Abstract:In order to link the fundamental research field of polymer crystallization with the technical important field of composite materials polymer-layered silicate nanocomposites from polyethylene (PE) are prepared and their morphology and properties are investigated. The effect of an external confinement introduced by highly anisotropic silicate layers of organically modified clay minerals on crystal growth and nanocomposite properties has been studied. The prepared nanocomposites of organically modified clay miner… Show more
“…All these observations are in agreement with the behavior reported for PA6 nanocomposites [14][15][16][17]. Generally speaking, presence of an inorganic filler results in poor rearrangement of polymer molecules and thus, favors the formation of the g-phase.…”
Section: Thermal Propertiessupporting
confidence: 91%
“…By comparing the melting peaks at various boehmite concentrations, this low temperature peak appears to grow at the expense of the high melting a-peak, so that the chain arrangement is probably similar to the a-structure. As the melting point is reduced one can speculate that this a 0 -structure forms crystallites with a lower lamellar thickness [15] or involves a distorted lamellar structure arising form the curvature induced by the boehmite cylinders. This should be compared to the observation that in PA6 nanocomposites containing montmorillonite clay platelets a higher melting phase of PA6 has been observed [16]; which probably results from the stabilization of the lamellar crystals.…”
Colloidal boehmite particles have been included into a polyamide-6 matrix by in situ polymerization. The particles have been used without any surface modification. Characterization of the nanocomposites has been carried out using transmission electron microscopy (TEM), dynamical mechanical analysis (DMA) and differential scanning calorimetry (DSC). TEM images indicate that the particles have been homogeneously dispersed in the polymer. DSC results show that the presence of boehmite affects the form of crystallization of polyamide-6, in which case formation of g-structure is favored over the a-structure and an additional a 0 -phase is formed. Some mechanical reinforcement of the matrix has been accomplished as indicated by DMA results. The modulus level off at high boehmite concentrations can be explained by the reduction of the crystallinity, which cancels the effect of the filler. q
“…All these observations are in agreement with the behavior reported for PA6 nanocomposites [14][15][16][17]. Generally speaking, presence of an inorganic filler results in poor rearrangement of polymer molecules and thus, favors the formation of the g-phase.…”
Section: Thermal Propertiessupporting
confidence: 91%
“…By comparing the melting peaks at various boehmite concentrations, this low temperature peak appears to grow at the expense of the high melting a-peak, so that the chain arrangement is probably similar to the a-structure. As the melting point is reduced one can speculate that this a 0 -structure forms crystallites with a lower lamellar thickness [15] or involves a distorted lamellar structure arising form the curvature induced by the boehmite cylinders. This should be compared to the observation that in PA6 nanocomposites containing montmorillonite clay platelets a higher melting phase of PA6 has been observed [16]; which probably results from the stabilization of the lamellar crystals.…”
Colloidal boehmite particles have been included into a polyamide-6 matrix by in situ polymerization. The particles have been used without any surface modification. Characterization of the nanocomposites has been carried out using transmission electron microscopy (TEM), dynamical mechanical analysis (DMA) and differential scanning calorimetry (DSC). TEM images indicate that the particles have been homogeneously dispersed in the polymer. DSC results show that the presence of boehmite affects the form of crystallization of polyamide-6, in which case formation of g-structure is favored over the a-structure and an additional a 0 -phase is formed. Some mechanical reinforcement of the matrix has been accomplished as indicated by DMA results. The modulus level off at high boehmite concentrations can be explained by the reduction of the crystallinity, which cancels the effect of the filler. q
“…The improved properties of the nanocomposite are either ascribed to the polymer-clay interface, [24,25] or to the clay aspect ratio. [6,26] According to Shelley et al, [27] the enhancement of stiffness, strength and barrier properties is the consequence of the existence of a confined polymer fraction having a higher local stiffness.…”
Section: Feature Articlementioning
confidence: 99%
“…Polyamide 6 [82,83] Polymerisation Epoxy [84,85] Poly(methyl methacrylate) [86,87] Poly(e-caprolactone) [88] Polyurethane [89] Polyimide [26,90] Polyamide 12 [91] Polyester [92,93] Melt compounding Polyamide 6 [29,94] Poly(propylene) [95,96] Polyethylene [24] Polyamide 66 [97] Poly(propylene) [98] Solution blending Polyethylene [99] Poly(vinylpyrrolidone) [100] Poly(vinyl alcohol) [101] Poly(ethylene oxide) [1] same metal as Mg 2þ in talcum occupies all sites, the silicate is neutral and mechanical processes can easily separate the layers. In the silicate layers of mica or smectic clay, Na þ , Ca þ or K þ act as counter charges in the gallery spacing resulting in a strong ionic bond which is hard to break.…”
Section: Polymer Matrix Technique Of Preparationmentioning
The present features review article discusses the crystallisation of the polymer matrix when containing silicate layers. The accent is put on nylons (polyamides) and poly(ethylene oxide) as typical hydrophilic polymers and, poly(propylene) from the hydrophobic group. The effects of the clay, either intercalated or exfoliated, on the crystallisation behaviour of the matrix are highlighted. In addition, the crucial aspects of the semicrystalline morphology of the matrix in the presence of the clay platelets are also debated. The overall crystallisation rate is reported to slow down for most of the crystallisable polymer matrices on account of a retarding growth effect exerted by the clay platelets. As far as the location of the exfoliated clay platelets in the polymer matrix is concerned, they are assumed to be rejected from the crystalline phase in the interspherulitic space.magnified image
“…Confinement effects are well known and have been described elsewhere. [14][15][16] Significant alterations in crystallite morphology [11,13,[17][18][19][20][21][22][23][24][25][26] and orientation, [11,13,17,18,21,24,[26][27][28] as well as the crystalline phase(s) present, [11,13,21,[26][27][28][29][30][31][32][33][34][35][36] will also affect the materials properties. Finally, the flexible nature of these layers [37] and their propensity to align at high strains [11,13,[26][27][28][38][39][40][41] and to induce void formation at high stresses [17,…”
We report the first multi‐system study of a layered‐silicate dispersion in polysiloxane/layered‐silicate nanocomposites. A variety of layered silicates (montmorillonite, synthetic fluoromica, laponite, and fluorohectorite) and cationic modifiers (single‐, twin‐, and triple‐tailed surfactants with tails of varying lengths and both primary and quaternary head‐groups) are combined to form organically modified layered silicates, which are then screened for compatibility with low‐molecular‐weight silanol‐terminated poly(dimethylsiloxane) (PDMS). Promising combinations are then selected and studied in greater depth with respect to both molecular weight and polysiloxane end‐group and substituent chemistry. We find that the PDMS backbone is generally incompatible with the layered silicates, regardless of modification type, and that dispersion in PDMS systems results from the presence of polar end‐groups, a result unprecedented in the field of polymer nanocomposites. We go on to quantify the substituent effect, not only with respect to end‐group chemistry, but taking into account changes in the polysiloxane backbone itself. For instance, in the absence of polar end‐groups we observe dispersion in the case of poly(methylphenylsiloxane) but not poly(3,3,3‐trifluoropropylmethylsiloxane). Finally, we apply a new epoxy/amine PDMS curing chemistry to PDMS‐nanocomposite production and show higher levels of layered‐silicate dispersion than observed in comparable silanol‐terminated PDMS‐based systems. Our findings serve as an indication of what is necessary to achieve a layered‐silicate dispersion in polysiloxane/layered‐silicate nanocomposites, and may indicate a more general approach for improving dispersion in systems where the polymer backbone is otherwise incompatible with the layered silicate.
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