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REVIEW 3 major objections 4 minor 64 references

Two-Dimensional Hexagonal BX3 (X = P, As) Monolayers as High-Capacity, Fast-Charging Anode Platforms for Lithium- and Sodium-Ion Batteries

T0 review · 3 major / 4 minor · reviewed 2026-08-01 · deepseek-v4-flash

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Pith's one-line read Hexagonal BP3 and BAs3 monolayers are shown to be fast-charging, high-capacity anodes for both lithium- and sodium-ion batteries, staying metallic at every state of charge.

desk verdict Routine DFT screening with a plausible Li result; the SIB capacity claim is undone by an internal stoichiometry contradiction. read the letter →

arxiv 2607.15514 v2 pith:CS5TV4JE submitted 2026-07-16 cond-mat.mtrl-sci

Jakkapat Seeyangnok , Joongjai Panpranot , Udomsilp Pinsook This is my paper · ORCID
classification cond-mat.mtrl-sci
keywords two-dimensionalanodeBP3monolayerBAs3lithium-ionbatterysodium-iondensityfunctionaltheorydiffusionbarriermultilayersodiation
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 sets out to show that two atomically thin materials — hexagonal monolayers of boron phosphide (BP3) and boron arsenide (BAs3) — can serve as dual-use battery anodes, storing lithium and sodium while remaining electrically conductive. Using density functional theory, the authors find that both hosts bind alkali ions most strongly at the same hollow site, and that ions hop between these sites with small energy barriers (0.19–0.40 eV), which implies fast charging. They report that lithium saturates at Li3BX3, giving BP3 a capacity of 775 mAh/g — about double graphite — while sodium storage extends to multilayer clusters, reaching 3875 mAh/g on BP3 at a low average voltage of 0.18 V. If these predictions hold, the materials would combine high capacity, low operating potential, and metallicity without conductive additives.

What carries the argument

The central object is the 2D hexagonal BX3 monolayer with a puckered lattice (X = P or As). The argument runs on three mechanisms: (1) an adsorption hierarchy that puts the H3 hollow site deepest, driven by combined ionic charge donation and covalent p-p hybridization; (2) a direct H3-to-H3 hopping path that skips a high-energy intermediate site, giving low diffusion barriers; and (3) for sodium, a transition beyond monolayer coverage into multilayer metallic clustering that keeps voltages positive and extends storage to extreme concentrations. These are linked through formation-energy convex hulls and open-circuit voltage profiles that identify the stable intercalation phases.

What would settle it

Recompute the formation energies of NaxBX3 with dispersion corrections and run ab initio molecular dynamics at 300 K for Na15BP3. If the Na15 phase decomposes into bulk sodium plus lower-concentration phases, or if its voltage plateau departs from the predicted ~0.10 V, the ultrahigh-capacity claim would be falsified; an experimental measurement of the sodium plating/stripping potential on BP3 would settle it directly.

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Extended reading notes

Core claim

The central claim is that 2D hexagonal BX3 (X = P, As) monolayers are high-performance dual-ion anodes: they bind Li and Na strongly at the H3 hollow site, diffuse ions quickly via direct H3-to-H3 hops (0.19–0.40 eV barriers), and stay metallic at every state of charge. Lithium saturates at Li3BX3, giving 775 mAh/g (BP3) and 341 mAh/g (BAs3) at average voltages of 0.39 and 0.35 V. Sodium continues to multilayer clusters up to Na15BX3 (Na12BX3 for BAs3), producing ultrahigh capacities of 3875 and 1365 mAh/g at 0.18 and 0.15 V. The stability of the multilayer sodiated phases is what makes the extreme sodium capacities possible.

Load-bearing premise

The ultrahigh sodium capacities rest on the assumption that multilayer sodium clusters up to Na15BX3 are thermodynamically stable against separation into bulk sodium, with a computed margin of only about 0.18 eV per atom using a functional that is known to be imperfect for alkali-metal cohesion and without van der Waals or finite-temperature checks.

Editorial extensions

If this is right

  • A BP3 anode could store twice as much lithium per gram as commercial graphite (775 vs 372 mAh/g) while charging at rates comparable to or better than graphite.
  • Sodium-ion batteries built on BP3 could reach gravimetric capacities near 3875 mAh/g, far above typical MXenes and most 2D anodes, if the multilayer sodiation phase is real.
  • Both hosts stay metallic throughout charge/discharge, so the electrode may not need conductive carbon additives, reducing weight and cost.
  • The low diffusion barriers (0.19–0.40 eV) imply fast room-temperature ion transport, which supports rapid charging.
  • Low average operating voltages (0.15–0.39 V) help maximize full-cell energy density.

Reading between the lines

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

  • The same multilayer-storage mechanism, if stable, may extend to potassium or other alkali ions on these hosts, potentially yielding similar ultrahigh capacities.
  • Real devices would need to verify volumetric capacity and whether the multilayer sodium clusters survive finite temperature and cycling; the current evidence is zero-temperature and dispersion-free.
  • The H3-site preference and direct hopping path suggest that strain engineering or chemical substitution on the pnictogen sublattice could tune diffusion barriers and capacities.
  • Because the paper identifies formation energies relative to bulk Na, a direct experimental test of sodium plating potential on BP3 would cleanly validate or overturn the ultrahigh-capacity claim.
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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 / 4 minor

Summary. The manuscript uses first-principles DFT (PBE, ONCV pseudopotentials) to evaluate two-dimensional hexagonal BP3 and BAs3 monolayers as dual-ion (Li and Na) battery anodes. It reports adsorption-site energetics, CI-NEB diffusion barriers, formation-energy convex hulls, OCV profiles, specific capacities, Bader/COHP bonding analyses, and density-of-states data. The central claims are: Li storage up to Li3BX3 with capacities 775 mAh/g (BP3) and 341 mAh/g (BAs3) at ~0.35-0.39 V; Na storage via multilayer metallic clustering up to Na15BP3/Na12BAs3 with ultrahigh capacities 3875/1365 mAh/g at ~0.15-0.18 V; low diffusion barriers (0.19-0.40 eV); and metallic conductivity maintained throughout charging. The Li results are internally consistent and survive scrutiny; the Na 'ultrahigh-capacity' claim contains an arithmetic inconsistency that is load-bearing.

Significance. If the reported Na-storage stoichiometry and capacities were reliable, the work would present a striking SIB anode candidate with capacities far above most 2D materials. The paper does include systematic calculations (site screening, convex hull, CI-NEB, Bader/COHP, DOS) and the Li-ion capacities are plausible and competitive. However, the marquee result—the Na capacity of 3875/1365 mAh/g—rests on an inconsistent definition of the maximum sodiation stoichiometry. The manuscript's own Figures and Conclusions identify the heavily sodiated supercell as Na72B8X24, which corresponds to x=9 per formula unit, not the x=15/12 used in the capacity equation. If the actual maximum is x=9, the capacities reduce to 2325/1024 mAh/g, which are far less distinctive. Because the central SIB claim is not supported by the data as presented, the significance of the work hinges on whether the authors can supply the missing high-concentration calculations or revise the claims accordingly.

major comments (3)
  1. [Eq. (3), Table I, Fig. 6, Conclusions] The central SIB capacity claim is internally inconsistent. The capacity in Eq. (3) is computed from x_max=15.0 (BP3) and 12.0 (BAs3), giving 3875 and 1365 mAh/g. However, the only explicitly identified heavily sodiated supercell in the manuscript is Na72B8X24 (Fig. 6 and Conclusions), which corresponds to x=9 per formula unit, not the claimed values. Under Eq. (3), x=9 gives 2325 mAh/g for BP3 and 1024 mAh/g for BAs3—the former exactly matching the prior BP3 SIB study cited as Ref. [40]. The manuscript does not report structures, total energies, or formation energies for Na120B8P24 or Na96B8As24 anywhere, although Table I lists rows at x=12, 13.5, and 15.0. Either the Table I entries at x>9 are based on unshown calculations, in which case the data must be presented, or the quoted maximum stoichiometry and capacities are wrong. As written, the 'ultrahigh' SIB capacity claim is unsupported
  2. [Eq. (1), Section III.A] The definition of x is ambiguous and appears to contain a factor-of-3 error. Eq. (1) and the text define x = N_adatom/N_X with N_X=8 for the 'host supercell.' The supercell is explicitly stated to be B8X24, containing 24 pnictogen atoms, so N_X should be 24 if X denotes pnictogen atoms. The text later states 'x=1/8 (0.125) corresponds to a single adsorbed alkali atom,' which is consistent with x being defined per BX3 formula unit (8 formula units in the cell) rather than per pnictogen atom. This mislabeling does not affect the numerical results if the intended quantity is per formula unit, but it creates confusion in every concentration label and should be corrected unambiguously.
  3. [Section III.A, Fig. 1c, Table I] The thermodynamic stability of multilayer Na phases at x>3 is asserted solely from PBE formation energies relative to bcc Na. The energy gain at x=15 is only -0.18 eV/atom for BP3 and -0.13 eV/atom for BAs3 in Table I. This margin is comparable to PBE's systematic errors for alkali-metal cohesive energies and well within the range where missing van der Waals interactions or vibrational contributions could change the sign. The paper provides no AIMD, phonon, or vdW-corrected checks for these multilayer structures, nor does it consider competition with Na-X compound formation. The positive OCV plateaus near 0.10 V and 0.03 V at high x are correspondingly fragile. The authors should either provide more robust evidence for the multilayer phases (e.g., vdW-DFT calculations, AIMD trajectories, or at least a discussion of the error bar) or moderate the 'safe, dendrite-free' claim.
minor comments (4)
  1. [Fig. 2 caption] The caption states the visible sodiation structures extend up to x=10.50, while Table I reports values up to x=15.0. If structures for x>10.5 were calculated, they are not shown; if they were not, Table I is unexplained.
  2. [Section III.A] The phrase 'guaranteeing a safe, dendrite-free operating mechanism near 0 V' is too strong. Even if the OCV remains positive, the margin of ~0.02-0.10 V at high x is small against typical DFT errors, and safety claims from thermodynamic hull data alone are speculative.
  3. [References [41,42]] The intrinsic phase stability of the pristine BP3/BAs3 monolayers is justified by citing two unpublished arXiv preprints by the same authors. Since these are not peer-reviewed, the stability premise is not independently established in the present manuscript.
  4. [Abstract/Conclusions] The abstract calls the materials 'structurally resilient,' but the manuscript contains no mechanical, thermal, or dynamic stability analysis beyond the PBE adsorption calculations. Either provide such evidence or soften the wording.

Circularity Check

0 steps flagged · score 0.0 of 10

No significant circularity: capacities and voltages are DFT-derived outputs, not fitted inputs; the Na72B8X24/x=15 mismatch is an internal consistency error, not a circular reduction.

full rationale

The central derivation chain is self-contained. Li and Na capacities are computed from Eq. (3) using the maximum stable stoichiometry read off the convex hull from Eq. (1), and voltages come from Eq. (2) between adjacent hull phases; neither equation contains the advertised capacity or voltage as an input. The diffusion barriers and PDOS metallicity are independent CI-NEB and electronic-structure outputs. The only self-references are refs. [41,42], cited for DFPT validation of the pristine BX3 hosts; that stability input is separate from the electrochemical quantities and is externally checkable, so it is not a load-bearing self-citation loop. One non-circular concern: the Conclusions equate the maximum sodiation stoichiometry with 'Na72B8X24' while the 3875/1365 mAh/g capacities use x=15/12 in Eq. (3); by the paper's own definition x=9 for Na72B8X24, which would give 2325/1024 mAh/g. This is an internal inconsistency/unsupported capacity claim, but it is not an equation that reduces to its own input, so it does not raise the circularity score.

Assumptions & free parameters 0 free parameters · 6 assumptions · 0 invented entities

The central claims rest on standard DFT approximations plus a specifically ad hoc assumption that multilayer Na metal is a legitimate anode storage phase. There are no fitted parameters in the electrochemical model; the xmax values are outputs of the convex hull, not inputs. The sparse sampling and lack of vdW/AIMD checks are the main epistemic weaknesses.

assumptions (6)
  • domain assumption PBE-GGA exchange-correlation functional provides adequate energetics for alkali adsorption on 2D hosts.
    Used throughout; no benchmark against experiment or higher-level methods, and PBE is known to have systematic errors for alkali-metal cohesion.
  • domain assumption The hexagonal BX3 structure and lattice parameters from prior DFPT preprints [41,42] are the relevant ground-state polymorphs.
    The paper cites only the authors' own arXiv preprints for phase stability; no independent peer-reviewed confirmation is provided.
  • domain assumption Bulk bcc Li/Na is the correct thermodynamic reference for the alkali chemical potential.
    Standard in the field, but the comparison is particularly delicate for the claimed multilayer Na stability margin.
  • domain assumption The formation-energy convex hull constructed from the sampled discrete concentrations identifies all stable phases.
    Only sparse x values are sampled (e.g., Li at x=0, 0.125, 0.5, 1, 1.5, 3, 4.5); intermediate stable phases could be missed.
  • ad hoc to paper Multilayer Na clusters remain commensurate with and bound to the host rather than phase-separating into bulk Na or Na-X compounds.
    The paper assumes Na up to Na15BX3 forms stable metallic layers on both sides of the sheet; no decomposition or phase-separation check is performed.
  • domain assumption A 40 Å vacuum spacing and 2×2×1 supercell are sufficient to suppress spurious periodic and interlayer interactions.
    Standard for monolayer DFT, but multilayer Na extends into the vacuum and convergence is not demonstrated.

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Cite this review

Pith. "Pith review of Two-Dimensional Hexagonal BX3 (X = P, As) Monolayers as High-Capacity, Fast-Charging Anode Platforms for Lithium- and Sodium-Ion Batteries." pith.science (2026). https://pith.science/paper/CS5TV4JE

@misc{pith2026260715514,
  author       = {Pith},
  title        = {Pith review of: Two-Dimensional Hexagonal BX3 (X = P, As) Monolayers as High-Capacity, Fast-Charging Anode Platforms for Lithium- and Sodium-Ion Batteries},
  year         = {2026},
  howpublished = {\url{https://pith.science/paper/CS5TV4JE}},
  note         = {Machine review of arXiv:2607.15514}
}
read the original abstract

The rapid advancement of alkali-metal ion batteries demands robust anode platforms combining high specific capacities with rapid charge-discharge kinetics. Using first-principles density functional theory (DFT), we systematically evaluate two-dimensional (2D) hexagonal BX3 (X = P, As) monolayers as high-performance dual-use anodes for lithium-ion (LIBs) and sodium-ion batteries (SIBs). Both metallic host architectures display strong thermodynamic affinities for Li+ and Na+ adsorption, favoring the hollow H3 site through synergistic ionic charge transfer and orbital hybridization. Climbing image nudged elastic band (CI-NEB) calculations reveal low direct H3 -> H3 diffusion barriers: 0.40 eV (BP3) and 0.26 eV (BAs3) for Li+, and 0.26 eV (BP3) and 0.19 eV (BAs3) for Na+, confirming exceptional high-rate kinetics. Thermodynamic convex hulls establish maximum stable lithiation at Li3BX3, yielding low average operating potentials of 0.39 V (BP3) and 0.35 V (BAs3) alongside theoretical specific capacities of 775 mAh/g and 341 mAh/g, respectively, with BP3 doubling commercial graphite (372 mAh/g). For SIBs, multi-layer sodiation expands storage up to Na15BP3 and Na12BAs3, delivering ultrahigh capacities of 3875 mAh/g (BP3) and 1365 mAh/g (BAs3) at low voltages of 0.18 V and 0.15 V. Crucially, projected density of states (PDOS) analyses confirm that both frameworks preserve intrinsic metallic conductivity throughout all charging stages. These combined properties establish 2D BX3 monolayers as outstanding, structurally resilient anode candidates for next-generation LIB and SIB energy storage technologies.

Figures

Figures reproduced from arXiv: 2607.15514 by the authors.

Figure 1
Figure 1. FIG. 1. Thermodynamic stability and electrochemical voltage char [PITH_FULL_IMAGE:figures/full_fig_p004_1.png] view at source ↗
Figure 2
Figure 2. FIG. 2. Top and side views of the optimized geometric configurations during progressive alkali metal adsorption on the BX [PITH_FULL_IMAGE:figures/full_fig_p006_2.png] view at source ↗
Figure 3
Figure 3. FIG. 3. Alkali metal ion diffusion kinetics on the BX [PITH_FULL_IMAGE:figures/full_fig_p007_3.png] view at source ↗
Figures from the paper (2 more)
Figure 5
Figure 5. Figure 5: FIG. 5. Electronic structure analysis and chemical bonding characteristics of alkali metal adsorption on the BX [PITH_FULL_IMAGE:figures/full_fig_p008_5.png]
Figure 6
Figure 6. Figure 6: FIG. 6. Calculated electronic properties of the BX [PITH_FULL_IMAGE:figures/full_fig_p009_6.png]

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