# Dynamic Mechanical Properties of Vietnam Modified Natural Rubber via Grafting with Styrene

Authors: T. A. Dung; N. T. Nhan; N. T. Thuong; D. Q. Viet; N. H. Tung; P. T. Nghia; S. Kawahara; T. T. Thuy
Journal: International Journal of Polymer Science
 (2017)

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## Abstract

The dynamic mechanical behavior of modified deproteinized natural rubber (DPNR) prepared by graft copolymerization with various styrene contents was investigated at a wide range of temperatures. Graft copolymerization of styrene onto DPNR was performed in latex stage using tert-butyl hydroperoxide (TBHPO) and tetraethylene pentamine (TEPA) as redox initiator. The mechanical properties were measured by tensile test and the viscoelastic properties of the resulting graft copolymers at wide range of temperature and frequency were investigated. It was found that the tensile strength depends on the grafted polystyrene; meanwhile the dynamic mechanical properties of the modification of DPNR meaningfully improved with the increasing of both homopolystyrene and grafted polystyrene compared to DPNR. The dynamic mechanical properties of graft copolymer over a large time scale were studied by constructing the master curves. The value ofbT has been used to prove the energetic and entropic elasticity of the graft copolymer.


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## Body

## 1. Introduction

With the progressive increase of global product demands and the continuous decrease of worldwide fossil resources alongside with the growing concerns about environmental pollutions and carbon emissions, it is very crucial to reduce the dependence on the nonrenewable fossil resources [1–3]. Natural rubber (NR) is one of the most valuable renewable resources. It has attracted great interest in many fields, such as in transportation and industrial and medical sectors, mainly due to outstanding properties such as high tensile strength, high elongation, and high elasticity [4–9].Although NR possesses many superior properties, it lacks some properties such as oil, weather, and abrasion resistances. Consequently, it has often been modified by chemical the techniques such as graft copolymerization or the physical techniques meet the demand requirement for other applications such as in tire industry, to prepare composites with desirable properties [10–17]. Among them, graft copolymerization is a well-established technique to prepare hybrid polymer with unique structure necessary for various applications by using different monomers. Styrene is one of the common monomer which was grafted onto natural rubber using graft copolymerization technique in latex stage or solution stage [18, 19]. The graft copolymer of styrene onto natural rubber possesses outstanding properties compared to that of pure natural rubber. However, for the application in industrial tire, it is necessary to understand the complex mechanical behavior of the graft copolymers.Dynamic mechanical analysis (DMA) is an important method to indicate relaxation dynamic of polymeric materials. A sinusoidal stress is applied and the strain in the material is measured, allowing one to determine the moduli. By studying the dependence of storage and loss moduli on temperature or frequency, it is possible to show the dynamic mechanical properties of the materials and their applications [20–23]. Graft copolymerization of styrene onto deproteinized natural rubber resulted in a formation of core-shell structure, in which natural rubber particle as a core was surrounded by polystyrene nanolayer as a shell [24]. This structure and polystyrene chain play an important role in outstanding mechanical properties of graft copolymer; for instance, the tensile strength of graft copolymer increases about 4 times that of natural rubber. The dynamic mechanical properties of graft copolymer had also been measured and the results showed that the storage modulus of graft copolymer increases about 25 times compared with that of natural rubber [24]. However, DMA measurement had been carried out in narrow range of frequencies from 0.1 to 100 Hz due to the limitation of the equipment. The DMA result cannot cover all dynamic behavior of graft copolymer [20–23]. To understand the effect of polystyrene chain and the structure on dynamic mechanical properties, it is obligatory to study the dynamic mechanical properties of graft copolymer over a wide frequency range or a large time scale [20–23]. Therefore, the time-temperature superposition principle has been applied to obtain master curves of the modulus for the polymer [21, 25–27].In the present study, the dependence of dynamic mechanical properties on styrene content of the graft-copolymer has been investigated. In addition, the master curves have been built to explore the dynamic mechanical properties in over a wide frequency range or a large time scale. The horizontal and vertical shift factors, which are the important factors in the time-temperature superposition principle, are calculated to determine elasticity of graft copolymer.


## 2. Experimental

### 2.1. Chemicals Reagents

NR latex used was commercial high ammonia natural rubber (HANR), which was purchased from Duy Hang Company, Vietnam. Dry rubber content (DRC) of HANR was about 60 wt.%. Sodium dodecyl sulfate (SDS, 98%) was obtained from Chameleon, Japan. Styrene was purchased from Sigma-Aldrich.Tert-butyl hydroperoxide (68%) and tetraethylene pentamine (TEPA, 95%) were purchased from TCI, Japan. 2-Butanone (99%) and acetone (99.5%) were obtained from Merck.


### 2.2. Preparation of DPNR Latex and Graft Copolymer Samples

Deproteinized natural rubber (DPNR) was prepared by incubation of the latex with 0.1 wt.% urea and 1 wt.% SDS at room temperature for 60 min followed by centrifugation at 10000 rpm for 30 min. The cream fraction was redispersed in 1 wt.% SDS solution, and it was washed twice by centrifugation to prepare the DPNR latex with 60 wt.% DRC. The resulting DPNR latex contained about 0.1 wt.% SDS [28].The graft copolymer samples are prepared by graft copolymerization using 3.5 × 10−5mol initiator/g dried rubber. The effect of styrene concentrations in the values of 1.0, 1.5, and 2.0 × 10−3mol/g dried rubber was investigated. The detail procedure for the graft copolymerization was carried out according to the following steps. The DPNR latex was first introduced into a 500 cm3 glass reactor equipped with a mechanical stirrer. The latex was first purged nitrogen for 60 min to remove the dissolved oxygen and stirred at a constant speed (400 rpm). Afterwards TBHPO/TEPA were added as an initiator followed by styrene as a monomer. The reaction was carried out by stirring the latex at above 400 rpm for 2.5 hours at room temperature [24, 29, 30].The unreacted styrene was removed by using a rotary evaporator under reduced pressure. The product was put in a glass petri dish and dried in a vacuum oven at 50°C for more than a week. Soxhlet extraction was performed to purify the product. The free polystyrene was extracted with acetone/2-butanone 3 : 1 mixture under nitrogen atmosphere in the dark for 24 h, followed by drying under reduced pressure for a week.The styrene conversion and grafting efficiency of graft copolymerization were determined by gravimetric method [24].


### 2.3. Characterization

The dynamic mechanical properties of the graft copolymer were measured with an Anton Paar Physica MCR 302. Specimen was a 12 mm diameter parallel plate geometry. The sample thickness was 1 mm in order to further the shear rate in the sample. Shear deformation was measured in the temperature range from −70 to 140°C with the impacted frequency from 0.1 to 10 s−1.The master curves were built following the time-temperature superposition principle. The horizontal shift factor,aT, and vertical shift factor, bT, are expressed by the WLF equations (1) and (2), respectively [21, 27, 31–33]. (1)log⁡aT=-C1T-TrC2+T-Tr,(2)Gt,Tr=GfaT,TbTwhereC1 and C2 are positive constants that depend on the material and the temperature.Tensile measurement was conducted using a Toyo Seiki Strograph VG10E according to JIS K6251. Film samples were cut with a Dumbbell-shaped No. 7. The crosshead speed was 200 mm min−1.


## 2.1. Chemicals Reagents

NR latex used was commercial high ammonia natural rubber (HANR), which was purchased from Duy Hang Company, Vietnam. Dry rubber content (DRC) of HANR was about 60 wt.%. Sodium dodecyl sulfate (SDS, 98%) was obtained from Chameleon, Japan. Styrene was purchased from Sigma-Aldrich.Tert-butyl hydroperoxide (68%) and tetraethylene pentamine (TEPA, 95%) were purchased from TCI, Japan. 2-Butanone (99%) and acetone (99.5%) were obtained from Merck.


## 2.2. Preparation of DPNR Latex and Graft Copolymer Samples

Deproteinized natural rubber (DPNR) was prepared by incubation of the latex with 0.1 wt.% urea and 1 wt.% SDS at room temperature for 60 min followed by centrifugation at 10000 rpm for 30 min. The cream fraction was redispersed in 1 wt.% SDS solution, and it was washed twice by centrifugation to prepare the DPNR latex with 60 wt.% DRC. The resulting DPNR latex contained about 0.1 wt.% SDS [28].The graft copolymer samples are prepared by graft copolymerization using 3.5 × 10−5mol initiator/g dried rubber. The effect of styrene concentrations in the values of 1.0, 1.5, and 2.0 × 10−3mol/g dried rubber was investigated. The detail procedure for the graft copolymerization was carried out according to the following steps. The DPNR latex was first introduced into a 500 cm3 glass reactor equipped with a mechanical stirrer. The latex was first purged nitrogen for 60 min to remove the dissolved oxygen and stirred at a constant speed (400 rpm). Afterwards TBHPO/TEPA were added as an initiator followed by styrene as a monomer. The reaction was carried out by stirring the latex at above 400 rpm for 2.5 hours at room temperature [24, 29, 30].The unreacted styrene was removed by using a rotary evaporator under reduced pressure. The product was put in a glass petri dish and dried in a vacuum oven at 50°C for more than a week. Soxhlet extraction was performed to purify the product. The free polystyrene was extracted with acetone/2-butanone 3 : 1 mixture under nitrogen atmosphere in the dark for 24 h, followed by drying under reduced pressure for a week.The styrene conversion and grafting efficiency of graft copolymerization were determined by gravimetric method [24].


## 2.3. Characterization

The dynamic mechanical properties of the graft copolymer were measured with an Anton Paar Physica MCR 302. Specimen was a 12 mm diameter parallel plate geometry. The sample thickness was 1 mm in order to further the shear rate in the sample. Shear deformation was measured in the temperature range from −70 to 140°C with the impacted frequency from 0.1 to 10 s−1.The master curves were built following the time-temperature superposition principle. The horizontal shift factor,aT, and vertical shift factor, bT, are expressed by the WLF equations (1) and (2), respectively [21, 27, 31–33]. (1)log⁡aT=-C1T-TrC2+T-Tr,(2)Gt,Tr=GfaT,TbTwhereC1 and C2 are positive constants that depend on the material and the temperature.Tensile measurement was conducted using a Toyo Seiki Strograph VG10E according to JIS K6251. Film samples were cut with a Dumbbell-shaped No. 7. The crosshead speed was 200 mm min−1.


## 3. Results and Discussion

### 3.1. Effect of Styrene Content on the Dynamic Mechanical Property of Graft Copolymers

In our previous work, it has been shown that the highest styrene conversion and grafting efficiency were achieved at 3.5 × 10–5mol initiator/g dried rubber and 1.5 × 10–3mol styrene/g dried rubber [24]. In the present study, we performed the graft copolymerization with various styrene concentrations to obtain graft copolymers that are DPNR-graft-PS, with different styrene contents. The parameters for the graft copolymerization were shown in Table 1. The conversion and grafting efficiency were calculated by gravimetric method as mentioned in our previous work [24].Table 1
The conversion and grafting efficiency of the graft copolymerization.
Sample
Styrene concentration(10−3 mol/g)
Conversion(%)
Grafting efficiency(%)
Total styrene content(phr)
Grafted styrene content(phr)
DPNR
0
0
0
0
0
DPNR-graft-PS 1
1.0
69.20
52.67
7.21
3.80
DPNR-graft-PS 1.5
1.5
91.03
75.02
14.22
10.67
DPNR-graft-PS 2
2.0
82.08
53.21
17.10
9.10Figure1 shows the temperature dependence of tan⁡δ (loss tangent) for DPNR and DPNR-graft-PS samples at 10 Hz. The peaks at −55°C and 105°C were characterized for glass transition temperature (Tg) of NR and PS, respectively [18]. From the DPNR to DPNR-graft-PS 2 sample, the height of the loss tangent peak at −55°C decreases, while that value at 105°C increases. This may be explained to be due to the increase of styrene content in the graft copolymer.Figure 1
Temperature dependence oftan⁡δ for DPNR and DPNR-graft-PS samples at 10 Hz.Figure2 shows the temperature dependence of loss modulus for DPNR and DPNR-graft-PS samples. The loss modulus expresses the viscous component and the dissipation capacity of the materials. In the temperature dependence of loss modulus curves of any NR or its graft copolymerization, there are three distinct regions. At low temperature, the graft copolymer in the glassy state shows a high value of the modulus. In the transition region from the glassy state to the rubbery state,G′′ significantly decreases to a constant value. This region is the onset of chain mobility and corresponds to the glass transition temperature Tg. At temperature higher than Tg, the value ofG′′ reaches the minimum, which is similar to that in the rubbery state. For the graft copolymer samples, an additional region appears at the temperature above Tg of polystyrene. This region is in rubbery flow state, which is characterized by having plastic component in the material. Thus, it is obvious that the width of this region increases with the increase of styrene content.Figure 2
Temperature dependence of loss modulus for DPNR and DPNR-graft-PS at 10 Hz.In our previous work, the graft copolymerization resulted in the formation of core-shell structure, in which NR particles as the core were surrounded by nanolayer of polystyrene [24]. The increase of styrene content in graft copolymer led to the increase of the polystyrene layer thickness [18, 24]. Thus, the changing in property of the graft-copolymer is explained to be due to the changing in styrene content.Variation of the storage modulus as a function of frequency for DPNR and DPNR-graft-PS at 30°C is shown in Figure 3. The storage modulus is related to the elastic modulus of polymer at the loading, in which the increase in the styrene content also resulted in the increase in storage modulus of graft copolymer. However, there is just a slight difference between storage modulus of DPNR-graft-PS 1.5 and DPNR-graft-PS 2. This may be explained to be due to the difference in amount of grafted styrene and homopolystyrene, in which the amount of grafted styrene of DPNR-graft-PS 1.5 was higher than that of DPNR-graft-PS 2, and the amount of homopolystyrene of DPNR-graft-PS 2 was higher than that of DPNR-graft-PS 1.5. The formation of homopolystyrene may have a negative effect on the property. The increase of homopolystyrene content in graft copolymer may result in the increasingly propagation of voids in the material. Because the polystyrene is harder than NR, during applying a load, the voids may be formed surrounding the polystyrene particles. When the voids are growing, it will lead to the propagation of voids and the material is collapsed. Therefore, the tensile strength of DPNR-graft-PS 1.5 was higher than that of DPNR-graft-PS 2, which is shown in Figure 4. These results suggested that not only the grafted styrene but also homopolystyrene is important factors effect on the tensile strength as well as dynamic mechanical properties of graft copolymers.Figure 3
Frequency dependence of storage modulus for DPNR and DPNR-graft-PS at 30°C.Figure 4
Stress-strain curves of un-vulcanized DPNR and various DPNR-graft-PS.From the reasons above, the DPNR-graft-PS 1.5, which contains the highest grafted styrene content, has been selected to construct the master curves to investigate the energetic and entropic elasticity of the graft copolymers.


### 3.2. Energetic and Entropic Elasticity of Graft Copolymer

Figure5 shows storage modulus, loss modulus, and tan⁡δ at various temperatures of DPNR and DPNR-graft-PS. The measurement covered from the glassy state to rubbery state. In the previous work [24], the value of theG′ at the plateau region of DPNR-graft-PS was about 25 times higher than that of DPNR. Furthermore, the valueG′′ of the graft copolymer was found to be nearly independent of the frequency. It was nearly constant as the frequency increased. These led to the decreases of the value of tan⁡δ for DPNR-graft-PS at the low-frequency region and the increase to almost constant value at the high-frequency region. These results may be explained by the effect of polystyrene layer in the graft copolymer with the core-shell structure. Therefore, in order to elucidate the relationship between viscoelastic properties and the core-shell structure, the dependence of the viscoelastic properties on temperature and frequency was investigated by constructing the master curves.Figure 5
Frequency sweep curves at various temperatures of DPNR and DPNR-graft-PS.The master curves of rubber samples were constructed based on the time-temperature superposition procedure. The line at –65°C (Tr = –65°C) is chosen as the baseline to move the lines at different temperatures to build the master curve. The tan⁡δ line is used to determine the horizontal shift factor, aT, so it is independent with the vertical shift factor, bT. Selecting the horizontal shift factor, aT, in temperatures to shift the tan⁡δ lines to the temperature Tr, we obtained the tan⁡δ master curves, which is shown in Figure 6.Figure 6
Master curves oftan⁡δ of DPNR and DPNR-graft-PS.In Figure6, the master curves are superimposed smoothly confirming that the measurements and the superposition are reliable. On the tan⁡δ master curve of DPNR, there is only one peak at the large oscillatory frequency due to the NR, whereas there are two peaks on the tan⁡δ master curve of DPNR-graft-PS, the peak in the large oscillatory frequency attributed to the NR and the remaining peak in the small oscillation frequency described to the polystyrene chains, which is grafted onto the NR via graft copolymerization.TheaT value is recalculated using the WLF equation (the solid line). Then, the dependence of aT on temperature for DPNR and DPNR-graft-PS is shown in Figure 7. The result indicates that the aT for DPNR depends on temperature which is in agreement with the WLF equation. It has been proved by the value of positive constants,C1 andC2. These have been found to be 14.33 and 47.24, respectively.Figure 7
Temperature dependence of horizontal shift factor of DPNR and DPNR-graft-PS.In the case of the island-matrix structure of rubber-filler system, the temperature dependence ofaT is identical to mechanical relaxation for the polymer matrix. aT is a ratio of any relaxation time at one temperature to its value of the chosen reference temperature [27, 34–39]. In previous work, Isono et al. have reported that the horizontal shift factor aT of rubber filled with carbon black particles was not changed by the changing of carbon black particles amount [36, 38]. Kawahara et al. have also reported that aT of natural rubber grafted with organosilane monomer was independent on the amount of silica [39, 40]. Therefore, the recovery of the rubber-filler system is only affected by rubber. Conversely, the dependence of aT on temperature of DPNR-graft-PS is just in agreement with WLF equation in the temperature range from Tr to Tr + 60°C. The WLF equation cannot be extended to the higher temperature other than Tr + 60°C. The different dependence of aT on temperature for filler rubber and graft copolymer is assumed to be due to the formation of chemical linkages between polystyrene and natural rubber that is formed via graft copolymerization. Thus, the recovery of the graft copolymer was contributed to not only NR but also polystyrene chains covering NR particles.After obtaining the values ofaT in the temperatures, the vertical shift factor is calculated to shift the linesG′ andG′′. The vertical shift factor is determined by formula (2). The master curves ofG′ andG′′ are shown in Figures 8 and 9.Figure 8
Master curves of loss modulus for DPNR and DPNR-graft-PS.Figure 9
Master curves of storage modulus for DPNR and DPNR-graft-PS.The master curve ofG′ andG′′ showed the remarkable state transitional regions of DPNR and DPNR-graft-PS. It is obviously seen that the elasticity region of the DPNR-graft-PS samples occurred earlier and maintained longer than that of DPNR, demonstrating that the graft copolymer has longer working time than DPNR. Apart from the fact that the glassy state and elastic state of DPNR-graft-PS are the same compared to DPNR, the DPNR-graft-PS sample also has a typical state transition of the polystyrene chain.The value of the vertical shift factor,bT, relates to the elasticity properties of materials. Elasticity is generally divided in two parts: energetic and entropic components [21, 34–38]. The entropic component relates to an ability to return back to initial form after applying a force. The force applying on the rubber will stretch out and orient the rubber chains. This will decrease the entropy of the chains and then create an entropic force. This entropic force plays a role in driving the rubber to initial form. Besides that, the energetic force associates with the intra- and intermolecular energy. In natural rubber, the intermolecular energy is approximate to zero, so the natural rubber indicates the pure entropic elasticity. However, in filled rubbers or thermoplastic elastomers, the interactions of polymer-polymer, polymer-filler, and filler-filler increase the intra- and intermolecular energy; then the energetic component contributes to the elasticity.The previous work found that a positive slope inbT-T curve corresponds to entropic elasticity, in case of natural rubber [27, 38, 40]. On the contrary, a negative slope in bT-T curve corresponds to energetic elasticity, for instance, natural rubber filled by carbon black particles or natural rubber grafted vinyltriethoxysilane [35, 38–40]. Figure 10 shows the dependence of bT on the temperature of the DPNR and DPNR-graft-PS. bT of DPNR gradually increased along the temperature corresponding to the purely entropic behavior of natural rubber. Meanwhile, the curve of DPNR-graft-PS sample had the same positive slope of bT line, but the value of bT was lower than that of DPNR sample in temperature range from Tr to 100°C. These data can be rationalized in terms of graft copolymer having both entropic and energetic components. Above 100°C, there was a prompt decrease in bT. This can be explained to be due to the influence of the polystyrene component since DPNR-graft-PS has the higher glass transition temperature than the homopolystyrene.Figure 10
Temperature dependence ofbT of DPNR and DPNR-graft-PS.


## 3.1. Effect of Styrene Content on the Dynamic Mechanical Property of Graft Copolymers

In our previous work, it has been shown that the highest styrene conversion and grafting efficiency were achieved at 3.5 × 10–5mol initiator/g dried rubber and 1.5 × 10–3mol styrene/g dried rubber [24]. In the present study, we performed the graft copolymerization with various styrene concentrations to obtain graft copolymers that are DPNR-graft-PS, with different styrene contents. The parameters for the graft copolymerization were shown in Table 1. The conversion and grafting efficiency were calculated by gravimetric method as mentioned in our previous work [24].Table 1
The conversion and grafting efficiency of the graft copolymerization.
Sample
Styrene concentration(10−3 mol/g)
Conversion(%)
Grafting efficiency(%)
Total styrene content(phr)
Grafted styrene content(phr)
DPNR
0
0
0
0
0
DPNR-graft-PS 1
1.0
69.20
52.67
7.21
3.80
DPNR-graft-PS 1.5
1.5
91.03
75.02
14.22
10.67
DPNR-graft-PS 2
2.0
82.08
53.21
17.10
9.10Figure1 shows the temperature dependence of tan⁡δ (loss tangent) for DPNR and DPNR-graft-PS samples at 10 Hz. The peaks at −55°C and 105°C were characterized for glass transition temperature (Tg) of NR and PS, respectively [18]. From the DPNR to DPNR-graft-PS 2 sample, the height of the loss tangent peak at −55°C decreases, while that value at 105°C increases. This may be explained to be due to the increase of styrene content in the graft copolymer.Figure 1
Temperature dependence oftan⁡δ for DPNR and DPNR-graft-PS samples at 10 Hz.Figure2 shows the temperature dependence of loss modulus for DPNR and DPNR-graft-PS samples. The loss modulus expresses the viscous component and the dissipation capacity of the materials. In the temperature dependence of loss modulus curves of any NR or its graft copolymerization, there are three distinct regions. At low temperature, the graft copolymer in the glassy state shows a high value of the modulus. In the transition region from the glassy state to the rubbery state,G′′ significantly decreases to a constant value. This region is the onset of chain mobility and corresponds to the glass transition temperature Tg. At temperature higher than Tg, the value ofG′′ reaches the minimum, which is similar to that in the rubbery state. For the graft copolymer samples, an additional region appears at the temperature above Tg of polystyrene. This region is in rubbery flow state, which is characterized by having plastic component in the material. Thus, it is obvious that the width of this region increases with the increase of styrene content.Figure 2
Temperature dependence of loss modulus for DPNR and DPNR-graft-PS at 10 Hz.In our previous work, the graft copolymerization resulted in the formation of core-shell structure, in which NR particles as the core were surrounded by nanolayer of polystyrene [24]. The increase of styrene content in graft copolymer led to the increase of the polystyrene layer thickness [18, 24]. Thus, the changing in property of the graft-copolymer is explained to be due to the changing in styrene content.Variation of the storage modulus as a function of frequency for DPNR and DPNR-graft-PS at 30°C is shown in Figure 3. The storage modulus is related to the elastic modulus of polymer at the loading, in which the increase in the styrene content also resulted in the increase in storage modulus of graft copolymer. However, there is just a slight difference between storage modulus of DPNR-graft-PS 1.5 and DPNR-graft-PS 2. This may be explained to be due to the difference in amount of grafted styrene and homopolystyrene, in which the amount of grafted styrene of DPNR-graft-PS 1.5 was higher than that of DPNR-graft-PS 2, and the amount of homopolystyrene of DPNR-graft-PS 2 was higher than that of DPNR-graft-PS 1.5. The formation of homopolystyrene may have a negative effect on the property. The increase of homopolystyrene content in graft copolymer may result in the increasingly propagation of voids in the material. Because the polystyrene is harder than NR, during applying a load, the voids may be formed surrounding the polystyrene particles. When the voids are growing, it will lead to the propagation of voids and the material is collapsed. Therefore, the tensile strength of DPNR-graft-PS 1.5 was higher than that of DPNR-graft-PS 2, which is shown in Figure 4. These results suggested that not only the grafted styrene but also homopolystyrene is important factors effect on the tensile strength as well as dynamic mechanical properties of graft copolymers.Figure 3
Frequency dependence of storage modulus for DPNR and DPNR-graft-PS at 30°C.Figure 4
Stress-strain curves of un-vulcanized DPNR and various DPNR-graft-PS.From the reasons above, the DPNR-graft-PS 1.5, which contains the highest grafted styrene content, has been selected to construct the master curves to investigate the energetic and entropic elasticity of the graft copolymers.


## 3.2. Energetic and Entropic Elasticity of Graft Copolymer

Figure5 shows storage modulus, loss modulus, and tan⁡δ at various temperatures of DPNR and DPNR-graft-PS. The measurement covered from the glassy state to rubbery state. In the previous work [24], the value of theG′ at the plateau region of DPNR-graft-PS was about 25 times higher than that of DPNR. Furthermore, the valueG′′ of the graft copolymer was found to be nearly independent of the frequency. It was nearly constant as the frequency increased. These led to the decreases of the value of tan⁡δ for DPNR-graft-PS at the low-frequency region and the increase to almost constant value at the high-frequency region. These results may be explained by the effect of polystyrene layer in the graft copolymer with the core-shell structure. Therefore, in order to elucidate the relationship between viscoelastic properties and the core-shell structure, the dependence of the viscoelastic properties on temperature and frequency was investigated by constructing the master curves.Figure 5
Frequency sweep curves at various temperatures of DPNR and DPNR-graft-PS.The master curves of rubber samples were constructed based on the time-temperature superposition procedure. The line at –65°C (Tr = –65°C) is chosen as the baseline to move the lines at different temperatures to build the master curve. The tan⁡δ line is used to determine the horizontal shift factor, aT, so it is independent with the vertical shift factor, bT. Selecting the horizontal shift factor, aT, in temperatures to shift the tan⁡δ lines to the temperature Tr, we obtained the tan⁡δ master curves, which is shown in Figure 6.Figure 6
Master curves oftan⁡δ of DPNR and DPNR-graft-PS.In Figure6, the master curves are superimposed smoothly confirming that the measurements and the superposition are reliable. On the tan⁡δ master curve of DPNR, there is only one peak at the large oscillatory frequency due to the NR, whereas there are two peaks on the tan⁡δ master curve of DPNR-graft-PS, the peak in the large oscillatory frequency attributed to the NR and the remaining peak in the small oscillation frequency described to the polystyrene chains, which is grafted onto the NR via graft copolymerization.TheaT value is recalculated using the WLF equation (the solid line). Then, the dependence of aT on temperature for DPNR and DPNR-graft-PS is shown in Figure 7. The result indicates that the aT for DPNR depends on temperature which is in agreement with the WLF equation. It has been proved by the value of positive constants,C1 andC2. These have been found to be 14.33 and 47.24, respectively.Figure 7
Temperature dependence of horizontal shift factor of DPNR and DPNR-graft-PS.In the case of the island-matrix structure of rubber-filler system, the temperature dependence ofaT is identical to mechanical relaxation for the polymer matrix. aT is a ratio of any relaxation time at one temperature to its value of the chosen reference temperature [27, 34–39]. In previous work, Isono et al. have reported that the horizontal shift factor aT of rubber filled with carbon black particles was not changed by the changing of carbon black particles amount [36, 38]. Kawahara et al. have also reported that aT of natural rubber grafted with organosilane monomer was independent on the amount of silica [39, 40]. Therefore, the recovery of the rubber-filler system is only affected by rubber. Conversely, the dependence of aT on temperature of DPNR-graft-PS is just in agreement with WLF equation in the temperature range from Tr to Tr + 60°C. The WLF equation cannot be extended to the higher temperature other than Tr + 60°C. The different dependence of aT on temperature for filler rubber and graft copolymer is assumed to be due to the formation of chemical linkages between polystyrene and natural rubber that is formed via graft copolymerization. Thus, the recovery of the graft copolymer was contributed to not only NR but also polystyrene chains covering NR particles.After obtaining the values ofaT in the temperatures, the vertical shift factor is calculated to shift the linesG′ andG′′. The vertical shift factor is determined by formula (2). The master curves ofG′ andG′′ are shown in Figures 8 and 9.Figure 8
Master curves of loss modulus for DPNR and DPNR-graft-PS.Figure 9
Master curves of storage modulus for DPNR and DPNR-graft-PS.The master curve ofG′ andG′′ showed the remarkable state transitional regions of DPNR and DPNR-graft-PS. It is obviously seen that the elasticity region of the DPNR-graft-PS samples occurred earlier and maintained longer than that of DPNR, demonstrating that the graft copolymer has longer working time than DPNR. Apart from the fact that the glassy state and elastic state of DPNR-graft-PS are the same compared to DPNR, the DPNR-graft-PS sample also has a typical state transition of the polystyrene chain.The value of the vertical shift factor,bT, relates to the elasticity properties of materials. Elasticity is generally divided in two parts: energetic and entropic components [21, 34–38]. The entropic component relates to an ability to return back to initial form after applying a force. The force applying on the rubber will stretch out and orient the rubber chains. This will decrease the entropy of the chains and then create an entropic force. This entropic force plays a role in driving the rubber to initial form. Besides that, the energetic force associates with the intra- and intermolecular energy. In natural rubber, the intermolecular energy is approximate to zero, so the natural rubber indicates the pure entropic elasticity. However, in filled rubbers or thermoplastic elastomers, the interactions of polymer-polymer, polymer-filler, and filler-filler increase the intra- and intermolecular energy; then the energetic component contributes to the elasticity.The previous work found that a positive slope inbT-T curve corresponds to entropic elasticity, in case of natural rubber [27, 38, 40]. On the contrary, a negative slope in bT-T curve corresponds to energetic elasticity, for instance, natural rubber filled by carbon black particles or natural rubber grafted vinyltriethoxysilane [35, 38–40]. Figure 10 shows the dependence of bT on the temperature of the DPNR and DPNR-graft-PS. bT of DPNR gradually increased along the temperature corresponding to the purely entropic behavior of natural rubber. Meanwhile, the curve of DPNR-graft-PS sample had the same positive slope of bT line, but the value of bT was lower than that of DPNR sample in temperature range from Tr to 100°C. These data can be rationalized in terms of graft copolymer having both entropic and energetic components. Above 100°C, there was a prompt decrease in bT. This can be explained to be due to the influence of the polystyrene component since DPNR-graft-PS has the higher glass transition temperature than the homopolystyrene.Figure 10
Temperature dependence ofbT of DPNR and DPNR-graft-PS.


## 4. Conclusions

The dynamic mechanical properties of graft copolymer of natural rubber with styrene with nanomatrix structure were investigated at wide range of temperature by using time-temperature superposition principle. It was found that the storage modulus and loss modulus of the graft copolymers are dependent both on grafted polystyrene and on homopolystyrene content. The moduli of graft copolymer were found to increase with increasing total styrene content. The moduli of graft copolymer were increased with the increase of styrene contents. The working time of the graft copolymer was found to be longer and higher than that of the deproteinized natural rubber. It was proved by the master curves. It is also discovered that the graft copolymer has both energetic and entropic elasticity similar to the other common fillers, suggesting that graft copolymer could play a role as an organic filler for natural rubber when being applied by sinusoidal stress.



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*Source: 4956102-2017-12-27.xml*