5. In Situ Polymerization 3907 5.1. General Polymerization 3907 5.2. Photopolymerization 3910 5.3. Surface-Initiated Polymerization 3912 5.4. Other Methods 3913 6. Colloidal Nanocomposites 3913 6.1. Sol-Gel Process 3914 6.2. In Situ Polymerization 3916 6.2.1. Emulsion Polymerization 3917 6.2.2. Emulsifier-Free Emulsion Polymerization 3919 6.2.3. Miniemulsion Polymerization 3920 6.2.4. Dispersion Polymerization 3921 6.2.5. Other Polymerization Methods 3923 6.2.6. Conducting Nanocomposites 3924 6.3. Self Assembly 3926 7. Other Preparative Methods 3926 8. Characterization and Properties 3928 8.1. Chemical Structure 3928 8.2. Microstructure and Morphology 3929 8.3. Mechanical Properties 3933 8.3.1. Tensile, Impact, and Flexural Properties 3933 8.3.2. Hardness 3936 8.3.3. Fracture Toughness 3937 8.3.4. Friction and Wear Properties 3937 8.4. Thermal Properties 3938 8.5. Flame-Retardant Properties 3941 8.6. Optical Properties 3942 8.7. Gas Transport Properties 3943 8.8. Rheological Properties 3945 8.9. Electrical Properties 3945 8.10. Other Characterization Techniques 3946 9. Applications 3947 9.1. Coatings 3947 9.2. Proton Exchange Membranes 3948 9.3. Pervaporation Membranes 3948 9.4. Encapsulation of Organic Light-Emitting Devices 3948

Polymer/Silica Nanocomposites: Preparation, Characterization, Properties, and Applications

Uneven distribution of nanoparticles in immiscible fluids: Morphology development in polymer blends

https://cyberleninka.org/article/n/397502.pdf

Melt rheology of organoclay and fumed silica nanocomposites

https://hal.archives-ouvertes.fr/hal-01087663/document

Structuration, selective dispersion and compatibilizing effect of (nano)fillers in polymer blends

Immiscible polymer blends stabilized with nano-silica particles: Rheology and effective interfacial tension

Largely improved toughness of PP/EPDM blends by adding nano-SiO2 particles

Polyoxymethylene (POM)/elastomer/filler ternary composites were prepared, in which thermoplastic polyurethane (TPU) and an inorganic filler, CaCO 3 were used to achieve balanced machanical properties of POM. A two -step processing method, in which the elastomer and the filler were mixed to a masterbatch first and then the masterbatch was melt-blendend with pure POM, was used to obtain a coreshell microstructure with CaCO 3 covered by TPU. A brittleductile transition phenomenon was observed with increasing TPU content for this ternary system. To better understand the toughening mechanism, we investigated the fractured surface, interparticle distance, and the spherulite size of POM as function of the TPU and Ca CO 3 content. The critical TPU content depended on not only the content of CaCO 3 , but also the size of CaCO 3 particles. The observed brittle-ductile transition was discussed based on the crystallinity and spherulite size of POM as well as Wu's critical interparticle distance theory. The results showed that the impact strengh of POM/TPU/CaCO 3 ternary system depends on a critical, interparticle distance, which varies from one system to another. The dependence of the impact strengh on the spherulite size was considered for the first time, and a single curve was constructed. A critical spherulite size of 40 micron was found, at which brittle-ductile transition occurs, regardless of the TPU and CaCO 3 content or the size of CaCO 3 particles. Our results indicate that the spherulite size of POM indeed plays a role in determining the toughness, and must be considered when discussing the toughening mechanism.

Brittle-ductile transition and toughening mechanism in POM/TPU/CaCO3 ternary composites

In this article, the phase morphology and mechanical properties of polypropylene (PP)/ethylene–octane copolymer (POE) blends with fixed ratio (60/40) obtained via different processing conditions, including barrel temperature, injection speed, and mold temperature, have been investigated. SEM was carried out for detailed characterization of phase morphology from the skin to the core, layer by layer. It was interesting that for all the processing conditions no dispersed POE elastomer was observed in the skin layer but elongated POE particles with large size were observed in the subskin layer. From the transition zone to the core layer, an increased phase separation was observed, which could lead to a formation of cocontinuous morphology, depending on the processing condition used. Higher barrel temperature, lower mold temperature, and higher injection speed could result in a smaller size of POE phase. The tensile strength and impact strength were found not sensitive to barrel temperature and mold temperature but to the low injection speed, both tensile strength and impact strength had a higher value for specimen obtained via low injection speed. The formation of the skin-core morphology and the effect of processing conditions on the phase morphology were discussed based on crystallization kinetics of PP matrix, rheology, and shear induced phase mixing. © 2007 Wiley Periodicals, Inc. J Appl Polym Sci 2007

Hierarchy structure in injection molded polypropylene/ethylene–octane copolymer blends

A kind of hydrophilic nano-SiO2 was applied to poly(ethylene terephthalate)/polyamide-6 (PA-6) blends. Melt-blended composites were prepared at various component ratios and different nano-SiO2 levels. Mechanical, morphological, dynamic mechanical, and thermal tests were carried out to characterize the properties, morphology, and compatibilization of the composites. Increased impact strength, tensile strength, and modulus were observed by adding nano-SiO2 particles in the blends. The nano-SiO2 particles were found to be preferentially dispersed in PA-6, resulting in an increase of glass transition temperature and crystallization of PA-6. The mechanism of morphology and properties changes was discussed based on the selective dispersion of nano-SiO2 particles in the blends. © 2007 Wiley Periodicals, Inc. J Appl Polym Sci 104: 2288–2296, 2007

Morphology and properties of PET/PA-6/SiO2 ternary composites

Background: Poly(ethylene terephthalate) (PET)/polyamide-6 (PA-6) blends are promising for engineering and food-packaging applications. However, their poor toughness limits their use. In this study, an ethylene–acrylate–(maleic anhydride) terpolymer (E-AE-MA) was added to PET/PA-6 blends in order to improve the toughness.



Results: Izod impact tests indicated an excellent toughening effect of E-AE-MA. E-AE-MA particles were observed to be selectively dispersed at the interface between PET and PA-6 phases and in the domain of the PA-6 phase. Fourier transform infrared spectroscopy and differential scanning calorimetry results demonstrated that the formation of E-AE-MA layers around PA-6 particles cut off the interaction between PET and PA-6, resulting in an enlarged PA-6 phase domain.



Conclusion: Based on the experimental results, a core–shell microstructure, with PA-6 as a hard core and E-AE-MA as a soft shell, could be suggested. The formation of this core–shell microstructure, along with the increased PA-6 phase domain size, is the main toughening mechanism of E-AE-MA in PET/PA-6 blends. Copyright © 2007 Society of Chemical Industry

Effect of ethylene–acrylate–(maleic anhydride) terpolymer on mechanical properties and morphology of poly(ethylene terephthalate)/polyamide-6 blends

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