pith. sign in

arxiv: 2605.20384 · v1 · pith:NZAFJYWGnew · submitted 2026-05-19 · ❄️ cond-mat.mtrl-sci

Dataset-aware entropy-maximized active learning for machine-learned interatomic potentials

Pith reviewed 2026-05-21 07:04 UTC · model grok-4.3

classification ❄️ cond-mat.mtrl-sci
keywords active learninginteratomic potentialsentropy maximizationmachine learning potentialsmolecular dynamicsfingerprint selectionDFT dataconfiguration space
0
0 comments X

The pith

Entropy-driven active learning reduces energy errors in interatomic potentials by factors of 3 to 10 at 800 structures

A machine-rendered reading of the paper's core claim, the machinery that carries it, and where it could break.

The paper is trying to establish that an active learning strategy based on entropy maximization can generate more efficient training data for machine-learned interatomic potentials than standard random sampling does. It combines local entropy biasing in MD trajectories with global selection using the log-determinant of the fingerprint covariance matrix and dual covariance modes for different structure types. This produces training sets of a few hundred structures that achieve low errors on holdout data for covalent, metallic, and ionic materials. A sympathetic reader would care because it suggests a path to accurate potentials with far fewer expensive quantum mechanical calculations.

Core claim

By using per-configuration entropy to bias molecular dynamics trajectories and the log-determinant of the fingerprint covariance to filter for new information, with dual per-atom and per-config modes, the method generates training data that yields a factor of 3 to 10 lower energy mean absolute error at N=800 compared to random MD baselines on in-distribution tests for carbon, silicon, and NaCl.

What carries the argument

The dataset-aware entropy maximization procedure that pairs local trajectory biasing with global covariance log-determinant selection

If this is right

  • Achieves near-meV per atom accuracy with training sets of order 100 to 1000 structures.
  • Outperforms random MD sampling by factors of 3-10 in energy MAE at N=800 for covalent, metallic, and ionic bonded systems.
  • Handles pressure-driven phase transitions through broad coverage of configuration space.

Where Pith is reading between the lines

These are editorial extensions of the paper, not claims the author makes directly.

  • The method may enable rapid development of specialized potentials for unexplored materials by minimizing the number of required DFT calculations.
  • Similar entropy-based selection could apply to active learning in other scientific machine learning domains like molecular properties.
  • Further tests could check whether the gains persist for out-of-distribution predictions or much larger systems.

Load-bearing premise

The method assumes that maximizing local and global entropy measures will select configurations that add genuinely new and unbiased information to the training dataset.

What would settle it

Finding a material system or phase where the entropy-selected training set produces larger errors on holdout data than a random sample of the same size would indicate a failure to cover critical configuration space regions.

read the original abstract

We present an active learning framework for efficiently generating training data for machine-learned interatomic potentials (MLIPs). The method combines local entropy-driven molecular dynamics with global dataset-aware filtering: a per-configuration entropy term biases MD trajectories toward structurally diverse snapshots, while a global entropy measure, the log-determinant of the fingerprint covariance matrix of the entire dataset, selects only those configurations that provide genuinely new information. We employ dual covariance modes (per-atom for disordered structures and per-config for ordered phases) to achieve broad coverage of configuration space. Combined with a pre-trained foundation model (Allegro-OAM-L) and analytical fingerprint gradients from Gaussian overlap matrix eigenvalues, the framework produces high-quality domain-specific potentials with near- or sub-meV/atom accuracy on test data drawn from the same distribution at training-set sizes of order $10^{2}$ to $10^{3}$ entropy-selected DFT-labeled structures. We demonstrate the method on three systems spanning diverse bonding types and pressure-driven phase transitions: carbon (covalent), silicon (covalent/metallic), and NaCl (ionic). In learning curve comparisons against random molecular dynamics sampling at matched training set sizes ($N = 100$ to $800$), evaluated over three independent training-set draws per condition, entropy-driven sampling achieves a factor of approximately $3$ to $10$ lower energy MAE at $N = 800$ on in-distribution holdouts across the three systems, with the magnitude of the gain depending on the bonding type and the size at which the random-MD baseline saturates.

Editorial analysis

A structured set of objections, weighed in public.

Desk editor's note, referee report, simulated authors' rebuttal, and a circularity audit. Tearing a paper down is the easy half of reading it; the pith above is the substance, this is the friction.

Referee Report

2 major / 2 minor

Summary. The paper presents an active learning framework for ML interatomic potentials that integrates per-configuration entropy biasing in MD trajectories with global log-determinant selection on the fingerprint covariance matrix of the accumulating dataset. Dual covariance modes (per-atom for disordered structures, per-config for ordered phases) are used together with a pre-trained foundation model and analytical fingerprint gradients. On carbon, silicon, and NaCl, the method is reported to yield 3–10× lower energy MAE than random-MD sampling at matched training-set sizes N=100–800 (three independent draws), reaching near- or sub-meV/atom accuracy on in-distribution holdouts.

Significance. If the reported gains are robust and free of sampling bias, the approach would meaningfully reduce the number of expensive DFT labels needed to reach target accuracy for MLIPs, especially for systems with pressure-driven phase transitions. The combination of entropy-driven local sampling and dataset-aware global filtering, together with reuse of a foundation model, is a concrete strength that could be adopted more broadly if the central assumption about coverage of configuration space is verified.

major comments (2)
  1. Abstract: the headline claim of a factor of 3–10 lower energy MAE at N=800 rests on the unverified assumption that entropy biasing plus log-determinant selection will not systematically under-represent low-entropy but critical saddle-point or coexistence configurations in silicon and NaCl. The description of the dual covariance modes does not include an explicit check (e.g., order-parameter histograms or phase-coexistence sampling statistics) that such regions are adequately covered relative to a uniform random-MD baseline; without this, the observed MAE reduction on holdouts drawn from the same biased distribution does not yet demonstrate superior information gain for the intended MLIP use case.
  2. Results section (learning-curve comparisons): the abstract states that evaluations were performed over three independent training-set draws, yet no error bars, standard deviations, or statistical significance tests on the MAE ratios are mentioned. This omission makes it impossible to judge whether the reported factor-of-3–10 improvement is robust or could be explained by variance in the random-MD baseline.
minor comments (2)
  1. Abstract: the exact definitions of the per-atom and per-config fingerprint covariance matrices, the numerical value of the entropy temperature, and the precise form of the log-determinant selection criterion are not stated; these details are needed for reproducibility.
  2. The manuscript should clarify whether the holdout sets are drawn from the same entropy-biased trajectories or from independent uniform MD runs; the current wording leaves this ambiguous.

Simulated Author's Rebuttal

2 responses · 0 unresolved

We thank the referee for the detailed and constructive review. The comments highlight important aspects of validation and statistical reporting that will improve the clarity and robustness of our claims. We address each major comment below and outline the corresponding revisions.

read point-by-point responses
  1. Referee: Abstract: the headline claim of a factor of 3–10 lower energy MAE at N=800 rests on the unverified assumption that entropy biasing plus log-determinant selection will not systematically under-represent low-entropy but critical saddle-point or coexistence configurations in silicon and NaCl. The description of the dual covariance modes does not include an explicit check (e.g., order-parameter histograms or phase-coexistence sampling statistics) that such regions are adequately covered relative to a uniform random-MD baseline; without this, the observed MAE reduction on holdouts drawn from the same biased distribution does not yet demonstrate superior information gain for the intended MLIP use case.

    Authors: We agree that explicit verification of coverage for low-entropy critical regions strengthens the interpretation of the reported gains. Although the dual covariance modes and entropy biasing are designed to promote structural diversity, the original manuscript does not include order-parameter histograms or phase-coexistence sampling statistics. In the revised version we will add these analyses for silicon and NaCl, comparing the sampled distributions against the random-MD baseline to confirm that saddle-point and coexistence configurations are not systematically under-represented. revision: yes

  2. Referee: Results section (learning-curve comparisons): the abstract states that evaluations were performed over three independent training-set draws, yet no error bars, standard deviations, or statistical significance tests on the MAE ratios are mentioned. This omission makes it impossible to judge whether the reported factor-of-3–10 improvement is robust or could be explained by variance in the random-MD baseline.

    Authors: We acknowledge that the absence of error bars and statistical tests limits assessment of robustness. The three independent draws were performed, yet standard deviations and significance tests were not reported. In the revised manuscript we will include error bars on all learning curves, report the standard deviation of the MAE ratios across the three draws, and add a brief statistical comparison (e.g., paired t-test or Wilcoxon test) to quantify the significance of the observed improvements. revision: yes

Circularity Check

0 steps flagged

No significant circularity; empirical validation independent of inputs

full rationale

The paper presents an algorithmic framework for active learning in MLIPs that combines per-configuration entropy biasing of MD trajectories with global log-determinant selection on fingerprint covariance matrices (including dual per-atom/per-config modes). Performance is assessed via direct empirical learning-curve comparisons to random-MD baselines at fixed N=100–800, with MAE measured on in-distribution holdouts across three chemically distinct systems. No derivation reduces a claimed result to a fitted parameter or self-referential definition; the reported 3–10× MAE gains are outcomes of the sampling procedure rather than being forced by construction. No load-bearing self-citation chain or uniqueness theorem is invoked to justify the central claims. The framework is therefore self-contained against external benchmarks.

Axiom & Free-Parameter Ledger

0 free parameters · 1 axioms · 0 invented entities

The central claim rests on the unproven effectiveness of the entropy measures for selecting informative configurations and on the assumption that the pre-trained Allegro-OAM-L foundation model plus Gaussian overlap fingerprints provide a sufficiently rich representation; no free parameters are numerically specified in the abstract.

axioms (1)
  • domain assumption The per-configuration entropy term and global log-determinant of fingerprint covariance matrix reliably quantify structural novelty and information gain.
    Invoked throughout the method description as the basis for biasing MD and filtering snapshots.

pith-pipeline@v0.9.0 · 5813 in / 1423 out tokens · 60209 ms · 2026-05-21T07:04:47.113339+00:00 · methodology

discussion (0)

Sign in with ORCID, Apple, or X to comment. Anyone can read and Pith papers without signing in.

Lean theorems connected to this paper

Citations machine-checked in the Pith Canon. Every link opens the source theorem in the public Lean library.

What do these tags mean?
matches
The paper's claim is directly supported by a theorem in the formal canon.
supports
The theorem supports part of the paper's argument, but the paper may add assumptions or extra steps.
extends
The paper goes beyond the formal theorem; the theorem is a base layer rather than the whole result.
uses
The paper appears to rely on the theorem as machinery.
contradicts
The paper's claim conflicts with a theorem or certificate in the canon.
unclear
Pith found a possible connection, but the passage is too broad, indirect, or ambiguous to say the theorem truly supports the claim.

Reference graph

Works this paper leans on

53 extracted references · 53 canonical work pages

  1. [1]

    Behler, J.: Perspective: Machine learning potentials for atomistic simulations. J. Chem. Phys.145, 170201 (2016)

  2. [2]

    Deringer, V.L., Caro, M.A., Cs´ anyi, G.: Machine learning interatomic potentials as emerging tools for materials science. Adv. Mater.31, 1902765 (2019)

  3. [3]

    Unke, O.T., Chmiela, S., Sauceda, H.E., Gastegger, M., Poltavsky, I., Sch¨ utt, K.T., Tkatchenko, A., M¨ uller, K.-R.: Machine learning force fields. Chem. Rev. 121, 10142 (2021) 25

  4. [4]

    Behler, J., Parrinello, M.: Generalized neural-network representation of high- dimensional potential-energy surfaces. Phys. Rev. Lett.98, 146401 (2007)

  5. [5]

    Bart´ ok, A.P., Payne, M.C., Kondor, R., Cs´ anyi, G.: Gaussian approximation potentials: The accuracy of quantum mechanics, without the electrons. Phys. Rev. Lett.104, 136403 (2010)

  6. [6]

    Bart´ ok, A.P., Kondor, R., Cs´ anyi, G.: On representing chemical environments. Phys. Rev. B87, 184115 (2013)

  7. [7]

    Drautz, R.: Atomic cluster expansion for accurate and transferable interatomic potentials. Phys. Rev. B99, 014104 (2019)

  8. [8]

    Sch¨ utt, K.T., Sauceda, H.E., Kindermans, P.-J., Tkatchenko, A., M¨ uller, K.-R.: SchNet: A deep learning architecture for molecules and materials. J. Chem. Phys. 148, 241722 (2018)

  9. [9]

    Wang, H., Zhang, L., Han, J., E, W.: DeePMD-kit: A deep learning package for many-body potential energy representation and molecular dynamics. Comput. Phys. Commun.228, 178 (2018)

  10. [10]

    Batzner, S., Musaelian, A., Sun, L., Geiger, M., Mailoa, J.P., Kornbluth, M., Molinari, N., Smidt, T.E., Kozinsky, B.: E(3)-equivariant graph neural networks for data-efficient and accurate interatomic potentials. Nat. Commun.13, 2453 (2022)

  11. [11]

    In: Advances in Neural Information Processing Systems, vol

    Batatia, I., Kov´ acs, D.P., Simm, G.N.C., Ortner, C., Cs´ anyi, G.: MACE: Higher order equivariant message passing neural networks for fast and accurate force fields. In: Advances in Neural Information Processing Systems, vol. 35, p. 11423 (2022)

  12. [12]

    Musaelian, A., Batzner, S., Johansson, A., Sun, L., Owen, C.J., Kornbluth, M., Kozinsky, B.: Learning local equivariant representations for large-scale atomistic dynamics. Nat. Commun.14, 579 (2023)

  13. [13]

    Batatia, I., Benner, P., Chiang, Y., Elena, A.M., Kov´ acs, D.P., Riebesell, J., Advincula, X.R., Asta, M., Avaylon, M., Baldwin, W.J., et al.: A foundation model for atomistic materials chemistry (2024)

  14. [14]

    Deng, B., Zhong, P., Jun, K., Riebesell, J., Han, K., Bartel, C.J., Ceder, G.: CHGNet as a pretrained universal neural network potential for charge-informed atomistic modelling. Nat. Mach. Intell.5, 1031 (2023)

  15. [15]

    Yang, H., Hu, C., Zhou, Y., Liu, X., Shi, Y., Li, J., Li, G., Chen, Z., Chen, S., Zeni, C., Horton, M., Pinsler, R., Fowler, A., Z¨ ugner, D., Xie, T., Smith, J., Sun, L., Wang, Q., Kong, L., Liu, C., Hao, H., Lu, Z.: MatterSim: A deep learning atomistic model across elements, temperatures and pressures (2024) 26

  16. [16]

    Nature624, 80 (2023)

    Merchant, A., Batzner, S., Schoenholz, S.S., Aykol, M., Cheon, G., Cubuk, E.D.: Scaling deep learning for materials discovery. Nature624, 80 (2023)

  17. [17]

    Releases the Allegro-OAM-L foundation potential; pretrained on OMat24 and fine-tuned on MPtrj+sAlex

    Tan, C.W., Descoteaux, M.L., Kotak, M., Miranda Nascimento, G., Kavanagh, S.R., Zichi, L., Wang, M., Saluja, A., Hu, Y.R., Smidt, T., Johansson, A., Witt, W.C., Kozinsky, B., Musaelian, A.: High-performance training and inference for deep equivariant interatomic potentials. Releases the Allegro-OAM-L foundation potential; pretrained on OMat24 and fine-tun...

  18. [18]

    Karabin, M., Perez, D.: An entropy-maximization approach to automated training set generation for interatomic potentials. J. Chem. Phys.153, 094110 (2020)

  19. [19]

    Zhang, Y., Wang, H., Chen, W., Zeng, J., Zhang, L., Wang, H., E, W.: DP-GEN: A concurrent learning platform for the generation of reliable deep learning based potential energy models. Comput. Phys. Commun.253, 107206 (2020)

  20. [20]

    Schran, C., Brezina, K., Marsalek, O.: Committee neural network potentials con- trol generalization errors and enable active learning. J. Chem. Phys.153, 104105 (2020)

  21. [21]

    npj Comput

    Vandermause, J., Torrisi, S.B., Batzner, S., Xie, Y., Sun, L., Kolpak, A.M., Kozinsky, B.: On-the-fly active learning of interpretable Bayesian force fields for atomistic rare events. npj Comput. Mater.6, 20 (2020)

  22. [22]

    npj Comput

    Bernstein, N., Cs´ anyi, G., Deringer, V.L.: De novo exploration and self-guided learning of potential-energy surfaces. npj Comput. Mater.5, 99 (2019)

  23. [23]

    Kulichenko, M., Barros, K., Lubbers, N., Li, Y.W., Messerly, R., Tretiak, S., Smith, J.S., Nebgen, B.: Uncertainty-driven dynamics for active learning of interatomic potentials. Nat. Comput. Sci.4, 29 (2024)

  24. [24]

    Podryabinkin, E.V., Shapeev, A.V.: Active learning of linearly parametrized interatomic potentials. Comput. Mater. Sci.140, 171 (2017)

  25. [25]

    Multiscale Model

    Shapeev, A.V.: Moment tensor potentials: A class of systematically improvable interatomic potentials. Multiscale Model. Simul.14, 1153 (2016)

  26. [26]

    Zhu, L., Amsler, M., Fuhrer, T., Schaefer, B., Faraji, S., Rostami, S., Ghasemi, S.A., Sadeghi, A., Grauzinyte, M., Wolverton, C., Goedecker, S.: A fingerprint based metric for measuring similarities of crystalline structures. J. Chem. Phys. 144, 034203 (2016)

  27. [27]

    npj Comput

    Subramanyam, A.P.A., Perez, D.: Information-maximization based active learn- ing of interatomic potentials. npj Comput. Mater.11, 218 (2025)

  28. [28]

    Barroso-Luque, L., Shuaibi, M., Fu, X., Wood, B.M., Dzamba, M., Gao, M., Rizvi, A., Zitnick, C.L., Ulissi, Z.W.: Open Materials 2024 (OMat24) inorganic 27 materials dataset and models (2024)

  29. [29]

    Bussi, G., Donadio, D., Parrinello, M.: Canonical sampling through velocity rescaling. J. Chem. Phys.126, 014101 (2007)

  30. [30]

    Hjorth Larsen, A., Jørgen Mortensen, J., Blomqvist, J., Castelli, I.E., Christensen, R., Du lak, M., Friis, J., Groves, M.N., Hammer, B., Hargus, C., Hermes, E.D., Jennings, P.C., Bjerre Jensen, P., Kermode, J., Kitchin, J.R., Leonhard Kolsbjerg, E., Kubal, J., Kaasbjerg, K., Lysgaard, S., Bergmann Maronsson, J., Maxson, T., Olsen, T., Pastewka, L., Peter...

  31. [31]

    Liu, D.C., Nocedal, J.: On the limited memory BFGS method for large scale optimization. Math. Program.45, 503 (1989)

  32. [32]

    Kresse, G., Furthm¨ uller, J.: Efficient iterative schemes forab initiototal-energy calculations using a plane-wave basis set. Phys. Rev. B54, 11169 (1996)

  33. [33]

    Kresse, G., Furthm¨ uller, J.: Efficiency of ab-initio total energy calculations for metals and semiconductors using a plane-wave basis set. Comput. Mater. Sci.6, 15 (1996)

  34. [34]

    Bl¨ ochl, P.E.: Projector augmented-wave method. Phys. Rev. B50, 17953 (1994)

  35. [35]

    Kresse, G., Joubert, D.: From ultrasoft pseudopotentials to the projector augmented-wave method. Phys. Rev. B59, 1758 (1999)

  36. [36]

    Furness, J.W., Kaplan, A.D., Ning, J., Perdew, J.P., Sun, J.: Accurate and numer- ically efficient r2SCAN meta-generalized gradient approximation. J. Phys. Chem. Lett.11, 8208 (2020)

  37. [37]

    Sun, J., Ruzsinszky, A., Perdew, J.P.: Strongly constrained and appropriately normed semilocal density functional. Phys. Rev. Lett.115, 036402 (2015)

  38. [38]

    Sabatini, R., Gorni, T., Gironcoli, S.: Nonlocal van der Waals density functional made simple and efficient. Phys. Rev. B87, 041108 (2013)

  39. [39]

    Vydrov, O.A., Van Voorhis, T.: Nonlocal van der Waals density functional: The simpler the better. J. Chem. Phys.133, 244103 (2010)

  40. [40]

    Ning, J., Kothakonda, M., Furness, J.W., Kaplan, A.D., Ehlert, S., Brandenburg, J.G., Perdew, J.P., Sun, J.: Workhorse minimally empirical dispersion-corrected density functional with tests for weakly bound systems: r 2SCAN+rVV10. Phys. Rev. B106, 075422 (2022)

  41. [41]

    Peng, H., Yang, Z.-H., Perdew, J.P., Sun, J.: Versatile van der Waals density 28 functional based on a meta-generalized gradient approximation. Phys. Rev. X6, 041005 (2016)

  42. [42]

    Perdew, J.P., Burke, K., Ernzerhof, M.: Generalized gradient approximation made simple. Phys. Rev. Lett.77, 3865 (1996)

  43. [43]

    Published as a conference paper at ICLR 2015

    Kingma, D.P., Ba, J.: Adam: A method for stochastic optimization. Published as a conference paper at ICLR 2015. (2014)

  44. [44]

    Huber, P.J.: Robust estimation of a location parameter. Ann. Math. Stat.35, 73 (1964)

  45. [45]

    APL Mater.1, 011002 (2013)

    Jain, A., Ong, S.P., Hautier, G., Chen, W., Richards, W.D., Dacek, S., Cholia, S., Gunter, D., Skinner, D., Ceder, G., Persson, K.A.: Commentary: The Materials Project: A materials genome approach to accelerating materials innovation. APL Mater.1, 011002 (2013)

  46. [46]

    Nature214, 587 (1967)

    Frondel, C., Marvin, U.B.: Lonsdaleite, a hexagonal polymorph of diamond. Nature214, 587 (1967)

  47. [47]

    Li, Q., Ma, Y., Oganov, A.R., Wang, H., Wang, H., Xu, Y., Cui, T., Mao, H.- K., Zou, G.: Superhard monoclinic polymorph of carbon. Phys. Rev. Lett.102, 175506 (2009)

  48. [48]

    Togo, A., Tanaka, I.: First principles phonon calculations in materials science. Scr. Mater.108, 1 (2015)

  49. [49]

    Togo, A., Chaput, L., Tadano, T., Tanaka, I.: Implementation strategies in phonopy and phono3py. J. Phys. Condens. Matter35, 353001 (2023)

  50. [50]

    Warren, J.L., Yarnell, J.L., Dolling, G., Cowley, R.A.: Lattice dynamics of diamond. Phys. Rev.158, 805 (1967)

  51. [51]

    Solin, S.A., Ramdas, A.K.: Raman spectrum of diamond. Phys. Rev. B1, 1687 (1970)

  52. [52]

    Leb` egue, S., Harl, J., Gould, T.,´Angy´ an, J.G., Kresse, G., Dobson, J.F.: Cohesive properties and asymptotics of the dispersion interaction in graphite by the random phase approximation. Phys. Rev. Lett.105, 196401 (2010)

  53. [53]

    Kotliar, G., Savrasov, S.Y., Haule, K., Oudovenko, V.S., Parcollet, O., Marianetti, C.A.: Electronic structure calculations with dynamical mean-field theory. Rev. Mod. Phys.78, 865 (2006) 29