Pith. sign in

REVIEW 3 major objections 6 minor 33 references

Operando observation of strain relaxation in fatigued pearlitic steel

T0 review · 3 major / 6 minor · reviewed 2026-08-01 · deepseek-v4-flash

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

Pith's one-line read Fatigued pearlitic railway steel relaxes its elastic strain spread by nearly 40% upon heating to 550°C, with recovery beginning below 250°C, driven by dislocations annihilating between cementite lamellae rather than by lattice rotation or s

desk verdict New operando DFXM observation of strain relaxation in pearlite, but the headline 40% narrowing is not a like-for-like comparison because pre- and post-annealing strain maps sample different grain regions. read the letter →

arxiv 2607.16867 v1 pith:EVJHFXCJ submitted 2026-07-18 cond-mat.mtrl-sci

Louis Lesage , Johan Ahlström , Yubin Zhang , Can Y{i}ld{i}r{i}m This is my paper · ORCID
classification cond-mat.mtrl-sci
keywords dark-fieldX-raymicroscopypearliticsteelstrainrelaxationannealingrailwaywheelsdislocationannihilationresidualfatigue
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 tracks a single pearlite colony—a lamellar ferrite/cementite grain—in a fatigued railway wheel steel as it is heated to 550°C. It finds the elastic strain spread inside the colony narrows by nearly 40%, with relaxation starting below 250°C, and that this happens without measurable lattice rotation or new sub-cell boundaries. The authors attribute the relaxation to short-range annihilation of dislocations confined between cementite lamellae, and they connect this grain-scale recovery to the macroscopic softening that limits railway wheel life in service. The work matters because it reveals a localized, operando mechanism that conventional diffraction averaging would miss.

What carries the argument

Dark-field X-ray microscopy (DFXM) imaging of the (110) ferrite reflection, combining layer mosaicity scans to map local orientation and energy-scan strain maps to measure d-spacing changes. The paper's core evidence is the comparison of these layer maps before and after annealing: a 40% reduction in strain spread, a diffraction-ring FWHM drop from 0.033° to 0.011°, and a modest ~10% reduction in the mode of the geometrically necessary dislocation density, together pointing to confined dislocation annihilation between cementite lamellae as the relaxation mechanism.

What would settle it

Measure strain distributions in the same colony using an independent strain-free reference—for example, the lattice parameter of a fully recrystallized stress-free sample or an absolute d0 from a powder standard—instead of the post-annealing sample's own most frequent d-spacing. If the narrowing and recentering disappear or differ by more than the stated ~40%, the claimed relaxation is largely an artifact of the reference choice. Alternatively, direct transmission electron microscopy of the same colony before and after annealing could check for the predicted short-range dislocation annihilatio

Watch

Extended reading notes

Core claim

Using dark-field X-ray microscopy on a single pearlitic colony from a low-cycle-fatigued R7T wheel steel, the authors observe that annealing to 550°C reduces the width of the elastic strain distribution by roughly 40%, with the onset of recovery already below 250°C. Orientation maps stay essentially unchanged and no sub-cell formation is seen, so the recovery is not classical polygonization or recrystallization; instead, the strain narrowing is attributed to short-range dislocation annihilation or absorption at ferrite-cementite interfaces within the interlamellar spacing. This grain-scale relaxation is proposed as the microstructural origin of the hardness drop in pearlitic railway steels e

Load-bearing premise

The analysis treats the most common d-spacing after annealing as the strain-free reference, so the post-annealing strain distribution is forced to centre near zero; if the annealed state still contains locked-in strain, the measured 40% narrowing overstates the true relaxation.

Editorial extensions

If this is right

  • Railway wheel steels that experience frictional heating above about 250°C will begin to lose the work-hardened, compressive strain state in surface pearlite colonies before any visible spheroidisation occurs.
  • Predictive models of wheel softening and fatigue life should include sub-250°C grain-scale recovery of ferrite elastic strain, not only pearlite spheroidisation at 500°C and above.
  • Because the relaxation occurs without lattice rotation, narrowing of diffraction line profiles in fatigued pearlite can be interpreted as a reduction in dislocation density rather than as recrystallization or sub-grain formation.
  • The same DFXM approach can quantify strain relaxation in other lamellar or interface-confined microstructures where dislocation motion is restricted to narrow channels.

Reading between the lines

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

  • A natural extension would be to anneal a virgin, never-fatigued pearlite colony under the same conditions, isolating the contribution of fatigue-induced dislocations from thermal expansion and unavoidable microstructural evolution.
  • The proposed mechanism predicts that relaxation should be fastest where the interlamellar spacing is smallest, since annihilation is confined to the ferrite lamellae; mapping colonies with different spacings would provide a direct test.
  • Because the strain maps cover only a limited angular range of the grain, the 40% figure describes the mapped portion; full-orientation integration could shift the quantitative value, although the directional conclusion would likely stand.
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

3 major / 6 minor

Summary. The paper reports operando Dark-Field X-ray Microscopy (DFXM) observations of a single pearlite colony in a fatigued R7T railway-wheel steel during annealing up to 550 °C. Orientation maps show negligible lattice rotation and no sub-cell formation, while projection mosaicity maps reveal a progressive increase in the mapped grain area. Layer-resolved strain maps before and after the thermal cycle show a decrease in the diffraction-ring FWHM from 0.033° to 0.011° and a ~40% reduction in the standard deviation of the elastic strain distribution. A small reduction in the mode of the GND-density distribution is also reported. The authors attribute the strain relaxation to short-range dislocation annihilation confined between cementite lamellae and connect this grain-scale recovery to macroscopic softening of pearlitic railway steels.

Significance. If the quantitative claims hold, this would be a valuable grain-scale, operando demonstration that recovery begins below 250 °C in fatigued pearlitic steel, with direct relevance to railway-wheel service conditions. The study has several strengths: two independent observables support the qualitative strain-spread narrowing (diffraction-ring FWHM and strain-map standard deviation), the GND analysis carefully restricts to regions present in both conditions, and the Debye-Scherrer ring result provides a useful negative control with an explicit resolution caveat. The single-grain nature of the study is stated as a limitation. However, the quantitative strain-map comparison is compromised by possible region mismatch between the pre- and post-annealing maps, and the strain reference is defined in a way that makes the reported 'recentering' tautological. These issues are fixable but require reanalysis or careful rewording, so the present version warrants major revision.

major comments (3)
  1. [Fig. 4(d)–(e) and accompanying text] The strain-map comparison before and after annealing may not be like-for-like. The text states that the central φ value in the strain scans was adjusted after annealing to align with newly visible regions in the mosaicity maps, and it does not state that the strain histograms were restricted to pixels present in both conditions. This is in contrast to the GND-density analysis, which explicitly considers only portions of the grain present both before and after annealing. If the post-annealing strain histogram includes newly visible, low-strain regions that were absent in the pre-annealing histogram, the standard deviation will decrease even if the originally visible material is unchanged. Please recompute Fig. 4(e) using a common mask, or quantify the spatial overlap and show that the 40% narrowing is robust. If a common-mask analysis is not possible, the 40% value should be presented as
  2. [Fig. 4(e) and 'strain-free reference' definition] The strain values are calculated relative to the most frequent d-spacing observed post-annealing, which is treated as the strain-free reference. This definition forces the post-annealing strain distribution to center near zero, so the statement that the distribution 'recenters around the strain-free value' is circular. The narrowing of the standard deviation is independent of this reference choice and remains a valid observation, but the claims that both compressive and tensile strains 'relax' and that the distribution 'recenters' are not supported by an independent measurement. Please remove the recentering language or validate the reference using an independently annealed standard or another method.
  3. [Fig. 3 and 'below 250 °C' claim] The abstract and conclusions state that recovery starts below 250 °C, but the supporting evidence is an increase in projected area in projection mosaicity maps, not strain measurements at intermediate temperatures. The attribution of the area increase to strain relaxation is presented as a hypothesis. Since no layer strain maps were acquired during the temperature ramps, the onset temperature of strain relaxation is not directly measured. Please either provide intermediate-temperature strain data or rephrase the claim as an area increase below 250 °C that is consistent with, but not proof of, strain relaxation.
minor comments (6)
  1. [Fig. 4(c) and (e)] Please report the number of pixels and layers included in the strain histograms and explicitly state whether the same common-region mask used for the GND analysis was applied to the strain analysis. This would clarify the comparability of the two distributions.
  2. [Fig. 4(a)] The FWHM is quoted in degrees and the text notes that it convolutes strain and grain thickness. Consider adding the corresponding strain conversion using Bragg’s law, or state clearly why an angular-width comparison is used instead.
  3. [Eq. (1)] Please provide a brief justification for α = 2 and for the use of the 175 nm pixel distance in the GND-density estimate. A short derivation or a more explicit citation would help readers assess the prefactor.
  4. [Strain reference terminology] The term 'strain-free reference' is loaded; unless the post-annealing state is independently validated as truly strain-free, consider calling it the 'internal reference' or 'post-annealing reference' to avoid implying an absolute strain zero.
  5. [Appendix B] The comparison of the (110) peak with the Si calibrant is useful, but the text should note that the Si calibrant and the steel sample are measured at different energies and possibly different detector distances. This does not change the conclusion but improves clarity.
  6. [General] A few typographical and minor grammatical issues remain, e.g., inconsistent capitalization of 'darfix' and a missing dash in 'Debye-Scherrer'. A careful proofread is recommended.

Circularity Check

1 steps flagged · score 4.0 of 10

Mild circularity: the strain 'recentering' is imposed by the post-annealing reference choice, but the 40% width narrowing is reference-independent.

  1. self definitional [Results, layer strain maps / Fig. 4.e, paragraph beginning 'Fig. 4.d presents strain maps...' and the strain-calculation sentence]
    "The strain values were calculated relative to the most frequent d-spacing observed in the sample post-annealing, which was treated as the strain-free reference, given the expected strain relaxation during annealing. ... The post-annealing distribution demonstrates a notable reduction in the elastic strain spread, with the standard deviation decreasing by almost 40 %. Both compressive and tensile strains appear to relax, as the distribution recenters around the strain-free value."

    The post-annealing strain distribution is defined relative to its own most frequent d-spacing, so its center is zero by construction. Saying that it 'recenters around the strain-free value' is therefore not an empirical observation of relaxation; it is a restatement of the chosen reference. Likewise, the pre-annealing 'predominantly compressive' offset is measured against the post-annealing mode, so the sign carries no independent information about relaxation. The standard-deviation narrowing is translation-invariant and is not invalidated by this particular step.

full rationale

The one clear circular element is the use of the post-annealing modal d-spacing as the strain-free reference and then reporting that the distribution 'recenters' around it. This is a definitional consequence, not an independent measurement. However, the paper's central quantitative claim, the ~40% reduction in the width (standard deviation) of the strain distribution, is not an artifact of this reference choice: a uniform shift of all strain values does not change the spread. The diffraction-ring FWHM reduction from 0.033 deg to 0.011 deg and the GND analysis also provide partially independent support for relaxation. I considered the reader's additional concern that the pre- and post-annealing strain maps may not cover identical grain regions: the text notes that the central phi value was adjusted after annealing to align with newly visible regions, and only the mu angle was integrated, so the comparison may be confounded. That is a validity risk, but not circularity: the width reduction is not forced by the reference convention, and the paper did restrict the GND comparison to portions present in both conditions. No load-bearing self-citation chain or imported uniqueness theorem is used; citations to prior DFXM work are methodological. Overall, the circularity is limited to the 'recentering' interpretation, so a moderate score of 4 is appropriate rather than a higher score that would imply the main narrowing result reduces by construction.

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

The paper introduces no new entities or forces. The central claim rests on three main assumptions: (1) the annealed state is a valid zero-strain reference (an ad hoc choice that partially builds in the result), (2) a single bright grain is representative, and (3) projected-area changes during ramps act as a proxy for strain relaxation. There is one fitted parameter—the post-annealing reference d-spacing—that directly affects the reported strain values. Additional methodological constants (α=2, b=0.247 nm, x=175 nm) are taken from literature and are not fitted here.

free parameters (1)
  • Post-annealing reference d-spacing = Most frequent d-spacing in the post-annealing strain maps
    Used as the zero-strain reference for all strain calculations (Fig. 4d,e). The value is fit from the post-annealing data itself, so the post-annealing strain distribution is centered at zero by construction.
assumptions (4)
  • ad hoc to paper The post-annealing d-spacing state is a valid strain-free reference
    Invoked in the strain calculation: 'strain values were calculated relative to the most frequent d-spacing observed in the sample post-annealing, which was treated as the strain-free reference'. If the annealed state retains residual strain, the reported recentering is misleading.
  • domain assumption The selected pearlite colony is representative of the fatigue-affected material
    Only a single colony, chosen for highest diffraction intensity, was mapped. The paper acknowledges 'there is no evidence suggesting that this observation can be generalized to all grains in the sample'.
  • domain assumption The increase in projected grain area during annealing is due to elastic strain reduction, not other microstructural changes
    Used to infer recovery starting below 250°C from mosaicity maps (Fig. 3b). Orientation stability is argued from layer maps before/after, but no direct in-ramp orientation or strain data at the onset temperature are presented.
  • domain assumption Grain shape and size remain unchanged during annealing
    Assumed when interpreting the FWHM reduction of the diffraction ring (0.033° to 0.011°) as purely strain-related: 'The grain shape and size are expected to remain unchanged at the studied temperatures, so their contribution to the FWHM is constant.'

how reviews work

0 comments
Cite this review

Pith. "Pith review of Operando observation of strain relaxation in fatigued pearlitic steel." pith.science (2026). https://pith.science/paper/EVJHFXCJ

@misc{pith2026260716867,
  author       = {Pith},
  title        = {Pith review of: Operando observation of strain relaxation in fatigued pearlitic steel},
  year         = {2026},
  howpublished = {\url{https://pith.science/paper/EVJHFXCJ}},
  note         = {Machine review of arXiv:2607.16867}
}
read the original abstract

Pearlitic steels are the material of choice for railway wheels and rails, where their lamellar ferrite-cementite structure balances cost, strength, and wear resistance. However, in use, cyclic loading combined with frictional heat softens the steel, promoting fatigue and eventual failure. Here we use Dark-Field X-ray Microscopy (DFXM) to follow, operando, the grain-scale response of a fatigued pearlitic colony during annealing up to 550 {\deg}C. Orientation maps reveal negligible lattice rotation and no sub-cell formation, indicating that the cementite lamellae suppress long-range dislocation motion. Strain maps nonetheless show pronounced relaxation: the elastic strain spread narrows by nearly 40%, with recovery starting below 250 {\deg}C, within the operating temperatures of railway wheels. We attribute this relaxation to short-range annihilation of dislocations confined between lamellae, linking grain-scale strain recovery to the macroscopic softening of pearlitic railway steels in service.

Figures

Figures reproduced from arXiv: 2607.16867 by the authors.

Figure 1
Figure 1. SEM secondary electrons image of a cross-section of a R7T specimen. [PITH_FULL_IMAGE:figures/full_fig_p003_1.png] view at source ↗
Figure 2
Figure 2. (a) Setup for DFXM at the ESRF ID03 beamline. The near-field detector and the [PITH_FULL_IMAGE:figures/full_fig_p005_2.png] view at source ↗
Figure 3
Figure 3. Evolution of the mosaicity maps during annealing/cooling (a) Mosaicity maps of the [PITH_FULL_IMAGE:figures/full_fig_p006_3.png] view at source ↗
Figures from the paper (3 more)
Figure 4
Figure 4. Figure 4: Evolution of grain layers before and after annealing. (a) Portion of the diffraction [PITH_FULL_IMAGE:figures/full_fig_p007_4.png]
Figure 4
Figure 4. Figure 4: e. The observed strain in the grain of interest appears to be predominantly [PITH_FULL_IMAGE:figures/full_fig_p008_4.png]
Figure 5
Figure 5. Figure 5: Proposed mechanism upon annealing: strain relaxation without long-range lattice [PITH_FULL_IMAGE:figures/full_fig_p009_5.png]

Discussion (0). Continue with ORCID to comment.

Reference graph

Works this paper leans on

33 extracted references

  1. [1]

    Walther, D

    F. Walther, D. Eifler, Fatigue behaviour of railway wheels at different tem- peratures: interrelation of the microstructure and the fatigue behaviour of railway wheels at ambient and elevated temperatures, Materials Testing 46 (4) (2004) 158–162

    2004

  2. [2]

    A. J. Perez-Unzueta, J. H. Beynon, Microstructure and wear resistance of pearlitic rail steels, Wear 162 (1993) 173–182

    1993

  3. [3]

    K. M. Lee, A. A. Polycarpou, Wear of conventional pearlitic and improved bainitic rail steels, Wear 259 (1-6) (2005) 391–399

    2005

  4. [4]

    Nikas, J

    D. Nikas, J. Ahlström, A. Malakizadi, Mechanical properties and fatigue behaviour of railway wheel steels as influenced by mechanical and thermal loadings, Wear 366 (2016) 407–415. 10

    2016

  5. [5]

    Faccoli, A

    M. Faccoli, A. Ghidini, A. Mazzù, Changes in the microstructure and me- chanical properties of railway wheel steels as a result of the thermal load caused by shoe braking, Metallurgical and Materials Transactions A 50 (4) (2019) 1701–1714

    2019

  6. [6]

    Taniyama, T

    A. Taniyama, T. Takayama, M. Arai, T. Hamada, Structure analysis of ferrite in deformed pearlitic steel by means of x-ray diffraction method with synchrotron radiation, Scripta materialia 51 (1) (2004) 53–58

    2004

  7. [7]

    Ghosh, K

    P. Ghosh, K. Kormout, U. Lienert, J. Keckes, R. Pippan, Deformation characteristics of ultrafine grained and nanocrystalline iron and pearlitic steel-an in situ synchrotron investigation, Acta Materialia 160 (2018) 22– 33

    2018

  8. [8]

    Zhang, C

    Y. Zhang, C. Jessop, D. Nikas, T. Yu, W. Liu, J. Ahlström, Stress relief during annealing of railway wheel steel characterized by synchrotron x- ray micro-diffraction, in: IOP Conference Series: Materials Science and Engineering, Vol. 1249, IOP Publishing, 2022, p. 012043

    2022

Show all 33 references
  1. [9]

    Lesage, J

    L. Lesage, J. Ball, J. Ahlström, W. Ludwig, A. Shukla, C. Yildirim, Chal- lenges in mapping pearlite using 3d synchrotron techniques, Accepted by IOP Conference Series: Materials Science and Engineering (2026)

    2026

  2. [10]

    H. F. Poulsen, A. Jakobsen, H. Simons, S. R. Ahl, P. Cook, C. Detlefs, X-ray diffraction microscopy based on refractive optics, Applied Crystal- lography 50 (5) (2017) 1441–1456

    2017

  3. [11]

    Ahlström, B

    J. Ahlström, B. Karlsson, Fatigue behaviour of rail steel - a comparison between strain and stress controlled loading, Wear 258 (7-8) (2005) 1187– 1193

    2005

  4. [12]

    Ahlström, E

    J. Ahlström, E. Kabo, A. Ekberg, Temperature-dependent evolution of the cyclic yield stress of railway wheel steels, Wear 366 (2016) 378–382

    2016

  5. [13]

    Isern, T

    H. Isern, T. Brochard, T. Dufrane, P. Brumund, E. Papillon, D. Scortani, R. Hino, C. Yildirim, R. Rodriguez Lamas, Y. Li, et al., The esrf dark-field x-ray microscope at id03, in: Journal of Physics: Conference Series, Vol. 3010, IOP Publishing, 2025, p. 012163

    2025

  6. [14]

    Lesage, Y

    L. Lesage, Y. Watier, H. Isern, A. Shukla, V. Sanna, T. Dufrane, Y. Zhang, C. Detlefs, C. Yıldırım, A high-temperature furnace for mul- timodal synchrotron-based x-ray microscopy and diffraction imaging, Syn- chrotron Radiation 33 (1) (2026)

    2026

  7. [15]

    F. Nix, D. MacNair, The thermal expansion of pure metals: copper, gold, aluminum, nickel, and iron, Physical review 60 (8) (1941) 597

    1941

  8. [16]

    Garriga Ferrer, R

    J. Garriga Ferrer, R. Rodríguez-Lamas, H. Payno, W. De Nolf, P. Cook, V. A. Solé Jover, C. Yildirim, C. Detlefs, darfix–data analysis for dark-field x-ray microscopy, Synchrotron Radiation 30 (3) (2023) 527–537. 11

    2023

  9. [17]

    Yildirim, C

    C. Yildirim, C. Jessop, J. Ahlström, C. Detlefs, Y. Zhang, 3d mapping of orientation variation and local residual stress within individual grains of pearlitic steel using synchrotron dark field x-ray microscopy, Scripta Materialia 197 (2021) 113783

    2021

  10. [18]

    S. R. Ahl, H. Simons, Y. Zhang, C. Detlefs, F. Stöhr, A. C. Jakobsen, D. J. Jensen, H. F. Poulsen, Ultra-low-angle boundary networks within recrystallizing grains, Scripta Materialia 139 (2017) 87–91

    2017

  11. [19]

    A. A. W. Cretton, A. Zelenika, F. Frankus, C. Yıldırım, C. Detlefs, F. B. Grumsen, G. Winther, H. F. Poulsen, Observation of the formation and sharpening of geometrically necessary boundaries, Materials Research Let- ters 13 (7) (2025) 759–767

    2025

  12. [20]

    A. J. Wilkinson, D. Randman, Determination of elastic strain fields and ge- ometrically necessary dislocation distributions near nanoindents using elec- tron back scatter diffraction, Philosophical magazine 90 (9) (2010) 1159– 1177

    2010

  13. [21]

    Moussa, M

    C. Moussa, M. Bernacki, R. Besnard, N. Bozzolo, About quantitative ebsd analysis of deformation and recovery substructures in pure tantalum, in: IOP Conference Series: Materials Science and Engineering, Vol. 89, IOP Publishing, 2015, p. 012038

    2015

  14. [22]

    Yildirim, A

    C. Yildirim, A. Shukla, Y. Zhang, N. Mavrikakis, L. Lesage, V. Sanna, M. Sarkis, Y. Li, M. La Bella, C. Detlefs, et al., 3d/4d imaging of complex and deformed microstructures with pink-beam dark field x-ray microscopy, Communications Materials 6 (1) (2025) 198

    2025

  15. [23]

    Nikas, X

    D. Nikas, X. Zhang, J. Ahlström, Evaluation of local strength via mi- crostructural quantification in a pearlitic rail steel deformed by simulta- neous compression and torsion, Materials Science and Engineering: A 737 (2018) 341–347

    2018

  16. [24]

    S. Dhar, J. Ahlström, X. Zhang, H. Danielsen, D. Juul Jensen, Multi-axial fatigue of head-hardened pearlitic and austenitic manganese railway steels: A comparative study, Metallurgical and Materials Transactions A 51 (11) (2020) 5639–5652

    2020

  17. [25]

    F. J. Humphreys, M. Hatherly, Recrystallization and Related Annealing Phenomena, Pergamon, Oxford, U.K., 1995

    1995

  18. [26]

    S. Li, T. Yip, R. Ramanujan, M. Liang, Insitu tem studies of the mecha- nisms of crack nucleation and propagation in fully lamellar microstructures, Materials science and technology 19 (7) (2003) 902–906

    2003

  19. [27]

    Ghaffarian, A

    H. Ghaffarian, A. K. Taheri, S. Ryu, K. Kang, Nanoindentation study of ce- mentite size and temperature effects in nanocomposite pearlite: A molecu- lar dynamics simulation, Current Applied Physics 16 (9) (2016) 1015–1025. 12

    2016

  20. [28]

    Y. Chen, G. Csiszár, J. Cizek, X. Shi, C. Borchers, Y. Li, F. Liu, R. Kirch- heim, Defect recovery in severely deformed ferrite lamellae during annealing and its impact on the softening of cold-drawn pearlitic steel wires, Metal- lurgical and Materials Transactions A 47 (2) (2...

    2016

  21. [29]

    Janakiram, P

    S. Janakiram, P. S. Phani, G. Ummethala, S. K. Malladi, J. Gautam, L. A. Kestens, New insights on recovery and early recrystallization of ferrite- pearlite banded cold rolled high strength steels by high speed nanoinden- tation mapping, Scripta Materialia 194 (2021) 113676

    2021

  22. [30]

    Liang, Y.-J

    L.-W. Liang, Y.-J. Wang, Y. Chen, H.-Y. Wang, L.-H. Dai, Dislocation nu- cleation and evolution at the ferrite-cementite interface under cyclic load- ings, Acta Materialia 186 (2020) 267–277

    2020

  23. [31]

    Cvetkovski, J

    K. Cvetkovski, J. Ahlström, B. Karlsson, Thermal degradation of pearlitic steels: influence on mechanical properties including fatigue behaviour, Ma- terials Science and Technology 27 (3) (2011) 648–654

    2011

  24. [32]

    Kieffer, V

    J. Kieffer, V. Valls, N. Blanc, C. Hennig, New tools for calibrating diffrac- tion setups, Synchrotron Radiation 27 (2) (2020) 558–566

    2020

  25. [33]

    Ashiotis, A

    G. Ashiotis, A. Deschildre, Z. Nawaz, J. P. Wright, D. Karkoulis, F. E. Picca, J. Kieffer, The fast azimuthal integration python library: pyfai, Applied Crystallography 48 (2) (2015) 510–519. Appendix A. DFXM acquisition details The table below shows the scanning parameters us...

    2015

Pith tools

Reviewed August 1, 2026 · model on record in the stance chip above.