Lateral domain size

Adechanical stahility. ChemisoriDtion to tire surface, intennolecular interactions and crosslinking between adjacent compounds—if possible—all contribute to tire resulting stability of tire monolayer film. Lateral force microscopy investigations revealed tliat tire mechanical stability towards lateral forces on tire nanometre scale is likely to be detennined by tire defect density and tire domain size on a nano- to micrometre scale [163, 1731. 

Els and McGill [48] reported the action of maleic anhydride on polypropylene-polyisoprene blends. A graft copolymer was found in situ through the modifier, which later enhanced the overall performance of the blend. Scott and Macosko [49] studied the reactive and nonreactive compatibilization of nylon-ethylene-propylene rubber blends. The nonreactive polyamide-ethylene propylene blends showed poor interfacial adhesion between the phases. The reactive polyamide-ethylene propylene-maleic anhydride modified blends showed excellent adhesion and much smaller dispersed phase domain size. 

Several structure sizes caused by microphase separation occurring in the induction period as well as by crystallization were determined as a function of annealing time in order to determine how crystallization proceeds [9,18]. The characteristic wavelength A = 27r/Qm was obtained from the peak positions Qm of SAXS while the average size of the dense domains, probably having a liquid crystalline nematic structure as will be explained later, was estimated as follows. The dense domain size >i for the early stage of SD was calculated from the spatial density correlation function y(r) defined by Debye and Buche[50]... 

The systems undergoing phase transitions (like spinodal decomposition) often exhibit scaling phenomena [ 1—4] that is, a morphological pattern of the domains at earlier times looks statistically similar to a pattern at later times apart from the global change of scale implied by the growth of L(f)—the domain size. Quantitatively it means, for example, that the correlation function of the order parameter (density, concentration, magnetization, etc.)... 

The search for theoretical relations concerning domain size and shape is ongoing, and several efforts to derive a theoretical formulation have been made. The first attempt was by Donatelll et al, in 1977 [29], who derived an equation especially for seml-IPN s of the first kind (polymer I crosslinked, polymer II linear) and extended to full IPN s by assuming that the molecular weight of polymer II is infinite. Later, this equation was simplified for... 

There has been considerable interest in the characterization of the conformation and orientation of amphiphilic molecules in Langmuir monolayers in the past few decades [1-5]. Monolayers at the air-water interface are widely employed as convenient experimental paradigms that mimic many vital biological processes. The advantages realized when using monolayers as models for biological interfaces arise primarily from the ease with which experimental variables may be manipulated. These include parameters that are not readily controlled in bulk phases or in films prepared on solid substrates, such as lateral pressure, surface area, and domain size and shape [6]. 

The first moment q t) of the structure factor is also computed in order to observe the coarsening processes in the later stage of phase separation more clearly. This quantity q t), the inverse of which is a measure of the average domain size, is defines as... 

For each composition a series of five to seven samples were produced with increasing delay time between the beginning of the PU formation (to) and the initiation (ti) of the PBMA formation. All series showed a smooth decrease in opacity and in PBMA domain size with increased delay time. The data for the 5 5 compositions are shown in Table I. In this and later Tables, designations such as "11-4.5" refer to the 11 series, sample 4, nominal composition containing a PU weight fraction of 0.5. For similar delay times the 3 7 compositions were... 

The N -LC film samples were prepared by dissolving chiral Poly-4 or achiral Poly-4 with chiral dopant (10 wt %) in toluene (5-10 wt %) to form a lyotropic LC state. The LC solution was subsequently cast onto a quartz plate, which was later exposed to toluene vapor for one hour and dried slowly at room temperature. Toluene vapor exposure of the N -LC film was performed to increase the domain size of the N -LC phase. 

It was reported earlier that PEI and PPSU formed a clear miscible blend with a single Tg observed by DSC and DMA (Ramiro et al. 2006). However, they could not ascertain the absence of a dispersed phase. This was because the refractive indices of the two components were too close to be differentiated. Later, it was found that the clarity in these blends is likely a result of small domain size of the dispersed phase (<0.5 pm) as determined by TEM (Kailasam et al. 2009). These PEI/PPSU blends are hydrolysis-resistant- capable of >1,000 steam autoclave cycles at 134 °C, while still retaining good ductility, toughness, and transparency (Sanner 2011). 

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