Pith. sign in

REVIEW 4 major objections 4 minor 105 references

For molten polyethylenes, pressure shifts all relaxation times equally; branching, not molecular-weight spread, sets how strongly.

Reviewed by Pith at T0; open to challenge. T0 means a machine referee read the full paper against a public rubric. the ladder, T0–T4 →

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

T0 review · deepseek-v4-flash

2026-08-01 04:41 UTC pith:HL7DMGR4

load-bearing objection A careful, useful four-sample study of pressure-dependent PE rheology; the central claims are plausible but the superposition evidence is partly built into the fitting and the branching attribution is confounded by the sample set. the 4 major comments →

arxiv 2607.22469 v1 pith:HL7DMGR4 submitted 2026-07-24 cond-mat.soft physics.flu-dyn

Effects of long-chain branching, short-chain branching, and polydispersity on pressure sensitive rheology of polymer melts

Lilian Lin , Matthew Joe , Heon E. Park This is my paper
classification cond-mat.soft physics.flu-dyn
keywords polyethylenepressure-viscosity coefficienttime-pressure superpositionpiezorheologically simpleshort-chain branchinglong-chain branchingpolydispersityhigh-pressure sliding plate rheometer
verification ladder T0 review T1 audit T2 compute T3 formal T4 reserved

The pith

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

This paper tries to separate three structural features—short-chain branching, long-chain branching, and molecular-weight polydispersity—in setting how strongly molten polyethylene thickens under pressure. Using a high-pressure sliding plate rheometer on four polyethylene grades at 170 °C and up to 69 MPa, it finds that every sample's viscosity curves at different pressures collapse onto one master curve using a single horizontal shift factor. That is, pressure acts as a uniform brake on all relaxation modes, leaving the shear-thinning shape intact. The central result is the ranking of pressure-viscosity coefficients: linear broad-MWD HDPE is least sensitive, the two short-chain-branched copolymers are more sensitive and nearly identical despite different polydispersity, and the long-chain-branched copolymer is most sensitive. The conclusion is that branches dominate pressure sensitivity, while polydispersity is nearly irrelevant to it.

Core claim

The paper reports that four architecturally distinct polyethylenes—ranging from a strictly linear polymer with a very broad molecular-weight distribution to a long-chain-branched metallocene copolymer—all obey time-pressure superposition with a single pressure shift factor up to 69 MPa. This single factor shifts the entire viscosity curve, so pressure rescales every relaxation time by the same amount without changing the shape of the flow curve. The same branched sample that is known to violate time-temperature superposition is piezorheologically simple. The pressure-viscosity coefficient rises from about 11 GPa⁻¹ for linear HDPE to 18–19 GPa⁻¹ for the short-chain-branched copolymers and 25

What carries the argument

The central object is the horizontal pressure shift factor a_P(P), determined by superimposing stress-versus-shear-rate data measured at 23, 46, and 69 MPa onto the 0.1 MPa reference curve after correcting density effects with a vertical shift factor b_P(P). Its logarithmic slope as a function of pressure defines the Barus pressure-viscosity coefficient β. The argument works because a single a_P(P) superposes the entire flow curve: pressure changes only the characteristic time and zero-shear viscosity, not the Cross-model shape exponent. Mechanistically, the authors attribute this to pressure acting through a roughly uniform activation volume for all rearranging segments—a 'global brake'—whe

Load-bearing premise

The four commercial samples differ in several ways at once, so the interpretation depends on the assumption that unmeasured differences—catalyst type, comonomer identity, exact molecular-weight-distribution shape, and the presence of short-chain branches in the long-chain-branched sample—do not drive the ranking of pressure coefficients.

What would settle it

Prepare a matched set of model polyethylenes (or hydrogenated polybutadienes) with the same weight-average molecular weight and chemistry, with polydispersity varied from about 2 to 14 at zero branching, and measure the Barus coefficient at 170 °C in a sliding plate rheometer. If β changes by more than replicate scatter (~1 GPa⁻¹) with polydispersity, the claim that polydispersity is negligible collapses; if a long-chain-branched sample with no short branches shows no increase in β, the long-chain-branching claim collapses.

Watch this falsifier — get emailed when new claim-graph text bears on it.

If this is right

  • Within the tested window (170 °C, 0.1–69 MPa), a single master curve per polyethylene grade suffices for viscosity at any pressure, so high-pressure flow predictions can be built from one atmospheric-pressure flow curve plus a pressure shift factor.
  • Because pressure leaves the shear-thinning exponent unchanged, the shear-thinning mechanism is pressure-independent for these melts; pressure only multiplies the characteristic time and zero-shear viscosity.
  • The branched sample's known failure of time-temperature superposition does not imply failure of time-pressure superposition; the two superpositions probe different physics and must be checked separately.
  • For material design, introducing short- or long-chain branching is a way to raise pressure sensitivity, while broadening or narrowing molecular-weight distribution (in the range tested) will not move the pressure-viscosity coefficient.

Where Pith is reading between the lines

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

  • If the global-brake mechanism is general, comb, star, and H-branched melts that are thermorheologically complex should nevertheless obey time-pressure superposition; a direct test would be to run pressure superposition on well-defined star or comb polybutadiene or polystyrene.
  • The comparison with polystyrene suggests a predictive trend: regular, bulky side groups raise β more than sparse alkyl branches. A natural next experiment is polypropylene, whose methyl branches are smaller than butene or octene branches; the paper's logic would predict a β between linear HDPE and the branched ethylene copolymers.
  • Because the long-chain-branched sample also contains short-chain branches, its β = 25 GPa⁻¹ bundles both effects; a sample with long-chain branching but essentially no short branches would separate the long-chain contribution. If such a sample shows β near 19 GPa⁻¹ rather than 25, the ranking of long-chain versus short-chain effects would need adjustment.
  • The measured values apply at 170 °C and up to 70 MPa; whether the single-shift-factor picture survives near the glass transition or at much higher pressures, where free-volume effects become important, is untested by this data.

Editorial analysis

A structured set of objections, weighed in public.

Desk editor's note, referee report, simulated authors' rebuttal, and a circularity audit.

Referee Report

4 major / 4 minor

Summary. The paper reports high-pressure shear rheometry of four commercial polyethylenes (HDPE, LLDPE, LmPE, BmPE) using a high-pressure sliding plate rheometer at 170 °C and pressures up to 69 MPa. The authors combine PVT measurements with the Tait equation to obtain vertical shift factors, fit the 0.1 MPa flow curves with the Cross model, and then determine horizontal pressure shift factors by aligning reduced stress data to that model. They claim that all samples are piezorheologically simple, that the long-chain branched sample is piezorheologically simple despite being thermorheologically complex, and that pressure–viscosity coefficients deduced from the Barus equation show that both short- and long-chain branching increase pressure sensitivity while polydispersity has negligible effect.

Significance. If the central claims hold, the paper provides a useful experimental constraint for high-pressure processing simulations: pressure acts as a uniform scaling of relaxation times, and branching architecture — not MWD breadth — controls the pressure–viscosity coefficient of polyethylene. The study uses a demanding, relatively uncommon instrument with uniform shear and pressure fields, and the authors report replicate measurements, thermal stability checks, and careful PVT characterization. These experimental strengths are real and valuable. However, the superposition claim and the resulting β values depend on a fitting procedure that is not independently validated, and the sample set does not cleanly separate the structural variables. The paper is therefore a valuable contribution in need of substantial strengthening before the headline conclusions can be considered established.

major comments (4)
  1. [§3.3, Eq. (13)] The horizontal shift factor a_P is not determined by direct data collapse onto measured 0.1 MPa data; it is obtained by least-squares fitting of reduced stress to the Cross model at P0, explicitly because no overlapping data points exist at the reference pressure. The statement that all samples 'successfully superposed' is therefore partly a statement that a one-parameter shift can make each pressure dataset resemble the reference Cross model. If the Cross model does not represent the true reference flow curve within experimental error — especially for HDPE and BmPE, where η0 is extrapolated — model error will be absorbed into a_P and propagate into β via Eq. (20). The authors should report superposition residuals per pressure, per sample, and ideally demonstrate model-free overlap or compare with an alternative reference representation.
  2. [§3.2, Table 3; §3.4, Eq. (20)] For HDPE and BmPE the Newtonian plateau lies outside the accessible shear-rate range, so η0 is obtained by extrapolation through the Cross model. Because Eq. (20) uses η0(P) = η0(P0) a_P(P) b_P(P), the Barus coefficient inherits all extrapolation uncertainty. The paper reports neither confidence intervals for η0 nor for β, and Figure 7 shows only three points per sample. The claim that 'polydispersity has a negligible effect' and that 'both SCB and LCB significantly increase pressure sensitivity' needs a quantitative uncertainty analysis: standard errors on β, sensitivity to the extrapolation range, and ideally a comparison with an alternative functional form for the pressure dependence.
  3. [§2.1, Table 1; §3.4] The four commercial samples do not isolate the structural variables. BmPE contains both LCB and SCB (octene comonomer), so its β cannot be attributed to LCB alone; LLDPE and LmPE differ in comonomer type (octene vs butene), comonomer content, and PDI (3.8 vs 2.3), and HDPE is made with a different catalyst and has PDI 13.6. The pairwise comparisons in §3.4 that attribute differences in β to SCB, LCB, and PDI are therefore confounded by residual material differences. The authors should explicitly acknowledge this limitation and, if possible, add compositional/MWD characterization or use more matched samples to support the attribution.
  4. [§3.4, Figure 7, Table 3] There is a numerical inconsistency between the text and the table: §3.4 states BmPE has β = 25.1 GPa⁻¹ and LLDPE/LmPE have β ≈ 19.5 GPa⁻¹, while Table 3 lists 25.00, 18.67, and 18.44 GPa⁻¹, respectively. Additionally, no uncertainty or goodness-of-fit measure is given for the linear fits in Figure 7. These values are central to the paper's main claim, so the discrepancy and the missing error analysis must be resolved.
minor comments (4)
  1. [Keywords] Typo: 'Burus model' should be 'Barus model'.
  2. [§3.3] There is a dangling 'Error! Reference source not found.' after Eq. (16) that must be corrected.
  3. [§3.4] The text says LLDPE has PDI 2.1, but Table 1 lists 3.8 for LLDPE and 2.3 for LmPE. Please verify the correct value.
  4. [§3.3, Figures 3–6] The figures would be much more informative if the superposition residuals were shown (e.g., relative deviation of shifted data from the reference Cross curve). Residuals are essential for judging whether the master curves are statistically consistent.

Circularity Check

1 steps flagged

Model-based superposition makes the piezorheological-simplicity claim partly self-fulfilling, but β differences are still data-driven and the overall derivation is not definitionally circular.

specific steps
  1. self definitional [§3.3, Eq. 13 and following paragraph; conclusion of §3.3]
    "where fitting parameters, η0(P0), λ(P0), and m(P0), are independent of pressure, and thus parameters obtained for 0.1 MPa are valid for data at the other pressures. ... the rheological data for each polymer was able to be successfully superposed onto a single master curve using a single pressure shift factor, a_P(P) for each pressure. This indicates that all four samples, regardless of their molecular structure, exhibit piezorheologically simple behavior"

    Eq. 13 fixes the Cross-model shape (η0(P0), λ(P0), m(P0)) as pressure-independent and defines a_P(P) as the single horizontal shift minimizing deviation from that reference model. The subsequent 'successful superposition' claim is therefore the output of the same least-squares minimization rather than an independent raw-data collapse test, and the conclusion that pressure does not alter shear thinning is exactly the pressure-independence assumption inserted in Eq. 13. Because the paper states there were no overlapping data points at 0.1 MPa, the fit cannot validate the assumed shape unless residuals or per-pressure uncertainties are reported, which they are not; the β values in Table 3 inherit any bias in a_P. The step is only partly circular: a single a_P could still fail to bring all pre

full rationale

The central claim is experimental rather than a first-principles derivation, so circularity must be assessed in how superposition and β are constructed. The main issue is that a_P(P) is obtained by least-squares fitting reduced stress data to the 0.1 MPa Cross model with η0, λ, and m fixed as pressure-independent (Eq. 13). This makes 'piezorheologically simple behavior' and 'pressure does not alter shear-thinning' partly restate the fitting ansatz, not a fully independent data-collapse test. It is not fully forced, because a poor fit would be possible in principle and the raw shifted data are shown, but no residuals or superposition-quality metrics are reported, and η0 for HDPE/BmPE is extrapolated, so the β ranking carries unquantified model error. The self-citations (refs 14, 55, 96) are used as methods or prior observations and are not load-bearing uniqueness claims; the structural attribution (SCB vs LCB vs PDI) is confounded by sample design rather than circular. Overall this is one low-to-moderate construction step in the superposition claim, not a collapse of the paper's central derivation into its inputs.

Axiom & Free-Parameter Ledger

6 free parameters · 10 axioms · 0 invented entities

No new physical entities are introduced. The 'global brake' activation-volume picture is a mechanistic interpretation, not a new entity. The ledger is dominated by empirical fitting: Cross parameters, Tait parameters, pressure shift factors, and the Barus β all come from fits to the measured curves.

free parameters (6)
  • Cross model η0(P0) per sample = HDPE 31.29; LLDPE 11.4; LmPE 8.40; BmPE 53.2 kPa·s (Table 3)
    Fitted to 0.1 MPa flow curves; η0(P) = η0(P0)·a_P·b_P is the quantity whose pressure slope defines β.
  • Cross model λ(P0) per sample = HDPE 2.43; LLDPE 0.15; LmPE 0.029; BmPE 7.85 s (Table 3)
    Characteristic time from Cross fit; λ(P) = λ(P0)·a_P is used to shift the shear-rate axis.
  • Cross model exponent m(P0) per sample = HDPE 0.577; LLDPE 0.662; LmPE 0.725; BmPE 0.541 (Table 3)
    Shape exponent; assumed constant with pressure, which underpins the claim that pressure does not alter shear-thinning.
  • Tait parameters v0, v1, B0, B1 per sample = Table 2 (16 numbers)
    Fitted to PVT data; used to compute b_P(P), the vertical shift factor at rheometer pressures.
  • Horizontal pressure shift factors a_P at 23/46/69 MPa = Table 3 (12 values; e.g., BmPE 1.846/3.000/5.287, HDPE 1.312/1.613/2.137)
    Obtained by least-squares alignment of reduced stress onto the reference Cross model; central to β.
  • Barus pressure coefficient β per sample = HDPE 10.87; LLDPE 18.67; LmPE 18.44; BmPE 25.00 GPa⁻¹ (Table 3)
    Slope of ln[a_P b_P] vs P; the headline output, not independently measured.
axioms (10)
  • domain assumption Tait/Wohl equation describes PVT behavior
    Eqs. 1–3; empirical EOS used to interpolate specific volume, and hence b_P, at rheometer pressures.
  • domain assumption Barus exponential pressure dependence
    Eq. 20; assumed to extract β from only three pressure points (23, 46, 69 MPa).
  • domain assumption A single horizontal shift factor suffices over the entire shear-rate range
    Eqs. 13/16–18; the superposition premise being tested. Since a_P is fitted to the reference Cross model, success is partly by construction.
  • domain assumption Vertical shift factor equals density ratio only
    Eq. 5; ignores any intrinsic modulus change beyond density.
  • domain assumption No wall slip below 100 kPa
    Section 2.2.4; upper shear rate is chosen so stress stays below 100 kPa, citing ref 44.
  • domain assumption Thermal degradation is negligible (<5% in 5 h)
    Section 2.2.2; SAOS time sweep at 1 rad/s and 5% strain; extrapolated to all samples and pressures.
  • domain assumption BmPE LCB content and thermorheological complexity are taken from literature
    Table 1 and §3.3 rely on refs 96/103 for LCB = 0.06/1000 C and ref 73 for TTS failure; not measured in this paper.
  • ad hoc to paper Samples isolate SCB/LCB/PDI effects
    Table 1/§2.1: BmPE has both LCB and SCB, LLDPE/LmPE differ in comonomer and PDI, HDPE has a different catalyst and broad MWD; the comparison assumes residual differences are negligible.
  • ad hoc to paper Uniform activation volume for all relaxation modes
    §3.3 explanation of piezosimplicity (pressure as a global brake); a proposed mechanism not directly tested.
  • domain assumption Cross model adequately represents flow curves at all pressures
    Eqs. 7–8 fit at 0.1 MPa; Eq. 18 extrapolates to high pressure using the same m(P0).

pith-pipeline@v1.3.0-alltime-deepseek · 35 in / 16025 out tokens · 164804 ms · 2026-08-01T04:41:22.639700+00:00 · methodology

0 comments
read the original abstract

The rheological behavior of polymer melts under high pressure is a critical factor in many industrial processes like injection molding and extrusion, yet it is often inadequately characterized. At operating pressures that can exceed 100 MPa, viscosity can increase by orders of magnitude, making atmospheric-pressure data insufficient for accurate process simulation. This pressure induced viscosity increase is highly dependent on molecular architectures of the materials. This study aims to deconstruct the influence of specific structural features such as short-chain branching (SCB), long-chain branching (LCB), and polydispersity on the pressure sensitivity of the viscosity of polyethylene. Utilizing a high-pressure sliding plate rheometer (HPSPR) to ensure accurate measurements under uniform shear and pressure, we characterized four distinct polyethylene melts. All samples, regardless of their structure, exhibited piezorheologically simple behavior, allowing the application of time-pressure superposition over the entire shear rate range. A key finding is that the long-chain branched sample, known from the literature to be thermorheologically complex, was found to be piezorheologically simple. This dichotomy is explained by the different physical mechanisms of temperature and pressure. The pressure sensitivity of the viscosity, quantified by the pressure-viscosity coefficient, was found to be strongly dependent on molecular branching. Both SCB and LCB significantly increase the pressure sensitivity while polydispersity had a negligible effect. These results demonstrate that molecular branches are the dominant structural parameter controlling the rheological response of polyethylene to pressure, providing crucial insights for the development of more accurate predictive models for high-pressure polymer processing.

discussion (0)

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

Reference graph

Works this paper leans on

105 extracted references · 79 canonical work pages

  1. [1]

    Recycling and rheology of poly(lactic acid) (PLA) to make foams using supercritical fluid

    Lin, L.; Lee, Y.; Park, H.E. Recycling and rheology of poly(lactic acid) (PLA) to make foams using supercritical fluid. Physics of Fluids 2021, 33, doi:10.1063/5.0050649

    work page doi:10.1063/5.0050649 2021

  2. [2]

    -J.; Park, H.E.; Cho, B

    An, H. -J.; Park, H.E.; Cho, B. -U. Effect of Temperature of Tetraethylammonium Hydroxide/Urea/Cellulose Solution on Surface Tension and Cellulose Bead Size. Journal of Korea Technical Association of The Pulp and Paper Industry 2021, 53, 69-76, doi:10.7584/jktappi.2021.12.53.6.69

    work page doi:10.7584/jktappi.2021.12.53.6.69 2021

  3. [3]

    Xu, F.; Park, H.E.; Cho, B. -U. Porous carboxymethylcellulose/polyethyleneimine composite beads: formation process, enhanced physical properties, and pH -induced response mechanism. Cellulose 2024, 31, 6295 -6316, doi:10.1007/s10570-024-05987-6

    work page doi:10.1007/s10570-024-05987-6 2024

  4. [4]

    Controlling coefficients of thermal expansion in thermoplastic materials: effects of zinc cyanide and ionic liquid

    Egerton, S.; Sim, C.; Park, H.E.; Staiger, M.P.; Patil, K.M.; Cowan, M.G. Controlling coefficients of thermal expansion in thermoplastic materials: effects of zinc cyanide and ionic liquid. Materials Advances 2022, 3, 4155- 4158, doi:10.1039/d2ma00338d

    work page doi:10.1039/d2ma00338d 2022

  5. [5]

    Enhanced Degradability, Mechanical Properties, and Flame Retardation of Poly(Lactic Acid) Composite with New Zealand Jade (Pounamu) Particles

    Lin, L.; Dang, Q.A.; Park, H.E. Enhanced Degradability, Mechanical Properties, and Flame Retardation of Poly(Lactic Acid) Composite with New Zealand Jade (Pounamu) Particles. Polymers 2023, 15, doi:10.3390/polym15153270

    work page doi:10.3390/polym15153270 2023

  6. [6]

    Biodegradable Composite Film of Brewers’ Spent Grain and Poly(Vinyl Alcohol)

    Lin, L.; Mirkin, S.; Park, H.E. Biodegradable Composite Film of Brewers’ Spent Grain and Poly(Vinyl Alcohol). Processes 2023, 11, doi:10.3390/pr11082400

    work page doi:10.3390/pr11082400 2023

  7. [7]

    Enhancing Biodegradation of Poly(lactic acid) in Compost at Room Temperature by Compounding Jade Particles

    Lin, L.; Joe, M.; Dang, Q.A.; Park, H.E. Enhancing Biodegradation of Poly(lactic acid) in Compost at Room Temperature by Compounding Jade Particles. Polymers 2025, 17, doi:10.3390/polym17152037

    work page doi:10.3390/polym17152037 2025

  8. [8]

    Capillary flow of sodium and zinc ionomers

    Zuliki, M.; Zhang, S.; Tomkovic, T.; Hatzikiriakos, S.G. Capillary flow of sodium and zinc ionomers. Physics of Fluids 2020, 32, doi:10.1063/1.5145303

    work page doi:10.1063/1.5145303 2020

  9. [9]

    A review of the state-of-the-art nanofluid spray and jet impingement cooling

    Tyagi, P.K.; Kumar, R.; Mondal, P.K. A review of the state-of-the-art nanofluid spray and jet impingement cooling. Physics of Fluids 2020, 32, doi:10.1063/5.0033503

    work page doi:10.1063/5.0033503 2020

  10. [10]

    -Q.; Tian, F.-B

    Ma, J.; Huang, Q.; Zhu, Y.; Xu, Y. -Q.; Tian, F.-B. Effects of fluid rheology on dynamics of a capsule through a microchannel constriction. Physics of Fluids 2023, 35, doi:10.1063/5.0165614. - 18 -

    work page doi:10.1063/5.0165614 2023

  11. [11]

    On viscoelastic cavitating flows: A numerical study

    Naseri, H.; Koukouvinis, P.; Malgarinos, I.; Gavaises, M. On viscoelastic cavitating flows: A numerical study. Physics of Fluids 2018, 30, doi:10.1063/1.5011978

    work page doi:10.1063/1.5011978 2018

  12. [12]

    A fundamental rule: Determining the importance of flow prior to polymer crystallization

    McIlroy, C. A fundamental rule: Determining the importance of flow prior to polymer crystallization. Physics of Fluids 2019, 31, doi:10.1063/1.5129119

    work page doi:10.1063/1.5129119 2019

  13. [13]

    Van Gurp –Palmen relations for long -chain branching from general rigid bead -rod theory

    Kanso, M.A.; Giacomin, A.J. Van Gurp –Palmen relations for long -chain branching from general rigid bead -rod theory. Physics of Fluids 2020, 32, doi:10.1063/5.0004513

    work page doi:10.1063/5.0004513 2020

  14. [14]

    Effects of pressure and supercritical fluids on the viscosity of polyethylene

    Park, H.E.D., J.M. Effects of pressure and supercritical fluids on the viscosity of polyethylene. Macromolecules 2006, 39, 5438-5452, doi:10.1021/ma060735+

    work page doi:10.1021/ma060735 2006

  15. [15]

    WLF model for the pressure dependence of zero shear viscosity of polycarbonate

    Rudolph, N.M.; Agudelo, A.C.; Granada, J.C.; Park, H.E.; Osswald, T.A. WLF model for the pressure dependence of zero shear viscosity of polycarbonate. Rheologica Acta 2016, 55, 673-681, doi:10.1007/s00397-016-0945-4

    work page doi:10.1007/s00397-016-0945-4 2016

  16. [16]

    High Pressure Rheology for Quantitative Elastohydrodynamics, 2nd ed.; Elsevier: 2019

    Bair, S.S. High Pressure Rheology for Quantitative Elastohydrodynamics, 2nd ed.; Elsevier: 2019

    2019

  17. [17]

    Large Deformation of Materials With Complex Rheological Properties at Normal and High Pressure; Nova Science Pub Inc: 1996

    Levitas, V.I. Large Deformation of Materials With Complex Rheological Properties at Normal and High Pressure; Nova Science Pub Inc: 1996

    1996

  18. [18]

    A novel method for determining the pressure dependent characteristics of polymer melt during micro injection molding

    Liu, J.; Zhao, B.; Kontziampasis, D.; Jiang, B.; Wu, W. A novel method for determining the pressure dependent characteristics of polymer melt during micro injection molding. Polymer Testing 2024, 137, doi:10.1016/j.polymertesting.2024.108520

    arXiv 2024

  19. [19]

    Annular Newtonian Poiseuille flow with pressure -dependent wall slip

    Housiadas, K.D.; Gryparis, E.; Georgiou, G.C. Annular Newtonian Poiseuille flow with pressure -dependent wall slip. European Journal of Mechanics - B/Fluids 2025, 109, 299-308, doi:10.1016/j.euromechflu.2024.10.012

    work page doi:10.1016/j.euromechflu.2024.10.012 2025

  20. [20]

    Pressure-Dependent Yield Stress of Organoclay-Based Gels

    Burger, N.A.; Loppinet, B.; Clarke, A.; Petekidis, G. Pressure-Dependent Yield Stress of Organoclay-Based Gels. Langmuir 2025, 41, 20638-20647, doi:10.1021/acs.langmuir.5c02052

    work page doi:10.1021/acs.langmuir.5c02052 2025

  21. [21]

    Effect of temperature on gelation and cross -linking of gelatin methacryloyl for biomedical applications

    Park, H.E.; Gasek, N.; Hwang, J.; Weiss, D.J.; Lee, P.C. Effect of temperature on gelation and cross -linking of gelatin methacryloyl for biomedical applications. Physics of Fluids 2020, 32, doi:10.1063/1.5144896

    work page doi:10.1063/1.5144896 2020

  22. [22]

    Porcine Lung-Derived Extracellular Matrix Hydrogel Properties Are Dependent on Pepsin Digestion Time

    Pouliot, R.A.; Young, B.M.; Link, P.A.; Park, H.E.; Kahn, A.R.; Shankar, K.; Schneck, M.B.; Weiss, D.J.; Heise, R.L. Porcine Lung-Derived Extracellular Matrix Hydrogel Properties Are Dependent on Pepsin Digestion Time. Tissue Engineering Part C: Methods 2020, 26, 332-346, doi:10.1089/ten.tec.2020.0042

    arXiv 2020

  23. [23]

    Development of alginate and gelatin -based pleural and tracheal sealants

    Gasek, N.; Park, H.E.; Uriarte, J.J.; Uhl, F.E.; Pouliot, R.A.; Riveron, A.; Moss, T.; Phillips, Z.; Louie, J.; Sharma, I.; et al. Development of alginate and gelatin -based pleural and tracheal sealants. Acta Biomaterialia 2021, 131, 222-235, doi:10.1016/j.actbio.2021.06.048

    work page doi:10.1016/j.actbio.2021.06.048 2021

  24. [24]

    Pressure Effect on the Rheological Behavior of Highly Filled Solid Propellant During Extrusion Flow

    Zhang, J.; Zheng, W.; Yuan, Z.; Chen, J.; Pei, J.; Xue, P. Pressure Effect on the Rheological Behavior of Highly Filled Solid Propellant During Extrusion Flow. Polymers 2025, 17, doi:10.3390/polym17152003

    work page doi:10.3390/polym17152003 2025

  25. [25]

    Rheology in the Presence of Carbon Dioxide (CO2) to Study the Melt Behavior of Chemically Modified Polylactide (PLA)

    Dörr, D.; Standau, T.; Murillo Castellón, S.; Bonten, C.; Altstädt, V. Rheology in the Presence of Carbon Dioxide (CO2) to Study the Melt Behavior of Chemically Modified Polylactide (PLA). Polymers 2020, 12, doi:10.3390/polym12051108

    work page doi:10.3390/polym12051108 2020

  26. [26]

    Influence of Carbon Dioxide on the Glass Transition of Styrenic and Vinyl Pyridine Polymers: Comparison of Calorimetric, Creep, and Rheological Experiments

    Harden, F.; Kargar, M.; Handge, U.A.; Mari, M. Influence of Carbon Dioxide on the Glass Transition of Styrenic and Vinyl Pyridine Polymers: Comparison of Calorimetric, Creep, and Rheological Experiments. Advances in Polymer Technology 2022, 2022, 1-15, doi:10.1155/2022/5602902

    work page doi:10.1155/2022/5602902 2022

  27. [27]

    Dynamics and Rheology of Supramolecular Assemblies at Elevated Pressures

    Burger, N.A.; Meier, G.; Bouteiller, L.; Loppinet, B.; Vlassopoulos, D. Dynamics and Rheology of Supramolecular Assemblies at Elevated Pressures. The Journal of Physical Chemistry B 2022, 126, 6713 -6724, doi:10.1021/acs.jpcb.2c03295

    work page doi:10.1021/acs.jpcb.2c03295 2022

  28. [28]

    Advances and challenges in the high-pressure rheology of complex fluids

    Ahuja, A.; Lee, R.; Joshi, Y.M. Advances and challenges in the high-pressure rheology of complex fluids. Advances in Colloid and Interface Science 2021, 294, doi:10.1016/j.cis.2021.102472

    arXiv 2021

  29. [29]

    A novel theoretical strategy for modeling viscosity of polymer melts: Modified friction theory with PC-SAFT

    Fan, W.; Ji, Y. A novel theoretical strategy for modeling viscosity of polymer melts: Modified friction theory with PC-SAFT. Fluid Phase Equilibria 2021, 550, doi:10.1016/j.fluid.2021.113262

    arXiv 2021

  30. [30]

    Effect of Different Pressures on Polymer Flow at a Contraction Path: A Real - Time Numerical Approach

    Azmi, M.A.; Ariff, Z.M.; Shuib, R.K.; Rusli, A.; Ku Ishak, K.M.; Shafiq, M.D.; Abdul Hamid, Z.A.; Zakaria, Z.; Abu Bakar, M.H.; Abdullah, M.K. Effect of Different Pressures on Polymer Flow at a Contraction Path: A Real - Time Numerical Approach. Makara Journal of Technology 2024, 28, 80-88, doi:10.7454/mst.v28i3.1678

    work page doi:10.7454/mst.v28i3.1678 2024

  31. [31]

    Strategy of Coupling Artificial Intelligence with Thermodynamic Mechanism for Predicting Complex Polymer Viscosities

    Wang, S.; Sadowski, G.; Ji, Y. Strategy of Coupling Artificial Intelligence with Thermodynamic Mechanism for Predicting Complex Polymer Viscosities. ACS Sustainable Chemistry & Engineering 2024, 12, 4631 -4643, doi:10.1021/acssuschemeng.3c08185

    work page doi:10.1021/acssuschemeng.3c08185 2024

  32. [32]

    Measurement Techniques and Methods for the Pressure Coefficient of Viscosity of Polymer Melts

    Liao, Y.; Hu, Y.; Tan, Y.; Ikeda, K.; Okabe, R.; Wu, R.; Ozaki, R.; Xu, Q.; Munoz -Espi, R. Measurement Techniques and Methods for the Pressure Coefficient of Viscosity of Polymer Melts. Advances in Polymer Technology 2023, 2023, 1-15, doi:10.1155/2023/2020247

    work page doi:10.1155/2023/2020247 2023

  33. [33]

    In-situ measurement of transient polymer melt flow at injection mold gate using pressure sensing and mass conservation principle

    Chen, J.-Y.; Chen, X.-P.; Huang, M.-S. In-situ measurement of transient polymer melt flow at injection mold gate using pressure sensing and mass conservation principle. Measurement 2025, 256, - 19 - doi:10.1016/j.measurement.2025.118246

    arXiv 2025

  34. [34]

    Influence of hydrostatic pressure on rheological properties of polymer melts —A review

    Münstedt, H. Influence of hydrostatic pressure on rheological properties of polymer melts —A review. Journal of Rheology 2020, 64, 751-774, doi:10.1122/1.5142059

    work page doi:10.1122/1.5142059 2020

  35. [35]

    A Review of High-Temperature and High-Pressure Experimental Apparatus Capable of Generating Differential Stress

    Ren, D.; Li, H. A Review of High-Temperature and High-Pressure Experimental Apparatus Capable of Generating Differential Stress. Frontiers in Earth Science 2022, 10, doi:10.3389/feart.2022.852403

    arXiv 2022

  36. [36]

    Research on the Pressure Control Technology of Ultra-high Temperature & High Pressure Rheometer

    Tianfu, H.; Meinan, L.; Yanbin, C.; Qi, W. Research on the Pressure Control Technology of Ultra-high Temperature & High Pressure Rheometer. Procedia Engineering 2014, 73, 172-177, doi:10.1016/j.proeng.2014.06.185

    work page doi:10.1016/j.proeng.2014.06.185 2014

  37. [37]

    Evaluation and comparison of routes to obtain pressure coefficients from high-pressure capillary rheometry data

    Cardinaels, R.; Van Puyvelde, P.; Moldenaers, P. Evaluation and comparison of routes to obtain pressure coefficients from high-pressure capillary rheometry data. Rheologica Acta 2006, 46, 495-505, doi:10.1007/s00397- 006-0148-5

    work page doi:10.1007/s00397- 2006

  38. [38]

    Measurement of pressure coefficient of melt viscosity: drag flow versus capillary flow

    Park, H.E.; Lim, S.T.; Laun, H.M.; Dealy, J.M. Measurement of pressure coefficient of melt viscosity: drag flow versus capillary flow. Rheologica Acta 2008, 47, 1023-1038, doi:10.1007/s00397-008-0296-x

    work page doi:10.1007/s00397-008-0296-x 2008

  39. [39]

    Untersuchungen über die Zustandsgleichung

    Wohl, A. Untersuchungen über die Zustandsgleichung. Zeitschrift für Physikalische Chemie 1921, 99U, 234-241, doi:10.1515/zpch-1921-9918

    work page doi:10.1515/zpch-1921-9918 1921

  40. [40]

    Report on some of the physical properties of fresh water and of sea -water

    Tait, P.G. Report on some of the physical properties of fresh water and of sea -water. In Report on the Scientific Results of the Voyage of H.M.S. Challenger during the Years 1873 -1876: Physics and Chemistry, Vol II, Part IV 1888, Tait, P.G., Ed.; Cambridge University Press: Cambridge, 1900; pp. 1-355

    1900

  41. [41]

    Study of the Compressions of Several High Molecular Weight Hydrocarbons

    Cutler, W.G.; McMickle, R.H.; Webb, W.; Schiessler, R.W. Study of the Compressions of Several High Molecular Weight Hydrocarbons. The Journal of Chemical Physics 1958, 29, 727-740, doi:10.1063/1.1744583

    work page doi:10.1063/1.1744583 1958

  42. [42]

    Transport Phenomena, Revised 2nd Edition ed.; John Wiley & Sons: Danvers, MA, 2007

    Bird, R.B.S., Warren E.; Lightfoot, Edwin N. Transport Phenomena, Revised 2nd Edition ed.; John Wiley & Sons: Danvers, MA, 2007

    2007

  43. [43]

    Standard Pressure -Volume-Temperature Data for Polymers ; Technomic Publishing: Lancaster, Pennsylvania, 1995

    Zoller, P.W., David J. Standard Pressure -Volume-Temperature Data for Polymers ; Technomic Publishing: Lancaster, Pennsylvania, 1995

    1995

  44. [44]

    Wall slip and spurt flow of polybutadiene

    Park, H.E.; Lim, S.T.; Smillo, F.; Dealy, J.M.; Robertson, C.G. Wall slip and spurt flow of polybutadiene. Journal of Rheology 2008, 52, 1201-1239, doi:10.1122/1.2964199

    work page doi:10.1122/1.2964199 2008

  45. [45]

    Polydispersity influence in rheological behavior of linear chains by molecular dynamics

    Blanco-Dí az, E.G.; Castrejón -González, E.O.; Rico -Ramí rez, V.; Aztatzi -Pluma, D.; Dí az -Ovalle, C.O. Polydispersity influence in rheological behavior of linear chains by molecular dynamics. Journal of Molecular Liquids 2018, 268, 832-839, doi:10.1016/j.molliq.2018.07.099

    work page doi:10.1016/j.molliq.2018.07.099 2018

  46. [46]

    Viscosity model for polydisperse polymer melts

    Nichetti, D.; Manas-Zloczower, I. Viscosity model for polydisperse polymer melts. Journal of Rheology 1998, 42, 951-969, doi:10.1122/1.550908

    work page doi:10.1122/1.550908 1998

  47. [47]

    Effects of the Polydispersity on Rheological Properties of Entangled Polystyrene Solutions

    Ye, X.; Sridhar, T. Effects of the Polydispersity on Rheological Properties of Entangled Polystyrene Solutions. Macromolecules 2005, 38, 3442-3449, doi:10.1021/ma049642n

    work page doi:10.1021/ma049642n 2005

  48. [48]

    Effects of pressure and dissolved carbon dioxide on the rheological properties of molten polymers

    Park, H.E. Effects of pressure and dissolved carbon dioxide on the rheological properties of molten polymers. McGill University, Montreal, Quebec, Canada, 2005

    2005

  49. [49]

    Ü ber die Reaktionsgeschwindigkeit bei der Inversion von Rohrzucker durch Säuren

    Arrhenius, S. Ü ber die Reaktionsgeschwindigkeit bei der Inversion von Rohrzucker durch Säuren. Zeitschrift für Physikalische Chemie 1889, 4U, 226-248, doi:10.1515/zpch-1889-0416

    doi:10.1515/zpch-1889-0416

  50. [50]

    Viscosity, Plasticity, and Diffusion as Examples of Absolute Reaction Rates

    Eyring, H. Viscosity, Plasticity, and Diffusion as Examples of Absolute Reaction Rates. The Journal of Chemical Physics 1936, 4, 283-291, doi:10.1063/1.1749836

    doi:10.1063/1.1749836 1936

  51. [51]

    Theory of the Viscosity of Liquids as a Function of Temperature and Pressure

    Ewell, R.H.; Eyring, H. Theory of the Viscosity of Liquids as a Function of Temperature and Pressure. The Journal of Chemical Physics 1937, 5, 726-736, doi:10.1063/1.1750108

    work page doi:10.1063/1.1750108 1937

  52. [52]

    Isothermals, isopiestics and isometrics relative to viscosity

    Barus, C. Isothermals, isopiestics and isometrics relative to viscosity. American Journal of Science 1893, s3-45, 87- 96, doi:10.2475/ajs.s3-45.266.87

    doi:10.2475/ajs.s3-45.266.87

  53. [53]

    Untersuchungen Aber die innere Reibnng der Flüssigkeiten

    Batschinski, A.J. Untersuchungen Aber die innere Reibnng der Flüssigkeiten. I. Zeitschrift für Physikalische Chemie 1913, 84U, 643-706, doi:10.1515/zpch-1913-8442

    work page doi:10.1515/zpch-1913-8442 1913

  54. [54]

    The Temperature Dependence of Relaxation Mechanisms in Amorphous Polymers and Other Glass -forming Liquids

    Williams, M.L.; Landel, R.F.; Ferry, J.D. The Temperature Dependence of Relaxation Mechanisms in Amorphous Polymers and Other Glass -forming Liquids. Journal of the American Chemical Society 2002, 77, 3701 -3707, doi:10.1021/ja01619a008

    doi:10.1021/ja01619a008 2002

  55. [55]

    Influence of long-chain branching on time-pressure and time-temperature shift factors for polystyrene and polyethylene

    Park, H.E.; Dealy, J.; Münstedt, H. Influence of long-chain branching on time-pressure and time-temperature shift factors for polystyrene and polyethylene. Rheologica Acta 2006, 46, 153-159, doi:10.1007/s00397-006-0116-0

    work page doi:10.1007/s00397-006-0116-0 2006

  56. [56]

    The free volume interpretation of the dependence of viscosities and viscoelastic relaxation times on concentration, pressure, and tensile strain

    Ferry, J.D.; Stratton, R.A. The free volume interpretation of the dependence of viscosities and viscoelastic relaxation times on concentration, pressure, and tensile strain. Kolloid-Zeitschrift 1960, 171, 107 -111, doi:10.1007/bf01520041

    work page doi:10.1007/bf01520041 1960

  57. [57]

    Role of Free Volume in the Pressure Dependence of the Viscosity of Liquids

    Matheson, A.J. Role of Free Volume in the Pressure Dependence of the Viscosity of Liquids. The Journal of Chemical Physics 1966, 44, 695-699, doi:10.1063/1.1726747. - 20 -

    work page doi:10.1063/1.1726747 1966

  58. [58]

    Rheology and Structure of Molten, Olefin Multiblock Copolymers

    Park, H.E.; Dealy, J.M.; Marchand, G.R.; Wang, J.; Li, S.; Register, R.A. Rheology and Structure of Molten, Olefin Multiblock Copolymers. Macromolecules 2010, 43, 6789-6799, doi:10.1021/ma1012122

    work page doi:10.1021/ma1012122 2010

  59. [59]

    Evaluation of molecular linear viscoelastic models for polydisperse H polybutadienes

    Li, S.W.; Park, H.E.; Dealy, J.M. Evaluation of molecular linear viscoelastic models for polydisperse H polybutadienes. Journal of Rheology 2011, 55, 1341-1373, doi:10.1122/1.3635384

    work page doi:10.1122/1.3635384 2011

  60. [60]

    On the pressure dependency of the viscosity of molten polymers

    Kadijk, S.E.; Van Den Brule, B.H.A.A. On the pressure dependency of the viscosity of molten polymers. Polymer Engineering & Science 2004, 34, 1535-1546, doi:10.1002/pen.760342004

    work page doi:10.1002/pen.760342004 2004

  61. [61]

    Pressure and Temperature Dependence of LDPE Viscosity and Free Volume: The Effect of Molecular Structure

    Sedlacek, T.; Lengalova, A.; Zatloukal, M.; Cermak, R.; Saha, P. Pressure and Temperature Dependence of LDPE Viscosity and Free Volume: The Effect of Molecular Structure. International Polymer Processing 2006, 21, 98- 103, doi:10.3139/217.1909

    work page doi:10.3139/217.1909 2006

  62. [62]

    Properties of Polymers: Their Correlation with Chemical Structure; Their Numerica Estimation and Prediction from Additive Group Contributions, 4th ed.; Elsevier: Amsterdam, 2009

    Van Krevelen, D.W.T.N., K. Properties of Polymers: Their Correlation with Chemical Structure; Their Numerica Estimation and Prediction from Additive Group Contributions, 4th ed.; Elsevier: Amsterdam, 2009

    2009

  63. [63]

    The effects of pressure and temperature upon the viscosities of liquids with special reference to polymeric liquids

    Cogswell, F.N.; McGowan, J.C. The effects of pressure and temperature upon the viscosities of liquids with special reference to polymeric liquids. British Polymer Journal 2007, 4, 183-198, doi:10.1002/pi.4980040304

    work page doi:10.1002/pi.4980040304 2007

  64. [64]

    The Effect of Temperature and Pressure on the Mechanical Properties of Thermo- and/or Piezorheologically Simple Polymeric Materials in Thermodynamic Equilibrium – A Critical Review

    Tschoegl, N.W.; Knauss, W.G.; Emri, I. The Effect of Temperature and Pressure on the Mechanical Properties of Thermo- and/or Piezorheologically Simple Polymeric Materials in Thermodynamic Equilibrium – A Critical Review. Mechanics of Time-Dependent Materials 2002, 6, 53-99, doi:10.1023/a:1014421519100

    work page doi:10.1023/a:1014421519100 2002

  65. [65]

    Viscoelastic Relaxation Modulus Characterization Using Prony Series

    Pacheco, J.E.L.; Bavastri, C.A.; Pereira, J.T. Viscoelastic Relaxation Modulus Characterization Using Prony Series. Latin American Journal of Solids and Structures 2015, 12, 420-445, doi:10.1590/1679-78251412

    work page doi:10.1590/1679-78251412 2015

  66. [66]

    Detecting Structural Polydispersity in Branched Polybutadienes

    Li, S.W.; Park, H.E.; Dealy, J.M.; Maric, M.; Lee, H.; Im, K.; Choi, H.; Chang, T.; Rahman, M.S.; Mays, J. Detecting Structural Polydispersity in Branched Polybutadienes. Macromolecules 2010, 44, 208 -214, doi:10.1021/ma101803h

    work page doi:10.1021/ma101803h 2010

  67. [67]

    Polymer-polymer interfacial slip in multilayered films

    Lee, P.C.; Park, H.E.; Morse, D.C.; Macosko, C.W. Polymer-polymer interfacial slip in multilayered films. Journal of Rheology 2009, 53, 893-915, doi:10.1122/1.3114370

    work page doi:10.1122/1.3114370 2009

  68. [68]

    Polymer-polymer interfacial slip by direct visualization and by stress reduction

    Park, H.E.L., Patrick C.; Macosko, Christopher W. Polymer-polymer interfacial slip by direct visualization and by stress reduction. Journal of Rheology 2010, 54, 1207-1218, doi:10.1122/1.3479389

    work page doi:10.1122/1.3479389 2010

  69. [69]

    In situ shrinking fibers enhance strain hardening and foamability of linear polymers

    Kim, E.S.; Park, H.E.; Lee, P.C. In situ shrinking fibers enhance strain hardening and foamability of linear polymers. Polymer 2018, 136, 1-5, doi:10.1016/j.polymer.2017.12.040

    work page doi:10.1016/j.polymer.2017.12.040 2018

  70. [70]

    Enhanced Foamability with Shrinking Microfibers in Linear Polymer

    Kim, E.S.; Park, H.E.; Lopez-Barron, C.R.; Lee, P.C. Enhanced Foamability with Shrinking Microfibers in Linear Polymer. Polymers 2019, 11, doi:10.3390/polym11020211

    work page doi:10.3390/polym11020211 2019

  71. [71]

    Temperature Dependence of the Viscoelastic Behavior of Polystyrene

    Plazek, D.J. Temperature Dependence of the Viscoelastic Behavior of Polystyrene. The Journal of Physical Chemistry 2002, 69, 3480-3487, doi:10.1021/j100894a039

    work page doi:10.1021/j100894a039 2002

  72. [72]

    Rheological Investigation of Polybutadienes Having Different Microstructures over a Large Temperature Range

    Zorn, R.; McKenna, G.B.; Willner, L.; Richter, D. Rheological Investigation of Polybutadienes Having Different Microstructures over a Large Temperature Range. Macromolecules 2002, 28, 8552 -8562, doi:10.1021/ma00129a014

    work page doi:10.1021/ma00129a014 2002

  73. [73]

    Thermorheological Behavior of Polyethylene: Effects of Microstructure and Long Chain Branching

    Wood-Adams, P.; Costeux, S. Thermorheological Behavior of Polyethylene: Effects of Microstructure and Long Chain Branching. Macromolecules 2001, 34, 6281-6290, doi:10.1021/ma0017034

    work page doi:10.1021/ma0017034 2001

  74. [74]

    Properties of amorphous and crystallizable hydrocarbon polymers

    Raju, V.R.; Rachapudy, H.; Graessley, W.W. Properties of amorphous and crystallizable hydrocarbon polymers. IV. Melt rheology of linear and star‐branched hydrogenated polybutadiene. Journal of Polymer Science: Polymer Physics Edition 2003, 17, 1223-1235, doi:10.1002/pol.1979.180170707

    arXiv 2003

  75. [75]

    High-pressure Rheological Measurement Methods: A Review

    Kulisiewicz, L.D., Antonio. High-pressure Rheological Measurement Methods: A Review. Applied Rheology 2009, 20, 13018

    2009

  76. [76]

    High pressure capillary rheometry of polymeric fluids

    Couch, M.A.; Binding, D.M. High pressure capillary rheometry of polymeric fluids. Polymer 2000, 41, 6323-6334, doi:10.1016/s0032-3861(99)00865-4

    work page doi:10.1016/s0032-3861(99)00865-4 2000

  77. [77]

    Hubmann, M.; Schuschnigg, S.; Ð uretek, I.; Groten, J.; Holzer, C. Enhancing High-Pressure Capillary Rheometer Viscosity Data Calculation with the Propagation of Uncertainties for Subsequent Cross-Williams, Landel, and Ferry (WLF) Parameter Fitting. Polymers 2023, 15, doi:10.3390/polym15143147

    work page doi:10.3390/polym15143147 2023

  78. [78]

    The multipass rheometer

    Mackley, M.R.; Marshall, R.T.J.; Smeulders, J.B.A.F. The multipass rheometer. Journal of Rheology 1995, 39, 1293-1309, doi:10.1122/1.550637

    work page doi:10.1122/1.550637 1995

  79. [79]

    Development of an improved falling ball viscometer for high-pressure measurements with supercritical CO2

    Calvignac, B.; Rodier, E.; Letourneau, J.-J.; Vitoux, P.; Aymonier, C.; Fages, J. Development of an improved falling ball viscometer for high-pressure measurements with supercritical CO2. The Journal of Supercritical Fluids 2010, 55, 96-106, doi:10.1016/j.supflu.2010.07.012

    work page doi:10.1016/j.supflu.2010.07.012 2010

  80. [80]

    High-pressure cell for measuring the zero-shear viscosity of polymer melts

    Mattischek, J.-P.; Sobczak, R. High-pressure cell for measuring the zero-shear viscosity of polymer melts. Review of Scientific Instruments 1997, 68, 2101-2105, doi:10.1063/1.1148076

    work page doi:10.1063/1.1148076 1997

Showing first 80 references.