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arxiv: 2602.19642 · v2 · submitted 2026-02-23 · ❄️ cond-mat.mtrl-sci

Recognition: 2 theorem links

· Lean Theorem

Corrosion Evolution of T91 Steel in Static Lead-Bismuth Eutectic Under an Oxidising Environment

Minyi Zhang , Weiyue Zhou , Michael P. Short , Paul A.J. Bagot , Michael P. Moody , Felix Hofmann
Authors on Pith no claims yet

Pith reviewed 2026-05-15 20:50 UTC · model grok-4.3

classification ❄️ cond-mat.mtrl-sci
keywords T91 steellead-bismuth eutecticcorrosionoxide scaleintergranular attackmartensite decompositionBCC phasenuclear structural materials
0
0 comments X

The pith

T91 steel forms an iron-enriched BCC surface layer in oxidizing lead-bismuth eutectic, with oxide scale stability deciding whether corrosion stays intergranular or spreads.

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

The paper examines the corrosion of T91 ferritic-martensitic steel in static lead-bismuth eutectic under high-temperature oxidizing conditions relevant to liquid-metal nuclear systems. Corrosion begins along grain boundaries through LBE ingress and chromium-oxygen diffusion, but local chromium depletion triggers martensite decomposition into ferrite that slows further attack. A stable, coherent oxide scale emerges as the key barrier that prevents intergranular penetration and limits damage to isolated regions. Unexpectedly, an iron-rich body-centered cubic phase layer grows on the surface, contradicting earlier reports that described only oxide layers. These observations matter because they identify concrete surface features that could be promoted to control corrosion rates in LBE-cooled reactors.

Core claim

In T91 steel exposed to static lead-bismuth eutectic under oxidizing conditions, LBE penetrates along grain boundaries, inducing chromium depletion that decomposes martensite to ferrite and thereby slows corrosion; a stable coherent oxide scale then determines whether attack remains localized or broadens, while an iron-enriched body-centered cubic phase unexpectedly forms as the outermost surface layer instead of the oxide-only structures reported previously.

What carries the argument

The stable coherent oxide scale that blocks intergranular LBE ingress, together with the iron-enriched BCC surface phase that forms during exposure.

If this is right

  • Promoting a stable oxide scale on T91 can restrict LBE attack to isolated grain boundaries rather than allowing widespread corrosion.
  • Chromium depletion and resulting ferrite formation provide a built-in slowing mechanism once corrosion starts.
  • The iron-enriched BCC layer replaces the expected oxide surface and may change how the material responds to further environmental exposure.
  • Material selection and surface treatment for LBE systems can target oxide scale coherence to reduce intergranular damage.

Where Pith is reading between the lines

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

  • Similar oxide-scale control and BCC-layer formation may appear in other 9Cr ferritic-martensitic steels under comparable oxidizing LBE conditions.
  • Adjusting oxygen levels in the LBE could be used to tune oxide scale growth and thereby extend the period before intergranular attack begins.
  • Surface mechanical properties or subsequent coating adhesion may differ from expectations because of the BCC layer rather than a conventional oxide.

Load-bearing premise

The iron-enriched BCC surface phase and the corrosion-slowing martensite decomposition are intrinsic responses to the oxidizing LBE environment rather than artifacts of sample preparation or limited test conditions.

What would settle it

Repeated tests on freshly prepared T91 samples with longer exposure times and independent surface analysis that still fail to detect the iron-enriched BCC phase would show the phase is not produced by the corrosion process itself.

Figures

Figures reproduced from arXiv: 2602.19642 by Felix Hofmann, Michael P. Moody, Michael P. Short, Minyi Zhang, Paul A.J. Bagot, Weiyue Zhou.

Figure 1
Figure 1. Figure 1: Different corrosion patterns for 70 h, 245 h, and 506 h corroded samples in [PITH_FULL_IMAGE:figures/full_fig_p012_1.png] view at source ↗
Figure 3
Figure 3. Figure 3: SEM-EBSD results highlighting the surface formed Fe-enriched layer with dashed rectangular [Sample: 70 h, oxidising environment, 700 ℃ , LBE]. (a) SEM image corresponding to EBSD maps. (b) EBSD-IPFZ map, showing only material indexed as BCC. (c) EBSD grain average misorientation map. After a prolonged exposure of 506 h, corrosion continues to propagate preferentially along martensitic GBs. However, the ext… view at source ↗
Figure 4
Figure 4. Figure 4: SEM-EDX and EBSD of oxidised GBs [Sample: 506 h, oxidising environment, 700 ℃, LBE]. (a) EDX map highlighting Fe. (b) EDX map highlighting Cr. (c) EDX map highlighting Si. (d) EBSD-IPFZ map. (e) EDX line scan result following the line shown in [PITH_FULL_IMAGE:figures/full_fig_p019_4.png] view at source ↗
Figure 5
Figure 5. Figure 5: Combining the results shown in Fig. 5(b) [PITH_FULL_IMAGE:figures/full_fig_p019_5.png] view at source ↗
Figure 5
Figure 5. Figure 5: Low energy SEM-EDX results [Sample: 245 h, oxidising environment, 700 ℃, LBE]. (a) SEM image with a red dashed box highlighting the GB oxidised region. (b) EDX result highlighting the Cr with the yellow dashed box showing the Cr depleted zone. (c) EDX result highlighting O. (d) EDX result highlighting Si. Pb and Bi were not detected in these maps [PITH_FULL_IMAGE:figures/full_fig_p020_5.png] view at source ↗
Figure 7
Figure 7. Figure 7: SEM-EDX line scan results for 245 h corroded sample in oxidising environment. (a) SEM SE image showing the position of the line scan and Mo-enriched precipitates. (b) EDX line scan result showing content of Cr, Fe, Mo, Si, and O. (c) EDX line scan showing Si and Cr content at the surface region. Cracks, potentially caused by the mismatch in thermal expansion between the substrate and the oxide scale, are o… view at source ↗
Figure 13
Figure 13. Figure 13: SEM-EDX and EBSD results for one representative area with no obvious corrosion in SEM view [Sample: 506 h, oxidising environment, 700 ℃, LBE]. (a) SEM view. (b) SEM-EDX result highlighting Cr. (c) SEM-EDX result highlighting Cr and Si. (d) SEM-EBSD IPFZ map. (e) SEM-EBSD grain average misorientation with scale bar. 4. Discussion In this study, T91 samples exposed to LBE under oxidizing conditions for 70 h… view at source ↗
read the original abstract

Understanding corrosion in liquid metal-cooled nuclear systems is essential in order be able to control it. While much literature exists detailing corrosion rates and mechanisms of structural materials in liquid metals, much still remains to be discovered in new regimes of temperature, chemistry, and impurity content. We focus on a less-studied set of conditions, specifically to investigate how liquid lead-bismuth eutectic (LBE) corrodes ferritic/martensitic steels under high-temperature oxidizing conditions. We find that corrosion follows grain boundaries, transitioning from intergranular attack to broader area corrosion as it progresses. Both chromium and oxygen diffusion play vital roles in this process. Mechanistically speaking, the ingress of LBE induces regions of martensite decomposition to ferrite via localized chromium depletion, somewhat slowing corrosion. A stable, coherent oxide scale appears to be the deciding factor that controls whether intergranular LBE attack occurs or not. Most surprisingly, a layer of iron enriched body-centred cubic phase forms on the surface of LBE-corroded T91 at these conditions, contradicting previous studies, which reported only oxide-based surface layers.

Editorial analysis

A structured set of objections, weighed in public.

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

Referee Report

3 major / 2 minor

Summary. The paper examines the corrosion evolution of T91 ferritic/martensitic steel in static lead-bismuth eutectic (LBE) under high-temperature oxidizing conditions. Corrosion proceeds via intergranular attack that transitions to broader area corrosion, with Cr and O diffusion playing key roles. Localized Cr depletion induces martensite-to-ferrite decomposition that slows further attack. A stable coherent oxide scale is presented as the primary control on whether intergranular LBE penetration occurs. Most notably, an iron-enriched BCC surface layer is reported on LBE-exposed samples, contradicting prior studies that observed only oxide-based surface layers.

Significance. If the microstructural observations hold after addressing the noted concerns, the work supplies useful mechanistic detail on LBE corrosion of T91 under oxidizing regimes relevant to liquid-metal-cooled nuclear systems. The emphasis on oxide-scale protection and the reported BCC phase (if confirmed as environment-specific) could guide alloy design and operating limits. The study is grounded in consistent qualitative microstructural evidence, though its impact is tempered by the absence of quantitative metrics and controls.

major comments (3)
  1. [microstructural characterization and Discussion] The claim of an iron-enriched BCC surface phase that contradicts previous oxide-only reports (Abstract and Discussion) is load-bearing for the novelty argument. No controls are described (e.g., identically prepared and analyzed unexposed T91 at the same temperature and oxygen potential) to exclude polishing-induced transformation, surface relaxation, or technique-specific effects (EBSD indexing or XRD penetration depth). This directly affects whether the observation is intrinsic to the LBE environment.
  2. [Discussion] The central assertion that a stable, coherent oxide scale is the deciding factor controlling intergranular LBE attack (Abstract and Discussion) rests on qualitative interpretation of microstructures without supporting quantitative data such as oxide thickness distributions, coverage statistics, or statistical correlation between oxide presence and attack depth across multiple samples or time points.
  3. [Methods] The manuscript lacks full experimental details on temperature, oxygen potential, test durations, sample preparation, and characterization protocols (including error bars or replicate statistics). This absence makes it difficult to assess reproducibility and to evaluate whether the reported martensite decomposition and slowed corrosion are robust or limited by the specific test conditions.
minor comments (2)
  1. [Figures] Figure captions and labels should explicitly indicate the corrosion stage, magnification, and technique (e.g., SEM, EBSD, XRD) for each panel to improve clarity.
  2. [Abstract] The abstract would benefit from stating the specific temperature and oxygen concentration range to place the conditions in context with prior LBE studies.

Simulated Author's Rebuttal

3 responses · 0 unresolved

We thank the referee for their thorough review and valuable comments. We address each major comment below and will revise the manuscript accordingly to improve clarity and completeness.

read point-by-point responses

  1. Referee: [microstructural characterization and Discussion] The claim of an iron-enriched BCC surface phase that contradicts previous oxide-only reports (Abstract and Discussion) is load-bearing for the novelty argument. No controls are described (e.g., identically prepared and analyzed unexposed T91 at the same temperature and oxygen potential) to exclude polishing-induced transformation, surface relaxation, or technique-specific effects (EBSD indexing or XRD penetration depth). This directly affects whether the observation is intrinsic to the LBE environment.

    Authors: We agree that additional controls would strengthen the claim regarding the iron-enriched BCC phase. In the revised version, we will include microstructural analysis of unexposed T91 samples subjected to the same preparation and characterization procedures to rule out artifacts from polishing or other effects. We will also provide more details on the EBSD indexing and XRD conditions to address concerns about technique-specific effects. revision: yes

  2. Referee: [Discussion] The central assertion that a stable, coherent oxide scale is the deciding factor controlling intergranular LBE attack (Abstract and Discussion) rests on qualitative interpretation of microstructures without supporting quantitative data such as oxide thickness distributions, coverage statistics, or statistical correlation between oxide presence and attack depth across multiple samples or time points.

    Authors: The referee is correct that our interpretation is primarily qualitative. While we observed consistent patterns across samples, we lack comprehensive quantitative statistics. In the revision, we will add available quantitative data on oxide thicknesses and attempt to provide coverage estimates from the existing micrographs. However, due to the nature of the study with limited replicates, full statistical correlation may not be feasible, and we will adjust the language to reflect the qualitative nature of the evidence. revision: partial

  3. Referee: [Methods] The manuscript lacks full experimental details on temperature, oxygen potential, test durations, sample preparation, and characterization protocols (including error bars or replicate statistics). This absence makes it difficult to assess reproducibility and to evaluate whether the reported martensite decomposition and slowed corrosion are robust or limited by the specific test conditions.

    Authors: We will revise the Methods section to include all requested experimental details, including precise values for temperature, oxygen potential, test durations, sample preparation protocols, and characterization methods. Where available, we will include error bars and information on replicates. revision: yes

Circularity Check

0 steps flagged

No circularity: purely observational experimental study

full rationale

The paper reports experimental observations of corrosion in T91 steel under LBE exposure using microscopy and surface analysis. No equations, models, fitted parameters, predictions, or derivations are present in the abstract or described content. Claims about oxide scales controlling intergranular attack, martensite decomposition, and the iron-enriched BCC surface phase are presented as direct empirical findings without any self-referential reduction to inputs. No self-citations form load-bearing chains, and no ansatzes or renamings of known results occur. The derivation chain is absent, making the study self-contained against external benchmarks.

Axiom & Free-Parameter Ledger

0 free parameters · 0 axioms · 0 invented entities

Experimental materials study with no free parameters, mathematical axioms, or postulated entities; observations rest on standard diffusion and phase-transformation principles in metallurgy.

pith-pipeline@v0.9.0 · 5516 in / 1126 out tokens · 28075 ms · 2026-05-15T20:50:23.550010+00:00 · methodology

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Reference graph

Works this paper leans on

65 extracted references · 65 canonical work pages

  1. [1]

    Department of Materials, University of Oxford, Parks Road, Oxford, OX1 3PH, United Kingdom

    work page

  2. [2]

    Max-Planck-Institute for Sustainable Materials, Max -Planck-Straße 1, Düsseldorf, 40237, Germany

    work page

  3. [3]

    4.Department of Nuclear Science and Engineering, Massachusetts Institute of Technology, 77 Massachusetts Avenue, Cambridge, MA 02139, USA

    Department of Engineering Science, University of Oxford, Parks Road, Oxford, OX1 3PJ, United Kingdom. 4.Department of Nuclear Science and Engineering, Massachusetts Institute of Technology, 77 Massachusetts Avenue, Cambridge, MA 02139, USA. 5.Australia's Nuclear Science and Technology Organisation , New Illawarra R oad, Sydney, Lucas Heights NSW 2234, Aus...

    work page

  4. [4]

    Introduction Liquid metals, such as lead –bismuth eutectic (LBE), pure lead (Pb), and lead– lithium (PbLi) alloys, are considered promising candidate coolants for Generation IV fast nuclear fission reactors, magnetic confinement fusion reactors, and concentrated solar po wer systems. These coolants possess several advantageous properties [1], including lo...

    work page

  5. [5]

    oxidizing

    Materials and Methods 2.1 Materials T91, also known as Fe -9Cr-1Mo steel, is a ferritic/martensitic (F/M) steel with body- centred cubic (BCC) lattice structure. The materials used in this study was purchased from Edelstahl Witten-Krefeld GMBH in the quenched and tempered (Q&T) condition, having undergone heat treatment in accordance with the manufacturer...

    work page

  6. [6]

    Its manifestation can vary with exposure duration (70 h, 245 h, and 506 h in this study) as well as spatially within a single specimen

    Results 3.1 Differences in observed corrosion patterns Corrosion is a complex process influenced by several microstructural factors, including surface condition, grain orientation, and grain boundary distribution among other factors [24]. Its manifestation can vary with exposure duration (70 h, 245 h, and 506 h in this study) as well as spatially within a...

    work page

  7. [7]

    1(a) and (b)

    Intergranular internal corrosion — This type occurs preferentially along grain boundaries (GBs), as shown in Fig. 1(a) and (b). The differences are that, as shown in Fig. 1(a), oxidation occurs along GBs with lath morphology in the 70 h exposure sample, whereas in the 245 h sample (Fig. 1(b)), oxidation extends predominantly along much more equiaxed grain...

    work page

  8. [8]

    1(d) –(f)), corrosion extends beyond GBs into the grain interior

    Wider a rea corrosion — In some regions (Fig. 1(d) –(f)), corrosion extends beyond GBs into the grain interior. These regions appear sporadically and may represent an advanced stage of intergranular corrosion, in which corrosion initiates at grain boundaries and extends into adjacent grains, forming wider corroded areas . The red arrows in Fig. 1( f) indi...

    work page

  9. [9]

    These regions may be the result of partial passivation at elevated temperatures (>600 ℃ )

    Unaffected regions — For all three exposure-times areas that exhibit no visible corrosion could be identified, indicating local variations in corrosion 11 susceptibility. These regions may be the result of partial passivation at elevated temperatures (>600 ℃ ). As mentioned earlier, passivation under these conditions is likely to be in complete. However, ...

    work page

  10. [10]

    Combining this crystallographic information with our EDX results suggests that the surface layer is composed of ferrite rather than an oxide

    are both face -centred cubic (FCC) phases . Combining this crystallographic information with our EDX results suggests that the surface layer is composed of ferrite rather than an oxide . This differs from previous reports , which commonly identified the surface layer as Fe 3O4 [28, 29] . This BCC layer is spatially heterogeneous and discontinuous across t...

    work page

  11. [11]

    Discussion In this study, T91 samples exposed to LBE under oxidizing conditions for 70 h, 245 h and 506 h at 700 ℃ were analyzed. The oxides located at different positions of the oxide film have been examined in using EDX and EBSD to understand the evolution of 32 both chemical composition and crystallograph y. Intergranular internal oxidation , wider are...

    work page

  12. [12]

    In the reducing environment, the dissolution of elements (Cr, Ni, Fe…) plays the main role in the corrosion, which induces a corrosion pattern that does not follow the GBs

    Conclusion Based on the mechanistic analysis presented in the discussion, the oxidation and corrosion behaviour of T91 exposed to oxygen -controlled LBE at 700 °C can be described by the following conclusions: Corrosion follows GBs: The corrosion process begins with intergranular internal corrosion, with Cr-enriched and Si-enriched oxides forming along gr...

    work page

  13. [13]

    Acta Materialia, 2025

    Gong, X., et al., Atomic -scale dissolution corrosion mechanism of additively - manufactured 316L steels in liquid lead-bismuth eutectic. Acta Materialia, 2025. 290: p. 120963

    work page 2025

  14. [14]

    Acta Materialia, 2024: p

    Zhang, M., et al., Nano -scale corrosion mechanism of T91 steel in static lead - bismuth eutectic: A combined APT, EBSD, and STEM investigation. Acta Materialia, 2024: p. 119883

    work page 2024

  15. [15]

    Saint Anne’s Academic Review, 2019

    Davis, T.P., Dispelling misconceptions of nuclear energy technology: How Generation IV nuclear reactors could become the key to achieving the Paris Agreement and the United Kingdom’s net zero CO2 emissions target by 2050. Saint Anne’s Academic Review, 2019. 9

    work page 2050

  16. [16]

    Toloczko, and B.H

    Garner, F.A., M.B. Toloczko, and B.H. Sencer, Comparison of swelling and irradiation creep behavior of fcc -austenitic and bcc -ferritic/martensitic alloys at high neutron exposure. Journal of Nuclear Materials, 2000. 276(1-3): p. 123-142

    work page 2000

  17. [17]

    Materialia, 2020

    Davis, T.P., et al., Atom probe characterisation of segregation driven Cu and Mn – Ni–Si co -precipitation in neutron irradiated T91 tempered -martensitic steel. Materialia, 2020. 14

    work page 2020

  18. [18]

    Journal of Nuclear Materials, 1996

    Kohyama, A., et al., Low-activation ferritic and martensitic steels for fusion application. Journal of Nuclear Materials, 1996. 233: p. 138-147

    work page 1996

  19. [19]

    Kurata, Y. and S. Saito, Temperature Dependence of Corrosion of Ferritic/Martensitic and Austenitic Steels in Liquid Lead -Bismuth Eutectic. Materials Transactions, 2009. 50(10): p. 2410-2417

    work page 2009

  20. [20]

    Progress in Nuclear Energy, 2014

    Alemberti, A., et al., Overview of lead -cooled fast reactor activities. Progress in Nuclear Energy, 2014. 77: p. 300-307

    work page 2014

  21. [21]

    Rebak, R.B. and D.D. Ellis. Passivation Characteristics of Ferritic Stainless Materials in Simulated Reactor Environments. in NACE CORROSION. 2016. NACE

    work page 2016

  22. [22]

    Journal of Nuclear materials,

    Li, N., Active control of oxygen in molten lead –bismuth eutectic systems to prevent steel corrosion and coolant contamination. Journal of Nuclear materials,

    work page

  23. [23]

    Journal of Nuclear Materials, 2019

    Popovic, M.P., et al., Oxidative passivation of Fe –Cr–Al steels in lead -bismuth eutectic under oxygen-controlled static conditions at 700° and 800° C. Journal of Nuclear Materials, 2019. 523: p. 172-181

    work page 2019

  24. [24]

    Stability of oxide layer formed on high-chromium steels in LBE under oxygen content and temperature fluctuation

    Weisenburger, A., et al. Stability of oxide layer formed on high-chromium steels in LBE under oxygen content and temperature fluctuation . in The 13th international conference on nuclear engineering abstracts. 2005

    work page 2005

  25. [25]

    Corrosion Science, 2025

    Zhang, M., et al., Correlated chromium carbide dissociation and phase transformation in liquid lead -bismuth eutectic corroded T91 steel. Corrosion Science, 2025. 249: p. 112851

    work page 2025

  26. [26]

    -L., et al., Impurities and oxygen control in lead alloys

    Courouau, J. -L., et al., Impurities and oxygen control in lead alloys. Journal of Nuclear Materials, 2002. 301(1): p. 53-59

    work page 2002

  27. [27]

    Journal of Nuclear Materials, 2001

    Barbier, F., et al., Compatibility tests of steels in flowing liquid lead –bismuth. Journal of Nuclear Materials, 2001. 295(2-3): p. 149-156

    work page 2001

  28. [28]

    Journal of Nuclear Materials, 1988

    Tas, H., et al., Liquid breeder materials. Journal of Nuclear Materials, 1988. 155: p. 178-187

    work page 1988

  29. [29]

    Terlain, and T

    Simon, N., A. Terlain, and T. Flament, The compatibility of austenitic materials with liquid Pb–17Li. Corrosion science, 2001. 43(6): p. 1041-1052. 43

    work page 2001

  30. [30]

    Gomez- Acebo, and F

    Laverde, D., T. Gomez- Acebo, and F. Castro, Continuous and cyclic oxidation of T91 ferritic steel under steam. Corrosion science, 2004. 46(3): p. 613-631

    work page 2004

  31. [31]

    Journal of Nuclear Materials, 2007

    Was, G., et al., Corrosion and stress corrosion cracking in supercritical water. Journal of Nuclear Materials, 2007. 371(1-3): p. 176-201

    work page 2007

  32. [32]

    Vallourec Industries, 1990

    Guntz, G., et al., The T91 book. Vallourec Industries, 1990

    work page 1990

  33. [33]

    Ballinger, and H

    Short, M., R. Ballinger, and H. Hänninen, Corrosion resistance of alloys F91 and Fe–12Cr–2Si in lead–bismuth eutectic up to 715 C. Journal of nuclear materials,

    work page

  34. [34]

    434(1-3): p. 259-281

    work page

  35. [35]

    2010, Massachusetts Institute of Technology

    Short, M.P., The Design of a functionally graded composite for service in high temperature lead and lead -bismuth cooled nuclear reactors . 2010, Massachusetts Institute of Technology

    work page 2010

  36. [36]

    Meisnar, M., et al., Low-energy EDX–A novel approach to study stress corrosion cracking in SUS304 stainless steel via scanning electron microscopy. Micron,

    work page

  37. [37]

    2013: Newnes

    Shreir, L.L., Corrosion: metal/environment reactions. 2013: Newnes

    work page 2013

  38. [38]

    ESTAR, PSTAR, and ASTAR: Computer Programs for Calculating Stopping- Power and Range Tables for Electrons, Protons, and Helium Ions

    Berger, M.J., Coursey, J.S., Zucker, M.A., and Chang, J. ESTAR, PSTAR, and ASTAR: Computer Programs for Calculating Stopping- Power and Range Tables for Electrons, Protons, and Helium Ions . NIST Standard Reference Database 124 2017 2.2.2026]; Available from: https://physics.nist.gov/PhysRefData/Star/Text/ESTAR.html?utm_source=chatg pt.com

    work page 2017

  39. [40]

    Zhang, and Z

    Chen, K., L. Zhang, and Z. Shen, Understanding the surface oxide evolution of T91 ferritic-martensitic steel in supercritical water through advanced characterization. Acta Materialia, 2020. 194: p. 156-167

    work page 2020

  40. [41]

    Acta Materialia, 2020

    Shen, Z., et al., New insights into the oxidation mechanisms of a Ferritic - Martensitic steel in high -temperature steam. Acta Materialia, 2020. 194: p. 522 - 539

    work page 2020

  41. [42]

    Langmuir,

    Chen, G., et al., Ultrastable lubricating properties of robust self- repairing tribofilms enabled by in situ-assembled polydopamine nanoparticles. Langmuir,

    work page

  42. [43]

    Corrosion Science, 2025: p

    Cairang, W., et al., Simultaneous proton irradiation and dissolution corrosion of SS316L in liquid Pb-4Bi alloy. Corrosion Science, 2025: p. 113010

    work page 2025

  43. [44]

    Zheng, and Y

    Zhou, Q., Z. Zheng, and Y. Gao, Abnormal selective dissolution by the partial recrystallization in a plastically deformed austenitic stainless steel. Corrosion Science, 2021. 188: p. 109548

    work page 2021

  44. [45]

    da Fonseca, and E.A

    de Souza Silva, E.M.F., G.S. da Fonseca, and E.A. Ferreira, Microstructural and selective dissolution analysis of 316L austenitic stainless steel. Journal of Materials Research and Technology, 2021. 15: p. 4317-4329

    work page 2021

  45. [46]

    Corrosion Science, 2015

    Martinelli, L., et al., Comparative oxidation behaviour of Fe -9Cr steel in CO2 and H2O at 550 C: Detailed analysis of the inner oxide layer. Corrosion Science, 2015. 100: p. 253-266

    work page 2015

  46. [47]

    Corrosion Science, 2008

    Martinelli, L., et al., Oxidation mechanism of a Fe –9Cr–1Mo steel by liquid Pb– Bi eutectic alloy (Part I). Corrosion Science, 2008. 50(9): p. 2523-2536

    work page 2008

  47. [48]

    Corrosion Science, 2008

    Martinelli, L., et al., Oxidation mechanism of an Fe–9Cr–1Mo steel by liquid Pb–Bi eutectic alloy at 470 C (Part II). Corrosion Science, 2008. 50(9): p. 2537-2548

    work page 2008

  48. [49]

    Ellingham, H.J., Reducibility of oxides and sulphides in metallurgical processes. J. Soc. Chem. Ind, 1944. 63(5): p. 125-160. 44

    work page 1944

  49. [50]

    Young, D.J., High temperature oxidation and corrosion of metals . Vol. 1. 2008: Elsevier

    work page 2008

  50. [51]

    Meier, and F.S

    Birks, N., G.H. Meier, and F.S. Pettit, Introduction to the high temperature oxidation of metals. 2006: Cambridge university press

    work page 2006

  51. [52]

    Ren, and T.R

    Tan, L., X. Ren, and T.R. Allen, Corrosion behavior of 9–12% Cr ferritic–martensitic steels in supercritical water. Corrosion science, 2010. 52(4): p. 1520-1528

    work page 2010

  52. [53]

    Bischoff, J. and A.T. Motta, Oxidation behavior of ferritic –martensitic and ODS steels in supercritical water. Journal of Nuclear Materials, 2012. 424(1-3): p. 261- 276

    work page 2012

  53. [54]

    Scientific reports, 2016

    Ye, Z., et al., Oxidation mechanism of T91 steel in liquid lead -bismuth eutectic: with consideration of internal oxidation. Scientific reports, 2016. 6(1): p. 35268

    work page 2016

  54. [55]

    Yang, and T

    Tan, L., Y. Yang, and T. Allen, Oxidation behavior of iron -based alloy HCM12A exposed in supercritical water. Corrosion Science, 2006. 48(10): p. 3123-3138

    work page 2006

  55. [56]

    Sridharan, and T

    Chen, Y., K. Sridharan, and T. Allen, Corrosion behavior of ferritic– martensitic steel T91 in supercritical water. Corrosion Science, 2006. 48(9): p. 2843-2854

    work page 2006

  56. [57]

    Sun, L. and W. Yan, Estimation of Oxidation Kinetics and O xide Scale Void Position of Ferritic ‐ Martensitic Steels in Supercritical Water. Advances in Materials Science and Engineering, 2017. 2017(1): p. 9154934

    work page 2017

  57. [58]

    Oxidation of Metals, 2019

    Li, Y., et al., Predictions and analyses on the growth behavior of oxide scales formed on ferritic– martensitic in supercritical water. Oxidation of Metals, 2019. 92(1): p. 27-48

    work page 2019

  58. [59]

    Surface and coatings technology, 2013

    Agüero, A., et al., Oxidation under pure steam: Cr based protective oxides and coatings. Surface and coatings technology, 2013. 237: p. 30-38

    work page 2013

  59. [60]

    Journal of Materials Science & Technology, 2016

    Ma, L., et al., Effects of Cr content on the microstructure and properties of 26Cr– 3.5 Mo –2Ni and 29Cr –3.5 Mo –2Ni super ferritic stainless steels. Journal of Materials Science & Technology, 2016. 32(6): p. 552-560

    work page 2016

  60. [61]

    Journal of nuclear materials, 2009

    Gilbert, M., et al., Vacancy defects in Fe: Comparison between simulation and experiment. Journal of nuclear materials, 2009. 386: p. 36-40

    work page 2009

  61. [62]

    Krishnamurthy, R. and D. Srolovitz, Stress distributions in growing oxide films. Acta materialia, 2003. 51(8): p. 2171-2190

    work page 2003

  62. [63]

    Materials Research, 2004

    Galerie, A., et al., Stress and adhesion of chromia-rich scales on ferritic stainless steels in relation with spallation. Materials Research, 2004. 7: p. 81-88

    work page 2004

  63. [64]

    Acta Materialia, 2006

    Bamba, G., et al., Thermal oxidation kinetics and oxide scale adhesion of Fe–15Cr alloys as a function of their silicon content. Acta Materialia, 2006. 54(15): p. 3917- 3922

    work page 2006

  64. [65]

    Vogt, J.-B. and I. Proriol Serre, A review of the surface modifications for corrosion mitigation of steels in lead and LBE. Coatings, 2021. 11(1): p. 53

    work page 2021

  65. [66]

    Coatings, 2021

    Wang, H., et al., Corrosion behavior and surface treatment of cladding materials used in high-temperature lead-bismuth eutectic alloy: A review. Coatings, 2021. 11(3): p. 364. 45 Supplementary S1. Higher magnification SEM images of the 70 h corroded sample. 46 S2. SEM-EDX results [Sample: 70 h, oxidising environment, 700 ℃, LBE]. (a) SEM image. (b), (c), ...

    work page 2021