Role of silanised halloysite nanotubes on the morphological and materials characteristics of thermoset composites

The effects of nano-reinforcements on the material characteristics of thermoset nanocomposites in relation to their different morphological structures are not yet well understood. This study investigates the effects of untreated halloysite (HNT) and vinyltrimethoxysilane (VTMS)–treated halloysite nanotubes (s-HNT) on the morphological and materials characteristics of highly crosslinked unsaturated polyester (UPE) nanocomposites. The grafting of the VTMS coupling agent on the halloysite surface was performed using the sol-gel process. Nanocomposites based on different weight percentages (1 wt % to 9 wt %) of HNT or s-HNT were prepared via high shear disperser, followed by the ultrasonication technique. The morphological structures and dispersion of halloysite particles in the UPE matrix were examined using transmission electron microscopy (TEM), and wide-angle and small-angle x-ray scattering (WAXS and SAXS). Fourier Transform Infrared (FT-IR) spectroscopy was used to determine the molecular structures and indicate the vibrational states of the chemical bonds obtained after curing. Thermogravimetric analysis (TGA) was applied to detect the thermal stability, and differential scanning calorimetry (DSC) spectra were applied to measure the glass transition temperature (Tg) in heating mode. The viscoelastic properties—the storage modulus (Eَ), loss modulus (E˝) and tan (δ)—were measured using dynamic mechanical analysis (DMA). Mechanical properties viz. tensile strength, Young’s modulus, elongation at break, flexural strength and modulus of the developed materials were determined. The elastic modulus was predicted using different mathematical models—the Halpin-Tsai, Smallwood-Einstein, Kerner, and Guth and Gold models—in order to further understand the correlation between the mechanical properties and the morphology. The tribological performance of neat UPE and different nanocomposite systems was also explored. Wear resistance was evaluated using block-on-ring (BOR) configuration against a stainless steel counterpart under dry sliding conditions with different operating parameters. The topography analysis of worn surfaces was examined using scanning electron microscopy (SEM) analysis to determine the wear mechanisms occurring in such materials. The micromechanism of plastic deformation of neat UPE and its nanocomposite systems was characterised under impact loading conditions. The impact strength and total energy were performed with a falling-weight impact tester at different temperatures (-20 °C, +20 °C and +60 °C). The morphologies of tensile-fractured surfaces and impacted-fractured surfaces of unfilled UPE and UPE filled with HNT and s-HNT nanocomposites were identified to delineate their fracture modes. The fracture toughness measurements represented by the critical stress intensity factor (KIc) and critical strain energy release rate (GIc) were calculated based on linear elastic fracture mechanics (LEFM) and two different geometries tested under two different loading conditions: a single-edge notch (SEN) specimen under three-point bending (SEN-3PB) and a compact tension (CT) specimen under tension. The crack initiation and propagation phenomenon were simulated using a traction-separation cohesive element method via ABAQUS finite element (FE) software. The SEM observations were used to identify the roles of HNT and s-HNT particles in toughening mechanisms and initiating plastic deformation in the nanocomposites. The results showed that the surface of s-HNT was rougher than the untreated HNT particles due to the presence of multiple interfacial bonding sites on the silanised surface, which induced better adhesion and load transfer among the interface regions. A more well-dispersed structure with less skewed-like aggregates was observed in the UPE/s-HNT over the UPE/HNT composites. The incorporation of HNT or s-HNT particles into the UPE nanocomposites changed their crystalline structure, indicating a high degree of nanotube orientation. The FT-IR spectra of the s-HNT powder exhibited that the Si-O-Si absorption band occurred in the region of 701 to 1,085 cm-1 wavenumbers. No significant change in the thermal stability of the nanocomposites was observed with the use of silane-treated nanoparticles. The effect of HNT or s-HNT on the Tg values was relatively insignificant, while they slightly reduced with increasing halloysite concentrations. This was likely because coupling of halloysite to the polymer through adsorption and hydrogen bonding led to strengthening the interface and reducing the Tg values. All material properties—such as tensile and flexural strength, impact strength and fracture toughness—except wear resistance, exhibited a steady-state increasing trend with the incorporation of up to 5 wt% HNT or s-HNT into the UPE resin. The 3% HNT/UPE or 3% s-HNT/UPE nanocomposites were found to obtain the highest values of these properties supported with uniformly dispersed particles. It was also proven that the computational results of damage zone and unstable crack propagation validated by the cohesive element method were convergent with the experimental data. Compared to the HNT, the addition of the same content of s-HNT particles indicated slightly higher strength and toughness owing to the well-dispersed silanised particles and the enhanced interfacial adhesion thereof on initiating/participating in plastic deformation in the nanocomposites. Further increase of halloysite, irrespective of whether they were untreated or silane-treated, showed gradual decreases in most material properties associated with the presence of large clusters in the UPE nanocomposites. The SEM observations of the fracture surfaces showed brittle fast fracture for neat UPE and coarser surfaces with different energy dissipation mechanisms for the nanocomposites. With the introduction of untreated halloysite, zone shielding and shear yielding mechanisms with the presence of full particle debonding —which activates void expansion and matrix shear deformation— were observed and suggested to be responsible for the toughness improvement in the the UPE/HNT nanocomposites. In addition, other major mechanisms—massive shear banding, crack deflection and local plastic deformation—occurred around the crack initiation zone, while river line patterns, a tail-like structure and the formation of microcracks mechanisms were observed in the UPE/s-HNT nanocomposites

13th International Conference on Fracture (ICF 2013)

In this study, the role of nanoclay particles (MMT) on micro- and nano-scale deformation and fracture behaviour of a crosslinked unsaturated polyester (UPE)-based nanocomposites is explored. Nanocomposites from well-dispersed MMT particles and the UPE resin were prepared by a combination of mechanical mixing and ultrasonication process. The morphological characteristics of nanocomposites were examined by TEM. Critical stress intensity factor (KIc) based on linear elastic fracture mechanics (LEFM) and compact tension (CT) configuration is evaluated. The fracture modes and toughening mechanisms of the fractured-surfaces were identified by SEM analysis. An intercalation/partially exfoliation structure of UPE/MMT nanocomposite with moderate enhancement in fracture toughness is observed. The addition of 3 wt.% MMT exhibits the highest KIc value of nanocomposite by a 61% improvement over the neat UPE. The fracture surface of the neat UPE seems to be a highly brittle fracture without crazing and a coarser surface with the appearance of plastic deformation zones of the nanocomposites

Effect of SiC addition on mechanical and wear characteristics of WC-32(W-Ti)C-6Co cemented carbides

The effect of silicon carbide (SiC) addition on mechanical and wear properties of cemented carbides was investigated in this study. Different percentages (1-7 wt.%) of SiC were added to the cemented carbides mixture of WC/32 wt. % (Ti-W) C/6 wt.% Co. The microstructural characteristics of the developed materials was identified using scanning electron microscopy (SEM) and Rockwell-A macrohardness (HRA), Vickers microhardness (Hv) as well as transverse rupture strength (TRS) were measured. The experimental results revealed that inserting SiC inclusion into the cemented carbides is found to be useless for two reasons. First, the microstructure of the developed carbides has more aggregations of largely contiguous SiC grains led to presence of rich/poor regions and consequently poor compatibility between carbides and the binder. Second, all properties of the cemented carbides greatly declined with the addition of SiC particles

The effects of material formulation and manufacturing process on mechanical and thermal properties of epoxy/clay nanocomposites

A holistic study was conducted to investigate the combined effect of three different pre-mixing processes, namely mechanical mixing, ultrasonication and centrifugation, on mechanical and thermal properties of epoxy/clay nanocomposites reinforced with different platelet-like montmorillonite (MMT) clays (Cloisite Na+, Cloisite 10A, Cloisite 15 or Cloisite 93A) at clay contents of 3–10 wt%. Furthermore, the effect of combined pre-mixing processes and material formulation on clay dispersion and corresponding material properties of resulting composites was investigated using X-ray diffraction (XRD), transmission electron microscopy (TEM), scanning electron microscopy (SEM), flexural and Charpy impact tests, Rockwell hardness tests and differential scanning calorimetry (DSC). A high level of clay agglomeration and partially intercalated/exfoliated clay structures were observed regardless of clay type and content. Epoxy/clay nanocomposites demonstrate an overall noticeable improvement of up to 10 % in the glass transition temperature (Tg) compared to that of neat epoxy, which is interpreted by the inclusion of MMT clays acting as rigid fillers to restrict the chain mobility of epoxy matrices. The impact strength of epoxy/clay nanocomposites was also found to increase by up to 24 % with the addition of 3 wt% Cloisite Na+ clays. However, their flexural strength and hardness diminished when compared to those of neat epoxy, arising from several effects including clay agglomeration, widely distributed microvoids and microcracks as well as weak interfacial bonding between clay particles and epoxy matrices, as confirmed from TEM and SEM results. Overall, it is suggested that an improved technique should be used for the combination of pre-mixing processes in order to achieve the optimal manufacturing condition of uniform clay dispersion and minimal void contents

Cracks, microcracks and fracture in polymer structures: Formation, detection, autonomic repair

The first author would like to acknowledge the financial support from the European Union under the FP7 COFUND Marie Curie Action. N.M.P. is supported by the European Research Council (ERC StG Ideas 2011 n. 279985 BIHSNAM, ERC PoC 2015 n. 693670 SILKENE), and by the EU under the FET Graphene Flagship (WP 14 “Polymer nano-composites” n. 696656)