Pith. sign in

REVIEW 3 major objections 5 minor 43 references

Segmental Dynamics in the Strain-hardening Regime for Poly(methyl methacrylate) Glasses with and without Melt-stretching

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

Challenge this review Re-run · record.json Download PDF Read on arXiv ↗ Review JSON

Pith's one-line read Segmental dynamics accelerate during strain-hardening of PMMA glasses.

desk verdict First systematic data on segmental dynamics deep in strain-hardening, but the headline acceleration at fixed true strain rate is likely a kinematic artifact of the engineering-strain-rate collapse. read the letter →

arxiv 2608.07330 v1 pith:HXWP7V5U submitted 2026-08-07 cond-mat.soft cond-mat.mtrl-sci

Enran Xing , Trevor Bennin , Masoud Razavi , M. D. Ediger This is my paper · ORCID
classification cond-mat.softcond-mat.mtrl-sci
keywords segmentaldynamicsstrain-hardeningpolymerglassesPMMAphotobleachingtruestrainratemelt-stretchingplasticdeformation
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 direct measurements of segmental relaxation times in lightly-crosslinked poly(methyl methacrylate) (PMMA) glasses deformed deep into the strain-hardening regime. Using a photobleaching probe-reorientation technique, the authors find that, at a given true strain rate, segmental dynamics accelerate as strain grows into the deep strain-hardening regime, reaching about 0.15 decade (roughly 40%) faster at a true strain of 0.8. Melt-stretched samples show more prominent strain-hardening and segmental dynamics about 12% faster at one temperature than quenched samples. The result supports a kinetic, friction-based picture of strain-hardening and contradicts a nonlinear-Langevin-equation-based theory that predicted slower segmental dynamics in this regime.

What carries the argument

The central object is the segmental relaxation time $\tau_{seg}$, measured by photobleaching: a polarized laser selectively bleaches aligned fluorescent probes, and the decay of optical anisotropy is fitted with a stretched exponential to extract $\tau_{seg}$. The mechanical analysis uses local strain tracking from photobleached line patterns to compute local engineering and true strain rates. The argument's key comparison is a log-log plot of $\tau_{seg}$ versus true strain rate, where the difference between early post-yield ($\varepsilon_{eng}<30\%$) and deep strain-hardening ($\varepsilon_{eng}>30\%$) bins reveals whether dynamics change at fixed true strain rate.

What would settle it

Perform the same photobleaching measurement in a deformation where the local true strain rate is actively held constant through the strain-hardening regime; if the log $\tau_{seg}$ versus true strain rate curve for deep hardening then overlaps the early post-yield line, the claimed acceleration is a history effect rather than a strain-hardening effect.

Watch

Extended reading notes

Core claim

The central claim is that strain-hardening in PMMA glasses is accompanied by an acceleration, not a deceleration, of segmental dynamics. When the local true strain rate is held as the comparison variable, relaxation times in the deep strain-hardening regime (local engineering strain above 30%) fall below the extrapolated early post-yield line by up to 0.15 decade at a true strain near 0.8. When engineering strain rate is used instead, deep-hardening data lie on the same line as early post-yield data, indicating that true strain rate is the more fundamental variable. Melt-stretched samples, which harden more strongly, show slightly faster segmental dynamics, and the size of the acceleration matches published bead-spring simulations.

Load-bearing premise

The analysis assumes that segmental dynamics depend only on the current local strain rate and strain, not on the deformation history, even though the experiments were run at constant global engineering strain rate so the local true strain rate changed throughout.

Editorial extensions

If this is right

  • At a fixed true strain rate, segmental mobility in a glassy polymer increases during strain-hardening, implying that the hardening stress and the molecular mobility are coupled.
  • The measured acceleration of about 0.15 decade at 0.8 true strain matches bead-spring simulations, giving experimental support to the friction-based mechanism of strain-hardening.
  • Melt-stretching, which enhances strain-hardening, also produces slightly faster segmental dynamics, so processing history and hardening strength can be read through segmental mobility.
  • The nonlinear-Langevin-equation prediction of slowed segmental dynamics during constant-true-strain-rate hardening is not supported by these experiments at the strains and rates studied.
  • When compared at the same engineering strain rate, early and deep hardening data fall on a single line, indicating that the apparent acceleration is specific to the true-strain-rate comparison.

Reading between the lines

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

  • If the history-independence assumption holds, $\tau_{seg}$ can be treated as a state function of local true strain rate and strain, which would let constitutive models incorporate segmental mobility as an internal variable without tracking the full deformation path.
  • A stricter test would be a feedback-controlled constant-true-strain-rate deformation; if the downward shift disappears under that protocol, the observed acceleration is an artifact of the varying strain-rate path rather than strain-hardening itself.
  • The melt-stretched versus quenched comparison suggests that pre-orientation leaves a memory that modifies post-yield mobility; varying the melt-stretching ratio systematically could map how much of the mobility boost comes from chain orientation versus increased hardening stress.
Share X Bluesky LinkedIn Reddit HN

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 paper reports photobleaching measurements of probe reorientation times (as a proxy for segmental dynamics) in lightly crosslinked PMMA glasses deformed in tension into the strain-hardening regime, at Tg−23 K and Tg−33 K. Samples were either quenched from the melt or melt-stretched before quenching. The authors report two main findings: (1) at a fixed local engineering strain rate, segmental dynamics are essentially identical for quenched samples just beyond yield and deep in the strain-hardening regime, while melt-stretched samples show about 0.05 decade faster dynamics at one of the two temperatures; (2) when the same data are plotted against local true strain rate, the deep-strain-hardening data appear accelerated by up to 0.15 decade relative to the early post-yield baseline at the same true strain rate. The paper interprets this as evidence that segmental mobility increases during strain-hardening under constant true strain rate, in qualitative agreement with simulations by Rottler and by Hoy and Robbins, and in contrast to the NLE theory prediction of deceleration.

Significance. If the central claim were established, it would provide much-needed experimental data on a controversial point: whether segmental dynamics accelerate or decelerate during strain-hardening in polymer glasses at constant true strain rate. The measurements are original, the sample preparation and photobleaching methodology are carefully described, and the authors are transparent about the key assumption of history independence. The comparison with simulations and with the NLE theory is a useful contribution. However, as detailed below, the central claim rests on an untested coordinate choice, and the paper currently overstates the level of support for the true-strain-rate interpretation.

major comments (3)
  1. [Results, Fig. 3 and Fig. 4; Discussion, first paragraph] The central claim that segmental dynamics accelerate at fixed true strain rate is not directly measured and is potentially an artifact of the coordinate transformation. The experiments are run at constant global engineering strain rate, and the local true strain rate decreases during each deformation because ε_true = ln(1+ε_eng) implies dε_true/dt = (dε_eng/dt)/(1+ε_eng). The data in Fig. 3 are described by a single master line in engineering strain rate for both the early post-yield and deep strain-hardening regimes. When the same data are replotted against true strain rate, every point shifts to the left by log(1+ε_eng); with the measured slope B ≈ −0.8 to −0.9, this shift alone produces an apparent downward displacement of the deep-hardening points by roughly 0.2–0.3 decade at true strain 0.8, comparable to or larger than the claimed 0.15 decade. The explicit history-independence assumption in the Discussion does not resolve which strain-rate measure controls segmental dynamics; Fig. 3 in fact suggests that engineering strain rate is the better variable. The authors should either (a) demonstrate that the residuals from the engineering-rate master line are statistically significant and correlated with strain, or (b) perform or cite experiments at controlled true strain rate, or (c) explicitly reframe the true-strain-rate comparison as model-dependent. Without this, the abstract's statement that 'our observations are in agreement with previously published simulation results' overstates the support.
  2. [Results, Fig. 5 and Discussion] The deviation plotted in Fig. 5 is computed relative to a baseline fitted to early post-yield data in true strain rate, but both the baseline and the deep-hardening points are derived from the same raw time series in which the local true strain rate varies. As a result, the deviation is not an independent measurement of a constant-true-strain-rate comparison. The paper should quantify the uncertainty in this deviation, including the effect of the choice of the early post-yield strain window (15–30%) and the propagation of strain-rate uncertainty into the horizontal coordinate. Currently, the error bars in Fig. 5 appear to come only from the relaxation-time scatter, not from the uncertainty in the true strain rate or from the baseline fit. The conclusion that experiments 'support' the Rottler simulation should be softened unless the deviation is shown to be inconsistent with the pure kinematic shift.
  3. [Results, Fig. 3; Abstract] The finding that melt-stretched samples have faster segmental dynamics by about 0.05 decade (which the abstract quotes as 'about 15%') is observed at Tg−33K but is not statistically significant at Tg−23K, as the text acknowledges. The abstract and conclusion should qualify this claim by temperature, rather than presenting it as a general result for melt-stretched PMMA glasses.
minor comments (5)
  1. [Methods, Photobleaching technique] The symbol τ_seg is introduced in the text but not defined explicitly before the KWW equation; the definition should be included with the fit equation.
  2. [Figure 1 caption and text] The strain rates in Fig. 1 are 2.7×10^-5 s^-1 (quenched) and 3.1×10^-5 s^-1 (melt-stretched); the figure caption and the text should be consistent on whether these are global or local engineering strain rates.
  3. [Figure 2b] The units in the text '10-4.5s to 10-4.2s' should read '10^-4.5 s^-1 to 10^-4.2 s^-1'; there are several missing superscripts and slashes in the manuscript.
  4. [Discussion, second paragraph] The phrase 'In Fig. 4 of our work, we find qualitative agreement with this result' is ambiguous; the authors mean the experimental data, not the figure number, and should rephrase.
  5. [Conclusion] The conclusion states that the experiments show acceleration 'under a constant true strain rate', but the experiments were performed at constant global engineering strain rate; this overstatement should be corrected.

Circularity Check

0 steps flagged · score 0.0 of 10

No significant circularity: the central claim is a direct experimental comparison against external simulations, and the fitted lines are descriptive baselines rather than inputs that force the conclusion.

full rationale

The paper's central result is that, at a given true strain rate, segmental dynamics in the deep strain-hardening regime are faster than just beyond yield by up to 0.15 decade (Figs. 4 and 5). This is obtained from direct photobleaching measurements of probe reorientation times, which have been previously validated as a segmental-dynamics reporter (Ref. 38, external to the authors' own method-development work). The linear fits in Figs. 3 and 4 are descriptive summaries of the measured log(τseg) versus log(strain rate) data; the deep strain-hardening deviation is quantified by comparing independently measured relaxation times to the early post-yield fitted line, not by constructing the result from fitted parameters. The comparison in Fig. 5 uses an external simulation, Rottler (Ref. 27), not a self-citation, and the Hoy-Robbins simulations (Refs. 25-26) are likewise external. Self-citations to Refs. 4, 15, 16, 33, 34, and 38 establish the photobleaching technique and previous post-yield behavior; these are methodological and are not used as the load-bearing justification for the strain-hardening acceleration claim. The paper explicitly flags its most fragile assumption in the first paragraph of the Discussion: "we assume that the segmental dynamics do not depend on the precise history of the deformation protocol." This is a stated limitation on the inference that local strain rate is the controlling variable, and the paper also notes that the choice of engineering strain rate as abscissa is "convenient but arbitrary" while true strain rate is asserted to be "the more fundamental parameter." Those assertions may be debatable, and the history-independence assumption is a legitimate correctness risk, but they do not amount to circularity: the conclusion is not equivalent to an input by definition, and no fitted parameter is renamed as a prediction. The measured acceleration is compared against an external simulation and against a competing theory's prediction, so the derivation chain is self-contained and independently checkable.

Assumptions & free parameters 2 free parameters · 3 assumptions · 0 invented entities

No invented entities are introduced. The central claim rests on two fitted baseline slopes and the explicit history-independence assumption. The probe-reorientation assumption is standard and previously validated.

free parameters (2)
  • Early post-yield baseline slope, log(tau_seg) vs log(true strain rate), Tg-33K = -0.91 ± 0.05
    Fit to quenched-sample data at εeng<30% (Fig. 4). Used as the reference to compute the deviation/acceleration in Fig. 5; the 40% acceleration claim depends on extrapolating this line.
  • Early post-yield baseline slope, log(tau_seg) vs log(true strain rate), Tg-23K = -0.79 ± 0.10
    Same role as above for the Tg-23K dataset used in Fig. 4 and Fig. 5.
assumptions (3)
  • ad hoc to paper Segmental dynamics are independent of deformation history; a slowly time-varying local strain rate gives the same tau_seg as a constant strain rate at the same instantaneous value.
    Stated in Discussion, first paragraph: 'we assume that the segmental dynamics do not depend on the precise history of the deformation protocol.' Required to convert constant-global-rate data into a claim about constant true strain rate behavior.
  • domain assumption Probe reorientation time of DPPC reports the segmental relaxation time in PMMA.
    Methods, photobleaching technique, cites ref 38 (Ricci et al.) for validation. This is a standard assumption in this group's prior work.
  • domain assumption During tensile deformation, the contraction ratio along the z-axis equals that along the y-axis, so true stress uses R^2.
    Methods: 'the contraction along the y-axis and z-axis was assumed to be identical.' Affects stress reporting, not the segmental dynamics measurements directly.

how reviews work

0 comments
Cite this review

Pith. "Pith review of Segmental Dynamics in the Strain-hardening Regime for Poly(methyl methacrylate) Glasses with and without Melt-stretching." pith.science (2026). https://pith.science/paper/HXWP7V5U

@misc{pith2026260807330,
  author       = {Pith},
  title        = {Pith review of: Segmental Dynamics in the Strain-hardening Regime for Poly(methyl methacrylate) Glasses with and without Melt-stretching},
  year         = {2026},
  howpublished = {\url{https://pith.science/paper/HXWP7V5U}},
  note         = {Machine review of arXiv:2608.07330}
}
read the original abstract

Strain-hardening is a feature of polymer glasses during large deformation, which helps to stabilize the glasses against breakage. Experimentally, little is known about the segmental dynamics during strain-hardening, and such data is important for building a molecular-level theory of polymer glasses deformed in this regime. Here, using a photobleaching technique, we measured the segmental dynamics of lightly-crosslinked poly(methyl methacrylate) (PMMA) glasses with and without melt-stretching, which were deformed into the strain-hardening regime with local engineering strain rates from 10^-4.6 s^-1 to 10^-4 s^-1 at Tg-23K and Tg-33K. We find that melt-stretched PMMA glasses show a more prominent strain-hardening feature and faster segmental dynamics by a factor of about 15% compared to PMMA without melt-stretching. At a given true strain rate, the segmental dynamics of PMMA without melt-stretching are accelerated in the deep strain-hardening regime from the value just beyond yield, by up to 40% at 0.8 true strain. Our observations are in agreement with previously published simulation results.

Figures

Figures reproduced from arXiv: 2608.07330 by the authors.

Figure 1
Figure 1. Mechanical behavior of quenched and melt [PITH_FULL_IMAGE:figures/full_fig_p010_1.png] view at source ↗
Figure 2
Figure 2. The evolution of segmental dynamics and local strain rates for a quenched [PITH_FULL_IMAGE:figures/full_fig_p013_2.png] view at source ↗
Figure 3
Figure 3. Segmental relaxation times as a function of local engineering strain rate for the quenched and the melt-stretched PMMA glasses in the post-yield regime. Engineering strain rate is correlated closely with segmental dynamics even when the engineering strain approaches 100%. For both types of samples, the results are well described by linear fitting. The solid lines are fittings to the data of quenched samples, includi… view at source ↗
Figures from the paper (2 more)
Figure 4
Figure 4. Figure 4: Segmental relaxation times for the quenched PMMA glasses in the early post-yield regime (εeng<30%) and the deep strain-hardening regime (εeng>30%) with respect to local true strain rate. Each type of open symbol represents one deformation that has reached εeng>30%, and…
Figure 5
Figure 5. Figure 5: Deviation of log(τseg/s) for PMMA glasses deformed into the deep strain-hardening regime (εeng>30%) relative to small strain data at the same true strain rate. The dotted line shows the simulation result from Rottler27, which is the deviation of the relaxation time fro…

Discussion (0). Continue with ORCID to comment.

Reference graph

Works this paper leans on

43 extracted references · 43 canonical work pages

  1. [1]

    van Breemen, L. C. A.; Engels, T. A. P.; Klompen, E. T. J.; Senden, D. J. A.; Govaert, L. E., Rate- and temperature-dependent strain softening in solid polymers. Journal of Polymer Science Part B: Polymer Physics 2012, 50 (24), 1757-1771

    work page 2012

  2. [2]

    I., A correlation between critical tensile strength and polymer cross-sectional area

    Vincent, P. I., A correlation between critical tensile strength and polymer cross-sectional area. Polymer 1972, 13, 558-560

    work page 1972

  3. [3]

    Meijer, H. E. H.; Govaert, L. E., Mechanical performance of polymer systems: The relation between structure and properties. Progress in Polymer Science 2005, 30, 915-938

    work page 2005

  4. [4]

    D., Measurement of Segmental Mobility during Constant Strain Rate Deformation of a Poly(methyl methacrylate) Glass

    Bending, B.; Christison, K.; Ricci, J.; Ediger, M. D., Measurement of Segmental Mobility during Constant Strain Rate Deformation of a Poly(methyl methacrylate) Glass. Macromolecules 2014, 47 (2), 800-806. 25

    work page 2014

  5. [5]

    V.; Balabaev, N

    Lyulin, A. V.; Balabaev, N. K.; Mazo, M. A.; Michels, M. A. J., Molecular Dynamics Simulation of Uniaxial Deformation of Glassy Amorphous Atactic Polystyrene. Macromolecules 2004, 37, 8785-8793

    work page 2004

  6. [6]

    A.; Toepperwein, G

    Riggleman, R. A.; Toepperwein, G. N.; Papakonstantopoulos, G. J.; de Pablo, J. J., Dynamics of a Glassy Polymer Nanocomposite during Active Deformation. Macromolecules 2009, 42, 3632-3640

    work page 2009

  7. [7]

    Liu, A. Y. H.; Rottler, J., Aging under stress in polymer glasses. Soft Matter 2010, 6 (19), 4858-4862

    work page 2010

  8. [8]

    J Chem Phys 2016, 145, 064505

    Rottler, J., Relaxation times in deformed polymer glasses: A comparison between molecular simulations and two theories. J Chem Phys 2016, 145, 064505

    work page 2016

Show all 43 references
  1. [9]

    Phys Rev Lett 2010, 104 (20), 205501

    Warren, M.; Rottler, J., Microscopic view of accelerated dynamics in deformed polymer glasses. Phys Rev Lett 2010, 104 (20), 205501

    2010

  2. [10]

    S., Microscopic Constitutive Equation Theory for the Nonlinear Mechanical Response of Polymer Glasses

    Chen, K.; Schweizer, K. S., Microscopic Constitutive Equation Theory for the Nonlinear Mechanical Response of Polymer Glasses. Macromolecules 2008, 41, 5908-5918

    2008

  3. [11]

    S., Theory of Yielding, Strain Softening, and Steady Plastic Flow in Polymer Glasses under Constant Strain Rate Deformation

    Chen, K.; Schweizer, K. S., Theory of Yielding, Strain Softening, and Steady Plastic Flow in Polymer Glasses under Constant Strain Rate Deformation. Macromolecules 2011, 44 (10), 3988-4000

    2011

  4. [12]

    B.; Chambers, R

    Adolf, D. B.; Chambers, R. S.; Caruthers, J. M., Extensive validation of a thermodynamically consistent, nonlinear viscoelastic model for glassy polymers. Polymer 2004, 45 (13), 4599-4621

    2004

  5. [13]

    A.; Caruthers, J

    Medvedev, G. A.; Caruthers, J. M., Development of a stochastic constitutive model for prediction of postyield softening in glassy polymers. Journal of Rheology 2013, 57 (3), 949- 1002. 26

    2013

  6. [14]

    M.; Medvedev, G

    Caruthers, J. M.; Medvedev, G. A., A Comparison of Constitutive Descriptions of the Thermo-Mechanical Behavior of Polymeric Glasses. In Polymer Glasses, Roth, C. B., Ed. CRC Press: Boca Raton, 2017

    2017

  7. [15]

    D., Enhanced Segmental Dynamics of Poly(lactic acid) Glasses during Constant Strain Rate Deformation

    Bennin, T.; Ricci, J.; Ediger, M. D., Enhanced Segmental Dynamics of Poly(lactic acid) Glasses during Constant Strain Rate Deformation. Macromolecules 2019, 52 (17), 6428-6437

    2019

  8. [16]

    D., Effect of Temperature on Postyield Segmental Dynamics of Poly(methyl methacrylate) Glasses: Thermally Activated Transitions Are Important

    Hebert, K.; Bending, B.; Ricci, J.; Ediger, M. D., Effect of Temperature on Postyield Segmental Dynamics of Poly(methyl methacrylate) Glasses: Thermally Activated Transitions Are Important. Macromolecules 2015, 48 (18), 6736-6744

    2015

  9. [17]

    N.; Thackray, G., The use of a mathematical model to describe isothermal stress-strain curves in glassy theromplastics

    Haward, R. N.; Thackray, G., The use of a mathematical model to describe isothermal stress-strain curves in glassy theromplastics. Proc. Roy. Soc. A. 1968, 302, 453-472

    1968

  10. [18]

    N., Strain hardening of thermoplastics

    Haward, R. N., Strain hardening of thermoplastics. Macromolecules 1993, 26, 5860- 5869

    1993

  11. [19]

    C.; Arruda, E

    Boyce, M. C.; Arruda, E. M., An Experimental and Analytical Investigation of the Large Strain Compressive and Tensile Response of Glassy Polymers. Polymer Engineering and Science 1990, 30 (20), 1288-1298

    1990

  12. [20]

    A.; van Beek, J

    Wendlandt, M.; Tervoort, T. A.; van Beek, J. D.; Suter, U. W., Segmental orientation in plastically deformed glassy PMMA. Journal of the Mechanics and Physics of Solids 2006, 54 (3), 589-610

    2006

  13. [21]

    C.; Lodge, T

    Hiemenz, P. C.; Lodge, T. P., Polymer Chemistry. 2nd ed.; CRC Press: Boca Raton, 2007

    2007

  14. [22]

    J., Open questions in the physics of deformation of polymer glasses

    Kramer, E. J., Open questions in the physics of deformation of polymer glasses. Journal of Polymer Science Part B: Polymer Physics 2005, 43 (23), 3369-3371. 27

    2005

  15. [23]

    van Melick, H. G. H.; Govaert, L. E.; Meijer, H. E. H., On the origin of strain hardening in glassy polymers. Polymer 2003, 44 (8), 2493-2502

    2003

  16. [24]

    S.; Robbins, M

    Hoy, R. S.; Robbins, M. O., Strain hardening of polymer glasses: Effect of entanglement density, temperature, and rate. Journal of Polymer Science Part B: Polymer Physics 2006, 44 (24), 3487-3500

    2006

  17. [25]

    S.; Robbins, M

    Hoy, R. S.; Robbins, M. O., Strain hardening in polymer glasses: limitations of network models. Phys Rev Lett 2007, 99 (11), 117801

    2007

  18. [26]

    S.; Robbins, M

    Hoy, R. S.; Robbins, M. O., Strain hardening of polymer glasses: Entanglements, energetics, and plasticity. Phys Rev E 2008, 77, 031801

    2008

  19. [27]

    Phys Rev E 2018, 98 (1-1), 010501

    Rottler, J., Molecular mobility in driven monomeric and polymeric glasses. Phys Rev E 2018, 98 (1-1), 010501

    2018

  20. [28]

    V.; Michels, M

    Vorselaars, B.; Lyulin, A. V.; Michels, M. A. J., Microscopic Mechanisms of Strain Hardening in Glassy Polymers. Macromolecules 2009, 42 (15), 5829-5842

    2009

  21. [29]

    S., Suppressed segmental relaxation as the origin of strain hardening in polymer glasses

    Chen, K.; Schweizer, K. S., Suppressed segmental relaxation as the origin of strain hardening in polymer glasses. Phys Rev Lett 2009, 102 (3), 038301

    2009

  22. [30]

    H.; Andrews, R

    Ender, D. H.; Andrews, R. D., Cold Drawing of Glassy Polystyrene under Dead Load. Journal of Applied Physics 1965, 36 (10), 3057-3062

    1965

  23. [31]

    Journal of Applied Polymer Sciences 1978, 22, 1619-1630

    Tanabe, Y.; Kanetsuna, H., Structure of Oriented Polystyrene Monofilaments and Its Relationship to Brittle-to-Ductile Transition. Journal of Applied Polymer Sciences 1978, 22, 1619-1630

    1978

  24. [32]

    D.; Cheng, S.; Li, X.; Lin, F.; Becker, M

    Zartman, G. D.; Cheng, S.; Li, X.; Lin, F.; Becker, M. L.; Wang, S.-Q., How Melt- Stretching Affects Mechanical Behavior of Polymer Glasses. Macromolecules 2012, 45 (16), 6719-6732. 28

    2012

  25. [33]

    N.; Paeng, K.; Swallen, S

    Lee, H. N.; Paeng, K.; Swallen, S. F.; Ediger, M. D., Direct Measurement of Molecular Mobility in Actively Deformed Polymer Glasses. Science 2009, 323, 231-234

    2009

  26. [34]

    N.; Paeng, K.; Swallen, S

    Lee, H. N.; Paeng, K.; Swallen, S. F.; Ediger, M. D., Dye reorientation as a probe of stress-induced mobility in polymer glasses. J Chem Phys 2008, 128 (13), 134902

    2008

  27. [35]

    N.; Paeng, K.; Swallen, S

    Lee, H. N.; Paeng, K.; Swallen, S. F.; Ediger, M. D.; Stamm, R. A.; Medvedev, G. A.; Caruthers, J. M., Molecular mobility of poly(methyl methacrylate) glass during uniaxial tensile creep deformation. Journal of Polymer Science Part B: Polymer Physics 2009, 47 (17), 1713- 1727

    2009

  28. [36]

    N.; Riggleman, R

    Lee, H. N.; Riggleman, R. A.; de Pablo, J. J.; Ediger, M. D., Deformation-Induced Mobility in Polymer Glasses during Multistep Creep Experiments and Simulations. Macromolecules 2009, 42 (12), 4328-4336

    2009

  29. [37]

    N.; Ediger, M

    Lee, H. N.; Ediger, M. D., Mechanical Rejuvenation in Poly(methyl methacrylate) Glasses? Molecular Mobility after Deformation. Macromolecules 2010, 43 (13), 5863-5873

    2010

  30. [38]

    D., Direct Comparison of Probe Reorientation and Linear Mechanical Measurements of Segmental Dynamics in Glassy Poly(methyl methacrylate)

    Ricci, J.; Bennin, T.; Ediger, M. D., Direct Comparison of Probe Reorientation and Linear Mechanical Measurements of Segmental Dynamics in Glassy Poly(methyl methacrylate). Macromolecules 2018, 51 (19), 7785-7793

    2018

  31. [39]

    T.; Schweizer, K

    Oyerokun, F. T.; Schweizer, K. S., Microscopic theory of rubber elasticity. J Chem Phys 2004, 120 (19), 9359-9370. 29 For Table of Contents Only: The editors may adjust the size of this figure as they see fit. 1 SUPPLEMENTAL INFORMATION Segmental Dynamics in the Strain-hardeni...

    2004

  32. [40]

    S1, we see that the strain-hardening modulus is largely independent of the strain rate for both types of PMMA glasses, for the range of strain rates utilized in this work

    Strain-hardening moduli for the quenched and the melt-stretched PMMA glasses In Fig. S1, we see that the strain-hardening modulus is largely independent of the strain rate for both types of PMMA glasses, for the range of strain rates utilized in this work. The strain- hardenin...

  33. [41]

    S2 illustrates the β behavior during the deformation shown in Fig

    Evolution of the KWW β parameter during a deformation deep into the strain-hardening regime Fig. S2 illustrates the β behavior during the deformation shown in Fig. 2. In support of the text in the main manuscript, we can see that β doesn’t evolve significantly after the deform...

  34. [42]

    error bars

    Role of engineering strain rate In relation to Fig. 3 in the main text, the comparison between the fitted lines for quenched sample data in the early post-yield regime (εeng<30%) and over the entire strain range is shown in Fig. S3. These fitted lines almost overlap with each ...

  35. [43]

    error bars

    Role of true strain rate In Fig. S5, similar to the case of the engineering strain rate, “error bars” estimated based on the standard deviations of log(𝜀̇𝑡𝑟𝑢𝑒/s-1) and log(τseg/s) are added to the data of Fig. 4. 5 Figure S5. Same as Fig. 4, with bars added indicating the aver...

Pith tools

Reviewed August 10, 2026 · model on record in the stance chip above.