Pith. sign in

REVIEW 4 major objections 4 minor 97 references

LAOStrain response of carbon black-polymer hydrogels: insights from rheo-TRUSAXS and rheo-electric experiment

T0 review · 4 major / 4 minor · reviewed 2026-08-04 · deepseek-v4-flash

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

Pith's one-line read Two carbon-black hydrogels yield by different routes, set by one ratio

desk verdict Rich LAOStrain dataset with a convincing conductive-gel mechanism, but the insulating-gel mechanism leans on a q_max shift that could just be fragmentation, so the dual-mechanism story needs tightening. read the letter →

arxiv 2509.08966 v1 pith:6MWYAPNU submitted 2025-09-10 cond-mat.soft cond-mat.mtrl-sciphysics.app-ph

Gauthier Legrand , Guilhem P. Baeza , William Chèvremont , Sébastien Manneville , Thibaut Divoux This is my paper · ORCID
classification cond-mat.softcond-mat.mtrl-sciphysics.app-ph
keywords carbonblackhydrogelyieldingLAOStrainrheo-TRUSAXSrheo-electricpercolationconductivity
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 studies hydrogels made of carbon black (CB) particles and a hydrophobically modified cellulose polymer (CMC). It shows that whether the gel is electrically conductive or insulating, both yield under large oscillatory shear via a 'type III' scenario: a monotonic decrease in the elastic modulus and an overshoot in the viscous modulus. However, the underlying microscopic events differ dramatically. Conductive gels yield at about 6% strain, breaking the percolated CB network into large clusters; at larger strains a transient, shear-induced network forms and conductivity rises above its rest value. Insulating gels yield at about 60% strain; shear brings CB particles closer together, increasing conductivity tenfold. A single control parameter, the CMC-to-CB mass ratio, separates the two behaviors across more than a hundred formulations.

What carries the argument

The central experiment couples large-amplitude oscillatory shear (LAOStrain) with time-resolved ultra-small-angle X-ray scattering (TRUSAXS) and simultaneous DC electrical conductivity measurements. TRUSAXS probes CB microstructure from ~0.1 to a few microns, while conductivity reports on connectivity at longer scales beyond the SAXS window. The critical CMC-to-CB mass ratio r_c, previously identified from linear rheology and impedance, is the organizing parameter that separates conductive from insulating microstructures and predicts the qualitative yielding behavior.

What would settle it

A dilute CB-CMC dispersion with weak interparticle correlations could be sheared while monitoring the Kratky peak: if the peak shifts without strong structure-factor contributions, the distance interpretation fails. Alternatively, cryo-TEM of sheared insulating gels would directly show whether particles are closer or merely fragmented.

Watch

Extended reading notes

Core claim

The paper establishes that the non-linear yielding of CB-CMC hydrogels under LAOStrain is controlled by the critical polymer-to-particle ratio r_c. Conductive hydrogels (r < r_c) yield at low strain by rupturing the percolated CB network at length scales above a few microns, evidenced by a drop in DC conductivity; beyond yielding, strong shear creates a transient percolated network of CB clusters that raises conductivity above the initial value. Insulating hydrogels (r > r_c) yield at much larger strain; rheo-TRUSAXS shows a decrease in average interparticle distance and cluster fragmentation, accompanied by a tenfold conductivity increase, yet still below conductive gels. These distinct mec

Load-bearing premise

The interpretation that the Kratky peak shift in insulating gels corresponds to a decrease in average center-to-center distance assumes the scattering peak is governed by the structure factor; the paper itself notes that for polydisperse attractive scatterers, the peak can be partly due to the form factor, so the shift could instead reflect cluster fragmentation.

Editorial extensions

If this is right

  • The ratio r_c can be used as a design variable to set whether a hydrogel yields abruptly at low strain or ductilely at high strain.
  • The transient conductivity increase under strong shear in conductive gels could enable shear-addressable electrical switching in soft materials.
  • The lack of TRUSAXS signal in conductive gels indicates failure occurs by localized brittle rupture, not gradual particle rearrangement.
  • The hysteresis in insulating gels implies that shear history permanently alters microstructure on experimental timescales, which must be accounted for in processing.
  • Electrical harmonics can serve as a sensitive probe of network breakage and reformation during oscillation, relating mechanical and electrical nonlinearities.

Reading between the lines

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

  • The transient re-percolation may be a general feature of percolated colloidal networks under oscillatory shear, suggesting a way to control electrical properties without changing composition.
  • The assumption that the Kratky peak shift in insulating gels reflects reduced interparticle distance could be tested by contrast-matched SANS under identical shear.
  • The relation between conductivity harmonics and mechanical power could be extended to other conductive composites to infer internal restructuring rates from electrical signals alone.
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

4 major / 4 minor

Summary. This manuscript reports a combined rheo-TRUSAXS and rheo-electric study of the Large Amplitude Oscillatory Shear (LAOStrain) response of carbon black–carboxymethylcellulose (CB-CMC) hydrogels. Building on the authors’ prior identification of a critical polymer-to-particle ratio r_c separating conductive (percolated CB network) from insulating (polymer-matrix, CB-crosslinked) gels, the paper characterizes the yielding behavior of more than one hundred compositions. The central claims are: (i) both gel types show a type III yielding scenario with a G'' overshoot and monotonic G' decrease; (ii) conductive gels yield at small strains, their DC conductivity drops at yield, and at larger amplitudes the conductivity recovers and even exceeds its rest value, which is interpreted as shear-induced formation of a transient, dynamically percolated CB network; (iii) insulating gels yield at much larger strains, their Kratky-peak q_max shifts to larger q, interpreted as both fragmentation of CB clusters and a decrease in average CB–CB distance, concomitant with a tenfold conductivity increase; and (iv) the nonlinear observables collapse into two regimes separated by r_c. The paper combines rheology, intra-cycle Fourier/Chebyshev analysis, time-resolved electrical conductivity, and time-resolved USAXS, with a detailed Appendix on the harmonic coupling between mechanical power and conductivity.

Significance. If the central claims hold, the paper is significant for the physics of yielding in colloid–polymer hydrogels: it proposes two distinct microscopic mechanisms—brittle-like rupture of a percolated CB network versus matrix-dominated yielding with particle-scale reorganization—controlled by a single compositional parameter, r_c. The experimental scope is unusually broad: more than 100 compositions were measured, and the rheo-electric data provide time-resolved, mechanically coupled conductivity spectra with a quantitative harmonic model (Eq. 11 and Appendix F). The ESRF data are made available via DOI. The rheo-TRUSAXS experiments on the insulating gels are the main direct structural evidence and are potentially very valuable. However, the structural interpretation contains an ambiguity that is load-bearing for the insulating-gel mechanism, and several internal numerical inconsistencies in key parameters (yield strain, power-law exponents) need to be resolved before the paper can be accepted.

major comments (4)
  1. [Abstract; §IV A; §IV D] The quantitative anchor of the paper—the yield strain—is inconsistent. The abstract states conductive gels yield at γ_y ≃ 6%, while §IV A gives γ_y ≃ 3% for the representative conductive gel (c_CMC = 0.01%, x_CB = 6%). For the insulating gel, §IV A gives γ_y ≃ 60%, but §IV D later refers to “the yield point, previously identified at γ_y ≃ 70% for this sample composition”, citing Fig. 3(b). Since γ_y is central to the binary classification and to the mechanism contrast, these internal contradictions must be corrected and a single, clearly defined criterion should be used consistently.
  2. [§IV A, Figs. 3 and 5] The power-law exponents are also presented inconsistently. The caption of Fig. 3 and the surrounding text quote ν′ = 0.92, ν′′ = 0.65 for the conductive gel and ν′ = 0.71, ν′′ = 0.34 for the insulating gel, whereas the discussion of Fig. 5 states that for conductive gels ν′ ≃ 1.5 and ν′′ ≃ 1 with ν′/ν′′ ≃ 1.5, and that insulating gels reach ν′/ν′′ ≃ 5. If the representative curves in Fig. 3 are fitted over a different strain range, the fitting ranges and criteria should be stated explicitly; as written, the reader cannot determine which exponent set characterizes the two classes.
  3. [§IV D; §III] The central structural evidence for the insulating-gel mechanism is the Kratky-peak shift q_max from 1.4×10⁻² to 2.2×10⁻² nm⁻¹. The text first calls this “the signature of the fragmentation of CB clusters under shear” and later concludes that shear “brings the CB particles and clusters closer together.” But §III explicitly warns that for polydisperse attractive systems q_max mixes form- and structure-factor contributions, so a form-factor change (fragmentation) alone can produce the same peak shift without any decrease in center-to-center distance. Since the conductivity increase is then attributed to reduced interparticle spacing, the two statements are not equivalent. Please separate these contributions (e.g., by modeling the form factor or using a structure-factor-sensitive invariant), or explicitly rephrase the conclusion as one of two alternatives.
  4. [§IV D; §II B] The rheo-TRUSAXS experiment on the insulating gel was performed on a sample aged only 3 min after preshear, at which G′ < G′′ at 1 rad/s, whereas the rheo-electric and rheological protocols use a 20-min recovery. The microstructural changes (q_max shift) and the conductivity increase are therefore not measured on the same material state, and the coupling between them is inferred across different aging times. Please demonstrate that the 3-min structure gives the same strain-induced evolution as the 20-min state, or weaken the combined mechanistic claim.
minor comments (4)
  1. [Fig. 11(c); Fig. 20(c)] The caption states q₂ = 4×10⁻² mm⁻¹; given the text and the q-axis, this should presumably be nm⁻¹. Please correct the unit.
  2. [Eq. (11); Appendix F] The text writes b_n ≃ a_{n−1}, but Eq. (F6) includes a_{n+1} and a phase term. State more explicitly the condition under which the a_{n+1} contribution is negligible in the reported strain range.
  3. [§IV A] The sentence “all experiments are conducted at a fixed frequency” is later qualified by the frequency-dependent study in Appendix B. Rephrase as “unless otherwise stated,” or move the qualification into the main text.
  4. [§IV C; §V] The transient shear-induced percolated network in conductive gels is presented initially as a hypothesis (“consistent with”), but the Discussion states it more categorically. Since the USAXS window shows no structural signal at these length scales, add one sentence reminding the reader that this aspect is inferred from conductivity and is not directly observed.

Circularity Check

0 steps flagged · score 0.0 of 10

No significant circularity: the nonlinear observables are measured independently and the r_c threshold is an external input from prior work, not a fitted prediction.

full rationale

The paper's central claims are empirical: LAOStrain rheology, rheo-TRUSAXS, and rheo-electric conductivity are measured as functions of strain amplitude for conductive and insulating CB-CMC hydrogels. The binary separation of nonlinear observables (γ_NL, γ_y, γ_OS, overshoot amplitude) across the polymer-to-particle ratio r is a measured outcome, and r_c was fixed beforehand from linear viscoelastic and electrical impedance spectroscopy in prior work [39]; the new data are not used to define r_c. The rheo-electric harmonic analysis in Eq. (11) fits a constant c1, but it is used only to test consistency between electrical and mechanical harmonics, not to force the main yielding scenarios. The only notable weakness is the interpretation of the Kratky peak shift q_max in insulating gels: Section III explicitly states that q_max reflects a partially decoupled combination of form factor and structure factor, so the shift could stem from cluster fragmentation rather than a decrease in center-to-center distance. This is an interpretive ambiguity or a correctness risk, not a circular derivation: the paper does not define q_max as the interparticle distance, and the conductivity increase is an independent measurement used to infer closer CB-CB contacts. No fitted parameter is renamed as a prediction, no load-bearing self-citation chain supplies the central result, and no uniqueness theorem is imported from the authors' prior work. The derivation chain is therefore self-contained with respect to the paper's main qualitative conclusions.

Assumptions & free parameters 1 free parameters · 4 assumptions · 1 invented entities

The paper is experimental. The only fitted model parameter central to the analysis is the conductivity-power coupling constant c1. The main structural claims rely on standard scattering assumptions, the assumption that conductivity tracks CB connectivity, and the assumption of homogeneous strain; the q_max interpretation is the most fragile of these.

free parameters (1)
  • c1 (conductivity-power coupling constant) = 40 ± 5 mS·cm^-1·Pa^-1 (with γ0 expressed in strain units), Eq. (F18); also c1 in Eq. (11)
    Fitted to the harmonic amplitudes of the electrical conductivity versus strain. Used to relate conductivity harmonics to stress harmonics via Eq. (11). Not central to the main yielding claims, but is a fitted parameter in the analysis.
assumptions (4)
  • domain assumption The scattered intensity is dominated by carbon black because its scattering length density contrast is about 20 times that of CMC/water.
    Section II D: justifies attributing the USAXS signal to the CB microstructure.
  • domain assumption The position of the Kratky peak q_max reflects the most probable center-to-center distance between CB aggregates, with form factor and structure factor contributions partially decoupled.
    Section III states the coupling; Section IV D uses the q_max shift to infer changes in interparticle distance.
  • domain assumption DC conductivity is a direct real-time measure of the connectivity of the CB percolated network.
    Section IV C: the electrical response time (~10 ms) is much shorter than the oscillation period, so conductivity tracks network connectivity.
  • domain assumption The strain field is homogeneous in the rheo-electric parallel-plate geometry (negligible wall slip).
    Section II C notes smooth plates may lead to wall slip; interpretation of conductivity changes assumes bulk microstructure changes rather than slip artifacts.
invented entities (1)
  • Transient, dynamically percolated network of CB clusters under large-amplitude shear in conductive hydrogels independent evidence
    purpose: Explains the observed increase in DC conductivity above its rest value at high strain amplitudes and its rapid relaxation upon flow cessation.
    Supported by the conductivity overshoot (Fig. 10c) and relaxation to the rest value (Fig. 17a). Not directly observed by USAXS (no scattering change, Fig. 20), so it remains an inferred microstructure with an indirect falsifiable handle.

how reviews work

0 comments
Cite this review

Pith. "Pith review of LAOStrain response of carbon black-polymer hydrogels: insights from rheo-TRUSAXS and rheo-electric experiment." pith.science (2026). https://pith.science/paper/6MWYAPNU

@misc{pith2026250908966,
  author       = {Pith},
  title        = {Pith review of: LAOStrain response of carbon black-polymer hydrogels: insights from rheo-TRUSAXS and rheo-electric experiment},
  year         = {2026},
  howpublished = {\url{https://pith.science/paper/6MWYAPNU}},
  note         = {Machine review of arXiv:2509.08966}
}
read the original abstract

Colloid-polymer hydrogels are encountered in various applications, from flow batteries to drug delivery. Here, we investigate hydrogels composed of hydrophobic colloidal soot particles -- carbon black (CB) -- and carboxymethylcellulose (CMC), a food-grade polymer functionalized with hydrophobic groups binding physically to CB. As described in [Legrand et al., Macromolecules 56, 2298-2308 (2023)], CB-CMC hydrogels exist in two flavors: either electrically conductive when featuring a percolated network of CB particles decorated by CMC, or insulating where isolated CB particles act as physical cross-linkers within the CMC matrix. We compare these two types of CB-CMC hydrogels under Large Amplitude Oscillatory Shear (LAOS), combining rheometry with Time-Resolved Ultra-Small-Angle X-ray Scattering (TRUSAXS) and electrical conductivity measurements. Both types of hydrogels exhibit a "type III" yielding scenario, characterized by an overshoot in G'' and a monotonic decrease in G', although the underlying microscopic mechanisms differ markedly. Conductive CB-CMC hydrogels display a yield strain (6%) concomitant with a drop in DC conductivity, indicative of the macroscopic rupture of the percolated CB network at length scales larger than a few microns, beyond USAXS resolution. At larger strain amplitudes, the conductivity of the fluidized sample increases again, exceeding its initial value, consistent with shear-induced formation of a transient, dynamically percolated network of CB clusters. In contrast, insulating CB-CMC hydrogels exhibit a larger yield strain (60%), beyond which the sample flows and the average distance between CB particles decreases. This reorganization is concomitant with a more than tenfold increase in conductivity, although it remains below that of conductive hydrogels at rest.

Figures

Figures reproduced from arXiv: 2509.08966 by the authors.

Figure 1
Figure 1. FIG. 1. Representative Transmission Electron Microscopy [PITH_FULL_IMAGE:figures/full_fig_p003_1.png] view at source ↗
Figure 2
Figure 2. The impact of CMC concentration at fixed CB content is illustrated in Figs. 2(a) and 2(b) for xCB = 2% and 6%, respectively. All compositions yield Kratky plots with a characteristic third-order polynomial shape featuring a local maximum around qmax ≃ 2.10−2 nm−1 , corre￾sponding to a real-space length scale dmax = 2π/qmax ≃ 300 nm. In systems comprising attractive scatterers, this seemingly unique length-scale actu… view at source ↗
Figure 2
Figure 2. FIG. 2. Kratky plots of the scattering intensity ( [PITH_FULL_IMAGE:figures/full_fig_p005_2.png] view at source ↗
Figures from the paper (17 more)
Figure 3
Figure 3. Figure 3: FIG. 3. LAOStrain response of conductive (left) and insulating (right) CB-CMC hydrogels. Elastic modulus [PITH_FULL_IMAGE:figures/full_fig_p006_3.png]
Figure 4
Figure 4. Figure 4: FIG. 4. Phase diagram of aqueous CB-CMC dispersions as [PITH_FULL_IMAGE:figures/full_fig_p007_4.png]
Figure 5
Figure 5. Figure 5: FIG. 5. Attributes of the non-linear response and yielding transition of CB-CMC hydrogels plotted against the CMC-to-CB [PITH_FULL_IMAGE:figures/full_fig_p008_5.png]
Figure 6
Figure 6. Figure 6: FIG. 6. Key features of the overshoot in [PITH_FULL_IMAGE:figures/full_fig_p009_6.png]
Figure 7
Figure 7. Figure 7: FIG. 7. Lissajous-Bowditch plots of the normalized stress response under sinusoidal strain of increasing amplitude. Experiments [PITH_FULL_IMAGE:figures/full_fig_p010_7.png]
Figure 8
Figure 8. Figure 8: FIG. 8. Normalized Fourier coefficients [PITH_FULL_IMAGE:figures/full_fig_p011_8.png]
Figure 9
Figure 9. Figure 9: FIG. 9. LAOStrain intra-cycle analysis for the two types of CB-CMC hydrogels: a conductive gel ( [PITH_FULL_IMAGE:figures/full_fig_p012_9.png]
Figure 10
Figure 10. Figure 10: FIG. 10. LAOStrain experiments on a conductive CB-CMC [PITH_FULL_IMAGE:figures/full_fig_p014_10.png]
Figure 11
Figure 11. Figure 11: FIG. 11. LAOStrain experiments performed using rheo-TRUSAXS on an insulating CB-CMC hydrogel ( [PITH_FULL_IMAGE:figures/full_fig_p016_11.png]
Figure 12
Figure 12. Figure 12: FIG. 12. LAOStrain experiment on an insulating CB-CMC [PITH_FULL_IMAGE:figures/full_fig_p017_12.png]
Figure 13
Figure 13. Figure 13: ranges between 4.4 Pa and 5.8 Pa, and decreases for increasing strain amplitude as the wire unfolds. Note that the exact contribution of the wire rigidity to the rhe￾ological measurements actually depends on the manner in which the wire is attached to the rotor, which…
Figure 14
Figure 14. Figure 14: FIG. 14. (a) Electrical conductivity [PITH_FULL_IMAGE:figures/full_fig_p021_14.png]
Figure 17
Figure 17. Figure 17: FIG. 17. DC electrical conductivity [PITH_FULL_IMAGE:figures/full_fig_p022_17.png]
Figure 18
Figure 18. Figure 18: FIG. 18. Fluctuations of conductivity ∆ [PITH_FULL_IMAGE:figures/full_fig_p022_18.png]
Figure 16
Figure 16. Figure 16: FIG. 16. Ratio [PITH_FULL_IMAGE:figures/full_fig_p022_16.png]
Figure 19
Figure 19. Figure 19: FIG. 19. Harmonic amplitudes [PITH_FULL_IMAGE:figures/full_fig_p023_19.png]
Figure 20
Figure 20. Figure 20: FIG. 20. LAOStrain experiment performed using rheo-TRUSAXS on a conductive CB-CMC hydrogel ( [PITH_FULL_IMAGE:figures/full_fig_p024_20.png]

Discussion (0). Continue with ORCID to comment.

Reference graph

Works this paper leans on

97 extracted references · 1 linked inside Pith

  1. [1]

    The results are reported in Fig

    Lissajous-Bowditch (LB) curves We now go beyond the cycle-averaged rheological re- sponse of CB-CMC hydrogels to oscillatory shear, and ex- amine the intra-cycle stress response for increasing strain amplitudes. The results are reported in Fig. 7 as nor- malized Lissajous-Bowditch (LB), i.e., parametric plots of the shear stressσas a function of strainγ[F...

  2. [2]

    Fourier Transform Rheology In order to get more quantitative insight into the intra- cycle stress response, we turn to Fourier Transform rhe- ology [75, 77, 78]. In particular, the stress response to the sinusoidal strain inputγ(t) =γ 0 sin(ωt) can be de- composed into an elastic and a viscous component, which readsτ(t) =τ elast(t) +τ visc(t). This is don...

  3. [3]

    Plan France 2030

    Chebyshev decomposition A complementary approach to Fourier Transform rhe- ology, pioneered in refs. [48, 81] considers the decompo- sition of the non-linear stress response into Chebyshev polynomials. The elastic and viscous stresses,τ elast(γ) andτ visc( ˙γ), are expressed as follows: τelast(γ) =γ 0 X k,odd ekTk γ γ0 ,(3) τvisc( ˙γ) =ωγ0 X k,odd vkTk ˙γ...

  4. [4]

    This contribution was determined by performing a strain sweep atω= 2πrad.s −1 with an empty shear cell

    Impact of the wire on rheological measurements The copper wire closing the electrical circuit results in a residual torque that may affect mechanical measure- ments. This contribution was determined by performing a strain sweep atω= 2πrad.s −1 with an empty shear cell. The effective elastic modulusG wire measured as a function of the strain amplitudeγ 0 a...

  5. [5]

    Impact of the wire deformation on electrical measurements During LAOStrain experiments, the wire moves, which may impact electrical measurements. We address this is- sue by performing time-resolved rheo-electrical measure- ments on EGaIn alloy (Gallium-Indium eutectic 75.5%- 24.5% wt., ThermoFisher), a liquid metal at room tem- perature, which behaves as ...

  6. [6]

    Schexnailder and G

    P. Schexnailder and G. Schmidt, Nanocomposite polymer hydrogels, Colloid Polym. Sci.287, 1 (2009)

    2009

  7. [7]

    E. A. Appel, M. W. Tibbitt, M. J. Webber, B. A. Mattix, O. Veiseh, and R. Langer, Self-assembled hydrogels uti- lizing polymer–nanoparticle interactions, Nature Com.6, 6295 (2015)

    2015

  8. [8]

    J. J. Richards, A. D. Scherbarth, N. J. Wagner, and P. D. Butler, Mixed ionic/electronic conducting surface layers adsorbed on colloidal silica for flow battery applications, ACS Appl. Mater. Interfaces8, 24089 (2016)

    2016

Show all 97 references
  1. [9]

    Costa, E

    C. Costa, E. Lizundia, and S. Lanceros-M´ endez, Poly- mers for advanced lithium-ion batteries: State of the art and future needs on polymers for the different bat- tery components, Prog. Energy Combust. Sci.79, 100846 (2020)

    2020

  2. [10]

    Meslam, A

    M. Meslam, A. A. Elzatahry, and M. Youssry, Promising aqueous dispersions of carbon black for semisolid flow battery application, Colloids Surf. A: Physicochem. Eng. Asp. , 129376 (2022)

    2022

  3. [11]

    J. E. Smay, G. M. Gratson, R. F. Shepherd, J. Ce- 25 sarano III, and J. A. Lewis, Directed colloidal assembly of 3d periodic structures, Adv. Mater.14, 1279 (2002)

    2002

  4. [12]

    J. J. Richards and J. B. Hipp, The black powder behind battery power, Physics Today77, 26 (2024)

    2024

  5. [13]

    W. Poon, A. Pirie, and P. Pusey, Gelation in colloid– polymer mixtures, Faraday Discuss.101, 65 (1995)

    1995

  6. [14]

    Bergenholtz, W

    J. Bergenholtz, W. C. Poon, and M. Fuchs, Gelation in model colloid- polymer mixtures, Langmuir19, 4493 (2003)

    2003

  7. [15]

    Laurati, G

    M. Laurati, G. Petekidis, N. Koumakis, F. Cardinaux, A. B. Schofield, J. M. Brader, M. Fuchs, and S. U. Egelhaaf, Structure, dynamics, and rheology of colloid- polymer mixtures: From liquids to gels, J. Chem. Phys. 130(2009)

    2009

  8. [16]

    Koumakis and G

    N. Koumakis and G. Petekidis, Two step yielding in attractive colloids: transition from gels to attractive glasses, Soft Matter7, 2456 (2011)

    2011

  9. [17]

    Sprakel, S

    J. Sprakel, S. Lindstr¨ om, T. Kodger, and D. Weitz, Stress enhancement in the delayed yielding of colloidal gels, Phys. Rev. Lett.106, 248303 (2011)

    2011

  10. [18]

    Laurati, S

    M. Laurati, S. Egelhaaf, and G. Petekidis, Nonlinear rhe- ology of colloidal gels with intermediate volume fraction, J. Rheol.55, 673 (2011)

    2011

  11. [19]

    H. K. Chan and A. Mohraz, Two-step yielding and di- rectional strain-induced strengthening in dilute colloidal gels, Phys. Rev. E85, 041403 (2012)

    2012

  12. [20]

    Moghimi, A

    E. Moghimi, A. B. Schofield, and G. Petekidis, Yielding and resolidification of colloidal gels under constant stress, J. Condens. Matter Phys.33, 284002 (2021)

    2021

  13. [21]

    Koumakis, E

    N. Koumakis, E. Moghimi, R. Besseling, W. C. Poon, J. F. Brady, and G. Petekidis, Tuning colloidal gels by shear, Soft Matter11, 4640 (2015)

    2015

  14. [22]

    Moghimi, A

    E. Moghimi, A. R. Jacob, N. Koumakis, and G. Petekidis, Colloidal gels tuned by oscillatory shear, Soft Matter13, 2371 (2017)

    2017

  15. [23]

    Colombo, P

    G. Colombo, P. Leh´ ericey, F. J. Mu¨ uller, M. V. Majji, H. R. Vutukuri, J. W. Swan, and J. Vermant, Kinetic pathways to gelation and effects of flow-induced struc- turing in depletion gels, Ind. Eng. Chem. Res. (2025)

    2025

  16. [24]

    Dolan and S

    A. Dolan and S. F. Edwards, Theory of the stabilization of colloids by adsorbed polymer, Proc. R. Soc. A: Math. Phys. Eng. Sci.337, 509 (1974)

    1974

  17. [25]

    ´A. G. Garc ´ ıa, M. M. Nagelkerke, R. Tuinier, and M. Vis, Polymer-mediated colloidal stability: on the transition between adsorption and depletion, Adv. Colloid Interface Sci.275, 102077 (2020)

    2020

  18. [26]

    Iler, Relation of particle size of colloidal silica to the amount of a cationic polymer required for flocculation and surface coverage, J

    R. Iler, Relation of particle size of colloidal silica to the amount of a cationic polymer required for flocculation and surface coverage, J. Colloid Interface Sci.37, 364 (1971)

    1971

  19. [27]

    Otsubo, Elastic percolation in suspensions flocculated by polymer bridging, Langmuir6, 114 (1990)

    Y. Otsubo, Elastic percolation in suspensions flocculated by polymer bridging, Langmuir6, 114 (1990)

    1990

  20. [28]

    M. J. Gallegos, D. D. Soetrisno, F. Safi Samghabadi, and J. C. Conrad, Effects of polymer molecular weight on structure and dynamics of colloid–polymer bridging systems, J. Phys. Chem. B.127, 3969 (2023)

    2023

  21. [29]

    K. Wong, P. Lixon, F. Lafuma, P. Lindner, O. A. Char- riol, and B. Cabane, Intermediate structures in equilib- rium flocculation, J. Colloid Interface Sci.153, 55 (1992)

    1992

  22. [30]

    Spalla and B

    O. Spalla and B. Cabane, Growth of colloidal aggregates through polymer bridging, Colloid Polym. Sci.271, 357 (1993)

    1993

  23. [31]

    Zebrowski, V

    J. Zebrowski, V. Prasad, W. Zhang, L. Walker, and D. Weitz, Shake-gels: shear-induced gelation of laponite– peo mixtures, Colloids Surf. A: Physicochem. Eng. Asp. 213, 189 (2003)

    2003

  24. [32]

    D. C. Pozzo and L. M. Walker, Reversible shear gelation of polymer–clay dispersions, Colloids Surf. A: Physic- ochem. Eng. Asp.240, 187 (2004)

    2004

  25. [33]

    Kamibayashi, H

    M. Kamibayashi, H. Ogura, and Y. Otsubo, Shear- thickening flow of nanoparticle suspensions flocculated by polymer bridging, J. Colloid Interface Sci.321, 294 (2008)

    2008

  26. [34]

    Banerjee, J

    D. Banerjee, J. H. Lew, and P. F. Luckham, On the rhe- ological properties of silica–poly (ethylene-oxide) disper- sions:” shake-gels” ii the effect of silica concentration and molecular weight of polymer, Colloids Surf. A: Physic- ochem. Eng. Asp.703, 135195 (2024)

    2024

  27. [35]

    Otsubo and K

    Y. Otsubo and K. Umeya, Rheological properties of silica suspensions in polyacrylamide solutions, J. Rheol.28, 95 (1984)

    1984

  28. [36]

    Otsubo and K

    Y. Otsubo and K. Watanabe, Rheological studies on bridging flocculation, Colloids Surf.50, 341 (1990)

    1990

  29. [37]

    Cabane, K

    B. Cabane, K. Wong, P. Lindner, and F. Lafuma, Shear induced gelation of colloidal dispersions, J. Rheol.41, 531 (1997)

    1997

  30. [38]

    Dehne, F

    H. Dehne, F. Hecht, and A. Bausch, The mechanical properties of polymer–colloid hybrid hydrogels, Soft mat- ter13, 4786 (2017)

    2017

  31. [39]

    Dellatolas, M

    I. Dellatolas, M. Bantawa, B. Damerau, M. Guo, T. Di- voux, E. Del Gado, and I. Bischofberger, Local mecha- nism governs global reinforcement of nanofiller-hydrogel composites, ACS nano17, 20939 (2023)

    2023

  32. [40]

    Le Gulluche, N

    A.-C. Le Gulluche, N. Pantoustier, A. Brˆ ulet, O. Sanseau, P. Sotta, and A. Marcellan, Role of polymer– particle adhesion in the reinforcement of hybrid hydro- gels, Macromolecules56, 8024 (2023)

    2023

  33. [41]

    Pickrahn, B

    K. Pickrahn, B. Rajaram, and A. Mohraz, Relation- ship between microstructure, dynamics, and rheology in polymer-bridging colloidal gels, Langmuir26, 2392 (2010)

    2010

  34. [42]

    Adibnia and R

    V. Adibnia and R. J. Hill, Viscoelasticity of near-critical silica-polyacrylamide hydrogel nanocomposites, Polymer 112, 457 (2017)

    2017

  35. [43]

    E. E. Pashkovski, J. G. Masters, and A. Mehreteab, Vis- coelastic scaling of colloidal gels in polymer solutions, Langmuir19, 3589 (2003)

    2003

  36. [44]

    Legrand, S

    G. Legrand, S. Manneville, G. H. McKinley, and T. Di- voux, Dual origin of viscoelasticity in polymer-carbon black hydrogels: a rheometry and electrical spectroscopy study, Macromolecules56, 2298 (2023)

    2023

  37. [45]

    J. D. Keller, Sodium carboxymethylcellulose (cmc), in Food hydrocol.(CRC Press, 2020) pp. 43–109

    2020

  38. [46]

    C. G. Lopez, R. H. Colby, and J. T. Cabral, Electro- static and hydrophobic interactions in nacmc aqueous so- lutions: Effect of degree of substitution, Macromolecules 51, 3165 (2018)

    2018

  39. [47]

    DeButts, J

    E. DeButts, J. Hudy, and J. Elliott, Rheology of sodium carboxymethylcellulose solutions, Ind. Eng. Chem.49, 94 (1957)

    1957

  40. [48]

    J. H. Park, S. H. Kim, and K. H. Ahn, Role of car- boxymethyl cellulose binder and its effect on the prepara- tion process of anode slurries for li-ion batteries, Colloids Surf. A Physicochem. Eng. Asp.664, 131130 (2023)

    2023

  41. [49]

    Herv´ eou, G

    L. Herv´ eou, G. Legrand, T. Divoux, and G. P. Baeza, Un- derstanding polymer–colloid gels: a solvent perspective using low-field nmr, Soft Matter21, 342 (2025). 26

    2025

  42. [50]

    Legrand,Understanding Hydrogel Formation in Dis- persions of Carbon black and Carboxymethylcellulose : Rheological, Electrical and Structural Perspectives, Ph

    G. Legrand,Understanding Hydrogel Formation in Dis- persions of Carbon black and Carboxymethylcellulose : Rheological, Electrical and Structural Perspectives, Ph. D. thesis, Ecole Normale Sup´ erieure de Lyon (2024)

    2024

  43. [51]

    Legrand, G

    G. Legrand, G. P. Baeza, S. Manneville, and T. Divoux, Rheological properties of acid-induced carboxymethylcel- lulose hydrogels, Cellulose32, 903 (2025)

    2025

  44. [52]

    J. J. Richards, J. B. Hipp, J. K. Riley, N. J. Wagner, and P. D. Butler, Clustering and percolation in suspensions of carbon black, Langmuir33, 12260 (2017)

    2017

  45. [53]

    R. H. Ewoldt, A. Hosoi, and G. H. McKinley, New mea- sures for characterizing nonlinear viscoelasticity in large amplitude oscillatory shear, J. Rheol.52, 1427 (2008)

    2008

  46. [54]

    Erfanian, M

    E. Erfanian, M. Kamkar, D. Williams, Y. Za- mani Keteklahijani, R. Salehiyan, S. S. Ray, M. Arjmand, and U. Sundararaj, Dielectrorheology of aspect-ratio- tailored carbon nanotube/polyethylene composites under large deformations: Implications for high-temperature dielectrics, ...

    2021

  47. [55]

    Paulovicova, M

    K. Paulovicova, M. Rajnak, J. Tothova, B. Dolnik, M. Timko, and P. Kopcansky, Rheodielectric study of transformer-oil-based ferrofluids, Phys. Rev. E111, 045403 (2025)

    2025

  48. [56]

    Bauland, G

    J. Bauland, G. Legrand, S. Manneville, T. Divoux, A. Poulesquen, and T. Gibaud, Anti-thixotropic dy- namics in attractive colloidal dispersions: a shear re- structuring driven by elastic stresses, arXiv preprint arXiv:2501.16532 (2025)

    2025 arXiv

  49. [57]

    Narayanan, M

    T. Narayanan, M. Sztucki, T. Zinn, J. Kieffer, A. Homs- Puron, J. Gorini, P. Van Vaerenbergh, and P. Boesecke, Performance of the time-resolved ultra-small-angle X-ray scattering beamline with the extremely brilliant source, J. Appl. Crystallogr.55, 98 (2022)

    2022

  50. [58]

    Lindner and T

    P. Lindner and T. Zemb, Neutron, x-ray and light scat- tering : introduction to an investigative tool for colloidal and polymeric systems (1991)

    1991

  51. [59]

    G. P. Baeza, J. Oberdisse, A. Alegria, K. Saalw¨ achter, M. Couty, and A.-C. Genix, Depercolation of aggregates upon polymer grafting in simplified industrial nanocom- posites studied with dielectric spectroscopy, Polymer73, 131 (2015)

    2015

  52. [60]

    G. P. Baeza, A.-C. Genix, C. Degrandcourt, L. Petitjean, J. Gummel, R. Schweins, M. Couty, and J. Oberdisse, Effect of grafting on rheology and structure of a simplified industrial nanocomposite silica/sbr, Macromolecules46, 6621 (2013)

    2013

  53. [61]

    G. P. Baeza, A.-C. Genix, N. Paupy-Peyronnet, C. De- grandcourt, M. Couty, and J. Oberdisse, Revealing nanocomposite filler structures by swelling and small- angle x-ray scattering, Faraday discussions186, 295 (2016)

    2016

  54. [62]

    G. P. Baeza, A.-C. Genix, C. Degrandcourt, L. Petit- jean, J. Gummel, M. Couty, and J. Oberdisse, Multiscale filler structure in simplified industrial nanocomposite sil- ica/sbr systems studied by saxs and tem, Macromolecules 46, 317 (2013)

    2013

  55. [63]

    Genix and J

    A.-C. Genix and J. Oberdisse, Determination of the lo- cal density of polydisperse nanoparticle assemblies, Soft Matter13, 8144 (2017)

    2017

  56. [64]

    Donnet,Carbon black: science and technology (CRC Press, 1993)

    J.-B. Donnet,Carbon black: science and technology (CRC Press, 1993)

    1993

  57. [65]

    K. Hyun, S. H. Kim, K. H. Ahn, and S. J. Lee, Large am- plitude oscillatory shear as a way to classify the complex fluids, J. Non-Newton. Fluid Mech.107, 51 (2002)

    2002

  58. [66]

    Z. Xu, Y. Song, and Q. Zheng, Payne effect of carbon black filled natural rubber compounds and their carbon black gels, Polymer185, 121953 (2019)

    2019

  59. [67]

    X. Fan, H. Xu, Q. Zhang, D. Xiao, Y. Song, and Q. Zheng, Insight into the weak strain overshoot of car- bon black filled natural rubber, Polymer167, 109 (2019)

    2019

  60. [68]

    X. Shi, S. Sun, A. Zhao, H. Zhang, M. Zuo, Y. Song, and Q. Zheng, Influence of carbon black on the payne effect of filled natural rubber compounds, Composites Science and Technology203, 108586 (2021)

    2021

  61. [69]

    J. M. Hart, W. D. Carswell, V. Garc ´ ıa-Sakai, B. Frick, S. C. Boothroyd, L. R. Hutchings, N. Clarke, and R. L. Thompson, Structural and dynamic origins of payne ef- fect reduction by steric stabilization in silica reinforced poly (butadiene) nanocomposites, Polymer Composites (2025)

    2025

  62. [70]

    G. J. Donley, P. K. Singh, A. Shetty, and S. A. Rogers, Elucidating theG ′′ overshoot in soft materials with a yield transition via a time-resolved experimental strain decomposition, Proc. Natl. Acad. Sci. U.S.A.117, 21945 (2020)

    2020

  63. [71]

    F. J. M¨ uller, L. Isa, and J. Vermant, Toughening colloidal gels using rough building blocks, Nat. Comm.14, 5309 (2023)

    2023

  64. [72]

    Laurati, S

    M. Laurati, S. Egelhaaf, and G. Petekidis, Plastic re- arrangements in colloidal gels investigated by laos and ls-echo, J. Rheol.58, 1395 (2014)

    2014

  65. [73]

    Miyazaki, H

    K. Miyazaki, H. M. Wyss, D. A. Weitz, and D. R. Re- ichman, Nonlinear viscoelasticity of metastable complex fluids, Europhys. Lett.75, 915 (2006)

    2006

  66. [74]

    H. M. Wyss, K. Miyazaki, J. Mattsson, Z. Hu, D. R. Reichman, and D. A. Weitz, Strain-rate frequency su- perposition: A rheological probe of structural relaxation in soft materials, Phys. Rev. Lett.98, 238303 (2007)

    2007

  67. [75]

    Koumakis, A

    N. Koumakis, A. Pamvouxoglou, A. Poulos, and G. Pe- tekidis, Direct comparison of the rheology of model hard and soft particle glasses, Soft Matter8, 4271 (2012)

    2012

  68. [76]

    M. E. Helgeson, N. J. Wagner, and D. Vlassopoulos, Vis- coelasticity and shear melting of colloidal star polymer glasses, J. Rheol.51, 297 (2007)

    2007

  69. [77]

    Eckman, A

    N. Eckman, A. K. Grosskopf, G. Jiang, K. Kamani, M. S. Huang, B. Schmittlein, S. C. Heilshorn, S. Rogers, and E. A. Appel, Crosslink strength governs yielding behav- ior in dynamically crosslinked hydrogels, Biomater. Sci. (2025)

    2025

  70. [78]

    Radhakrishnan and S

    R. Radhakrishnan and S. M. Fielding, Shear banding in large amplitude oscillatory shear (laostrain and laostress) of soft glassy materials, J. Rheol.62, 559 (2018)

    2018

  71. [79]

    Perge, N

    C. Perge, N. Taberlet, T. Gibaud, and S. Manneville, Time dependence in large amplitude oscillatory shear: A rheo-ultrasonic study of fatigue dynamics in a colloidal gel, J. Rheol.58, 1331 (2014)

    2014

  72. [80]

    K. Hyun, M. Wilhelm, C. O. Klein, K. S. Cho, J. G. Nam, K. H. Ahn, S. J. Lee, R. H. Ewoldt, and G. H. McKinley, A review of nonlinear oscillatory shear tests: Analysis and application of large amplitude oscillatory shear (laos), Prog. Polym. Sci.36, 1697 (2011)

    2011

  73. [81]

    S. A. Rogers, B. M. Erwin, D. Vlassopoulos, and M. Cloitre, A sequence of physical processes determined and quantified in laos: Application to a yield stress fluid, J. Rheol.55, 435 (2011)

    2011

  74. [82]

    Wilhelm, Fourier-transform rheology, Macromol

    M. Wilhelm, Fourier-transform rheology, Macromol. Mater. Eng.287, 83 (2002)

    2002

  75. [83]

    R. H. Ewoldt, Defining nonlinear rheological material 27 functions for oscillatory shear, J. Rheol.57, 177 (2013)

    2013

  76. [84]

    M. D. Graham, Wall slip and the nonlinear dynamics of large amplitude oscillatory shear flows, J. Rheol.39, 697 (1995)

    1995

  77. [85]

    Atalık and R

    K. Atalık and R. Keunings, On the occurrence of even harmonics in the shear stress response of viscoelastic flu- ids in large amplitude oscillatory shear, Journal of non- newtonian fluid mechanics122, 107 (2004)

    2004

  78. [86]

    K. S. Cho, K. Hyun, K. H. Ahn, and S. J. Lee, A geomet- rical interpretation of large amplitude oscillatory shear response, J. Rheol.49, 747 (2005)

    2005

  79. [87]

    Kamkar, R

    M. Kamkar, R. Salehiyan, T. B. Goudoulas, M. Abbasi, C. Saengow, E. Erfanian, S. Sadeghi, G. Natale, S. A. Rogers, A. J. Giacomin,et al., Large amplitude oscilla- tory shear flow: Microstructural assessment of polymeric systems, Prog. Polym. Sci.132, 101580 (2022)

    2022

  80. [88]

    R. H. Ewoldt and N. A. Bharadwaj, Low-dimensional intrinsic material functions for nonlinear viscoelasticity, Rheol. Acta52, 201 (2013)

    2013

  81. [89]

    N´ ebouy, L

    M. N´ ebouy, L. Chazeau, J. Morthomas, C. Fusco, P. Dieudonn´ e-George, and G. P. Baeza, Flow-induced crystallization of a multiblock copolymer under large am- plitude oscillatory shear: Experiments and modeling, J. Rheol.65, 405 (2021)

    2021

  82. [90]

    Fournier, J

    S. Fournier, J. Chevalier, S. Perez-Robles, C. Carotenuto, M. Minale, H. Reveron, and G. P. Baeza, Spreading ce- ramic stereolithography pastes: Insights from shear-and orthogonal-rheology, J. Rheol.68, 83 (2024)

    2024

  83. [91]

    Helal, T

    H. Helal, T. Divoux, and G. H. McKinley, Simultaneous rheo-electric measurements of strongly conductive com- plex fluids, Phys. Rev. Applied6, 064004 (2016)

    2016

  84. [92]

    Colombo and E

    J. Colombo and E. Del Gado, Stress localization, stiffen- ing, and yielding in a model colloidal gel, J. Rheol.58, 1089 (2014)

    2014

  85. [93]

    Gibaud, C

    T. Gibaud, C. Perge, S. B. Lindstr¨ om, N. Taberlet, and S. Manneville, Multiple yielding processes in a colloidal gel under large amplitude oscillatory stress, Soft Matter 12, 1701 (2016)

    2016

  86. [94]

    Gordon, M

    R. Gordon, M. Kassar, and N. Willenbacher, Effect of polymeric binders on dispersion of active particles in aqueous lifepo4-based cathode slurries as well as on me- chanical and electrical properties of corresponding dry layers, ACS omega5, 11455 (2020)

    2020

  87. [95]

    M. K. Burdette-Trofimov, B. L. Armstrong, A. M. Rogers, L. Heroux, M. Doucet, G. Yang, N. D. Phillip, M. K. Kidder, and G. M. Veith, Understanding binder– silicon interactions during slurry processing, J. Phys. Chem. C124, 13479 (2020)

    2020

  88. [96]

    C. D. Reynolds, S. D. Hare, P. R. Slater, M. J. Simmons, and E. Kendrick, Rheology and structure of lithium-ion battery electrode slurries, Energy Technol.10, 2200545 (2022)

    2022

  89. [97]

    Y. Wang, A. V. Pisapati, X. F. Zhang, and X. Cheng, Re- cent developments in nanomaterial-based shear-sensitive drug delivery systems, Adv. Healthc. Mater.10, 2002196 (2021)

    2021

Pith tools

Reviewed August 4, 2026 · model on record in the stance chip above.