Microstructure and properties of highly filled rubber/clay nanocomposites prepared by melt blending
Introduction
In the past decade, polymer/clay nanocomposites (PCNs) have attracted much attention from both academic and industrial researchers, since these nanocomposites commonly show significantly improved mechanical properties, reduced moisture adsorption, superior flame retardancy and decreased permeability, when compared to their micro- and macrocomposite counterparts and their neat polymer matrices [1], [2], [3], [4], [5], [6], [7]. In general, there are two idealized morphologies that can be developed using nano-silicate fillers: (1) exfoliated (i.e., silicate layers are totally delaminated and disordered), and (2) intercalated (i.e., silicate layers are partially separated by polymer chains but ordered structure is still retained), which are shown in Fig. 1a and b, respectively. The spatial distribution of clay particles in exfoliated PCNs is much more homogeneous than that in intercalated nanocomposites. In the exfoliated PCNs, the individual clay layer acts as the basic reinforcing unit. In contrast, in the intercalated PCNs, the reinforcement unit is the intercalated clay stacks, the equivalent aspect ratio of which is much lower than that of an individual clay layer [8], [9]. As a result, an exfoliated structure is desirable to obtain best enhancements of properties. However, exfoliation is challenging, because it requires fine-tuning of clay surface chemistry, synthesis and processing conditions.
We expect almost all the polymer chains would be inserted into the intra-galleries of silicate layers when the concentration of organically modified clay (OMC) reaches a very high level, thereby the entire polymer matrix would be full of intercalated silicates as shown schematically in Fig. 1c. In this highly filled intercalated PCN, the dispersion homogeneity of the individual silicate layers would be much better than that in the conventional intercalated PCNs with low OMC contents, and akin to that in the exfoliated PCNs. Thus, it has been predicted that PCNs with the above mentioned microstructure, hereafter called the “highly-filled intercalated structure”, should possess very much improved mechanical and gas barrier properties.
Based on the theory of polymer melt intercalation in OMC [10], [11], it should be thermodynamically possible to obtain highly filled PCNs by melt blending. However, there are very few experimental studies on highly filled PCNs due to processing difficulties caused by the high viscosity of polymer melt filled with large amounts of nano-silicates [12], [13], [14]. To prepare highly filled PCNs with homogeneous dispersion of silicate platelets, both long processing time and high mixing torque are required. Hence, for thermoplastic polymer matrices, long processing times under high-temperature would result in polymer degradation and reduction of the resultant nanocomposite properties. Also, the processing equipment for plastics (i.e., screw extruder) hardly sustains such large mixing torques. To overcome these problems, Koo et al. [12], [13] used maleated polyethylene and maleated polypropylene with low molecular weights to prepare highly filled PCNs with the melt intercalation method. Zerda et al. [14] also prepared highly filled polymethyl methacrylate/clay intercalated nanocomposites using in situ polymerization intercalation in supercritical carbon dioxide. In these studies, however, very limited properties of these highly filled PCNs were measured. Compared to thermoplastics, the processing temperature of rubbers is relatively low (i.e., less than 60 °C), thus allowing long processing times. Moreover, the processing facility for rubbers (i.e., inner mixer and two-roll mill) can provide and bear large mixing torques.
In this work, we showed for the first time that a series of highly filled PCNs based on several rubber matrices could be successfully processed by melt blending. These fabricated nanocomposites filled with high clay contents (up to ∼60 wt%) display great improvement in storage modulus at ambient and high (e.g., 100 °C) temperatures, and large reduction in gas permeability. Furthermore, some novel and interesting phenomena were observed.
Section snippets
Materials and preparation of nanocomposites
Ethylene-propylene diene rubber (EPDM, grade 4045) and styrene–butadiene rubber (SBR, grade 1502) were provided by CNPC Jilin Chemical, China. Epichlorohydrin rubber (ECO, grade C65) was purchased from Wuhan Organic Industrial Co. Ltd., China. Nanomer® I.30P with an initial basal spacing ∼2.2 nm is a montmorillonite (MMT) modified by octadecylamine (Nanocor Inc., USA). Other reagents were commercially available products. The formulation of rubber/OMC compounds is described in Table 1. The weight
Microstructures of RCNs
WAXD patterns of pure OMC and RCNs with different OMC contents are shown in Fig. 2. For EPDMCNs with low OMC contents (as shown in Fig. 2b), there are two basal reflection (0 0 1) peaks for OMC dispersed in nanocomposites when OMC content is relatively low (i.e., 9.1 or 28.6 wt%). One locates at lower angle, whose basal spacing is obviously larger than 2.2 nm of the initial basal spacing of OMC, indicating the existence of intercalated structures. The other locates at higher angle, corresponding to
Conclusions
Our study has confirmed that highly filled rubber/clay nanocomposites (up to ∼60 wt%) can be successfully prepared by melt blending. It is seen for the first time that the melt-like transition of alkyl chains of surfactant still occurs in the OMC, and can considerably influence the mechanical properties of highly filled RCNs. The highly filled nanocomposites obtained have very high modulus at both ambient and high temperatures making them promising substitutes for fiber reinforced rubber
Acknowledgements
We would like to thank National Natural Science Foundation of China (50403029), Beijing Nova Program (H010410010112 and 2006A15) and the Australian Research Council (ARC) for the support of this project. Z.-Z. Yu and Y.-W. Mai are Australian Postdoctoral Fellow and Australian Federation Fellow, respectively, supported by the ARC. We also thank Szu-Hui Lim for her painstaking work on the high-magnification TEM micrographs in Fig. 4.
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