Over this temperature range, the misfit strain and root mean square roughness (rms(roughness)) peak at 600 degrees C, decreasing beyond this peak value. The tunability of the dielectric constant at 100 kHz is highest (60% for a field strength FLT3 inhibitor of 300 kV/cm) at the lowest values of rms(roughness) and misfit strain and decreases as these values increase. It is also shown that the morphology of the Pt underlayers is strongly affected by the processing conditions. This in turn influences the tunable behavior of the BST films as much as the substrate temperature during growth and the consequent microstructural variations.”
“Nonisothermal crystallization kinetics and melting behavior

of poly(epsilon-caprolactone)-b-poly(ethylene glycol)-b-poly(epsilon-caprolactone) triblock copolymer (PCL-PEG-PCL), in which the weight fraction of the PCL block LDK378 is 0.87, has been studied by differential scanning calorimetry (DSC). The nonisothermal crystallization data at various cooling rates are analyzed with the Ozawa, modified Avrami, and Mo models. The modified Avrami and Mo models were found to describe the nonisothermal crystallization processes fairly well. The values of the Avrami exponent

n were near three, suggesting the crystallization process with a three-dimensional crystallite growth by heterogeneous nucleation mechanism. The crystallization activation energy estimated from the cooling scans using Kissinger’s method was 168.9 KJ/mol. The phenomenon of the double melting behavior was observed for the PCL block during melting process after nonisothermal crystallization, being the reflection of a complicated crystallization process and the existence of the amorphous middle PEG block. (C) 2009 Wiley Periodicals, Inc. J Appl. Polym Sci 114: buy AC220 1133-1140, 2009″
“In order to image a source or a scatterer embedded in a three dimensional solid, acoustic/elastic wave data from an actual experiment are time reversed

and backpropagated through a numerical model of the medium. The model makes use of estimates for the elastic constants of the laboratory solid. These estimates may not be very precise, for example, due to experimental uncertainties. Poor characterization of the medium leads to the degradation of the time reversal focus, therefore, to poor medium imaging. In this work, we report on the results of investigating the time reversal focus degradation as the estimates depart from the real values. Very small deviations from the medium’s actual elastic constants degrade the time reversal focus dramatically. However, decreasing the total duration of the signals used for time reversal can attenuate the degradation in some cases. We propose a new method to compensate for the deviations of the model medium’s elastic constants from the actual values.