are microstructurally comparable (grain size, shape, texture) so that differences in localization are attributed to chemistry/temperature (and thus SFE) rather than microstructure.
    Section 'Plastic localization response' states all materials are single-phase FCC with similar microstructure; however, grain sizes span 25-50 micrometers and strain levels differ, so equivalence is approximate.
  • domain assumption DFT/AIMD-based SFE calculations with PBE functional, 270-atom SQS supercells, and selection of the maximum-SFE slip-cut provide accurate SFEs at finite temperatures.
    Methods section 'Stacking fault energy calculation'; the paper acknowledges SFE variation across slip-cut configurations but does not report uncertainty or benchmark against experiment.
  • domain assumption HR-DIC measurements on the specimen surface after unloading and the associated H-DIC discontinuity extraction faithfully quantify plastic localization intensity.
    Methods 'High-Resolution Digital Image Correlation'; prior work establishes the approach (refs. 30,31), but the claimed resolution of below 10 nm and the treatment of unresolved diffuse events are assumed.

how reviews work

0 comments
Cite this review

Pith. "Pith review of Dynamic Plastic Deformation Delocalization in FCC Solid Solution Metals." pith.science (2026). https://pith.science/paper/VMQ5KRUF

@misc{pith2026250705293,
  author       = {Pith},
  title        = {Pith review of: Dynamic Plastic Deformation Delocalization in FCC Solid Solution Metals},
  year         = {2026},
  howpublished = {\url{https://pith.science/paper/VMQ5KRUF}},
  note         = {Machine review of arXiv:2507.05293}
}
read the original abstract

Metallic materials undergo irreversible deformation under mechanical loading, leading to intense local plastic localization that reduces their mechanical performance. We identify a new mechanism of plastic deformation localization that dynamically promotes the homogenization of plasticity in face-centered cubic solid solution-strengthened metallic alloys. We observe that this mechanism occurs within a narrow range of stacking fault energies and involves competing deformation between nanoscale twinning and slip. This phenomenon is attributed to a new mechanism referred to as dynamic plastic deformation delocalization, which opens a new design space for enhancing the mechanical performance of metallic materials. We demonstrate that the activation of this mechanism has a significant impact on fatigue properties, greatly enhancing fatigue strength when it occurs.

Figures

Figures reproduced from arXiv: 2507.05293 by the authors.

Figure 1
Figure 1. (a) HR-DIC εxx longitudinal strain maps for CrMnFeCoNi deformed at room temperature (300K) up to a macroscopic plastic strain of 0.95%, (b) CrMnFeCoNi deformed at liquid nitrogen temperature (77K) up to a macroscopic plastic strain of 0.83% and (c) CrCoNi deformed at room temperature up to a macroscopic plastic strain of 1.66%. The tensile direction is horizontal. The inverse pole figure maps along the loading direc… view at source ↗
Figure 2
Figure 2. (a) Average plastic localization in nanometers for several FCC solid-solution-strengthened alloys deformed up to a macroscopic plastic strain of 0.8% at different temperatures. (b,c) Distribution of the number of grains as a function of the maximum plastic localization for the investigated materials. Materials that develop intense plastic localization are represented using solid lines and solid symbols (b), whereas … view at source ↗
Figure 3
Figure 3. Reduced regions of the HR-DIC εxx longitudinal strain maps for (a) VCoNi deformed at room temperature, (d) CrMnFeCoNi deformed at room temperature, (h) FeNi36 deformed at room temperature, and (k) CrCoNi deformed at 77K. The macroscopic plastic strains up to which the materials were deformed are included on the respective HR-DIC maps. Grains developing intense plastic localization and diffused plasticity were select… view at source ↗
Figures from the paper (5 more)
Figure 4
Figure 4. Figure 4: BF-STEM DCI micrographs from (a) a (high) localizing grain for CrMnFeCoNi deformed at 77K, (b) a (low) delocalizing grain for CrMnFeCoNi deformed at 77K and (c) a (lower) delocalizing grain for CrCoNi deformed at 300K. The figure insets display reduced regions of the H…
Figure 5
Figure 5. Figure 5: (a) BF-STEM DCI micrograph from a (low) delocalizing grain for the CrCoNi alloy deformed at 77K. (b,c) Atomic resolution HAADF-STEM images within two deformation events from (a). (d,e) Associated center of symmetry analysis. (f) BF-STEM DCI micrograph from a (lower) de…
Figure 6
Figure 6. Figure 6: (a) Schematic of stacking fault energy (SFE) calculation upon slip; Partial burgers vector (bp) along <112> direction is applied at intrinsic stacking fault (ISF) point; Stacking sequence (such as ABCABABC) is denoted after slip. (b) Example of SFEs in random VCoNi all…
Figure 7
Figure 7. Figure 7: (a) Observed variations in average plastic localization for several FCC solid-solution-strengthened alloys deformed at a macroscopic plastic strain of 0.8%. Three distinct regimes were identified: one exhibiting intense plastic localization (labeled as "High"), another…
Figure 8
Figure 8. Figure 8: (a) Fatigue life at room temperature of the investigated CrCoNi, CrMnFeCoNi alloys, and 316L stainless steel as a function of the maximum applied stress in the very high cycle fatigue regime. The maximum stress is expressed as a percentage of the yield strength. (b) Fa…

Discussion (0). Continue with ORCID to comment.

Reference graph

Works this paper leans on

68 extracted references · 51 canonical work pages

  1. [2]

    N., Miracle, D

    Senkov, O. N., Miracle, D. B. & Firstov, S. A.Metallic materials with high structural efficiency, vol. 146 (Springer Science & Business Media, 2004)

    work page 2004

  2. [3]

    Anoop, C.et al.A review on steels for cryogenic applications.Mater. Perform. Charact.10, 20200193, DOI: 10.1520/ MPC20200193 (2021)

    work page 2021

  3. [4]

    A., Prajitno, D

    Basuki, E. A., Prajitno, D. H. & Muhammad, F. Alloys developed for high temperature applications. InAIP Conference Proceedings, vol. 1805 (AIP Publishing, 2017)

    work page 2017

  4. [5]

    https://www.science.org/doi/pdf/10.1126/science.1254581

    Gludovatz, B.et al.A fracture-resistant high-entropy alloy for cryogenic applications.Science345, 1153–1158, DOI: 10.1126/science.1254581 (2014). https://www.science.org/doi/pdf/10.1126/science.1254581. 6.Ritchie, R. O. The conflicts between strength and toughness.Nat. Mater.10, 817–822, DOI: 10.1038/nmat3115 (2011)

    doi:10.1126/science.1254581 2014

  5. [7]

    Otto, F.et al.The influences of temperature and microstructure on the tensile properties of a cocrfemnni high-entropy alloy.Acta Materialia61, 5743–5755, DOI: https://doi.org/10.1016/j.actamat.2013.06.018 (2013)

    work page doi:10.1016/j.actamat.2013.06.018 2013

  6. [8]

    Today25, 21–27, DOI: https://doi.org/10.1016/j.mattod.2019.03.001 (2019)

    Ding, Q.et al.Real-time nanoscale observation of deformation mechanisms in crconi-based medium- to high-entropy alloys at cryogenic temperatures.Mater. Today25, 21–27, DOI: https://doi.org/10.1016/j.mattod.2019.03.001 (2019)

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

  7. [9]

    S., Haridas, R

    Mishra, R. S., Haridas, R. S. & Agrawal, P. High entropy alloys – tunability of deformation mechanisms through integration of compositional and microstructural domains.Mater. Sci. Eng. A812, 141085, DOI: 10.1016/j.msea.2021.141085 (2021). 10.Stinville, J.et al.On the origins of fatigue strength in crystalline metallic materials.Science377, 1065–1071 (2022)

    work page arXiv 2021

  8. [11]

    Cyclic slip irreversibility and fatigue life: A microstructure-based analysis.Acta Materialia61, 1197–1203, DOI: https://doi.org/10.1016/j.actamat.2012.10.029 (2013)

    Mughrabi, H. Cyclic slip irreversibility and fatigue life: A microstructure-based analysis.Acta Materialia61, 1197–1203, DOI: https://doi.org/10.1016/j.actamat.2012.10.029 (2013)

    doi:10.1016/j.actamat.2012.10.029 2013

Show all 68 references
  1. [12]

    Cyclic slip irreversibilities and the evolution of fatigue damage.Metall

    Mughrabi, H. Cyclic slip irreversibilities and the evolution of fatigue damage.Metall. Mater. Transactions B40, 431–453, DOI: 10.1007/s11663-009-9240-4 (2009)

    2009 doi

  2. [13]

    Microstructural fatigue mechanisms: Cyclic slip irreversibility, crack initiation, non-linear elastic damage analysis.Int

    Mughrabi, H. Microstructural fatigue mechanisms: Cyclic slip irreversibility, crack initiation, non-linear elastic damage analysis.Int. J. Fatigue57, 2–8, DOI: 10.1016/j.ijfatigue.2012.06.007 (2013). 14.Forrest, P. G.Fatigue of metals(Elsevier, 2013)

    2013 doi

  3. [15]

    2025.120888 (2025)

    Wang, P.et al.The highest fatigue strength for steels.Acta Materialia289, 120888, DOI: https://doi.org/10.1016/j.actamat. 2025.120888 (2025)

    2025

  4. [16]

    & Ashby, M

    Fleck, N., Kang, K. & Ashby, M. Overview no. 112: The cyclic properties of engineering materials.Acta Metall. et Materialia42, 365–381, DOI: https://doi.org/10.1016/0956-7151(94)90493-6 (1994)

    1994 doi

  5. [17]

    & Coryell, S

    Patel, S., deBarbadillo, J. & Coryell, S. Superalloy 718: Evolution of the alloy from high to low temperature application. In Ott, E.et al.(eds.)Proceedings of the 9th International Symposium on Superalloy 718 & Derivatives: Energy, Aerospace, and Industrial Applications, 23–4...

    1970

  6. [19]

    & Yang, C

    Kang, L. & Yang, C. A review on high-strength titanium alloys: Microstructure, strengthening, and properties.Adv. Eng. Mater.21, DOI: 10.1002/adem.201801359 (2019)

    2019 doi

  7. [20]

    Stinville, J.et al.Direct measurements of slip irreversibility in a nickel-based superalloy using high resolution digital image correlation.Acta Materialia186, 172–189 (2020)

    2020

  8. [21]

    & Man, J

    Polák, J. & Man, J. Initiation of stage i fatigue cracks – experiments and models.Procedia Eng.101, 386–394, DOI: https://doi.org/10.1016/j.proeng.2015.02.047 (2015). 3rd International Conference on Material and Component Performance under Variable Amplitude Loading, V AL 2015. 14/25

    2015 doi

  9. [22]

    & and, G

    Ferro, A., Mazzetti, P. & and, G. M. On the effect of the crystalline structure on fatigue: Comparison between body-centred metals (ta, nb, mo and w) and face-centred and hexagonal metals.The Philos. Mag. A J. Theor. Exp. Appl. Phys.12, 867–875, DOI: 10.1080/14786436508218923 ...

    1965 doi

  10. [24]

    & Fan, G

    Wu, H. & Fan, G. An overview of tailoring strain delocalization for strength-ductility synergy.Prog. Mater. Sci.113, 100675, DOI: https://doi.org/10.1016/j.pmatsci.2020.100675 (2020)

    2020

  11. [25]

    L., Hestroffer, J

    Ahmadikia, B., Beyerlein, A. L., Hestroffer, J. M., Kumar, M. A. & Beyerlein, I. J. Designing ti-6al-4v microstructure for strain delocalization using neural networks.J. Mater. Sci. Mater. Theory8, DOI: 10.1186/s41313-024-00055-9 (2024)

    2024 doi

  12. [26]

    Anjaria, D.et al.Plastic deformation delocalization at cryogenic temperatures in a nickel-based superalloy.Acta Materialia 276, 120106, DOI: https://doi.org/10.1016/j.actamat.2024.120106 (2024)

    2024

  13. [27]

    & Xiang, S

    Chen, F., Liu, F., Tan, Y .-B., Shi, W. & Xiang, S. Breaking the strength-ductility trade-off via heterogeneous structure in fecocrnimo0.2 high-entropy alloy.J. Mater. Res. Technol.29, 265–275, DOI: https://doi.org/10.1016/j.jmrt.2024.01.037 (2024)

    2024 doi

  14. [28]

    An, Z.et al.Hierarchical grain size and nanotwin gradient microstructure for improved mechanical properties of a non-equiatomic cocrfemnni high-entropy alloy.J. Mater. Sci. & Technol.92, 195–207, DOI: https://doi.org/10.1016/j.jmst. 2021.02.059 (2021)

    2021 doi

  15. [29]

    & Cem Tasan, C

    Kang, J. & Cem Tasan, C. Beyond the dynamic hall-petch effect: Mechanical twinning for microscopic strain delocalization. Scripta Materialia255, 116346, DOI: 10.1016/j.scriptamat.2024.116346 (2025)

    2025

  16. [30]

    Charact.169, 110600, DOI: https://doi.org/10.1016/j.matchar.2020.110600 (2020)

    Stinville, J.et al.Measurement of elastic and rotation fields during irreversible deformation using heaviside-digital image correlation.Mater. Charact.169, 110600, DOI: https://doi.org/10.1016/j.matchar.2020.110600 (2020)

    2020

  17. [31]

    Bourdin, F.et al.Measurements of plastic localization by heaviside-digital image correlation.Acta Materialia157, 307 – 325, DOI: https://doi.org/10.1016/j.actamat.2018.07.013 (2018)

    2018 doi

  18. [32]

    Yang, B.et al.Grain size dependence of microscopic strain distribution in a high entropy alloy at the onset of plastic deformation.Acta Materialia285, 120682, DOI: https://doi.org/10.1016/j.actamat.2024.120682 (2025)

    2025

  19. [33]

    & Texier, D

    Jullien, M., Black, R., Stinville, J., Legros, M. & Texier, D. 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. A912, 146927, DOI: https: //doi.org/10.1016/j.msea.2024.146927 (2024)

    2024

  20. [34]

    W., Nicolas, A., Lebensohn, R

    Mello, A. W., Nicolas, A., Lebensohn, R. A. & Sangid, M. D. Effect of microstructure on strain localization in a 7050 aluminum alloy: Comparison of experiments and modeling for various textures.Mater. Sci. Eng. A661, 187–197, DOI: 10.1016/j.msea.2016.03.012 (2016)

    2016 doi

  21. [35]

    Alaie, A.et al.Effect of microstructure pattern on the strain localization in dp600 steels analyzed using combined in-situ experimental test and numerical simulation.Mater. Sci. Eng. A638, 251–261, DOI: 10.1016/j.msea.2015.04.071 (2015)

    2015 doi

  22. [36]

    & Mills, M

    Loretto, M., Phillips, P. & Mills, M. Stacking fault tetrahedra in metals.Scripta Materialia94, 1–4, DOI: https: //doi.org/10.1016/j.scriptamat.2014.07.020 (2015)

    2015 doi

  23. [37]

    Story of stacking fault tetrahedra.Mater

    Kiritani, M. Story of stacking fault tetrahedra.Mater. Chem. Phys.50, 133–138, DOI: https://doi.org/10.1016/ S0254-0584(97)80250-7 (1997)

    1997

  24. [38]

    & Tieu, K

    Zhang, L., Lu, C., Michal, G., Deng, G. & Tieu, K. The formation and destruction of stacking fault tetrahedron in fcc metals: A molecular dynamics study.Scripta Materialia136, 78–82, DOI: 10.1016/j.scriptamat.2017.04.019 (2017)

    2017 doi

  25. [39]

    Savage, J. C. Dislocation pileup as a representation of strain accumulation on a strike-slip fault.J. Geophys. Res. Solid Earth111, DOI: https://doi.org/10.1029/2005JB004021 (2006). https://agupubs.onlinelibrary.wiley.com/doi/pdf/10.1029/ 2005JB004021

    2006 doi

  26. [40]

    Chakravarthy, S. S. & Curtin, W. Effect of source and obstacle strengths on yield stress: A discrete dislocation study.J. Mech. Phys. Solids58, 625–635, DOI: https://doi.org/10.1016/j.jmps.2010.03.004 (2010)

    2010 doi

  27. [41]

    Heczko, M.et al.Role of deformation twinning in fatigue of crconi medium-entropy alloy at room temperature.Scripta Materialia202, 113985, DOI: https://doi.org/10.1016/j.scriptamat.2021.113985 (2021)

    2021

  28. [42]

    Pandey, P.et al.On the faulting and twinning mediated strengthening and plasticity in a strengthened coni-based superalloy at room temperature.Acta Materialia252, 118928, DOI: https://doi.org/10.1016/j.actamat.2023.118928 (2023). 15/25

    2023

  29. [43]

    C., Jo, Y

    Yang, D. C., Jo, Y . H., Ikeda, Y ., Körmann, F. & Sohn, S. S. Effects of cryogenic temperature on tensile and impact properties in a medium-entropy vconi alloy.J. Mater. Sci. & Technol.90, 159–167, DOI: https://doi.org/10.1016/j.jmst.2021.02.034 (2021)

    2021 doi

  30. [44]

    Fang, Y .et al.An in situ ambient and cryogenic transmission electron microscopy study of the effects of temperature on dislocation behavior in crconi-based high-entropy alloys with low stacking-fault energy.Appl. Phys. Lett.119, DOI: 10.1063/5.0069086 (2021)

    2021 doi

  31. [45]

    Nöhring, W. G. & Curtin, W. Dislocation cross-slip in fcc solid solution alloys.Acta Materialia128, 135–148, DOI: https://doi.org/10.1016/j.actamat.2017.02.027 (2017)

    2017 doi

  32. [46]

    Commun.16, DOI: 10.1038/s41467-025-58480-4 (2025)

    Xie, B.et al.Divergent evolution of slip banding in crconi alloys.Nat. Commun.16, DOI: 10.1038/s41467-025-58480-4 (2025)

    2025 doi

  33. [47]

    Frank, F. C. & Read, W. T. Multiplication processes for slow moving dislocations.Phys. Rev.79, 722–723, DOI: 10.1103/PhysRev.79.722 (1950)

    1950 doi

  34. [48]

    Lu, K.et al.Superior low-cycle fatigue properties of cocrni compared to cocrfemnni.Scripta Materialia194, 113667, DOI: https://doi.org/10.1016/j.scriptamat.2020.113667 (2021)

    2021

  35. [49]

    Z.et al.High cycle fatigue deformation mechanisms of a single phase crmnfeconi high entropy alloy

    Ghomsheh, M. Z.et al.High cycle fatigue deformation mechanisms of a single phase crmnfeconi high entropy alloy. Mater. Sci. Eng. A777, 139034, DOI: https://doi.org/10.1016/j.msea.2020.139034 (2020)

    2020

  36. [50]

    & Zhang, Z

    Li, P., Li, S., Wang, Z. & Zhang, Z. Fundamental factors on formation mechanism of dislocation arrangements in cyclically deformed fcc single crystals.Prog. Mater. Sci.56, 328–377, DOI: https://doi.org/10.1016/j.pmatsci.2010.12.001 (2011)

    2011 doi

  37. [51]

    & Mazza, E

    Pham, M., Holdsworth, S., Janssens, K. & Mazza, E. Cyclic deformation response of aisi 316l at room temperature: Mechanical behaviour, microstructural evolution, physically-based evolutionary constitutive modelling.Int. J. Plast.47, 143–164, DOI: https://doi.org/10.1016/j.ijpl...

    2013 doi

  38. [52]

    Chen, Q.et al.Small crack behavior and fracture of nickel-based superalloy under ultrasonic fatigue.Int. J. Fatigue27, 1227–1232, DOI: https://doi.org/10.1016/j.ijfatigue.2005.07.022 (2005). Fatigue Damage of Structural Materials V

    2005 doi

  39. [53]

    & Christ, H.-J

    Kolyshkin, A., Zimmermann, M., Kaufmann, E. & Christ, H.-J. Experimental investigation and analytical description of the damage evolution in a ni-based superalloy beyond 106 loading cycles.Int. J. Fatigue93, 272–280, DOI: https: //doi.org/10.1016/j.ijfatigue.2016.03.017 (2016)...

    2016 doi

  40. [54]

    & Christ, H.-J

    Stöcker, C., Zimmermann, M. & Christ, H.-J. Effect of precipitation condition, prestrain and temperature on the fatigue behaviour of wrought nickel-based superalloys in the vhcf range.Acta Materialia59, 5288–5304, DOI: https: //doi.org/10.1016/j.actamat.2011.05.005 (2011)

    2011 doi

  41. [55]

    & Christ, H.-J

    Stöcker, C., Zimmermann, M. & Christ, H.-J. Localized cyclic deformation and corresponding dislocation arrangements of polycrystalline ni-base superalloys and pure nickel in the vhcf regime.Int. J. Fatigue33, 2–9, DOI: https://doi.org/10. 1016/j.ijfatigue.2010.04.008 (2011). A...

    2011

  42. [56]

    & Saintier, N

    Marti, N., Favier, V ., Gregori, F. & Saintier, N. Correlation of the low and high frequency fatigue responses of pure polycrystalline copper with mechanisms of slip band formation.Mater. Sci. Eng. A772, 138619, DOI: https://doi.org/10. 1016/j.msea.2019.138619 (2020)

    2020

  43. [57]

    Charpagne, M.et al.Automated and quantitative analysis of plastic strain localization via multi-modal data recombination. Mater. Charact.163, 110245, DOI: https://doi.org/10.1016/j.matchar.2020.110245 (2020)

    2020

  44. [58]

    & De Graef, M

    Phillips, P., Brandes, M., Mills, M. & De Graef, M. Diffraction contrast stem of dislocations: Imaging and simulations. Ultramicroscopy111, 1483–1487, DOI: 10.1016/j.ultramic.2011.07.001 (2011)

    2011 doi

  45. [59]

    R., Miao, J., Mills, M

    Niu, C., LaRosa, C. R., Miao, J., Mills, M. J. & Ghazisaeidi, M. Magnetically-driven phase transformation strengthening in high entropy alloys.Nat. Commun.9, DOI: 10.1038/s41467-018-03846-0 (2018)

    2018 doi

  46. [60]

    B., Koohbor, B

    Montgomery, C. B., Koohbor, B. & Sottos, N. R. A robust patterning technique for electron microscopy-based digital image correlation at sub-micron resolutions.Exp. Mech.59, 1063–1073, DOI: 10.1007/s11340-019-00487-2 (2019)

    2019 doi

  47. [61]

    Mech.58, DOI: 10.1007/s11340-017-0363-2 (2017)

    Valle, V .et al.Crack analysis in mudbricks under compression using specific development of stereo-digital image correlation.Exp. Mech.58, DOI: 10.1007/s11340-017-0363-2 (2017)

    2017 doi

  48. [62]

    Very high cycle fatigue measuring techniques.Int

    Stanzl-Tschegg, S. Very high cycle fatigue measuring techniques.Int. J. Fatigue60, 2–17, DOI: 10.1016/j.ijfatigue.2012. 11.016 (2014). 16/25

    2014 doi

  49. [63]

    Stanzl, S. A new experimental method for measuring life time and crack growth of materials under multi-stage and random loadings.Ultrasonics19, 269–272, DOI: 10.1016/0041-624x(81)90017-2 (1981)

    1981 doi

  50. [64]

    & Sander, M

    Stäcker, C. & Sander, M. Experimental, analytical and numerical analyses of constant and variable amplitude loadings in the very high cycle fatigue regime.Theor. Appl. Fract. Mech.92, 394–409, DOI: 10.1016/j.tafmec.2017.07.021 (2017)

    2017 doi

  51. [65]

    & Furthmüller, J

    Kresse, G. & Furthmüller, J. Efficient iterative schemes for ab initio total-energy calculations using a plane-wave basis set. Phys. Rev. B54, 11169–11186, DOI: 10.1103/PhysRevB.54.11169 (1996)

    1996 doi

  52. [66]

    van de Walle, A.et al.Efficient stochastic generation of special quasirandom structures.Calphad42, 13–18, DOI: https://doi.org/10.1016/j.calphad.2013.06.006 (2013)

    2013 doi

  53. [67]

    You, D.et al.Short-range ordering mechanics in fcc materials.Int. J. Plast.174, 103919, DOI: https://doi.org/10.1016/j. ijplas.2024.103919 (2024)

    2024

  54. [68]

    K., Mohammed, A

    You, D., Celebi, O. K., Mohammed, A. S. K., Bucsek, A. & Sehitoglu, H. The derivation of crss in pure ti and ti-al alloys. Int. J. Plast.184, 104187, DOI: https://doi.org/10.1016/j.ijplas.2024.104187 (2025)

    2025

  55. [69]

    Intrinsic stacking faults in body-centred cubic crystals.The Philos

    Vítek, V . Intrinsic stacking faults in body-centred cubic crystals.The Philos. Mag. A J. Theor. Exp. Appl. Phys.18, 773–786, DOI: 10.1080/14786436808227500 (1968). https://doi.org/10.1080/14786436808227500

    1968 doi

  56. [70]

    & Joubert, D

    Kresse, G. & Joubert, D. From ultrasoft pseudopotentials to the projector augmented-wave method.Phys. Rev. B59, 1758–1775, DOI: 10.1103/PhysRevB.59.1758 (1999)

    1999 doi

  57. [71]

    P., Burke, K

    Perdew, J. P., Burke, K. & Ernzerhof, M. Generalized gradient approximation made simple.Phys. Rev. Lett.77, 3865–3868, DOI: 10.1103/PhysRevLett.77.3865 (1996)

    1996 doi

  58. [72]

    Hoover, W. G. Canonical dynamics: Equilibrium phase-space distributions.Phys. Rev. A31, 1695–1697, DOI: 10.1103/ PhysRevA.31.1695 (1985)

    1985

  59. [73]

    A unified formulation of the constant temperature molecular dynamics methods.The J

    Nosé, S. A unified formulation of the constant temperature molecular dynamics methods.The J. Chem. Phys.81, 511–519, DOI: 10.1063/1.447334 (1984). https://pubs.aip.org/aip/jcp/article-pdf/81/1/511/18949062/511_1_online.pdf

    1984 doi

  60. [74]

    Low" plastic localization. Compared to the

    You, D.et al.Inverse design of short-range order arrangement via neural network.Int. J. Solids Struct.309, 113175, DOI: https://doi.org/10.1016/j.ijsolstr.2024.113175 (2025). Acknowledgments J.C.S., D.A., M.C. and S.S. acknowledge the National Science Foundation (NSF) DMR CARE...

    2025

Pith tools

Reviewed August 6, 2026 · model on record in the stance chip above.