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REVIEW 3 major objections 5 minor 67 references

Nanoscale structure formation in nickel-aluminum alloys synthesized far from equilibrium

T0 review · 3 major / 5 minor · reviewed 2026-08-10 · deepseek-v4-flash

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Pith's one-line read Magnetron-sputtered Ni-Al films with 11–24% aluminum form a coherent, strained two-phase "nano-solution" with a single lattice parameter, and annealing decomposes it while changing hardness.

desk verdict Solid experimental map of sputtered Ni-Al films, with a real nameable ambiguity in the central 'nano-solution' claim that the authors themselves concede; worth peer review, but the interpretation needs sharpening. read the letter →

arxiv 2501.08530 v3 pith:IRHKB6TC submitted 2025-01-15 cond-mat.mtrl-sci

Zhehao Chen , Aslak J J Fellman , Katarzyna Mulewska , Kenichiro Mizohata , Davide Gambino , Yanling Ge , Eryang Lu , Flyura Djurabekova
show 4 more authors
Andreas Delimitis Lukasz Kurpaska Kostas Sarakinos Filip Tuomisto
This is my paper · ORCID
classification cond-mat.mtrl-sci
keywords Ni-Alalloysmagnetronsputteringnano-solutionL12phasecoherentstrainmetastablephasesthinfilmshardness
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

This paper reports that magnetron-sputtered nickel-aluminum films with aluminum fractions $x$ between 0.11 and 0.24 do not form a simple random alloy or a coarse phase mixture. Instead, nanometer-scale domains of the disordered $\gamma$ phase and the ordered $\mathrm{L1}_2$ $\gamma'$ phase interlock coherently and share one lattice parameter, a metastable structure the authors call a nano-solution. The claim matters because it shows that far-from-equilibrium vapor deposition can self-organize ordered intermetallic phases into strain-coupled nanostructures with mechanical properties distinct from either single phase. Annealing a $\mathrm{Ni}_{0.86}\mathrm{Al}_{0.14}$ film shows this structure persists to 673 K while hardness rises from 5.5 to 6.0 GPa, then decomposes into separate $\gamma$ and $\gamma'$ domains at 873 K and above, with hardness falling to about 4 GPa.

What carries the argument

The load-bearing object is the "nano-solution": a coherent interlocking of $\gamma$ (disordered fcc) and $\gamma'$ (ordered $\mathrm{L1}_2$) domains that are too small for their interfacial strain fields to decay, so both phases are locked to a single average lattice parameter. The paper identifies this structure through the combination of a single symmetric (002) XRD reflection, (001) superlattice reflections, and HRTEM intensity profiles across a $\gamma'/\gamma$ interface that match a simulated two-phase supercell. The single lattice parameter, which expands with Al content and follows the computed $\gamma'$ curve more closely as $x$ approaches 0.24, is the observable that carries the argument; annealing converts the single peak into two peaks, showing that the shared lattice is a metastable, strain-imposed state rather than an equilibrium one.

What would settle it

Measure the local aluminum composition of individual $\gamma$ and $\gamma'$ domains in an as-deposited $\mathrm{Ni}_{0.86}\mathrm{Al}_{0.14}$ film with sub-nanometre probe analysis (for example atom-probe tomography or high-resolution STEM-EDS). If the domains share the global composition yet show one common lattice parameter, the strained nano-solution is confirmed; if they have different compositions chosen so that each domain's unstrained lattice parameter equals the measured value, the alternative equilibrium interpretation wins and the coherency-strain hardening story would need revision.

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Extended reading notes

Core claim

The central claim is that for $0.11 \le x \le 0.24$ the films consist of coexisting $\gamma$ and $\gamma'$ domains intermixed at the atomic scale, forming a coherent strained lattice with a single lattice parameter that increases with global Al content. The evidence is a symmetric (002) XRD peak with no splitting, a (001) superlattice reflection from the $\mathrm{L1}_2$ phase appearing only for $x \ge 0.11$, and HRTEM images with matching simulations showing domains only a few nanometers across. The two phases meet through a transition zone about 1.4 nm wide, roughly eight (002) planes, and the authors argue that strain from coherent interfaces cannot relax inside such small domains, so the lattice adopts an average parameter between the computed equilibrium values of $\gamma$ and $\gamma'$. Annealing at 673 K leaves the nano-solution intact and hardens the film from 5.5 to 6.0 GPa, while annealing at 873 and 1073 K splits the (002) peak into distinct $\gamma$ and $\gamma'$ reflections, coarsens the domains, and softens the film to about 4 GPa, confirming the structure is metastable.

Load-bearing premise

The interpretation depends on assuming that the single symmetric (002) XRD peak reflects two strained phases with different natural lattice constants locked to one average value, rather than two phases whose local compositions coincidentally give them the same equilibrium lattice parameter.

Editorial extensions

If this is right

  • Composition alone tunes the lattice parameter and hardness of as-deposited films across the two-phase window, because the nano-solution behaves like a substitutional solid solution but substitutes nanometer-scale phase domains for individual atoms.
  • A 673 K anneal of $\mathrm{Ni}_{0.86}\mathrm{Al}_{0.14}$ films raises hardness to about 6 GPa without dissolving the nano-solution, indicating a practical low-temperature strengthening step for sputtered Ni-Al coatings.
  • Annealing above 873 K decomposes the nano-solution into distinct $\gamma$ and $\gamma'$ domains and softens the film to about 4 GPa, so thermal exposure is a direct control for switching between hardened and softened states.
  • The measurable lattice parameter of the $\gamma'$ phase can be systematically shifted by the surrounding $\gamma$ phase, providing a structural-design route for metastable $\gamma/\gamma'$ intermetallic alloys.

Reading between the lines

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

  • If coherency strain is the operative stabilizer, sputtering other alloy pairs with larger equilibrium lattice mismatches should produce even harder nano-solutions, and the hardness gain should scale with mismatch; this is testable without changing the deposition method.
  • The suggestion that formation proceeds by surface-directed spinodal decomposition implies a kinetic signature: varying substrate temperature or deposition rate should change domain size in a predictable diffusion-limited way, which would distinguish spinodal decomposition from nucleation and growth.
  • The fact that the nano-solution at $x=0.14$ matches the hardness of the near-stoichiometric $\gamma'$ film at $x=0.24$ suggests coherency strain can substitute for raw $\gamma'$ content, possibly reducing aluminum demand in hard coatings; the paper does not address this economic angle.
  • Extending the annealing study to $x=0.24$ would show whether the age-hardening window widens or narrows as the $\gamma'$ fraction dominates, and whether the 673 K hardening step persists in films that are already mostly ordered.
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Editorial analysis

A structured set of objections, weighed in public.

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

Referee Report

3 major / 5 minor

Summary. The manuscript reports on epitaxial Ni1-xAlx thin films (x up to 0.24) grown on MgO(001) by magnetron sputtering. XRD, TEM/HRTEM/SAD, EDS, and nanoindentation show that for x < 0.11 the films are a random FCC γ solid solution, while for 0.11 ≤ x ≤ 0.24 a single (002) XRD peak and superlattice (001) reflections coexist. The authors interpret this as a coherent, strained γ/γ′ nano-solution with one average lattice parameter, which is metastable upon annealing: at 673 K it persists with a slight hardness increase, whereas at 873 K and 1073 K it decomposes into distinct γ and γ′ domains with softening. DFT and machine-learned (tabGAP) potential calculations are used to compare computed lattice parameters of γ and γ′ phases with the experimental values.

Significance. If the central interpretation holds, the paper demonstrates a new metastable coherent two-phase nanostructure in a canonical intermetallic system, formed by far-from-equilibrium sputter deposition, with implications for non-equilibrium synthesis routes and for strain-based design of mechanical properties. The experimental work is broad and uses complementary, generally well-executed probes (XRD, HRTEM with image simulation, SAD, EDS, nanoindentation), and the computational comparison with DFT and a tabGAP potential is a useful addition. However, the key physical claim—that the observed single lattice parameter arises from two phases with different intrinsic lattice parameters that are strained into coherency—is not uniquely established, and the authors explicitly leave open a simpler alternative. The hardness evidence for the nano-solution's benefit is also weaker than the conclusions state.

major comments (3)
  1. [Section 3.2, Fig. 4] The central claim that the films contain a coherent strained γ/γ′ nano-solution with a single average lattice parameter is not uniquely established. The authors state, 'Although our results do not unequivocally rule out the above-explained scenario,' referring to the possibility that γ and γ′ have identical equilibrium lattice parameters because their local compositions differ. In that alternative, the single (002) peak and matching (001) superlattice reflections arise from a conventional fine two-phase mixture at local equilibrium, not from coherency strain. The 'fine tuning' argument against this scenario is qualitative and depends on the computed lattice-parameter curves without local composition measurements. To make the strained-nano-solution claim load-bearing, the authors should provide quantitative evidence, for example atomic-scale composition mapping (STEM-EDS or APT) showing that the phase compositions are close to the global composition, or strain/lattice-parameter mapping (e.g., GPA on HRTEM images) showing continuous variation around the average value.
  2. [Section 3.3, Fig. 5(b2)] The conclusion that the nano-solution provides 'enhanced hardness in relation to single-phase structures' is not supported by the data as presented. The hardness at x = 0.14 is 5.5 ± 0.3 GPa and at x = 0.24 (γ′-phase dominated) is 5.4 ± 0.4 GPa, so the two values are statistically indistinguishable. The comparison with x = 0.07 (3.1 ± 0.3 GPa) is clear, but the claim that the nano-solution is harder than the single-phase γ′ structure at x = 0.24 requires either a statistical test or additional data. Similarly, the 'age-hardening' at 673 K from 5.5 ± 0.3 to 6.0 ± 0.3 GPa is within overlapping error bars and should not be stated as a definite increase without a significance assessment.
  3. [Section 2.2 and Fig. 4] The lattice-parameter data extracted from XRD (Fig. 4) are plotted without any uncertainty estimates, which is problematic because the central discrimination between the strained-coherent and equal-lattice-parameter scenarios rests on the comparison between the experimental single lattice parameter and the computed γ/γ′ curves. Without error bars, the reader cannot judge whether the experimental values are actually inconsistent with a scenario in which each phase has its own equilibrium lattice parameter at its local composition. In addition, the authors state that the tabGAP potential was modified by tuning its hyperparameters to match DFT lattice-constant predictions; therefore the MS and DFT curves are not an independent prediction, and the statement that their agreement 'lends confidence to the accuracy of the machine-learned interatomic potential' should be moderated. This issue affects the quantitative basis for the 'fine tuning' argument, though it does not by itself invalidate the experimental observations.
minor comments (5)
  1. [Section 3.1] In the text describing Fig. 1(c), the peak at 2θ = 51.24° is attributed to 'Ni3Al(001)'; this should be Ni3Al(002), as (001) is the superlattice reflection at about 25°.
  2. [Section 3.1 and Fig. 2 caption] The superlattice reflection used for dark-field imaging is denoted (101̅) in the text but (011̅) in the Fig. 2 caption; please make the notation consistent.
  3. [Section 3.3] The phrase 'reduced module Y' should be 'reduced modulus Y'; also, in the same paragraph, 'constat' should be 'constant'.
  4. [Section 3.2] The statement that 'the (002) fringes are intermittently visible' for the Ni0.86Al0.14 sample is vague; a more quantitative description (e.g., fraction of the image area with visible (001) fringes) would strengthen the claim of atomic-scale intermixing.
  5. [Section 3.2] The proposal that 'structure formation may proceed via surface-directed spinodal decomposition' is speculative and not tested by the present data; since the manuscript does not present time-resolved or composition-fluctuation measurements, this sentence should be explicitly labeled as a hypothesis, not a conclusion.

Circularity Check

0 steps flagged · score 0.0 of 10

No circularity: the central claims are experimental observations; DFT/MS calculations serve as comparison, not as fitted inputs defining the phases.

full rationale

The paper's main claims—phase formation, single lattice parameter, nano-solution microstructure, annealing behavior, and hardness trends—are derived from XRD, TEM/HRTEM, SAD, EDS, and nanoindentation data. The DFT and MS calculations are used only to compute reference lattice parameters as a function of Al content for the γ and γ′ phases. The MS potential is admittedly tuned so that its lattice parameters match DFT (Section 2.2), but this does not feed back into the experimental identification of phases: the existence of γ and γ′ domains is established by XRD superlattice reflections, SAD superlattice spots, and HRTEM lattice fringes, independently of the calculations. The paper explicitly concedes that the data do not rule out an alternative interpretation in which the two phases have equal equilibrium lattice parameters at their local compositions (Section 3.2). That concession is an honest statement of ambiguity, not a circular derivation: the measured single (002) peak and the measured (001) superlattice reflections are inputs, and the strained-coherent-lattice interpretation is one of two possible readings of those inputs. Similarly, the hardness comparison between x=0.14 and x=0.24 is stated with overlapping error bars, which weakens the strength of the claim but does not make the claim equivalent to a fitted parameter or to a self-citation. The only self-referencing element is the use of a recently developed machine-learned potential (Ref. [50]) whose accuracy is independently benchmarked against DFT within the paper; the conclusions do not rest on the potential's predictions as a definition of the observed phases. Therefore no load-bearing step reduces to its own inputs by construction, and no significant circularity is present.

Assumptions & free parameters 1 free parameters · 5 assumptions · 2 invented entities

The central experimental claim does not depend on fitted parameters. One free parameter is the tuning of the tabGAP potential to DFT, which weakens the computational comparison but not the experimental inference. The main axioms are standard DFT settings, transferability of the ML potential, and the structural interpretation of a single XRD peak. The nano-solution is an inferred entity with falsifiable handles; the proposed spinodal pathway is not independently evidenced.

free parameters (1)
  • tabGAP potential hyperparameters for Ni-Al = listed in Supporting Information Section S2
    The authors modified hyperparameters of the AlCrCuFeNi tabGAP potential so that MS lattice constants match DFT results; this fitting means subsequent MS-experiment agreement is not an independent prediction.
assumptions (5)
  • domain assumption PBE-GGA and PAW pseudopotentials give accurate lattice constants for Ni-Al.
    Section 2.2: all DFT calculations use PBE/PAW, with no benchmarking against other functionals.
  • domain assumption The tabGAP machine-learned potential trained on DFT data is transferable to Ni-Al lattice constants after hyperparameter tuning.
    Section 2.2: MS calculations rely on this potential; the authors adjusted it to match DFT.
  • domain assumption The single symmetric XRD (002) peak and common (001) spacing in HRTEM imply one coherent average lattice parameter rather than overlapping peaks from composition-tuned phases.
    Section 3.2: the alternative equal-lattice-parameter scenario is acknowledged but not ruled out.
  • domain assumption The (001) superlattice reflections in XRD, SAD, and FFT uniquely indicate L12 ordering, not another ordered phase.
    Sections 3.1 and 3.2: the superlattice spots are assigned to the L12 Ni3Al structure.
  • domain assumption Nanoindentation hardness at 40 to 100 nm depth reflects film properties rather than substrate contributions.
    Section 2.1: depth control and qualitatively similar trends at different depths are used to justify film-dominated response.
invented entities (2)
  • nano-solution (coherent strained γ/γ′ intermix) independent evidence
    purpose: Explains the single lattice parameter, symmetric XRD peak, and hardness maximum at x=0.14 in as-deposited films
    The structure is inferred from XRD, HRTEM, and DF imaging, and is falsifiable: it predicts a single lattice parameter and specific transition-zone widths. However, the authors admit an alternative equal-lattice-parameter scenario is not ruled out.
  • surface-directed spinodal decomposition as formation pathway
    purpose: Proposed mechanism for nanoscale intermixing during vapor deposition
    Proposed in Section 3.2 without quantitative test; no experimental or simulation evidence links the observed morphology specifically to spinodal decomposition.

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Pith. "Pith review of Nanoscale structure formation in nickel-aluminum alloys synthesized far from equilibrium." pith.science (2026). https://pith.science/paper/IRHKB6TC

@misc{pith2026250108530,
  author       = {Pith},
  title        = {Pith review of: Nanoscale structure formation in nickel-aluminum alloys synthesized far from equilibrium},
  year         = {2026},
  howpublished = {\url{https://pith.science/paper/IRHKB6TC}},
  note         = {Machine review of arXiv:2501.08530}
}
read the original abstract

The present study reports on the structure formation in thin epitaxial nickel-aluminum films (Ni1-xAlx; Al atomic fraction x up to x=0.24) grown on MgO(001) substrates by magnetron sputtering. Experimental and computational data demonstrate that for x<0.11, the films exhibit the face-centered cubic random solid-solution Ni1-xAlx structure ({\gamma}). Whereas in the range x=0.11-0.24 the phase coexists with the ordered L12 structure ({\gamma}' phase). The two phases are homogenously intermixed forming a coherent and strained nano-solution, which exhibits a single lattice parameter that expands as the Al content increases. Isothermal annealing of films containing x=0.14 of Al, coupled with structural and nano-mechanical characterization, reveal that the nano-solution retains its overall integrity for temperatures up to 673 K, while the film hardness increases from 5.5 GPa (as deposited films) to 6 GPa. Further increase of the annealing temperature to 873 K and 1073 K causes the nano-solution to dissolve into distinct {\gamma} and {\gamma}' phase domains and the hardness to decrease down to values of 4 GPa. These findings confirm the metastable nature of the as-deposited thin Ni1-xAlx alloy films and underpin the effectiveness of high supersaturation/undercooling for creating non-equilibrium phases and self-organized nanostructures upon synthesis of multicomponent materials.

Figures

Figures reproduced from arXiv: 2501.08530 by the authors.

Figure 1
Figure 1. Fig.1. XRD patterns of Ni and Ni [PITH_FULL_IMAGE:figures/full_fig_p032_1.png] view at source ↗

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Works this paper leans on

67 extracted references · 51 canonical work pages

  1. [1]

    A.R. Paul, M. Mukherjee, D. Singh, A Critical Review on the Properties of Intermetallic Compounds and Their Application in the Modern Manufacturing, Cryst. Res. Technol. 57(3) (2021), doi:10.1002/crat.202100159

    work page doi:10.1002/crat.202100159 2021

  2. [2]

    Tiwari, A.U

    S.K. Tiwari, A.U. Rao, A.S. Kharb, A.K. Chawla, D.K. Avasthi, A review of mechanical and tribological properties of Ni3Al-based coatings-synthesis and high-temperature behavior, Phys. Scr. 98(7) (2023), doi:10.1088/1402-4896/acd81c

    work page doi:10.1088/1402-4896/acd81c 2023

  3. [3]

    Jozwik, W

    P. Jozwik, W. Polkowski, Z. Bojar, Applications of Ni3Al Based Intermetallic Alloys— Current Stage and Potential Perceptivities, Materials 8(5) (2015) 2537-2568, doi:10.3390/ma8052537

    work page doi:10.3390/ma8052537 2015

  4. [4]

    Pollock, S

    T.M. Pollock, S. Tin, Nickel-Based Superalloys for Advanced Turbine Engines: Chemistry, Microstructure and Properties, J. Propuls. Power 22(2) (2006) 361-374, doi:10.2514/1.18239

    doi:10.2514/1.18239 2006

  5. [5]

    Vander Voort, S.R

    G.F. Vander Voort, S.R. Lampman, B.R. Sanders, et al., ASM Handbook, vol. 9: Metallography and Microstructures, ASM International, Materials Park, OH, 2004

    work page 2004

  6. [6]

    Liu, S.-L

    X.L. Liu, S.-L. Shang, Y.-J. Hu, Y. Wang, Y. Du, Z.-K. Liu, Insight into γ-Ni/γ′-Ni3Al interfacial energy affected by alloying elements, Mater. Des. 133 (2017) 39-46, doi:10.1016/j.matdes.2017.07.028

    work page doi:10.1016/j.matdes.2017.07.028 2017

  7. [7]

    Forghani, J.C

    F. Forghani, J.C. Han, J. Moon, R. Abbaschian, C.G. Park, H.S. Kim, M. Nili-Ahmadabadi, On the control of structural/compositional ratio of coherent order-disorder interfaces, J. Alloys Compd. 777 (2019) 1222-1233, doi:10.1016/j.jallcom.2018.10.128

    work page doi:10.1016/j.jallcom.2018.10.128 2019

  8. [8]

    Unocic, N

    R.R. Unocic, N. Zhou, L. Kovarik, C. Shen, Y. Wang, M.J. Mills, Dislocation decorrelation and relationship to deformation microtwins during creep of a γ′ precipitate strengthened Ni- based superalloy, Acta Mater. 59(19) (2011) 7325-7339, doi:10.1016/j.actamat.2011.07.069

    work page doi:10.1016/j.actamat.2011.07.069 2011

Show all 67 references
  1. [9]

    K. Aoki, K. Ishikawa, T. Masumoto, Ductilization of Ni3Al by alloying with boron and substitutional elements, Mater. Sci. Eng. A 192-193 (1995) 316-323, doi:10.1016/0921- 5093(94)03213-0. 25

    1995 doi

  2. [10]

    K. Aoki, O. Izumi, On the Ductility of the Intermetallic Compound Ni<SUB>3</SUB>Al, Transactions of the Japan Institute of Metals 19(4) (1978) 203-210, doi:10.2320/matertrans1960.19.203

    1978 doi

  3. [11]

    Cahn, P.A

    R.W. Cahn, P.A. Siemers, J.E. Geiger, P. Bardhan, The order-disorder transformation in Ni3Al and Ni3Al Fe alloys—I. Determination of the transition temperatures and their relation to ductility, Acta Metallurgica 35(11) (1987) 2737-2751, doi:10.1016/0001-6160(87)90273-2

    1987 doi

  4. [12]

    Cheng, E

    Y.C. Cheng, E. Ma, Atomic-level structure and structure–property relationship in metallic glasses, Prog. Mater. Sci. 56(4) (2011) 379-473, doi:10.1016/j.pmatsci.2010.12.002

    2011 doi

  5. [13]

    Katrusiak, P.F

    A. Katrusiak, P.F. McMillan (Eds.), High-Pressure Crystallography: From Fundamental Phenomena to Technological Applications, Springer Science & Business Media, Dordrecht, 2010

    2010

  6. [14]

    Handbook of deposition technologies for films and coatings: science, applications and technology[M]

    Martin P M. Handbook of deposition technologies for films and coatings: science, applications and technology[M]. William Andrew, 2009

    2009

  7. [15]

    Baker, F.S

    I. Baker, F.S. Ichishita, V.A. Surprenant, E.M. Schulson, Rapidly solidified and annealed powders of Ni3Al, Metallography 17(3) (1984) 299-314, doi:10.1016/0026-0800(84)90064-8

    1984 doi

  8. [16]

    Gaffet, P

    E. Gaffet, P. Ochin, A. Dezellus, J.C. Rouchaud, Chemically disordered Ni3Al synthesized by rapid solidification: an experimental investigation of the quenching parameters, Mater. Sci. Eng. A 160(2) (1993) 251-259, doi:10.1016/0921-5093(93)90454-m

    1993 doi

  9. [17]

    J. Li, Y.L. Tang, N. Shen, W. Pan, Effects of solidification kinetics on phase selection of Ni–Al alloys, J. Alloys Compd. 329(1-2) (2001) 157-161, doi:10.1016/s0925-8388(01)01573- 0

    2001 doi

  10. [18]

    Koch, Rapid solidification of intermetallic compounds, International Materials Reviews 33(1) (2013) 201-219, doi:10.1179/imr.1988.33.1.201

    C.C. Koch, Rapid solidification of intermetallic compounds, International Materials Reviews 33(1) (2013) 201-219, doi:10.1179/imr.1988.33.1.201

    2013 doi

  11. [19]

    Y.-F. Li, C. Li, J. Wu, H.-J. Li, Y.-C. Liu, H.-P. Wang, Microstructural Feature and Evolution of Rapidly Solidified Ni3Al-Based Superalloys, Acta Metall. Sin. (Eng. Lett.) 32(6) (2018) 764-770, doi:10.1007/s40195-018-0839-9. 26

    2018 doi

  12. [20]

    H. Li, L. Zheng, H. Zhang, S. Li, H. Zhang, S. Gong, Effects of solidification parameters on microstructures of Ni3Al based single crystal, Procedia Eng. 27 (2012) 1187-1192, doi:10.1016/j.proeng.2011.12.570

    2012 doi

  13. [21]

    Y. Li, C. Li, L. Yu, Z. Ma, H. Li, Y. Liu, Characterization of γ′ precipitate and γ/γ′ interface in polycrystalline Ni3Al-based superalloys, Vacuum 176 (2020), doi:10.1016/j.vacuum.2020.109310

    2020

  14. [22]

    Deevi, V.K

    S.C. Deevi, V.K. Sikka, C.T. Liu, Processing, properties, and applications of nickel and iron aluminides, Prog. Mater. Sci. 42(1-4) (1997) 177-192, doi:10.1016/s0079- 6425(97)00014-5

    1997 doi

  15. [23]

    Sikka, M.L

    V.K. Sikka, M.L. Santella, J.E. Orth, Processing and operating experience of Ni3Al- based intermetallic alloy IC–221M, Mater. Sci. Eng. A 239-240 (1997) 564-569, doi:10.1016/s0921-5093(97)00631-x

    1997 doi

  16. [24]

    Chiba, S

    A. Chiba, S. Hanada, Relationship between the APD structure and ductility of rapidly solidified Ni3Al alloys, Intermetallics 4(1) (1996) 55-59, doi:10.1016/0966-9795(95)00018-t

    1996 doi

  17. [25]

    Barros, J.A.S

    A.M. Barros, J.A.S. Tenório, Microstructural changes observed in a rapidly solidified Ni3Al alloy during isothermal treatments, Intermetallics 8(2) (2000) 115-120, doi:10.1016/s0966-9795(99)00073-4

    2000 doi

  18. [26]

    Holleck, Metastable coatings — Prediction of composition and structure, Surf

    H. Holleck, Metastable coatings — Prediction of composition and structure, Surf. Coat. Technol. 36(1-2) (1988) 151-159, doi:10.1016/0257-8972(88)90145-4

    1988 doi

  19. [27]

    Rovere, D

    F. Rovere, D. Music, S. Ershov, M.t. Baben, H.-G. Fuss, P.H. Mayrhofer, J.M. Schneider, Experimental and computational study on the phase stability of Al-containing cubic transition metal nitrides, J. Phys. D: Appl. Phys. 43(3) (2010), doi:10.1088/0022-3727/43/3/035302

    2010 doi

  20. [28]

    Mayrhofer, A

    P.H. Mayrhofer, A. Hörling, L. Karlsson, J. Sjölén, T. Larsson, C. Mitterer, L. Hultman, Self-organized nanostructures in the Ti–Al–N system, Appl. Phys. Lett. 83(10) (2003) 2049- 2051, doi:10.1063/1.1608464. 27

    2003 doi

  21. [29]

    Palmquist, J

    J.P. Palmquist, J. Birch, U. Jansson, Deposition of epitaxial ternary transition metal carbide films, Thin Solid Films 405(1-2) (2002) 122-128, doi:10.1016/s0040-6090(01)01766- 7

    2002 doi

  22. [30]

    Euchner, P.H

    H. Euchner, P.H. Mayrhofer, Designing thin film materials - Ternary borides from first principles, Thin Solid Films 583 (2015) 46-49, doi:10.1016/j.tsf.2015.03.035

    2015 doi

  23. [31]

    Alling, A

    B. Alling, A. Karimi, I.A. Abrikosov, Electronic origin of the isostructural decomposition in cubic M1−xAlxN (M=Ti, Cr, Sc, Hf): A first-principles study, Surf. Coat. Technol. 203(5-7) (2008) 883-886, doi:10.1016/j.surfcoat.2008.08.027

    2008 doi

  24. [32]

    Hörling, L

    A. Hörling, L. Hultman, M. Odén, J. Sjölén, L. Karlsson, Mechanical properties and machining performance of Ti1−xAlxN-coated cutting tools, Surf. Coat. Technol. 191(2-3) (2005) 384-392, doi:10.1016/j.surfcoat.2004.04.056

    2005 doi

  25. [33]

    Rossnagel, Magnetron sputtering, J

    S.M. Rossnagel, Magnetron sputtering, J. Vac. Sci. Technol. A 38(6) (2020), doi:10.1116/6.0000594

    2020 doi

  26. [34]

    Bräuer, B

    G. Bräuer, B. Szyszka, M. Vergöhl, R. Bandorf, Magnetron sputtering – Milestones of 30 years, Vacuum 84(12) (2010) 1354-1359, doi:10.1016/j.vacuum.2009.12.014

    2010 doi

  27. [35]

    Musil, J

    J. Musil, J. Vlček, Magnetron sputtering of alloy and alloy-based films, Thin Solid Films 343-344 (1999) 47-50, doi:10.1016/s0040-6090(98)01567-3

    1999 doi

  28. [36]

    Jokinen, J

    J. Jokinen, J. Keinonen, P. Tikkanen, A. Kuronen, T. Ahlgren, K. Nordlund, Comparison of TOF-ERDA and nuclear resonance reaction techniques for range profile measurements of keV energy implants, Nucl. Instrum. Methods Phys. Res. B 119(4) (1996) 533-542, doi:10.1016/s0168-583x(...

    1996 doi

  29. [37]

    Ziegler, Srim-2003, Nucl

    J.F. Ziegler, Srim-2003, Nucl. Instrum. Methods Phys. Res. B 219-220 (2004) 1027- 1036, doi:10.1016/j.nimb.2004.01.208

    2004 doi

  30. [38]

    S. Shen, L. Hao, X. Liu, Y. Wang, Y. Li, J. Zhang, E. Fu, The design of Pd-containing high-entropy alloys and their hardening behavior under He ion irradiation, Acta Mater. 261 (2023), doi:10.1016/j.actamat.2023.119404. 28

    2023

  31. [39]

    Z. Chen, E. Lu, K. Mizohata, L. Anna, X. An, T. Suhonen, A. Laukkanen, J. Lagerbom, A. Pasanen, A. Vaajoki, F. Tuomisto, Suppression of helium migration in arc-melted and 3D- printed CoCrFeMnNi high entropy alloy, J. Nucl. Mater. 599 (2024), doi:10.1016/j.jnucmat.2024.155238

    2024

  32. [40]

    Madsen, T

    J. Madsen, T. Susi, The abTEM code: transmission electron microscopy from first principles, Open Res Eur 1 (2021) 24, doi:10.12688/openreseurope.13015.2

    2021 doi

  33. [41]

    See supporting information file for details of High-resolution TEM image simulations, Ni- Al classical interatomic potential parametrization, Film composition, Pole figure and rocking curve measurements and Nanoindentation measurements at different maximum depths

  34. [42]

    Fischer-Cripps, Critical review of analysis and interpretation of nanoindentation test data, Surf

    A.C. Fischer-Cripps, Critical review of analysis and interpretation of nanoindentation test data, Surf. Coat. Technol. 200(14-15) (2006) 4153-4165, doi:10.1016/j.surfcoat.2005.03.018

    2006 doi

  35. [43]

    C.L. Fu, K.M. Ho, First-principles calculation of the equilibrium ground-state properties of transition metals: Applications to Nb and Mo, Phys. Rev. B 28(10) (1983) 5480-5486, doi:10.1103/PhysRevB.28.5480

    1983 doi

  36. [44]

    Kresse, J

    G. Kresse, J. Hafner, Ab initio molecular dynamics for liquid metals, Phys. Rev. B 47(1) (1993) 558-561, doi:10.1103/physrevb.47.558

    1993 doi

  37. [45]

    Kresse, J

    G. Kresse, J. Furthmüller, Efficiency of ab-initio total energy calculations for metals and semiconductors using a plane-wave basis set, Comput. Mater. Sci. 6(1) (1996) 15-50, doi:10.1016/0927-0256(96)00008-0

    1996 doi

  38. [46]

    Kresse, J

    G. Kresse, J. Furthmuller, Efficient iterative schemes for ab initio total-energy calculations using a plane-wave basis set, Phys. Rev. B 54(16) (1996) 11169-11186, doi:10.1103/physrevb.54.11169

    1996 doi

  39. [47]

    Perdew, K

    J.P. Perdew, K. Burke, M. Ernzerhof, Generalized Gradient Approximation Made Simple, Phys. Rev. Lett. 77(18) (1996) 3865-3868, doi:10.1103/PhysRevLett.77.3865

    1996 doi

  40. [48]

    Methfessel, A.T

    M. Methfessel, A.T. Paxton, High-precision sampling for Brillouin-zone integration in metals, Phys. Rev. B 40(6) (1989) 3616-3621, doi:10.1103/physrevb.40.3616. 29

    1989 doi

  41. [49]

    Thompson, H.M

    A.P. Thompson, H.M. Aktulga, R. Berger, D.S. Bolintineanu, W.M. Brown, P.S. Crozier, P.J. in 't Veld, A. Kohlmeyer, S.G. Moore, T.D. Nguyen, R. Shan, M.J. Stevens, J. Tranchida, C. Trott, S.J. Plimpton, LAMMPS - a flexible simulation tool for particle-based materials modeling ...

    2022

  42. [50]

    arXiv:2503.07344 [cond-mat.mtrl-sci], doi:https://doi.org/10.48550/arXiv.2503.07344

    doi

  43. [51]

    Bartok, M.C

    A.P. Bartok, M.C. Payne, R. Kondor, G. Csanyi, Gaussian approximation potentials: the accuracy of quantum mechanics, without the electrons, Phys. Rev. Lett. 104(13) (2010) 136403, doi:10.1103/PhysRevLett.104.136403

    2010 doi

  44. [52]

    Byggmästar, K

    J. Byggmästar, K. Nordlund, F. Djurabekova, Simple machine-learned interatomic potentials for complex alloys, Phys. Rev. Mater. 6(8) (2022), doi:10.1103/PhysRevMaterials.6.083801

    2022 doi

  45. [53]

    Byggmastar, G

    J. Byggmastar, G. Nikoulis, A. Fellman, F. Granberg, F. Djurabekova, K. Nordlund, Multiscale machine-learning interatomic potentials for ferromagnetic and liquid iron, J. Phys.: Condens. Matter 34(30) (2022), doi:10.1088/1361-648X/ac6f39

    2022 doi

  46. [54]

    arXiv:2408.15779 [cond-mat.mtrl-sci], doi:https://doi.org/10.48550/arXiv.2408.15779

    doi arXiv

  47. [55]

    Nakai, H

    H. Nakai, H. Ciu, M. Adamik, G. Sáfran, P.B. Barna, M. Hashimoto, RBS and XHRTEM characterization of epitaxial Ni films prepared by biased d.c. sputter deposition on MgO(001), Thin Solid Films 263(2) (1995) 159-161, doi:10.1016/0040-6090(95)06589-x

    1995 doi

  48. [56]

    Milosevic, P

    E. Milosevic, P. Zheng, D. Gall, Electron Scattering at Epitaxial Ni(001) Surfaces, IEEE Trans. Electron Devices 66(10) (2019) 4326-4330, doi:10.1109/ted.2019.2934636

    2019

  49. [57]

    de Almeida, R

    P. de Almeida, R. Schäublin, A. Almazouzi, M. Victoria, F. Lévy, Microstructure and growth modes of stoichiometric NiAl and Ni 3 Al thin films deposited by r.f.-magnetron sputtering, Thin Solid Films 368(1) (2000) 26-34, doi:10.1016/s0040-6090(00)00854-3

    2000 doi

  50. [58]

    Yan, W.H

    Y.C. Yan, W.H. Cha, S. Liu, Y. Ma, J.H. Luan, Z. Rao, C. Liu, Z.W. Shan, J. Lu, G. Wu, Ductilization of 2.6-GPa alloys via short-range ordered interfaces and supranano precipitates, Science 387(6732) (2025) 401-406, doi:10.1126/science.adr4917. 30

    2025 doi

  51. [59]

    Lasalmonie, B

    A. Lasalmonie, B. Chenal, G. Hug, P. Beauchamp, Structure and anisotropy of antiphase boundaries in rapidly solidified Ni3Al, Philos. Mag. A 58(3) (1988) 543-554, doi:10.1080/01418618808210430

    1988 doi

  52. [60]

    Y. Li, Y. Pang, W. Liu, X. Wu, Z. Hou, Effect of Diffusivity on the Pseudospinodal Decomposition of the γ′ Phase in a Ni-Al Alloy, J. Phase Equilib. Diffus. 37(3) (2016) 261- 268, doi:10.1007/s11669-016-0450-6

    2016 doi

  53. [61]

    H. Hou, Y. Zhao, Y. Zhao, Simulation of the precipitation process of ordered intermetallic compounds in binary and ternary Ni–Al-based alloys by the phase-field model, Mater. Sci. Eng. A 499(1-2) (2009) 204-207, doi:10.1016/j.msea.2007.11.140

    2009 doi

  54. [62]

    Y.L. Lu, Z. Chen, Y.X. Wang, Microscopic phase-field simulation of the early precipitation mechanism of Ni3Al phase in Ni–Al alloys, Mater. Lett. 62(8-9) (2008) 1385-1388, doi:10.1016/j.matlet.2007.08.061

    2008 doi

  55. [63]

    Choo, J.S

    W.K. Choo, J.S. Lee, D.G. Kim, S.S. Park, Theoretical and experimental investigation on the phase decomposition process of Ni-rich Ni-Al system, Scripta Metallurgica 23(10) (1989) 1779-1784, doi:10.1016/0036-9748(89)90360-8

    1989 doi

  56. [64]

    Lee, An investigation of thermal aging effects on the mechanical properties of a Ni3Al-based alloy by nanoindentation, J

    D. Lee, An investigation of thermal aging effects on the mechanical properties of a Ni3Al-based alloy by nanoindentation, J. Alloys Compd. 480(2) (2009) 347-350, doi:10.1016/j.jallcom.2009.02.014

    2009 doi

  57. [65]

    Sun, S.A

    C. Sun, S.A. Maloy, K. Baldwin, Y. Wang, J.A. Valdez, Phase Stability of Ni/Ni3Al Multilayers Under Thermal Annealing and Irradiation, JOM 72(11) (2020) 3995-4001, doi:10.1007/s11837-020-04377-0

    2020 doi

  58. [66]

    X. Xia, Y. Peng, J. Zhang, X. He, S. Yin, J. Ding, C. Li, X. Chen, Y. Liu, Precipitation and growth behavior of γ′ phase in Ni3Al-based superalloy under thermal exposure, J. Mater. Sci. 54(20) (2019) 13368-13377, doi:10.1007/s10853-019-03821-0

    2019 doi

  59. [67]

    Ardell, Precipitation hardening, Metallurgical Transactions A 16(12) (1985) 2131- 2165, doi:10.1007/bf02670416

    A.J. Ardell, Precipitation hardening, Metallurgical Transactions A 16(12) (1985) 2131- 2165, doi:10.1007/bf02670416. 31 32 Figures and figure captions Fig.1. XRD patterns of Ni and Ni 1-xAlx films. Panel (a) shows patterns in the 2θ angle range 10 − 90°, while panels (b) and (...

    1985 doi

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