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REVIEW 4 major objections 7 minor 66 references

Mechanisms of Nanoscroll Formation and Particle Encapsulation in Janus MXenes

T0 review · 4 major / 7 minor · reviewed 2026-08-16 · deepseek-v4-flash

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Pith's one-line read Janus Ti2C MXene sheets roll themselves into nanoscrolls because asymmetric surface terminations create a 1–7% lattice strain mismatch that generates a bending moment around carbon atoms.

desk verdict The MD observation of spontaneous Janus MXene scrolling looks real and worth reporting, but the bending-moment model and the H2 chemistry ride on an unvalidated force field. read the letter →

arxiv 2608.12439 v1 pith:TKO2FFIZ submitted 2026-08-12 cond-mat.mtrl-sci physics.atom-phphysics.comp-ph

Sasan Rezaee , Fatemeh Mohammad Dezashibi , Ould el Moctar , Hossein Darban This is my paper · ORCID
classification cond-mat.mtrl-sciphysics.atom-phphysics.comp-ph
keywords JanusMXenesnanoscrollself-rollingbendingmomentcore@shellcompositereactivemoleculardynamicsinterlayerspacingH2evolution
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 tries to establish an atomistic mechanism for a phenomenon already achieved experimentally: why a Janus (two-faced) MXene sheet curls itself into a nanoscroll. Using reactive molecular dynamics validated against density functional theory, it shows that when the two faces of a Ti2C sheet carry different chemical groups (bare, -O, or -OH), the Ti-O and Ti-Ti distances on the two faces differ enough to produce a 1–7% lattice-induced strain. That strain mismatch creates a net bending moment about the carbon pivot atoms, so the sheet spontaneously rolls toward the face under compressive strain. The final shape is not arbitrary: for long flakes the sheet forms a multiwalled nanoscroll whose inner diameter and interlayer spacing are set by the termination pair, while small square flakes merely curve or, in one termination, close into a chiral nanotube. The same scrolling wraps a single anchored titanium nanoparticle into a core@shell structure, locally widening the interlayer spacing from 0.96 nm to 2.02 nm, but the simulation also shows that encapsulation releases H2 molecules that can form performance-degrading nanobubbles.

What carries the argument

The load-bearing object is the net bending moment about each carbon pivot atom. The paper's Eq. (3b) writes it as $\vec{M}_i = A_{(-O,-OH)}(2.25\sin\theta_{-OH}+\sin\theta_{-O})(-\hat{y})$, where $A_{(-O,-OH)} = Y A |\varepsilon_{-O}| r_{\mathrm{Ti-C}}$ ranges from $2.18\times10^{-19}$ to $4.46\times10^{-19}$ N·m. Each carbon sits between three Ti atoms on the -OH face and three on the -O face, so the strain-induced forces on the two faces are parallel but opposite; because they act on opposite sides of the carbon, their moments add instead of cancel. Since the strain acts only along the x direction, only moments about the y axis survive, and the right-hand rule selects the rolling direction toward the compressively strained face. The machinery also explains the metastability of bTi2C(O): both faces are compressive, with a net strain of only 4.5%, and the Ti-C bond-length variation is insufficient to hold a stable curvature, so Coulombic Ti-O interlayer attraction zips the semi-scrolled structure closed.

What would settle it

Compute the relaxed Ti-O bond lengths on the two faces of a free-standing (O)Ti2C(OH) monolayer with density functional theory. If the -O face's Ti-O bond is not shorter than the -OH face's bond (the paper finds 1.92 Å versus 1.95 Å), the reported 5.2% net strain and the bending moment that drives scrolling vanish, and the proposed mechanism would need revision.

Watch

Extended reading notes

Core claim

On its own terms, the paper's central discovery is that nanoscroll formation in Janus MXenes is a deterministic strain-driven process, not a stochastic curling artifact. Starting from the experimentally known Ti2C(OH)2 sheet and etching one face to -O or bare, the simulations find that the etched face contracts while the -OH face expands: the Ti-O bond length falls from 1.95 Å to 1.92 Å after H removal, giving net strains of -1.6% to -7.1% on the compressed face and tensile strains up to +4.2% on the opposite face. This differential strain produces a net bending moment around the carbon pivot atoms, expressed by Eq. (3b), with an average magnitude near $3.32\times10^{-19}$ N·m for (O)Ti2C(OH); the moment points the same way for every carbon atom, so the sheet rolls toward the face under compressive strain. Whether the final object is a curved sheet, a chiral nanotube, or a multiwalled nanoscroll is then set by curvature and flake size: at 120 nm length, (O)Ti2C(OH) and bTi2C(OH) form stable scrolls with interlayer spacings around 0.7 nm and inner diameters of 7–8 nm, whereas bTi2C(O) produces a metastable structure with spacing around 1.7 nm and inner diameter above 20 nm. When a single Ti nanoparticle is anchored on the bare face of bTi2C(OH), the sheet still scrolls, bonds to the particle, and locally expands the interlayer spacing to 2.02 nm; the particle's electron transfer to oxygen weakens O-H bonds and releases H2.

Load-bearing premise

The argument assumes that the reactive force field used for all simulations, which is validated only against bare Ti2C lattice parameters, layer thickness, and Young's moduli, also correctly captures the energetics of -O and -OH termination, O-H bond breaking, and H2 formation on functionalized surfaces.

Editorial extensions

If this is right

  • For long flakes the termination pair sets the scroll geometry: (O)Ti2C(OH) and bTi2C(OH) form stable multiwalled nanoscrolls with interlayer spacing around 0.7 nm and inner diameter 7–8 nm, while bTi2C(O) forms only a metastable structure with spacing around 1.7 nm and inner diameter above 20 nm.
  • Flake size is a second control: square flakes of 10–20 nm only curve (one 20 nm bTi2C(OH) flake closes into a chiral nanotube), whereas 40–100 nm flakes of the -OH-bearing systems scroll.
  • Clamping one end of the flake, equivalent to effectively doubling its length, increases the inner diameter by roughly 8–34% and interlayer spacing by up to 46%, depending on termination.
  • A nanoparticle does not stop scrolling: it is captured between MXene layers, bonds to the sheet, and raises the local interlayer spacing from 0.96 nm to 2.02 nm, so particle size can be a design handle for interlayer channels.
  • Encapsulation can release H2 that accumulates as nanobubbles, so a practical MXene-scroll electrode must mitigate this bubble-shielding effect.

Reading between the lines

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

  • If the carbon-pivot bending mechanism transfers to other MXene compositions such as Ti3C2, V2C, or Nb2C, the surface bond lengths alone might predict which termination pairs scroll and in which direction, making Eq. (3b) a design rule for a whole family of materials.
  • The H2 release pathway is tied to electron transfer from the titanium particle to oxygen; a silicon or sulfur core, which the authors could not simulate because their force field has no parameters for those elements, may not release H2 in the same way, so the nanobubble risk should not be assumed universal for core@shell MXene electrodes.
  • The locally enlarged spacing around a captured particle suggests that ordered arrays of nanoparticles could imprint a periodic interlayer-spacing pattern into a scroll, offering a lithography-free route to engineered ion channels, though scroll uniformity at high particle density remains untested.
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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 / 7 minor

Summary. The manuscript reports reactive molecular dynamics simulations of three Janus Ti2C MXene surface terminations (bare, -O, and -OH) under four boundary-condition classes, and claims that asymmetric surface termination produces 1-7% lattice-induced strain, which creates a bending moment about carbon pivot atoms and drives spontaneous curling, scrolling, or nanotube formation depending on flake size. It further reports that a Ti nanoparticle can be encapsulated by a scrolling sheet, locally enlarging the interlayer spacing, and that encapsulation is accompanied by H2 release. The paper validates the ReaxFF potential against DFT/experimental structural and elastic data for bare Ti2C, then uses an analytical-MD bending-moment model to explain scrolling directions and to compare moments across terminations.

Significance. The central qualitative observation, namely that flat Janus MXene sheets scroll spontaneously in MD without imposed moments, is directly demonstrated and is a useful step toward understanding the experimentally reported scalable synthesis route for MXene scrolls. The systematic morphology map as a function of surface termination and flake size, and the identification of H2 as a side product during nanoparticle encapsulation, are valuable and falsifiable predictions. However, the quantitative causal chain (strain mismatch, bending moment, scroll geometry) rests on force-field transferability to functionalized surfaces and on strain measurements made after relaxation on curved structures; these supports are currently weaker than the conclusions require. If the requested benchmarks and reanalyses are provided, the paper will make a solid contribution.

major comments (4)
  1. [Section 3.1 (Table 1)] The force-field validation is confined to bare Ti2C: Table 1 compares ReaxFF predictions against DFT for the in-plane lattice parameter, thickness, Ti-C bond length, and Young's moduli, with systematic errors up to 12.83% in the moduli. The simulations then use the same ReaxFF potential to model -O and -OH terminated surfaces, O-H dissociation, and H2 formation in Section 3.5, with no DFT benchmark for any functionalized structure. Because the strain mismatch in Table 2 and the H2 release mechanism both depend on the energetics and bond-length changes of these functional groups, the quantitative scrolling mechanism is unsupported unless the potential is validated for the functionalized systems. I request DFT calculations of equilibrium bond lengths, relative stabilities, and O-H dissociation energetics for the relevant terminations, or a clear statement that the quantitative claims are conditional on force-field fidelity.
  2. [Section 3.2 (Table 2) and Section 3.5 (Eqs. (3)-(5))] The strain values that drive the bending-moment model are measured after energy minimization on already-curled sheets, "near the end regions" (Table 2). These post-relaxation strains combine the intrinsic lattice mismatch with the geometric strain of curvature, and they are then substituted into Eqs. (3)-(5) as the pre-scrolling mismatch that generates the bending moment. This is a circular step for the quantitative claim. I note that the MD observation of spontaneous scrolling from flat sheets is not itself circular; however, the authors should compute the strain from flat, uncurled reference structures (e.g., before minimization or with curvature constrained) and confirm that the values in Table 2, and the ordering of bending moments, do not depend on the local curvature at the measurement site.
  3. [Section 3.5, Eqs. (1)-(5)] The analytical bending-moment calculation contains an ad hoc geometric parameter: the nominal cross-sectional area is defined with r approximately 2.5 Angstrom, "chosen to be slightly larger than the Ti-C bond length," and the position vectors are set equal to the Ti-C bond length. The absolute bending moments (2.18x10^-19 to 4.46x10^-19 N.m, and 5.39x10^-19 and 6.64x10^-19 N.m) therefore depend on this choice, and the claim that MD and analytical-MD agree "with the same order of magnitude" is not a strong consistency check unless the sensitivity to r is quantified. Please provide a sensitivity analysis over a physically plausible range of r and show that the qualitative ordering of the bending moments, which is the basis for the scrolling-direction and morphology claims, is robust.
  4. [Section 3.5 and Section 3.6] The H2-release prediction is a central applied finding, but it is supported only by a qualitative electronegativity argument and by reactive trajectories from a force field not validated for O-H dissociation on MXene surfaces. No DFT barriers or experimental benchmark are provided. Because the bubble-shielding claim is one of the paper's main practical conclusions, this mechanism should be corroborated by independent electronic-structure calculations or at least reported with an explicit uncertainty assessment.
minor comments (7)
  1. [Section 2.1 and Figure 1 caption] The x and y crystallographic directions are described inconsistently: Section 2.1 calls x:[100] the zigzag direction and y:[010] the armchair direction, whereas the Figure 1 caption says x is armchair and y is zigzag. Please correct this.
  2. [Section 2.1] The enumeration of simulation classes lists "Class I, II, III, and VI," but the fourth class is Class IV. Please correct the typo.
  3. [Author list and Author Contributions] The surname of the corresponding author appears as "Darban" in the author list and "Darband" in the Author Contributions section; please standardize.
  4. [Declaration of Interests] The declaration reads "The author declares" but the manuscript has multiple authors; this should be plural.
  5. [Figures 2, 3, 8 and text] There are repeated spelling errors, e.g., "nanoscrrolled" instead of "nanoscrolled" in several figure-related passages.
  6. [Equations (1)-(5)] The equations are poorly typeset and some symbols are undefined or ambiguous (for example, the nominal radius r and the cross-sectional area A, and the superscripts/subscripts on the moment terms). Please define all symbols in one consistent notation.
  7. [Section 2.2 and Figures 2-5, 8] The text states that simulations were run for at least 75 ns, but the reported energy and MSD plots show only the first 1 ns (and Figure 8 refers to a 2 ns snapshot). Please clarify the displayed time interval and whether the longer runs change the reported morphologies.

Circularity Check

0 steps flagged · score 2.0 of 10

No significant circularity; central scrolling results are direct MD observations, with one minor non-load-bearing self-citation.

full rationale

The central finding of the paper, spontaneous scrolling of Janus MXenes, is produced directly by reactive MD energy minimization and does not depend on the analytical bending-moment equations. The analytical model in Section 3.4 takes the post-relaxation surface strains from Table 2 (e.g., -1.6% and +3.6%) and computes a bending moment via Eqs. (3)-(5); this is a post-hoc mechanical interpretation rather than an independent prediction of the MD outcome, so it does not make the morphology results circular. Validation in Table 1 is against external DFT data for bare Ti2C and provides an independent benchmark for the force field; reference [44], a same-author preprint for further ReaxFF validation, is supplementary and not load-bearing. The limitation stated in Section 3.6, that TiNP is a model for Si/S and that H2 formation requires further force-field development, is an honest caveat rather than a hidden circular step. The score of 2 reflects only the minor non-load-bearing self-citation, not any circularity in the core derivation.

Assumptions & free parameters 1 free parameters · 5 assumptions · 0 invented entities

The central claim rests on one hand-chosen geometric parameter (r=2.5 Å) in the bending-moment model and on several domain assumptions: the transferability of the ReaxFF potential to Janus surfaces, the representativeness of 1 K equilibration, and the interpretation of post-minimization strains as the cause of scrolling. No new physical entities are postulated; the Ti nanoparticle is a model system, and H2 is a predicted reaction product.

free parameters (1)
  • Nominal cross-sectional radius r in the bending moment model = 2.5 Å
    Chosen in Section 3.4 as 'slightly larger than the Ti-C bond length' to include the atomic chains. It directly scales all computed bending moment magnitudes in Eq. (3) and is not justified by independent data.
assumptions (5)
  • domain assumption ReaxFF force field [38] accurately models the chemistry of Janus -O and -OH terminated Ti2C surfaces, including bond formation, bond dissociation, and H2 release.
    The validation in Table 1 covers only bare Ti2C structural and elastic properties. The central scrolling, encapsulation, and H2 predictions depend on this transferability.
  • domain assumption Energy minimization plus NVT equilibration at 1 K captures the intrinsic scrolling mechanism without thermal artifacts.
    Section 2.2 sets 1 K to remove thermal noise. The paper does not demonstrate that the same mechanism persists at room temperature or that the 1 K equilibrium state is representative.
  • ad hoc to paper Strains measured after energy minimization on already-curled sheets represent the pre-scrolling lattice mismatch that drives curling.
    Table 2 strains are measured 'after energy minimization' on curved configurations and are then used in Eqs. (3)-(5) to compute the bending moment claimed to cause the curvature. If the sheet has already relaxed, measured strains may be a consequence of bending rather than its cause.
  • ad hoc to paper The bending moment can be modeled with a nominal cross-sectional radius r of 2.5 Å and the Ti-C bond length as a lever arm for every carbon pivot atom.
    The radius r is selected to include the atomic chains and directly scales all absolute moment values. The authors acknowledge uncertainty in absolute values but assert trends are reliable.
  • domain assumption Periodic boundary conditions along the y-axis model an infinitely wide flake under plane strain.
    Classes I, II, and IV use a 15.45 nm or 7.70 nm width with PBC along y. This idealization ignores finite-width edge effects that could alter scrolling in real flakes.

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Pith. "Pith review of Mechanisms of Nanoscroll Formation and Particle Encapsulation in Janus MXenes." pith.science (2026). https://pith.science/paper/TKO2FFIZ

@misc{pith2026260812439,
  author       = {Pith},
  title        = {Pith review of: Mechanisms of Nanoscroll Formation and Particle Encapsulation in Janus MXenes},
  year         = {2026},
  howpublished = {\url{https://pith.science/paper/TKO2FFIZ}},
  note         = {Machine review of arXiv:2608.12439}
}
read the original abstract

Morphology transfer of 2D Janus MXenes into nanoscrolls unlocks unusual properties. Although a scalable synthesis route has been experimentally verified, the atomistic mechanism underlying nanoscroll formation remains poorly understood. We use large-scale reactive molecular dynamics simulations, validated against density functional theory (DFT) and experimental structural and elastic properties, to investigate stability and quantify the driving forces and geometry governing nanoscroll formation in three Janus MXenes, (Tx)Ti2C(Ty), where (Tx) and (Ty) denote the bottom and top surface terminations among bare (-b), -O, and -OH. Both square and infinitely wide flakes with lengths ranging from 10 to over 120 nm are simulated. We find that 1-7% lattice-induced strain generates a bending moment in these structures. The sheet scrolls, curves, or forms a nanotube depending on the resulting curvature and initial sheet size. For MXenes with an initial length of 120 nm, multiwalled nanoscrolls form with interlayer distances of around 0.7 nm and inner diameters of about 7 nm for (O)Ti2C(OH) and (b)Ti2C(OH), whereas (b)Ti2C(O) instead produces a much larger interlayer distance of around 1.7 nm and an inner diameter exceeding 20 nm. We show that spontaneous scrolling of a Janus MXene in the presence of an anchored nanoparticle produces a core@shell composite, in which the particle locally deforms the nanoscroll and widens the interlayer channels. This locally tunable, enlarged interlayer spacing offers a promising design route for MXene-based energy-storage electrodes. However, our simulations reveal H2 gas release during encapsulation, which promotes nanobubble formation that can reduce battery life.

Figures

Figures reproduced from arXiv: 2608.12439 by the authors.

Figure 1
Figure 1. a [PITH_FULL_IMAGE:figures/full_fig_p003_1.png] view at source ↗
Figure 1
Figure 1. The initial configurations of (a) plane strain, (b) free-standing MXene, and (c) plane strain supporting a single Ti nanoparticle. Plane strain configurations were modeled in two main classes: I: Free–Plane Strain–Free (FPSF), which means that both terminations of the MXene are free and can move freely, and II: Clamped–Plane Strain–Free (CPSF), which means that one termination is fixed as a clamp while the other ter… view at source ↗
Figure 2
Figure 2. d and e compare the evolution of the potential energy and MSD of Class I systems, respectively, over a 1 ns simulation [PITH_FULL_IMAGE:figures/full_fig_p007_2.png] view at source ↗
Figures from the paper (2 more)
Figure 3
Figure 3. Figure 3: d [PITH_FULL_IMAGE:figures/full_fig_p010_3.png]
Figure 8
Figure 8. Figure 8: c presents a magnified view of the nanoscrolled TiNP@bTi2C(OH) system at 2 ns. The figure clearly demonstrates that the presence of the TiNP alters the otherwise uniform interlayer spacing of the scrolled MXene sheets. In addition, the enlarged view of the TiNP confine…

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Pith tools

Reviewed August 16, 2026 · model on record in the stance chip above.