The fine-scale precipitates, that occurs during aging, the supersaturated Al–1.0 at.% Mg–x at.% Si (x = 0.6, 1.0 and 1.6) alloys have been investigated by differential scanning calorimetry (DSC), scanning electron microscopy (SEM) and X-ray diffraction (XRD) techniques. The strength of the alloys increases as a high density of very fine β″ coherent and β′ semicoherent precipitates nucleate. The precipitates compositions have been determined by analyzing the X-ray diffraction (XRD) charts, by using Scherrer equation. The obtained results showed that the β″ and β′ precipitates size lies in the nanometer range (from 5 nm to 32 nm). In addition, increasing Si concentration has exhibited an increase in the density of the precipitates, which fortifies the physical properties.

The fine-scale precipitates, that occurs during aging, the supersaturated Al–1.0 at.% Mg–x at.% Si (x = 0.6, 1.0 and 1.6) alloys have been investigated by differential scanning calorimetry (DSC), scanning electron microscopy (SEM) and X-ray diffraction (XRD) techniques. The strength of the alloys increases as a high density of very fine β″ coherent and β′ semicoherent precipitates nucleate. The precipitates compositions have been determined by analyzing the X-ray diffraction (XRD) charts, by using Scherrer equation. The obtained results showed that the β″ and β′ precipitates size lies in the nanometer range (from 5 nm to 32 nm). In addition, increasing Si concentration has exhibited an increase in the density of the precipitates, which fortifies the physical properties.

The fine-scale precipitates, that occurs during aging, the supersaturated Al–1.0 at.% Mg–x at.% Si (x = 0.6, 1.0 and 1.6) alloys have been investigated by differential scanning calorimetry (DSC), scanning electron microscopy (SEM) and X-ray diffraction (XRD) techniques. The strength of the alloys increases as a high density of very fine β″ coherent and β′ semicoherent precipitates nucleate. The precipitates compositions have been determined by analyzing the X-ray diffraction (XRD) charts, by using Scherrer equation. The obtained results showed that the β″ and β′ precipitates size lies in the nanometer range (from 5 nm to 32 nm). In addition, increasing Si concentration has exhibited an increase in the density of the precipitates, which fortifies the physical properties.

The fine-scale precipitates, that occurs during aging, the supersaturated Al–1.0 at.% Mg–x at.% Si (x = 0.6, 1.0 and 1.6) alloys have been investigated by differential scanning calorimetry (DSC), scanning electron microscopy (SEM) and X-ray diffraction (XRD) techniques. The strength of the alloys increases as a high density of very fine β″ coherent and β′ semicoherent precipitates nucleate. The precipitates compositions have been determined by analyzing the X-ray diffraction (XRD) charts, by using Scherrer equation. The obtained results showed that the β″ and β′ precipitates size lies in the nanometer range (from 5 nm to 32 nm). In addition, increasing Si concentration has exhibited an increase in the density of the precipitates, which fortifies the physical properties.

Both radial and spiral distortion of magnetic lens with the field distribution in the form B(z)αzn are analyzed by means of Scherzer's formula. To estimate the performance of the image in electron microscope the dimensionless quality factors (F.Z. Marai, T. Mulvey, Sherzer's formula and the correction of spiral distortion in the electron microscope, Ultramicroscopy 2 (1977) 187–192.), for both radial and spiral distortion is calculated. The results have been compared with different projector lenses.

A process for deep trench filling by BenzoCycloButene (BCB) polymer is explored. Deep trenches with 100-μm depth and different aspect ratios from 1.4 to 20 have been successfully filled by BCB. Besides, chemical mechanical polishing (CMP) of BCB is studied with the main goals of smoothing surface topography of substrate after BCB filling and removing excess BCB coating which may be necessary in some applications. Removal rate for BCB, V RR, of about 0.24 μm/min has been achieved for hard cured BCB films using acid slurry. After CMP, the BCB layer showed a roughness of about 1.36 nm (Rq, measured by atomic force microscopy, AFM).

Numerous techniques have been used to improve the voltage handling capability of high voltage power devices with the aim to obtain the breakdown of a plane junction. In this work, a new concept of low cost, low surface and high efficiency junction termination for power devices is presented and experimentally validated. This termination is based on a large and deep trench filled by BCB (BenzoCycloButene) associated to a field plate. Simulation results show the important impact of trench design and field plate width on termination performances. The experimental breakdown voltage of this Deep Trench Termination (DT2) is close to 1300 Volts: this value validates not only the concept of the DT2 but also the choice of the BCB as a good dielectric material for this termination.

A new method (VHR method) has been derived from Johnson-Mehl-Avrami (JMA) transformation rate equation to calculate the crystallization kinetic parameters of a glassy system. These parameters include the activation energy of crystallization E (kJ/mol), the kinetic exponent n and the frequency factor Ko (s-1). The VHR method starts with obtaining E. Let us consider xi(t) as the volume fractions of crystallization which are obtained at various heating rates βi (K/min). The method for obtaining E depends on finding the temperatures Ti (K) and the times ti (s) which are required to produce the same values of xi(t) at various values of βi. Next, the value of n is obtained by using the temperatures T1 (K) and T2 (K) and the times t1 (s) and t2 (s) which are extracted at two different values of the volume fraction x1(t) and x2(t) at the same heating rate. Finally, the value of Ko may be obtained at any value of x(t) after obtaining the values of E and n, successively. The applicability and the full descriptions of the VHR method have been thoroughly tested on computer simulated crystallization curves. Also,the validity ofthe VHR method has been checked in the cases of n being temperature-independent and temperature-dependent parameter. The VHR technique has been used to estimate the crystallization parameters of Se75.5Te20Sb4.5 chalcogenide glass under non-isothermal conditions.

A new method (VHR method) has been derived from Johnson-Mehl-Avrami (JMA) transformation rate equation to calculate the crystallization kinetic parameters of a glassy system. These parameters include the activation energy of crystallization E (kJ/mol), the kinetic exponent n and the frequency factor Ko (s-1). The VHR method starts with obtaining E. Let us consider xi(t) as the volume fractions of crystallization which are obtained at various heating rates βi (K/min). The method for obtaining E depends on finding the temperatures Ti (K) and the times ti (s) which are required to produce the same values of xi(t) at various values of βi. Next, the value of n is obtained by using the temperatures T1 (K) and T2 (K) and the times t1 (s) and t2 (s) which are extracted at two different values of the volume fraction x1(t) and x2(t) at the same heating rate. Finally, the value of Ko may be obtained at any value of x(t) after obtaining the values of E and n, successively. The applicability and the full descriptions of the VHR method have been thoroughly tested on computer simulated crystallization curves. Also,the validity ofthe VHR method has been checked in the cases of n being temperature-independent and temperature-dependent parameter. The VHR technique has been used to estimate the crystallization parameters of Se75.5Te20Sb4.5 chalcogenide glass under non-isothermal conditions.