International Journal of Polymer Science

International Journal of Polymer Science / 2015 / Article

Research Article | Open Access

Volume 2015 |Article ID 517260 | 6 pages |

Use of Rubber Process Analyzer for Characterizing the Molecular Weight Parameters of Natural Rubber

Academic Editor: Jan-Chan Huang
Received28 May 2015
Revised12 Aug 2015
Accepted13 Aug 2015
Published26 Aug 2015


The aim of this work is to introduce a simple and rapid method for characterizing the molecular weight parameters and other molecular structure parameters of natural rubber (NR) using a rubber process analyzer (RPA). In this work, NR of different molecular weights was prepared by milling. Molecular weight parameters were measured by gel permeation chromatography coupled with laser light scattering (GPC-LLS) for comparison with RPA results. It was verified that increasing of milling time leads to a decrease of the number-average molecular weight (), weight-average molecular weight (), and molecular weight distribution (MWD). The dynamic and rheological properties were evaluated on RPA by tests of strain sweep, frequency sweep, and stress relaxation. These results were used to characterize the average molecular weight, MWD, and viscosity of NR and were found to agree with those from GPC-LLS. This convenient and rapid technology for characterizing NR molecular weight parameters would be especially useful in the elastomer industry.

1. Introduction

Molecular weight is an important parameter for natural rubber (NR) characterization. A series of NR parameters (e.g., molecular weight, molecular weight distribution (MWD)) are commonly measured by gel permeation chromatography (GPC), laser light scattering (LLS), and nuclear magnetic resonance (NMR) [13]. Because these technologies are complicated and time consuming, an alternative simple and rapid technology is desired.

Mooney viscosity is a significant parameter that can be used to characterize the average molecular weight of raw rubber crudely. In the rubber industry, Mooney viscosity is a standard for evaluating raw rubber under ASTMD 1646 and ISO 289 [4] and has been used for characterizing raw rubber and mixed stocks for more than 70 years. Researches had shown that two styrene-butadiene rubber samples with different dynamic properties can have the same Mooney viscosity [5]. Therefore, this measurement alone cannot be used to characterize the elastomer molecular weight.

Polymer dynamic properties and rheological behavior are influenced by molecular weight, MWD, and long chain branching (LCB). Guimarães and coworkers [6] found that the rheological properties of high-density polyethylene/poly(ethylene-co-octene) metallocene elastomers (HDPE/EOC) blends are influenced significantly by the proportion of LCB and the molecular weight of the metallocene elastomer. Conversely, viscosity, elastic modulus, loss factor, and so forth can be used to give information about the molecular structure of polymer material. Zero-shear viscosity () is influenced by molecular weight, while and the relaxation spectrum can be used to calculate the molecular weight of polyethylene (PE) [7]. The shear-thinning phenomenon is very sharp in LCB polymers. Compared with linear molecular counterparts with the same molecular weight, LCB-PE has a higher shear viscosity at a low shear rate and a lower shear viscosity at high shear rate [8]. Azizi and coworkers [9] concluded that the melt flow index increased and the complex viscosity decreased with a decrease in polypropylene (PP) molecular weight. Moreover, the molecular weight and MWD were calculated from dynamic rheological data. In general, many studies have focused on the relationship between molecular structure and dynamic behavior.

The rubber process analyzer (RPA) is a dynamic mechanical rheological tester and it is universally used for characterizing raw elastomers and unvulcanized compounds [10]. Over the past 20 years, since the RPA was invented by Alpha Technologies, it has been used to characterize dynamic properties [11, 12], rheological properties [13], and the network structure [14] of elastomers. The blending of different elastomers and their compatibility [15], the dispersion of nanofillers in polymer matrices, and compatibility between filler and elastomers [16] are a major topic for application of the RPA to elastomers.

In summary, many studies have dealt with the characterization of polymer molecular structure by measurement of dynamic properties and rheological behavior, but limited research has focused on elastomers. Quite a few papers report that elastomer molecular weight and MWD characterization by RPA had been done.

In this work, NR with a series of different molecular weights was prepared by milling, and molecular weight parameters were measured by GPC-LLS. These parameters were then used as a reference standard for comparison with those obtained from RPA. The complex viscosity, relaxation times, elastic modulus, viscosity modulus, and loss factor measured by RPA were used to determine average molecular weight, MWD, and viscosity for NR with different milling times. Through this study, the molecular weight, MWD, and rheological properties of NR were characterized qualitatively using RPA.

2. Experimental

2.1. Material and Sample Preparation
2.1.1. Material

Natural rubber was purchased from Hainan Rubber Industry Group, China. Other chemicals were all of commercial grade.

2.1.2. Sample Preparation

Raw NR (300 g) was milled 5, 10, 15, 20, 25, and 30 times using a two-roller mill with 2 mm spacing. The milling temperature was 60°C. Milling was done in open air.

2.2. Measurements
2.2.1. Molecular Weight Analysis

Molecular weight was determined by GPC-LLS (GPC, Waters Corporation, USA). The GPC-LLS equipment consisted of an online degasser, an Agilent 1100 Series pump, a multiangle scattering detector (DAWN HELEOS, Wyatt Technology, Santa Barbara, CA, USA), online viscosity detector (Viscostar, Wyatt Technology, Santa Barbara, CA, USA), and refractive index detector (Optilab rEX model, Wyatt Technology, USA). The columns were two PL-MIXED-BL mixed bed columns (10 μm, 300 mm × 7.8 mm inner diameter) (Agilent). The columns were maintained at 30°C. The mobile phase, tetrahydrofuran (THF) (200 μL), was injected at a flow rate of 1.0 mL/min.

2.2.2. Mooney Viscosity [ML(1+4)100°C]

The ML(1+4)100°C was determined using a Mooney Viscometer (UM-2050, U-CAN, Taiwan) according to Chinese standard: GB/T 1232.1-2000.

2.2.3. RPA Analysis

An RPA2000 (Alpha Technologies, Akron, OH, USA) was used for dynamic and rheological measurements. The samples were cut from milled NR of about 6 g and placed into moulding chamber. A strain sweep was carried out at 1 Hz and 100°C. The frequency sweep was carried out at a strain of 14% and at 100°C. The stress relaxation was measured at a strain of 40% and at a temperature of 100°C, with a 2 min test time.

3. Results and Discussion

3.1. Molecular Weight

Gels are important components in NR but cannot be characterized by GPC and LLS. About the measurement method of molecular weight of NR, we often remove the gel portion and the sol portion is analyzed to determine the molecular weight. In general, the molecular weight measured by GPC-LLS represents the molecular weight of the sol portion. Table 1 shows the molecular weight averages and molecular weight distribution of NR milled a different number of times. With an increase in milling time, and decreased. The MWD decreases as the milling time increases, indicating that there is narrowing of the MWD as the milling time increases. It is proposed that the mechanical action decreases the molecular weight.


2.808 × 1052.163 × 1051.613 × 1051.272 × 1051.137 × 1051.106 × 105
3.736 × 1052.754 × 1052.039 × 1051.601 × 1051.417 × 1051.370 × 105

3.2. Mooney Viscosity

The Mooney viscosity is a basic parameter for characterizing NR and is used to evaluate the average molecular weight of the rubber material. Table 2 shows the ML(1+4) of NR milled 5, 10, 15, 20, 25, and 30 times. The greater the milling time, the lower the ML(1+4). The mechanical action therefore decreases the molecular weight and leads to a decrease in ML(1+4).



3.3. Viscosity

The complex viscosity obtained using the RPA is considered to be the apparent viscosity, because it corresponds closely to the apparent viscosity value measured using a capillary rheometer [13]. Equation (1) describes the relationship between apparent viscosity and shear rate, where and are rubber constants and and are the apparent viscosity and shear rate, respectively. Equation (2) is the natural logarithm of both sides of (1). A linear relationship exists between and . ConsiderFigure 1 shows a plot of complex viscosity versus shear rate for a frequency sweep test. An inverse linear relationship exists between and . The gradient of the straight line decreases with an increase in milling time.

Figure 2 shows a plot of complex viscosity versus shear rate for a strain sweep test. Two stages exist on the curves: a straight line parallel to axis and another similar to the frequency sweep.

For the stage parallel to axis, the constant is approximately equal to 1, and this represents a Newtonian behavior. For the other stage at higher strain, decreases with increased shear rate for the strain sweep. This is a shear-thinning behavior, a feature of non-Newtonian behavior, and is caused by the higher strain that destroys the molecular structure of the NR.

There is an obvious effect on the complex viscosity of NR with a different milling time. The value of decreases with an increase in milling time.

The value of zero-shear viscosity () of the NR cannot be calculated for different milling times. The value of is assumed to decrease with an increase in milling time, based on the drop of expressed by the straight line in Figures 1 and 2. The decrease in () is caused by a decrease in molecular weight of the NR.

3.4. Stress Relaxation

Figure 3 shows the stress relaxation of NR for different milling times. With an increase in milling time, the value of the elastic torque () decreases at the same relaxation time. Relaxation time is a polymer parameter used to characterize molecular motion and molecular structure. It not only depends on temperature and external force, but is also affected by the molecular structure and internal network of the polymer. Equation (3) expresses the relationship between stress relaxation time and stress , where is the initial stress. The elastic torque obtained from the stress relaxation measured by RPA is used as stress in this work. Equation (4) is obtained by rearranging (3) and shows the linear relationship between and time , where is the slope of the straight line in (4). A plot of versus time yields the linear relationship in Figure 4 with parameters in Table 3 calculated using (4). According to the results, the relaxation time and initial stress decrease in proportion to an increase in milling time. In general, with an increase in milling time, the relaxation time and initial stress decrease. The mechanical action causes the molecular weight to decrease, reduces molecular entanglement, and leads to ease of motion of the molecular chain. Hence,



: correlation coefficient.
3.5. Molecular Weight and Molecular Weight Distribution

The elastic modulus () and viscosity modulus () are two important parameters for characterizing the dynamic properties of the elastomer. represents the internal friction of the molecules in an elastomer. Under an external force, molecular chain orientation is caused by internal friction. When the elastomer molecular weight is lower than a certain value, there is a crossover point between the curves of and , which means that there is a balance in state of internal friction and disorientation [17]. With an increase in molecular weight, the crossover point moves to lower frequency because of restricted disorientation. The lower frequency allows for sufficient time for molecular orientation. The higher molecular weight molecules therefore need more time for molecular orientation. According to (5), is the crossover point which is in inverse proportion to the polydispersity [18]. In summary, data for the crossover point demonstrate that the molecular weight decreases with an increase in frequency and polydispersity increases with a decrease in . The lower frequency therefore corresponds to a higher molecular weight, and the higher modulus corresponds to lower polydispersity. Therefore,Figure 5 shows the curves of elastic modulus () and viscosity modulus () in response to the frequency sweep of NR for different milling times. Six graphs are shown of NR for milling times of 5, 10, 15, 20, 25, and 30. A crossover point [] exists in the graph when the milling time is more than 15. The crossover points are , , and . The existence of a crossover point indicates that frequency and modulus increase with milling time. For milling times less than 15, no crossover point exists because the higher molecular weight NR requires a smaller frequency for molecular orientation.

4. Conclusions

NR molecular weight and MWD as characterized by dynamic properties and rheological behavior correspond with those measured by GPC-LLS. With an increase in milling time, , , and MWD decrease. The complex viscosity of NR decreases with an increase in shear rate, and the increase in molecular weight increases the zero-shear viscosity. The relaxation parameter is calculated from , which is measured by RPA under stress relaxation. The average molecular weight and MWD are obtained from a crossover point between the curves of and under a frequency sweep. The crossover point represents the modulus and frequency, where lower frequency means a higher molecular weight, and higher modulus means lower polydispersity. This work provides a relationship between the dynamic properties and rheological behavior and molecular structure parameters of NR, offers a convenient and fast technique for the characterization of NR molecular structure, and is well suited to the elastomer industry.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.


This study was financially supported by the Fundamental Research Funds for Rubber Research Institute, CATAS (no. 1630022014013), and earmarked fund for China Agriculture Research System (CARS-34-GW9).


  1. C. Kim, J. S. Beuve, S. Guilbert, and F. Bonfils, “Study of chain branching in natural rubber using size-exclusion chromatography coupled with a multi-angle light scattering detector (SEC-MALS),” European Polymer Journal, vol. 45, no. 8, pp. 2249–2259, 2009. View at: Publisher Site | Google Scholar
  2. M. Röding, D. Bernin, J. Jonasson et al., “The gamma distribution model for pulsed-field gradient NMR studies of molecular-weight distributions of polymers,” Journal of Magnetic Resonance, vol. 222, pp. 105–111, 2012. View at: Publisher Site | Google Scholar
  3. O. Trhlíková, J. Zedník, P. Matějíček, M. Horáček, and J. Sedláček, “Degradation and cis-to-trans isomerization of poly[(2,4-difluorophenyl)acetylene]s of various initial molecular weight: SEC, NMR, DLS and EPR study,” Polymer Degradation and Stability, vol. 98, no. 9, pp. 1814–1826, 2013. View at: Publisher Site | Google Scholar
  4. J. Dick, ASTM in the Globalization of Rubber Standards and Specifications, Rubber Division, ACS, Philadelphia, Pa, USA, 1994.
  5. J. S. Dick, Ten Ways to Improve Test Productivity and Reduce Testing Costs, Rubber Division, ACS, Akron, Ohio, USA, 2004.
  6. M. J. O. C. Guimarães, F. M. B. Coutinho, M. C. G. Rocha, M. Farah, and R. E. S. Bretas, “Effect of molecular weight and long chain branching of metallocene elastomers on the properties of high density polyethylene blends,” Polymer Testing, vol. 22, no. 8, pp. 843–847, 2003. View at: Publisher Site | Google Scholar
  7. P. Li, S. Yang, and M. Wang, “Investigation of the molecular weight of polyethylene using rheological techniques,” Journal of Applied Polymer Science, vol. 126, no. 2, pp. 749–755, 2012. View at: Publisher Site | Google Scholar
  8. D. Yan, W.-J. Wang, and S. Zhu, “Effect of long chain branching on rheological properties of metallocene polyethylene,” Polymer, vol. 40, no. 7, pp. 1737–1744, 1999. View at: Publisher Site | Google Scholar
  9. H. Azizi, I. Ghasemi, and M. Karrabi, “Controlled-peroxide degradation of polypropylene: rheological properties and prediction of MWD from rheological data,” Polymer Testing, vol. 27, no. 5, pp. 548–554, 2008. View at: Publisher Site | Google Scholar
  10. P. Henry and D. John, “Viscoelastic characterization of rubber with a new dynamic mechanical tester,” Rubber World, vol. 206, p. 37, 1992. View at: Google Scholar
  11. H. Yu, Z. Zeng, G. Lu, and Q. Wang, “Processing characteristics and thermal stabilities of gel and sol of epoxidized natural rubber,” European Polymer Journal, vol. 44, no. 2, pp. 453–464, 2008. View at: Publisher Site | Google Scholar
  12. Z.-Q. Zeng, H.-P. Yu, Q.-F. Wang, and G. Lu, “Effects of coagulation processes on properties of epoxidized natural rubber,” Journal of Applied Polymer Science, vol. 109, no. 3, pp. 1944–1949, 2008. View at: Publisher Site | Google Scholar
  13. P.-Y. Wang, H.-L. Qian, C.-L. Yang, and Y. Chen, “Characterization of the aging behavior of raw epoxidized natural rubber with a rubber processing analyzer,” Journal of Applied Polymer Science, vol. 100, no. 2, pp. 1277–1281, 2006. View at: Publisher Site | Google Scholar
  14. P. Zhang, F. Zhao, Y. Yuan, X. Shi, and S. Zhao, “Network evolution based on general-purpose diene rubbers/sulfur/TBBS system during vulcanization (I),” Polymer, vol. 51, no. 1, pp. 257–263, 2010. View at: Publisher Site | Google Scholar
  15. D. K. Setua, K. N. Pandey, A. K. Saxena, and G. N. Mathur, “Characterization of elastomer blend and compatibility,” Journal of Applied Polymer Science, vol. 74, no. 3, pp. 480–489, 1999. View at: Publisher Site | Google Scholar
  16. J. Fröhlich, W. Niedermeier, and H.-D. Luginsland, “The effect of filler-filler and filler-elastomer interaction on rubber reinforcement,” Composites Part A: Applied Science and Manufacturing, vol. 36, no. 4, pp. 449–460, 2005. View at: Publisher Site | Google Scholar
  17. Y. Zhai, W. Yang, Y. Wang, B. Xie, and M. Yang, “Effect of moleuclar structure of LLDPE on dynamic rheological behaviors,” Polymeric Materials Science and Engineering, vol. 26, p. 88, 2010. View at: Google Scholar
  18. B. Schlund and L. A. Utracki, “Linear low density polyethylenes and their blends: part 1. Molecular characterization,” Polymer Engineering & Science, vol. 27, no. 5, pp. 359–366, 1987. View at: Publisher Site | Google Scholar

Copyright © 2015 Tianming Gao et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

More related articles

5922 Views | 2389 Downloads | 6 Citations
 PDF  Download Citation  Citation
 Download other formatsMore
 Order printed copiesOrder

Related articles

We are committed to sharing findings related to COVID-19 as quickly and safely as possible. Any author submitting a COVID-19 paper should notify us at to ensure their research is fast-tracked and made available on a preprint server as soon as possible. We will be providing unlimited waivers of publication charges for accepted articles related to COVID-19. Sign up here as a reviewer to help fast-track new submissions.