Materials

Na-Mnt, sample K10 from Southern Clay Products (Gonzales, Texas, USA), with a cation exchange capacity (CEC) of 102 meq/100 g of clay and specific surface area of 240 m²/g was used. Cis-1,4-polyisoprene rubber (IR2200) was obtained from Zeon Corporation (Tokyo, Japan). NRL with 50% solid content was provided by the 11^th Rubber Plant of Guangzhou, China. Cyclohexane, sodium lauryl sulfonate (SLS, as the main emulsifier), potassium oleate (as the co-emulsifier), sulfur (as the curing agent), zinc oxide (ZnO as the activator), zinc diethyldithiocarbamate (ZDC as the accelerator), N-isopropyl-N'-phenyl-p-phenylenediamine (4010NA as the antioxidant), potassium hydroxide (KOH as pH regulator), and casein (as stabilizer) were of industrial grade and were obtained from Sinopharm Chemical Reagent Co., Ltd (Shanghai, China). Distilled water was used throughout the experiments. All the experimental materials were used as received.

Preparation of Latex Composites

First, IR rubber solution (10 wt.% IR rubber solution in cyclohexane, oil phase) was prepared using a mechanical stirrer at a speed of 200–300 rpm in cyclohexane for 6 h at room temperature. An emulsifier solution of SLS and potassium oleate (aqueous phase: SLS, 1.5 wt.%; potassium oleate, 0.5 wt.%) was also prepared using a mechanical stirrer at a speed of 200–300 rpm in distilled water for 2 h at 45 ℃. A 50 wt.% slurry of Mnt in distilled water was prepared. Then the Mnt suspension was added to the oil phase and blended mechanically under strong shear force.

Secondly, various amounts of Mnt suspension (0, 1, 3, 4, and 5 phr, phr: parts per hundred of rubber) were added to an IR rubber cyclohexane solution and stirred mechanically at 300 rpm for 15 min. The amounts of Mnt were calculated on an IR mass basis. The Mnt-modified oil phase was obtained.

Third, the Mnt-modified oil phase was added to the aqueous phase for emulsification at a high speed (6000 rpm) for 30 min. After solvent recovery and centrifugal concentration processes, the latex composites with various amounts of Mnt (0, 1, 3, 4, and 5 phr) were obtained. The corresponding latex composites were named IRL, Mnt/IRL (1 phr), Mnt/IRL (3 phr), Mnt/IRL (4 phr), and Mnt/IRL (5 phr), respectively.

Preparation of the Composite Films

For preparation of the films, aqueous dispersions of ZnO (50%), ZDC (50%), 4010NA (50%), and sulfur (50%) were mixed in a planetary ball mill with the required amount of water and with the aid of casein stabilizer. Then the compounded latexes were prepared by mixing the IRL, Mnt/IRL (1 phr), Mnt/IRL (3 phr), Mnt/IRL (4 phr), and Mnt/IRL (5 phr) with the aqueous dispersion containing ZnO (50%), ZDC (50%), 4010NA (50%), sulfur (50%), and 10% KOH, and stirring for 30 min using a mechanical stirrer at a speed of 200–300 rpm. The compounded latex was then heated to 60°C in a water bath for 10 h to pre-vulcanize it. The formula for the compounded latex used was as follows: IR 100 phr, ZnO 2 phr, sulfur 1 phr, 4010 NA 1 phr, ZDC 1.5 phr, and KOH 0.3 phr. The pre-vulcanized latexes were then left to mature for >24 h without stirring to promote the diffusion of chemical additives, which ensured the uniform properties of the latex films. They were filtered through a sieve (300 mesh filter screen with a pore size of 48 μm). Finally, they were cast on a petri dish with a diameter of 80 mm and spread the latex evenly on the surface. The latexes were allowed to dry in the air until they became transparent and then were vulcanized in the oven at 100°C for 30 min. Before testing, the vulcanized rubber films were stored in a desiccator. A schematic diagram of process of preparing the IRL and Mnt/IRL latex composites is shown in Fig. 1.

Fig. 1

Schematic diagram of the preparation processes for IRL and Mnt/IRL latex composites

Characterization

Total Solid Content (TSC)

The latex was weighed accurately (0.200 ± 0.001 g, W ₀) and placed on a watch glass (diameter of 60 mm), then heated in a hot-air oven at 70 ± 2°C until a constant weight was achieved. The dried sample was removed from the oven and cooled to room temperature in a desiccator. The films were peeled off the watch glass and weighed, giving W _TSC. The TSC was calculated using Eq. 1. Three replicates were measured.

(1) $\mathrm{TSC}=W_{\mathrm{TSC}}/W_0\times 100\%$

Characterization of Mnt/IRL Latex Composites

The particle size and its distribution index, the TSC, and the ζ-potential of the latex composites were determined as a function of increasing Mnt content (Figs. 2 and 3). When the amount of Mnt was <5 phr, the TSC of the latex was high because the ζ-potential of Mnt was –20.9 mV. Negatively charged Mnt repels the negatively charged polyisoprene latex particles and promotes the stability of latex. When the ζ-potential values were > ± 30 mV, the physical stability of the colloidal systems is good, which indicates a long shelf life (Reference RiddickRiddick, 1968). As in Fig. 2, the surface charge of IRL had a negative value of > ± 30 mV. Thus, IRL and Mnt/IRL latex composites are expected to be stable when stored at ambient temperatures.

Fig. 2

The TSC, particle size, PDI, and ζ-potential of IRL and Mnt/IRL latex composites: Columns from left to right are IRL, Mnt/IRL (1 phr), Mnt/IRL (3 phr), Mnt/IRL (4 phr), Mnt/IRL (5 phr), NRL

Fig. 3

The particle-size distribution index of the IRL, Mnt, and Mnt/IRL latex composites

Compared to the particle size of the neat IRL, the mean particle size of the Mnt/IRL composite increased from ~420 to 475 nm as the amount of Mnt increased from 1 to 4 phr. However, when the amount of Mnt added increased to 5 phr, the particle size and TSC decreased. This is mainly attributed to agglomeration of the excess Mnt, which destroys the stability of the latex state. Furthermore, all the IRL composites had a single peak and a low PDI, indicating that the particles had a relatively narrow size distribution (Fig. 3). The particle size of all latex composites was smaller than that of Mnt (~1 μm), which is due to the strong shear during the emulsification process, resulting in a significant reduction in the Mnt particle size.

Compared to NRL, the above results indicated that when the amount of Mnt was <5 phr, all the as-prepared Mnt/IRL composites were stable, had a large solids content and small particle sizes, similar to the performance of NRL.

XRD of the Mnt and Mnt/IRL Composite Films

Mnt has characteristic diffraction peaks corresponding to its ordered silicate layers in the XRD patterns of the Mnt and Mnt/IRL composite films (Fig. 4). The peak intensity at 5.73°2θ corresponds to the reflection of the (001) planes of Mnt. The absence of a 001 reflection in the patterns of the composite films indicates that Mnt is present as exfoliated layers and a uniform structure is formed between Mnt and IR rubber macromolecular chains.

Fig. 4

XRD patterns of the Mnt and Mnt/IRL (3 phr) composite films

Morphology of the Mnt/IRL Latex Composites

The TEM images of the IRL and Mnt/IRL latex composites containing 0, 1, 3, 4, and 5 phr Mnt (Fig. 5) showed that when the amount of Mnt was 0 phr, the latex particles were spherical. With the addition of increasing amounts of Mnt, aggregated Mnt on the surface of the latex particles was observed. The best dispersion was observed when the amount of Mnt was 3 phr. At 4 phr Mnt, the latex particles began to aggregate to a significant extent. As the amount of Mnt increased to 5 phr, agglomeration occurred in the Mnt/IRL latex composites, and the spherical structure of the original latex particles was destroyed (Fig. 5e), which was consistent with the test results regarding particle size. The optimal amount of Mnt was 3 phr.

Fig. 5

TEM images of Mnt/IRL latex composites: a IRL, b Mnt/IRL (1 phr), c Mnt/IRL (3 phr), d Mnt/IRL (4 phr), and e Mnt/IRL (5 phr)

Thermogravimetric Analysis (TGA) of the IRL and Mnt/IRL Composite Films

The TGA and DTGA curves for IRL and Mnt/IRL composite films containing 3 and 5 phr Mnt (Fig. 6) revealed initial degradation of the films at ~334℃; the maximum degradation occurred at 373°C, which was the same as pristine IR. Mnt does not increase the thermal stability of the Mnt/IRL composite films.

Fig. 6

TGA and DTGA analysis of IRL and Mnt/IRL composite films

SEM of IRL and Mnt/IRL Composite Films

SEM of Raw Rubber Composite Films

Characterization of the morphology of the raw rubber film surface is shown in Fig. 7. The film samples were prepared by the casting method. The latexes were cast on a petri dish (diameter = 80 mm) and left to dry in air until transparent. This showed that the pure IRL films had a flat and smooth surface. When the amount of Mnt was ≤3 phr, there was little change to the surface, indicating good compatibility between the IR macromolecules and Mnt. However, when the amount of Mnt increased to 5 phr, significant aggregation of Mnt particles occurred and cracks appeared in the film surface. This occurred because Mnt particles, serving as dispersed phases, aggregated and formed stress concentration points in the film. Due to the rigidity of the Mnt particles, they did not deform under stress, leading to cracks on the surface of the film and a decrease in its strength. Therefore, when the amount of Mnt was 3 phr, the composite films had the best surface appearance.

Fig. 7

SEM images of the IRL and Mnt/IRL composite films surface: a IRL, b Mnt/IRL (1 phr), c Mnt/IRL (3 phr), and d Mnt/IRL (5 phr)

SEM of the Fractured Surface of IRL and Mnt/IRL Vulcanized Composite Films

The morphology of the fractured Mnt/IRL vulcanized composite films is shown in Fig. 8. The interface between filler and rubber matrix was investigated by observing the quenched section of the Mnt/IRL films. The cross-section of the pure IRL film was relatively flat, which indicated that the system was homogeneous. However, the vulcanized film with 3 phr Mnt had a rough and reticular section with obvious tensile filaments and a pulled Mnt lamellar structure, which indicated that Mnt enhanced the interfacial interaction between IR macromolecules and Mnt layers and increased the mechanical properties of the rubber film (Reference Jiang, Song, Zhai, Chi and YongHu et al., 2020). Mnt was well dispersed in the IR matrix and clusters and blocks of uneven size were not observed (Fig. 8c), even at higher magnification. Mnt was observed to be uniformly dispersed and wrapped in the IR macromolecules (Fig. 8d).

Fig. 8

SEM images of the fractured IRL and Mnt/IRL composite vulcanized films: a, b IRL and c, d Mnt/IRL (1 phr)

Mechanical Properties of the IRL and Mnt/IRL Composite Films

The measured mechanical properties of the vulcanized films of pure IRL and Mnt/IRL composite films with various amounts of Mnt (Fig. 9) revealed that, when the amount of Mnt was < 5 phr, the tensile strength and modulus at 300% elongation (M300) of the Mnt/IRL latex composites films were greater than those of the IRL film. With increase in the amount of Mnt, the tensile strength of the Mnt/IRL films increased and reached a maximum value of 16.5 MPa at 3 phr, a 1.4 × greater tensile strength value than those of pure IRL films, i.e. close to the strength of the pure NRL film. This indicates that a small addition of Mnt improves the tensile strength of the IRL films. The improvement in tensile strength of the nano-filler at low additions is mainly due to the strong interfacial interactions between the nano-filler and the rubber matrix, which leads to the uniform dispersion of nano-filler in rubber (Reference Chen, Wei, Zhu, Luo and LiuChen et al., 2019; Reference Song, Xu, Wu, Cheng, Guo and WangSong et al., 2017; Reference Sui, Zhong, Yang and YuSui et al., 2008). Above 3 phr Mnt, the tensile strength of the Mnt/IRL films decreased but remained higher than that of the pure IRL film. At high levels of Mnt, the tensile strength of the films decreased, possibly due to the aggregation of Mnt in the polyisoprene rubber matrix.

Fig. 9

Mechanical properties of the IRL and Mnt/IRL composite films: Columns from left to right are IRL, Mnt/IRL (1 phr), Mnt/IRL (3 phr), Mnt/IRL (4 phr), Mnt/IRL (5 phr), NRL

With increasing amounts of Mnt, the flexibility of polyisoprene macromolecular chains becomes limited and the elongation at break first decreases and then increases. The initial decrease in elongation at break is typically observed in polymer composites because the Mnt has large rigidity, large specific surface area, and a large aspect ratio, which helps to improve the stiffness and restrict the movement of the rubber chains (Reference Joly, Garnaud, Ollitrault, Bokobza and MarkJiang et al., 2015; Reference Rajaraman, Amarendra, Ponnamma, Thomas and VarugheseRajaraman et al., 2015). Moreover, under high loads, the filler–filler interaction reduces the elongation at break and leads to a reduction in flexibility (Reference Ravindren, Mondal, Nath and DasRavindren et al., 2018). The tendency for the elongation at break to increase with increasing amounts of Mnt is due to local Mnt agglomeration, which renders it unable to restrict the movement of the rubber macromolecular chain.

Vulcanization and Reinforcement Mechanism of the Mnt/IRL Composite Films

The aforementioned physical and mechanical properties can be explained from the perspective of Mnt dispersion in latex and the vulcanization mechanism of the rubber film, as illustrated in Fig. 10. During the latex mixing stage, the particles of IRL are mixed with the Mnt aqueous suspension comprising delaminated silicate layers. Each latex particle consists of several rubber macromolecules; these latex particles adsorb onto the already delaminated Mnt layers, resulting in a uniform dispersion of Mnt in the latex. After the drying and film-forming process, the IR rubber macromolecules enter the Mnt layers to form a Mnt/IRL composite film with a uniform dispersion of Mnt. The nanoscale dispersion of Mnt in the IR matrix results in strong binding forces between them and increases crosslinking density in the Mnt/IRL film. In addition, the presence of Mnt layers restricts the movement of the IR macromolecules during stress. This restriction enhances the overall rigidity of the macromolecular chains, leading to a decrease in elongation at break, an increase in tensile strength, and a decrease in the tendency for the growth of cracks.

Fig. 10

Vulcanization mechanism and structure scheme of Mnt/IRL composite films

Consequently, the tensile strength of the Mnt/IRL composite film is enhanced after adding a small amount of Mnt. However, when the amount of Mnt exceeds a certain value, the tensile strength of the composite decreases due to Mnt agglomeration, resulting in poor compatibility between Mnt and the IR matrix.