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REVIEW 2 major objections 4 minor 46 references

No band gap, no problem: Defects in InAs using a band-avoiding occupation-constrained density functional theory

T0 review · 2 major / 4 minor · reviewed 2026-07-30 · grok-4.5

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Pith's one-line read A constrained occupation scheme lets standard DFT predict defect levels in InAs even when the computed band gap collapses to zero.

desk verdict Practical occupation fix for collapsed-gap defect totals in InAs; internal numerics are careful, external ID of levels is still thin. read the letter →

arxiv 2607.27095 v1 pith:ZLRQQH2U submitted 2026-07-29 cond-mat.mtrl-sci physics.chem-ph

Peter A. Schultz , Arthur H. Edwards , Evan M. Anderson , Anthony C. Knighton , Leopoldo Diaz This is my paper · ORCID
classification cond-mat.mtrl-sciphysics.chem-ph
keywords densityfunctionaltheorybandgapproblempointdefectsInAsoccupation-constrainedDFTchargetransitionlevelsnarrow-gapsemiconductors
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

Standard density functional theory badly underestimates semiconductor band gaps, and in narrow-gap materials such as indium arsenide the gap can vanish entirely. That collapse has long been thought to block reliable first-principles predictions of the charge-transition energies of atomic defects. This paper argues that the difficulty is not fatal: the localized defect orbital still exists above the spuriously lowered conduction-band edge, and one can simply force the calculation to occupy that defect state while leaving the fake band-edge empty. The resulting band-avoiding occupation-constrained DFT yields clean total energies and defect levels for the common intrinsic defects in InAs. The levels are consistent with the sparse experimental clues that exist and explain why irradiated InAs shows a broad shallow-donor signature. If the method holds, quantitative defect chemistry becomes possible in a whole class of infrared and high-mobility materials that were previously off-limits to ordinary DFT.

What carries the argument

ba-occ-DFT: a Γ-specific non-Aufbau occupation constraint that skips the collapsed conduction-band-edge state and forces occupation of the flat, localized defect state, used together with local-moment countercharge boundary conditions and adequate k-point sampling.

What would settle it

A direct experimental identification of the As-antisite (0/+) and (+/2+) levels in InAs (or a large-supercell hybrid-functional calculation that cleanly resolves the same Γ-point state ordering) that disagrees with the predicted 0.35 eV and 0.12 eV positions would falsify the method.

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Extended reading notes

Core claim

Band-avoiding occupation-constrained DFT (ba-occ-DFT) separates band-edge errors from defect energetics: by emptying the spuriously collapsed conduction-band edge at Γ and occupying the localized defect orbital instead, one obtains uncorrupted total energies and therefore rigorous charge-transition levels for defects in InAs despite a zero DFT gap.

Load-bearing premise

The true localized defect orbital really does continue through the zone center above the fake conduction-band edge, so that forcing its occupation yields the physical defect ground-state energy rather than an artifact.

Editorial extensions

If this is right

  • Intrinsic primary defects in InAs terminate at stable (1+) charge states and therefore all act as shallow donors, explaining the broad DLTS shoulder seen after irradiation.
  • The As antisite remains a low-formation-energy double donor that can appear in as-grown material, analogous to EL2 in GaAs.
  • Ordinary PBE plus the occupation constraint and proper charged-supercell boundary conditions can replace hybrid functionals for defect levels in other zero-gap or narrow-gap III–V alloys.
  • The same occupation switch is unnecessary for valence-band-edge crossings; the dominant error is over-stabilization of the delocalized conduction edge, not defect delocalization.

Reading between the lines

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

  • The same Γ-point occupation switch should transfer directly to InSb, InAsSb, and related type-II superlattice detector materials where DFT gaps also collapse.
  • Once formation energies are trustworthy, multiscale kinetic models of radiation damage evolution (already demonstrated for GaAs) become feasible for InAs-based devices.
  • Codes that already support constrained occupations can implement ba-occ-DFT with only a k-point-dependent occupation mask, lowering the barrier to adoption.
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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

2 major / 4 minor

Summary. The manuscript introduces band-avoiding occupation-constrained DFT (ba-occ-DFT): at Γ, non-Aufbau occupations empty the spuriously collapsed conduction-band-edge (CBE) state and occupy the putative localized defect orbital, while off-Γ points use standard Aufbau. Combined with LMCC charged-supercell boundary conditions and PBE, the method is applied to intrinsic point defects in InAs (antisites, vacancies, divacancy, interstitials) in supercells up to 1000 atoms. The authors report converged defect transition levels despite a zero PBE gap, an effective defect band gap bounded by clean defect states, and qualitative consistency with sparse DLTS data (including a shallow-donor interpretation of a broad emission shoulder). HSE06 band structures in small cells are shown not to remove defect-band dispersion or Γ hybridization.

Significance. If the constrained total energies are physically faithful, the work supplies a practical route to defect levels in narrow-gap III–Vs where standard DFT gaps collapse and hybrid+jellium supercell calculations remain costly. The internal convergence campaign (64→1000 atoms, defect-band flattening, Γ-only vs off-Γ and Aufbau vs ba-occ bond-length diagnostics for AsIn) is careful and falsifiable. Predictions that primary displacement defects terminate as shallow donors offer a concrete experimental target. The approach extends a previously benchmarked total-energy/LMCC framework (Si, GaAs) rather than introducing an uncontrolled free parameter for the gap, which is a genuine methodological strength.

major comments (2)
  1. [Fig. 1(d); AsIn discussion and SM cross-ref] Central hypothesis (Fig. 1d and text): the claim that ba-occ-DFT yields uncorrupted localized-defect ground-state energies rests on inverted CBE/defect character at Γ and on adiabatic equivalence of the constrained KS state to the physical gapped defect. Main-text support is indirect (supercell flattening, avoided-crossing language, As–As bond lengths that track charge only under ba-occ, near-equality of Γ-(2×2×2) and off-Γ formation energies). A direct main-text diagnostic—e.g., real-space localization or projection of the occupied Γ orbital onto bulk Bloch/CBE character under both Aufbau and ba-occ—should be added (or the SM result elevated and quantified). Without it, absolute levels in Fig. 4 carry an unquantified systematic risk if residual hybridization remains.
  2. [Fig. 4 and surrounding paragraphs] Fig. 4 level diagram: VBE is bounded by InAs(2+/1+) and CBE is placed at the experimental gap, while an “effective defect band gap” is defined from the highest clean defect state. Charge-transition total-energy differences are method-internal; absolute placement relative to the true edges is not. The text should state explicitly which reported numbers are independent of the experimental-gap alignment, quote the numerical uncertainty from the shallow-bound choice of VBE, and avoid language (“rigorous defect level predictions”) that blurs this distinction.
minor comments (4)
  1. [passim; End Matter heading] Several run-on or missing-space tokens appear in the compiled text (e.g., “extremeinnarrow-gapsemiconductors”, “bandgapproblem”, “END MA TTER”). A full proofreading pass is needed.
  2. [Figs. 2 and 3] Fig. 2–3 band-structure panels would be clearer with an explicit legend for occupied vs empty states under ba-occ and a horizontal marker for the constrained defect level at Γ.
  3. [Discussion of experimental comparison] The experimental associations (Salman; Murawski) are appropriately hedged as non-conclusive; consider adding one sentence on what measurement (e.g., stress splitting, annealing kinetics, or ODMR) would discriminate the predicted AsIn second donor near the VBE.
  4. [End Matter] End Matter: briefly state whether spin-orbit coupling was tested for bulk InAs edges or any defect, even if only to justify its omission for the present total-energy differences.

Circularity Check

1 steps flagged · score 1.0 of 10

No construction-level circularity: defect levels are independent total-energy differences; only light methodological self-citation of LMCC/occ-DFT priors.

  1. self citation load bearing [Intro paragraphs on Si/GaAs validation; methods citing LMCC and finite-defect model]
    "Contrary to conventional wisdom concerning the band gap problem and defect levels, we previously demonstrated that a total-energy-based DFT method for charged defects [19] predicted defect levels in silicon (Si) to within 0.1(average)-0.2(max) eV of experiment... The crucial feature was incorporating rigorous Coulomb boundary conditions... via the local moment countercharge (LMCC) approach [20, 21]."

    The premise that DFT total energies plus LMCC already separate band-edge error from defect levels, and are therefore trustworthy once occupations are cleaned up, rests on the authors’ own prior Si/GaAs papers rather than an independent external benchmark for InAs. This is ordinary methodological self-citation and does not make the InAs numbers equal to their inputs by construction; it only slightly elevates reliance on an unverified-in-this-work chain. Not scored higher because the ba-occ constraint and the InAs total-energy differences themselves are new and not defined by those citations.

full rationale

The paper’s derivation chain is: (i) PBE supercell total energies with LMCC charged-boundary conditions; (ii) a new Γ-specific non-Aufbau occupation that empties the collapsed CBE and occupies the putative defect orbital (ba-occ-DFT); (iii) charge-transition levels from total-energy differences; (iv) diagram placement with VBE bounded by the computed InAs(2+/1+) and CBE set to the experimental gap only for display. None of these steps defines the output in terms of the input. There is no fit of a free parameter to InAs defect data that is then re-presented as a prediction, no uniqueness theorem imported from the authors, and no renaming of a known empirical pattern. Self-citations (LMCC, Si/GaAs DFT+LMCC benchmarks, occ-DFT machinery) supply the established numerical method and the prior claim that total-energy defect levels can be accurate despite a KS gap error; they do not algebraically force the InAs level positions. Post-hoc associations with Salman/Murawski DLTS features are not used as fit targets. The weakest point in the paper is the physical hypothesis that the constrained Γ occupation recovers the true localized-defect ground state—an assumption/correctness risk, not a circular reduction. Score 1 only for ordinary methodological self-citation that is not load-bearing for the numerical results.

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

The result rests on standard DFT total-energy machinery, the authors’ prior LMCC charged-supercell formalism, the physical hypothesis that a localized defect level remains well-defined above a collapsed CBE, and the usual practice of referencing levels to an experimental gap. No new particles or forces; the invented piece is the occupation protocol itself.

free parameters (2)
  • HSE06 exact-exchange fraction (0.25) = 0.25 (default)
    Standard HSE06 mixing used only for comparison band structures; not fitted to InAs defects and not used for the production levels.
  • Experimental InAs gap used to place CBE in level diagram = 0.42 eV (0 K literature)
    Fig. 4 sets CBE from the experimental 0.42 eV gap while VBE is theory-bounded; absolute alignment therefore imports an external number.
assumptions (5)
  • domain assumption PBE total energies of localized defects remain accurate to ~0.1–0.2 eV when band-edge occupations are correctly constrained, as previously validated for Si and GaAs with LMCC.
    Invoked throughout; underpins the claim that zero KS gap does not destroy defect energetics.
  • domain assumption LMCC local-moment countercharge removes finite-size electrostatic errors for charged supercells sufficiently for meV-level convergence.
    Cited from authors’ prior work; used for all charged formation energies.
  • ad hoc to paper At Γ the KS state ordering can invert so that the lowest empty (or spuriously occupied) orbital is CBE-like while a higher orbital is the localized defect; non-Aufbau occupation of the latter is the physical ground state.
    Central hypothesis of Fig. 1(d); verified internally by bond lengths and supercell flattening but not independently proved.
  • domain assumption Discrete Defect Occupation (uniform occupation of each band across the BZ, zero electronic temperature) is the correct baseline for mapping supercell occupations onto isolated-defect charge states.
    End Matter; standard in the authors’ prior defect papers.
  • domain assumption Large-core In d0 pseudopotential with NLCC is transferable enough for InAs defect energetics versus a d10 small-core PP.
    Asserted via bulk tests in SM; production calculations use d0.
invented entities (2)
  • ba-occ-DFT (band-avoiding occupation-constrained DFT protocol)
    purpose: Force occupation of localized defect states at Γ while skipping the collapsed CBE so that total energies remain those of the physical defect.
    Named and defined in this work; the occupation rule is the methodological contribution.
  • Effective defect band gap (EDBG) bounded by clean defect levels
    purpose: Provide an internal theory estimate of the gap from the highest clean acceptor-like and lowest clean donor-like defect positions when the KS gap is zero.
    Introduced in the InAs results discussion; used to claim consistency with experiment.

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Cite this review

Pith. "Pith review of No band gap, no problem: Defects in InAs using a band-avoiding occupation-constrained density functional theory." pith.science (2026). https://pith.science/paper/ZLRQQH2U

@misc{pith2026260727095,
  author       = {Pith},
  title        = {Pith review of: No band gap, no problem: Defects in InAs using a band-avoiding occupation-constrained density functional theory},
  year         = {2026},
  howpublished = {\url{https://pith.science/paper/ZLRQQH2U}},
  note         = {Machine review of arXiv:2607.27095}
}
read the original abstract

Density functional theory (DFT) underestimates the experimental band gap---the infamous band gap problem. As the band gap defines the energy scale of defect levels, this complicates computation of charge transition energies for atomic defects. In the extreme case of narrow-gap semiconductors, the DFT band gap collapses to zero, seemingly precluding quantitative predictions of defect levels. We present a band-avoiding occupation-constrained DFT (ba-occ-DFT) approach that prevents spurious occupation of band-edge states and enables reliable total energy calculations of atomic defects. Application to indium arsenide (InAs) shows that ba-occ-DFT circumvents the band gap problem, separates band-edge errors from defect level calculations, and enables rigorous defect level predictions in a narrow-gap semiconductor despite a zero DFT band gap.

Figures

Figures reproduced from arXiv: 2607.27095 by the authors.

Figure 1
Figure 1. FIG. 1. Band structures for crystalline InAs and idealized [PITH_FULL_IMAGE:figures/full_fig_p002_1.png] view at source ↗
Figure 2
Figure 2. FIG. 2. PBE band structure (a) the perfect crystal 64-atom [PITH_FULL_IMAGE:figures/full_fig_p002_2.png] view at source ↗
Figure 3
Figure 3. FIG. 3. The HSE06 band structure: (a) for the perfect [PITH_FULL_IMAGE:figures/full_fig_p003_3.png] view at source ↗
Figures from the paper (1 more)
Figure 4
Figure 4. Figure 4: FIG. 4. Predicted InAs defect level diagram, using the ba [PITH_FULL_IMAGE:figures/full_fig_p004_4.png]

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