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REVIEW 4 major objections 4 minor 33 references

Engineering Work Function to Stabilize Metal Oxides in Reactive Hydrogen

T0 review · 4 major / 4 minor · reviewed 2026-08-12 · deepseek-v4-flash

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Pith's one-line read The paper argues that the work function of a transition-metal compound is the tunable parameter controlling its reducibility in hydrogen radicals, with reduction halting at $4.2 \pm 0.4$ eV.

desk verdict Solid, honest extension of the authors' own nitride work-function model to complex oxides, but the causal claim is underdetermined because Sc fraction and work function are collinear in the single compositional series. read the letter →

arxiv 2411.17276 v1 pith:KSGACC6N submitted 2024-11-26 cond-mat.mtrl-sci

Abdul Rehman , Robbert W.E. van de Kruijs , Wesley T.E. van den Beld , Jacobus M. Sturm , Marcelo Ackermann This is my paper · ORCID
classification cond-mat.mtrl-sci
keywords complextransitionmetaloxidesthinfilmshydrogenreductionworkfunctionradicalsniobiumscandiumoxideX-rayphotoelectronspectroscopy
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 proposes that the work function of a transition-metal compound is a single tunable parameter governing how strongly hydrogen radicals attack it: materials with a lower work function are harder to reduce, and reduction effectively stops once the work function falls to $4.2 \pm 0.4$ eV. The authors demonstrate this in thin films by alloying high-work-function Nb$_2$O$_5$ (about 5.2 eV) with low-work-function Sc$_2$O$_3$ (about 3.5 eV) to form complex oxides NbSc$_y$O$_x$ with roughly 40%, 50%, and 75% scandium relative to niobium. As the scandium fraction rises, the measured work function falls almost linearly and the oxygen loss during 8 hours of hydrogen-radical exposure at 550°C shrinks accordingly. XPS shows that niobium stays in higher oxidation states (up to +5) after exposure in the scandium-rich samples, while pure Nb$_2$O$_5$ is largely reduced toward metallic niobium. If the claim holds, work function gives designers a practical knob for hydrogen-protective coatings and for preserving desired oxidation states in reactive hydrogen.

What carries the argument

The central object is the work function—the minimum energy needed to remove an electron from a material's surface—used through the threshold $\varphi_{\mathrm{TH}} = 4.2 \pm 0.4$ eV, carried over from transition-metal nitrides to oxides. The mechanism is compositional work-function tuning: alloying a high-work-function oxide (Nb$_2$O$_5$, about 5.2 eV) with a low-work-function oxide (Sc$_2$O$_3$, about 3.5 eV) produces the complex oxide NbSc$_y$O$_x$, whose work function tracks a weighted average of the constituents and can be moved across the threshold by adjusting the scandium fraction. Reduction is read out through XPS-measured O/Nb+Sc ratios, Nb 3d and Sc 2p oxidation-state fits, and work-function measurements from the secondary-electron cutoff, with KPAFM and TEM-EDS used to confirm the films are homogeneous single-phase complex oxides rather than mixtures of NbO$_x$ and ScO$_x$.

What would settle it

A decisive test would be to hold the oxide chemistry fixed while shifting only the work function—for example, by changing the surface termination or adding a thin surface dopant layer to the same niobium-scandium oxide film—and exposing both variants to identical hydrogen-radical conditions. If the model is right, the lower-work-function variant should lose measurably less oxygen and retain more niobium in the +5 state, and a variant starting below $4.2$ eV should show no further reduction at all.

Watch

Extended reading notes

Core claim

The central claim is that the work function of a transition-metal compound is the controlling parameter for its chemical stability in reactive hydrogen: reduction proceeds while the work function sits above a threshold of $4.2 \pm 0.4$ eV, and effectively halts once the work function reaches that level, even when further reduction is still thermodynamically favorable. This is demonstrated for oxides by tuning the Nb/Sc ratio in NbSc$_y$O$_x$: increasing the scandium fraction lowers the work function, decreases the percent oxygen loss after H* exposure, and leaves a larger fraction of niobium atoms in the +5 oxidation state (about 51% for the 75%-scandium sample, versus roughly 28% lower-valent niobium plus metallic niobium in pure Nb$_2$O$_5$). The same threshold was previously reported for transition-metal nitrides, so the paper argues for a unified picture in which H* preferentially binds to oxygen (or nitrogen) atoms above the threshold, enabling formation of volatile OH$_x$ (or NH$_x$), and binds to metal atoms below it, blocking that loss channel.

Load-bearing premise

The load-bearing premise is that the work function value itself, not the chemical identity or fraction of the added scandium atoms, is what decides whether hydrogen radicals stop reducing the oxide, and that the same $4.2 \pm 0.4$ eV stopping threshold measured for metal nitrides applies unchanged to metal oxides.

Editorial extensions

If this is right

  • Protective coatings can be made hydrogen-resistant by blending in a low-work-function oxide until the composite's work function drops below about 4.2 eV.
  • Higher oxidation states of a metal that normally reduces in hydrogen radicals can be preserved by embedding it in a low-work-function host, as shown for niobium in scandium-rich samples.
  • The same work-function threshold describes both nitrides and oxides, so screening for hydrogen-radical environments can start from published work-function values instead of trial-and-error chemistry.
  • A weighted average of the constituent oxides' work functions gives a usable first estimate for a complex oxide, making the design rule practical for thin-film deposition.
  • The halt in reduction is not caused by exhausting surface oxygen, since oxygen remains at the surface after exposure; the paper attributes the halt to a work-function-driven switch in where hydrogen binds.

Reading between the lines

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

  • Because the scandium additions change both work function and chemistry at once, the strongest causal test would vary work function while keeping composition fixed—for example by surface termination or thin doping—and check whether the 4.2 eV stopping point moves.
  • The proposed mechanism implies that below the threshold, the gas-phase products of hydrogen exposure should shift from oxygen-hydrogen species to hydrogen-metal species, a prediction that could be checked directly with residual-gas mass spectrometry during exposure.
  • If the threshold is set by the universal alignment of hydrogen levels rather than by the specific compound, then any complex transition-metal oxide with a work function at or below 4.2 eV is a candidate protective coating, which is a fast screening rule the paper does not itself state.
  • The same alloying logic should extend beyond oxides and nitrides to other transition-metal compounds such as carbides or sulfides, since the argument rests on work function rather than on the particular anion; this extension is not demonstrated in the paper.
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Editorial analysis

A structured set of objections, weighed in public.

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

Referee Report

4 major / 4 minor

Summary. The paper reports AR-XPS measurements of work function and O/Nb+Sc ratios for Nb2O5, three Nb-Sc complex oxides (Nb3Sc2O10.5, NbScO4, NbSc3O7), and Sc2O3 before and after exposure to hydrogen radicals at 550°C. The authors find that increasing Sc fraction lowers the initial work function and reduces the extent of oxygen loss during H* exposure; Nb 3d XPS shows that higher Nb oxidation states are retained after H* exposure in Sc-rich samples. They interpret these results as evidence that the work function is a tunable parameter controlling oxide reducibility, and that reduction stops when the work function reaches 4.2 ± 0.4 eV, a threshold previously reported for transition-metal nitrides. The manuscript also includes KPAFM validation of the XPS work-function measurements, AR-XPS/TEM-EDS evidence for homogeneous complex-oxide depth profiles, and XPS spectra of Nb and Sc.

Significance. If the work-function-controlled reducibility mechanism holds, the paper offers a simple design rule for hydrogen-resistant coatings and for stabilizing high oxidation states in reactive hydrogen, which would be practically relevant for EUV and fusion applications. The study is strengthened by direct work-function measurements, KPAFM validation, and evidence for homogeneous complex-oxide depth profiles. However, the central causal attribution is not uniquely identified: Sc fraction and work function are co-varied in a single compositional series, and the stopping threshold is inherited from nitride studies without an oxide-specific control. The paper is therefore a suggestive demonstration of correlation, not yet a decisive test of the proposed mechanism.

major comments (4)
  1. [Fig. 1a-b and Fig. 2b] The central causal claim—that work function, not Sc chemical identity, controls reducibility in H*—is underdetermined because Sc fraction and work function are co-varied in a single compositional series (Nb2O5, Nb3Sc2O10.5, NbScO4, NbSc3O7, Sc2O3). Higher Sc content could stabilize Nb+5 through thermodynamic site preferences, oxygen scavenging, or the ScOOH surface layer identified for Sc2O3 in Fig. 3, without any role for the work function per se. The manuscript needs a control that separates these variables, for example varying the work function at fixed Nb/Sc ratio (through stoichiometry, oxygen vacancies, or surface termination) or replacing Sc with another low-work-function cation and showing that the same work-function threshold, rather than the specific chemistry, controls the reduction.
  2. [Fig. 1c-d and text near 'reduction reaction ... stops'] The 4.2 ± 0.4 eV stop threshold is imported from transition-metal nitrides (ref. 15) and is not independently established for oxides. The final work functions of all samples lie within a narrow range, and the statement that reduction 'effectively stops' is not supported by a quantitative kinetic or statistical test; given the stated ±10% stoichiometry uncertainty, the final O/Nb+Sc values for the Sc-rich samples may be indistinguishable from one another. An oxide-specific test, such as showing that reduction resumes when the work function is raised above the threshold, or that a different oxide family stops at the same threshold, is needed.
  3. [Methodology and Fig. 1b-d] The % O-loss values are presented without propagated error bars, although the manuscript states a ±10% uncertainty in stoichiometry and ±0.2 eV uncertainty in work-function differences. Without error bars, the monotonic trend and the claim that reduction 'stops' for Sc-rich samples cannot be quantitatively assessed; for example, the difference between NbSc3O7 and Sc2O3 after H* exposure may be within the combined uncertainty. Error propagation should be added to all reported ratios and work-function differences, and the basis for the monotonic trend should be re-stated in light of those uncertainties.
  4. [Mechanistic paragraph after Fig. 1] The proposed mechanism invokes Van de Walle's universal hydrogen alignment to argue that H* adsorption on O atoms is favorable above 4.2 ± 0.4 eV and unfavorable below it, but no adsorption, level-alignment, or computational evidence specific to these oxides is presented. As written, the mechanism is a hypothesis imported from ref. 15; the manuscript should clearly label it as such and identify what experimental or computational data would test it, rather than presenting it as the established explanation of the measured correlation.
minor comments (4)
  1. [Introduction, first paragraph] 'Embitterment' should be 'embrittlement'.
  2. [Methodology, H* flux sentence] '10 211 H* m−2s−1' should be written as '10^21 H* m^-2 s^-1' to avoid ambiguity, and the 'N-type thermocouple' should be identified as a type-N thermocouple.
  3. [Figure 1 caption] The % O-loss formula is typeset awkwardly; place it on one line and define 'pre-exposed' consistently with the methodology section.
  4. [General presentation] The dependence of the threshold and mechanism on the authors' prior nitride publications (refs. 15 and 16) is stated only implicitly; the main text should state explicitly which quantities are measured here and which are adopted from prior work.

Circularity Check

0 steps flagged · score 0.0 of 10

No circularity by construction: the central work-function/reducibility correlation rests on independent measurements, and the self-cited nitride threshold is used as an external benchmark rather than fitted to the oxide data.

full rationale

The paper's derivation chain is: (i) Sc fraction is varied during reactive co-sputtering; (ii) work function is measured by XPS secondary-electron cutoff and cross-checked with KPAFM; (iii) reducibility is measured as % change in XPS O/(Nb+Sc) ratios; and (iv) Nb 3d and Sc 2p spectra are used to track oxidation states. These are distinct observables, and no equation in the paper defines one in terms of the other. The claim that a lower work function correlates with lower oxide reducibility is an empirical correlation over the measured series, not a fitted parameter renamed as a prediction. The 4.2 ± 0.4 eV stop threshold is explicitly stated as coming from the authors' earlier nitride work (refs. 15,16) and is then checked against the new oxide data ('aligning with our model'); it is not obtained by fitting the oxide data, so the 'fitted input called prediction' pattern does not apply. The main scientific weaknesses — collinearity between Sc fraction and work function across only three alloy compositions, and the untested transfer of the nitride threshold to oxides — are identification/interpretation limitations, not definitional circularity. Because the measured data stand independently and the numerical threshold is explicitly imported from prior work rather than derived from the present inputs, no circular step can be exhibited.

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

The paper introduces no free parameters and no invented entities. It relies on the prior work-function threshold from refs. 15/16, on the compositional weighted-average approximation, on the sufficiency of surface oxygen, and on Van de Walle's hydrogen-level alignment model.

assumptions (4)
  • domain assumption The 4.2±0.4 eV work function threshold for halting reduction, established for TM nitrides in ref. 15, applies to complex TM oxides.
    The paper uses this threshold to interpret the stopping of de-oxidation (Figure 1c,d) and to argue the mechanism; no independent measurement of the threshold for oxides is provided.
  • domain assumption The work function of NbScyOx can be approximated by the compositional weighted average of the work functions of Nb2O5 and Sc2O3.
    Used for the baseline in Figure 1a; the authors acknowledge it ignores surface termination, orientation, and heterostructuring.
  • domain assumption Sufficient O-atoms remain at the surface after H*-exposure, so the reduction reaction is not limited by subsurface oxygen diffusion.
    Stated in the text to justify interpreting the stopping of reduction as work-function-driven rather than diffusion-limited.
  • domain assumption H* binding preference switches from O-atoms to TM-atoms below the work function threshold, following Van de Walle's universal alignment of hydrogen levels.
    This is the mechanistic bridge connecting work function to reducibility; it is borrowed from refs. 17,18 and not derived in this paper.

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Cite this review

Pith. "Pith review of Engineering Work Function to Stabilize Metal Oxides in Reactive Hydrogen." pith.science (2026). https://pith.science/paper/KSGACC6N

@misc{pith2026241117276,
  author       = {Pith},
  title        = {Pith review of: Engineering Work Function to Stabilize Metal Oxides in Reactive Hydrogen},
  year         = {2026},
  howpublished = {\url{https://pith.science/paper/KSGACC6N}},
  note         = {Machine review of arXiv:2411.17276}
}
read the original abstract

Hydrogen, crucial for the green energy transition, poses a challenge due to its tendency to degrade surrounding wall materials. To harness hydrogen's potential, it is essential to identify materials' parameter(s) that modulate hydrogen-material interaction. In a recent publication, we have shown that the reduction (de-nitridation) of transition metal (TM)-nitrides in hydrogen radicals (H*) stops when their work function drops below a threshold limit. In this work, we tailor the work function of a complex TM-oxide by tuning the relative content of its constituent TM-atoms. We show that increasing the fraction of a low work function TM decreases the work function of the complex oxide, thereby decreasing its reducibility (de-oxidation) in H*. This leads to the stabilization of the higher oxidation states of a high work function TM, which otherwise readily reduce in H*. We propose that the work function serves as a tuneable parameter, modulating the interaction of hydrogen with TM compounds.

Figures

Figures reproduced from arXiv: 2411.17276 by the authors.

Figure 1
Figure 1. Measured work functions, % O-loss, and O/Nb+Sc ratios in the Nb2O5, Nb3Sc2O10.5, NbScO4, NbSc3O7, and Sc2O3 samples. (a) The work function of the pre￾exposed (0 h) samples decreases almost linearly with increasing Sc-fraction. (b) This de￾crease in the work function leads to a decrease in the O-loss in the samples upon H*-exposure, calculated as the % change in the O/Nb+Sc ratio∗ . (c-d) As O-atoms are removed from … view at source ↗
Figure 2
Figure 2. Nb 3d XPS spectra of (a) the pre-exposed and (b) the 8 h H*-exposed Nb2O5, Nb3Sc2O10.5, NbScO4, and NbSc3O7 samples. In the pre-exposed samples, Nb-atoms are predominantly in a +5 oxidation state. The oxidation states of Nb-atoms in the post-H*- exposed samples depend on the Sc-fraction in NbScyOx. A higher Sc-fraction results in a greater proportion of Nb-atoms remaining in higher oxidation states after H*-exposure… view at source ↗
Figure 3
Figure 3. Sc 2p XPS spectra of (a) the pre-exposed and (b) the 8 h H*-exposed Nb3Sc2O10.5, NbScO4, and NbSc3O7, along with 4 h H*-exposed Sc2O3 samples. In all the samples, Sc￾atoms are in a +3 oxidation state, with the Sc2O3 doublet appearing at lower binding energy and the ScOOH doublet at higher binding energy. For the samples where O-loss is substantial (Nb3Sc2O10.5 and NbScO4), the Sc 2p spectra show significant changes … view at source ↗
Figures from the paper (1 more)
Figure 4
Figure 4. Figure 4: Schematic of methodology. (a) NbScyOx samples are deposited via reactive DC magnetron co-sputtering. A thin layer of adventitious carbon (ad. C) formed on the samples’ surfaces during ambient storage. (b) The samples are first annealed at 550 ◦C for 2 h. (c-e) The samp…

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Reference graph

Works this paper leans on

33 extracted references · 33 canonical work pages

  1. [1]

    Japanese developments of fusion reactor plasma facing components

    Hino, T.; Akiba, M. Japanese developments of fusion reactor plasma facing components. Fusion Engineering and Design 2000, 49, 97--105

    work page 2000

  2. [2]

    B.; Traversa, E

    Stambouli, A. B.; Traversa, E. Fuel cells, an alternative to standard sources of energy. Renewable and sustainable energy reviews 2002, 6, 295--304

    work page 2002

  3. [3]

    The survey of key technologies in hydrogen energy storage

    Zhang, F.; Zhao, P.; Niu, M.; Maddy, J. The survey of key technologies in hydrogen energy storage. International journal of hydrogen energy 2016, 41, 14535--14552

    work page 2016

  4. [4]

    A review on hydrogen industrial aerospace applications

    Cecere, D.; Giacomazzi, E.; Ingenito, A. A review on hydrogen industrial aerospace applications. International journal of hydrogen energy 2014, 39, 10731--10747

    work page 2014

  5. [5]

    Etching of silicon nanowires on Ag (1 1 0) by atomic hydrogen

    Salomon, E.; Angot, T.; Thomas, C.; Layet, J.-M.; Palmgren, P.; Nlebedim, C.; G \"o thelid, M. Etching of silicon nanowires on Ag (1 1 0) by atomic hydrogen. Surface science 2009, 603, 3350--3354

    work page 2009

  6. [6]

    Sn etching with hydrogen radicals to clean EUV optics

    Van Herpen, M.; Klunder, D.; Soer, W.; Moors, R.; Banine, V. Sn etching with hydrogen radicals to clean EUV optics. Chemical Physics Letters 2010, 484, 197--199

    work page 2010

  7. [7]

    Atomic hydrogen cleaning of polar III--V semiconductor surfaces

    Bell, G.; Kaijaks, N.; Dixon, R.; McConville, C. Atomic hydrogen cleaning of polar III--V semiconductor surfaces. Surface Science 1998, 401, 125--137

    work page 1998

  8. [8]

    Kinetics of reduction of a RuO2 (110) film on Ru (0001) by H2

    Ugur, D.; Storm, A.; Verberk, R.; Brouwer, J.; Sloof, W. Kinetics of reduction of a RuO2 (110) film on Ru (0001) by H2. The Journal of Physical Chemistry C 2012, 116, 26822--26828

    work page 2012

Show all 33 references
  1. [9]

    K.; Vishwakarma, M

    Dwivedi, S. K.; Vishwakarma, M. Hydrogen embrittlement in different materials: A review. International Journal of Hydrogen Energy 2018, 43, 21603--21616

    2018

  2. [10]

    L.; Sofronis, P

    Martin, M. L.; Sofronis, P. Hydrogen-induced cracking and blistering in steels: A review. Journal of Natural Gas Science and Engineering 2022, 101, 104547

    2022

  3. [11]

    P.; Alexander, D

    Geissb \"u hler, J.; De Wolf, S.; Demaurex, B.; Seif, J. P.; Alexander, D. T.; Barraud, L.; Ballif, C. Amorphous/crystalline silicon interface defects induced by hydrogen plasma treatments. Applied Physics Letters 2013, 102

    2013

  4. [12]

    Y.; Hong, S.; Kim, D.-W.; Kim, J.-H.; Lee, H.-C

    Choe, E.-S.; Choi, S.; Kim, A.; Kim, K.-Y.; Yeom, H.-J.; Yoon, M. Y.; Hong, S.; Kim, D.-W.; Kim, J.-H.; Lee, H.-C. Evaluation of H2 Plasma-Induced Damage in Materials for EUV Lithography. Advanced Materials Interfaces 2024, 11, 2300867

    2024

  5. [13]

    Hydrogen permeation barriers: Basic requirements, materials selection, deposition methods, and quality evaluation

    Nemani c , V. Hydrogen permeation barriers: Basic requirements, materials selection, deposition methods, and quality evaluation. Nuclear Materials and Energy 2019, 19, 451--457

    2019

  6. [14]

    The challenges of plasma material interactions in nuclear fusion devices and potential solutions

    Rapp, J. The challenges of plasma material interactions in nuclear fusion devices and potential solutions. Fusion Science and Technology 2017, 72, 211--221

    2017

  7. [15]

    W.; van den Beld, W

    Rehman, A.; van de Kruijs, R. W.; van den Beld, W. T.; Sturm, J. M.; Ackermann, M. Work-Function-Dependent Reduction of Transition Metal Nitrides in Hydrogen Environments. The Journal of Physical Chemistry Letters 2024, 15, 11462--11467

    2024

  8. [16]

    W.; van den Beld, W

    Rehman, A.; van de Kruijs, R. W.; van den Beld, W. T.; Sturm, J. M.; Ackermann, M. Chemical interaction of hydrogen radicals (H*) with transition metal nitrides. The Journal of Physical Chemistry C 2023, 127, 17770--17780

    2023

  9. [17]

    Van de Walle, C. G. Universal alignment of hydrogen levels in semiconductors and insulators. Physica B: Condensed Matter 2006, 376, 1--6

    2006

  10. [18]

    G.; Neugebauer, J

    Van de Walle, C. G.; Neugebauer, J. Universal alignment of hydrogen levels in semiconductors, insulators and solutions. Nature 2003, 423, 626--628

    2003

  11. [19]

    XPS analysis of the surface composition of niobium for superconducting RF cavities

    Dacca, A.; Gemme, G.; Mattera, L.; Parodi, R. XPS analysis of the surface composition of niobium for superconducting RF cavities. Applied Surface Science 1998, 126, 219--230

    1998

  12. [20]

    M.; Jamison, K

    Vaughn, J. M.; Jamison, K. D.; Kordesch, M. E. 17.3: Work function reduction by multilayer oxides: Thermionic electron emission microscopy of scandium oxide and barium oxide on tungsten. 2010 IEEE International Vacuum Electronics Conference (IVEC). 2010; pp 421--422

    2010

  13. [21]

    Rooksby, H.; White, E. A. THE STRUCTURE OF 1: 1 COMPOUNDS OF RARE EARTH OXIDES WITH NIOBIA AND TANTALA. Acta cryst. 1963, 16

    1963

  14. [22]

    Rare-Earth Niobates and TantaIates of Defect Fluorite-and Weberite-Type Structures

    Rooksby, H.; White, E. Rare-Earth Niobates and TantaIates of Defect Fluorite-and Weberite-Type Structures. Journal of the American Ceramic Society 1964, 47, 94--96

    1964

  15. [23]

    D.; Baikie, I

    Orf, N. D.; Baikie, I. D.; Shapira, O.; Fink, Y. Work function engineering in low-temperature metals. Applied Physics Letters 2009, 94

    2009

  16. [24]

    Tuning the work function in transition metal oxides and their heterostructures

    Zhong, Z.; Hansmann, P. Tuning the work function in transition metal oxides and their heterostructures. Physical Review B 2016, 93, 235116

    2016

  17. [25]

    Brouns, D.; Bendiksen, A.; Broman, P.; Casimiri, E.; Colsters, P.; Delmastro, P.; de Graaf, D.; Janssen, P.; van de Kerkhof, M.; Kramer, R. et al. NXE pellicle: offering a EUV pellicle solution to the industry. Extreme Ultraviolet (EUV) Lithography VII. 2016; pp 567--576

    2016

  18. [26]

    M.; Kvon, V.; Nikipelov, A.; Astakhov, D.; Krainov, P.; Banine, V

    van de Kerkhof, M.; Yakunin, A. M.; Kvon, V.; Nikipelov, A.; Astakhov, D.; Krainov, P.; Banine, V. EUV-induced hydrogen plasma and particle release. Radiation Effects and Defects in Solids 2022, 177, 486--512

    2022

  19. [27]

    Zoldesi, C.; Bal, K.; Blum, B.; Bock, G.; Brouns, D.; Dhalluin, F.; Dziomkina, N.; Espinoza, J. D. A.; de Hoogh, J.; Houweling, S. et al. Progress on EUV pellicle development. Extreme Ultraviolet (EUV) Lithography V. 2014; pp 430--439

    2014

  20. [28]

    C.; Lau, L

    Biesinger, M. C.; Lau, L. W.; Gerson, A. R.; Smart, R. S. C. Resolving surface chemical states in XPS analysis of first row transition metals, oxides and hydroxides: Sc, Ti, V, Cu and Zn. Applied surface science 2010, 257, 887--898

    2010

  21. [29]

    Correlation between stoichiometry and properties of scandium oxide films prepared by reactive magnetron sputtering

    Belosludtsev, A.; Ju s kevi c ius, K.; Ceizaris, L.; Samuilovas, R.; Stanionyt \.e , S.; Jasulaitien \.e , V.; Ki c as, S. Correlation between stoichiometry and properties of scandium oxide films prepared by reactive magnetron sputtering. Applied Surface Science 2018, 427, 312--318

    2018

  22. [30]

    Water-induced scandium oxide dielectric for low-operating voltage n-and p-type metal-oxide thin-film transistors

    Liu, A.; Liu, G.; Zhu, H.; Song, H.; Shin, B.; Fortunato, E.; Martins, R.; Shan, F. Water-induced scandium oxide dielectric for low-operating voltage n-and p-type metal-oxide thin-film transistors. Advanced Functional Materials 2015, 25, 7180--7188

    2015

  23. [31]

    T.; Chai, L.; Helander, M

    Greiner, M. T.; Chai, L.; Helander, M. G.; Tang, W.-M.; Lu, Z.-H. Transition metal oxide work functions: the influence of cation oxidation state and oxygen vacancies. Advanced Functional Materials 2012, 22, 4557--4568

    2012

  24. [32]

    Scofield, J. H. Hartree-Slater subshell photoionization cross-sections at 1254 and 1487 eV. Journal of electron spectroscopy and related phenomena 1976, 8, 129--137

    1976

  25. [33]

    X-tools,

    Kim, J. W.; Kim, A. Absolute work function measurement by using photoelectron spectroscopy. Current applied physics 2021, 31, 52--59 mcitethebibliography main.bib0000664000000000000000000002610614721314466011175 0ustar rootroot@article C4RN1700, title= Atomic hydrogen cleaning...

    2021

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Reviewed August 12, 2026 · model on record in the stance chip above.