The acetyl benzo[f]coumarin condensed with phenyl hydrazine to afford the corresponding phenyl hydra
zone which cyclized into the pyrazolyl benzocoumarin under Vilsmeier reaction conditions. The pyrazolyla
ldehyde was used as starting material for synthesis of other heterocyclic compounds containing pyrazolylben
zocoumarin moiety. The ethyl benzo[f]coumarin carboxylate were subjected to react with other reagents to
synthesize thiazolidinyl and oxadiazolyl derivatives attached to benzocoumarin system. Some of novel syn
thesized compounds showed highly antibacterial and antifungal activities.

The acetyl benzo[f]coumarin condensed with phenyl hydrazine to afford the corresponding phenyl hydra
zone which cyclized into the pyrazolyl benzocoumarin under Vilsmeier reaction conditions. The pyrazolyla
ldehyde was used as starting material for synthesis of other heterocyclic compounds containing pyrazolylben
zocoumarin moiety. The ethyl benzo[f]coumarin carboxylate were subjected to react with other reagents to
synthesize thiazolidinyl and oxadiazolyl derivatives attached to benzocoumarin system. Some of novel syn
thesized compounds showed highly antibacterial and antifungal activities.

The acetyl benzo[f]coumarin condensed with phenyl hydrazine to afford the corresponding phenyl hydra
zone which cyclized into the pyrazolyl benzocoumarin under Vilsmeier reaction conditions. The pyrazolyla
ldehyde was used as starting material for synthesis of other heterocyclic compounds containing pyrazolylben
zocoumarin moiety. The ethyl benzo[f]coumarin carboxylate were subjected to react with other reagents to
synthesize thiazolidinyl and oxadiazolyl derivatives attached to benzocoumarin system. Some of novel syn
thesized compounds showed highly antibacterial and antifungal activities.

The effect of temperature on the sequence of the hardening precipitates in Al-1·1 wt-%Mg2Si balanced alloy has been investigated by means of differential scanning calorimetry, scanning electron microscopy and hardness measurements. The non-isothermal DSC thermograms exhibited seven reaction peaks. Out of these seven peaks, five are exothermic (representing precipitation) and two are endothermic (representing dissolution). The activation energy associated with the individual precipitates is calculated. The activation energy of nucleation of GP zones (54·3 kJ mol-1) is close to the migration energy of Si in Al (52·7 kJ mol-1). The activation energy associated with the precipitation of p" is determined as 77·6 kJ mol-1 and that for the formation of β' precipitates is 145·3 kJ mol-1. The latter value is close to that for Si diffusion in Al (124 kJ mol-1) and that of Mg diffusion in Al (131 kJ mol-1). It can be concluded that the precipitation of β' particles might be characterised by both the diffusion of Mg and Si atoms in Al to form β' precipitates

The effect of temperature on the sequence of the hardening precipitates in Al-1·1 wt-%Mg2Si balanced alloy has been investigated by means of differential scanning calorimetry, scanning electron microscopy and hardness measurements. The non-isothermal DSC thermograms exhibited seven reaction peaks. Out of these seven peaks, five are exothermic (representing precipitation) and two are endothermic (representing dissolution). The activation energy associated with the individual precipitates is calculated. The activation energy of nucleation of GP zones (54·3 kJ mol-1) is close to the migration energy of Si in Al (52·7 kJ mol-1). The activation energy associated with the precipitation of p" is determined as 77·6 kJ mol-1 and that for the formation of β' precipitates is 145·3 kJ mol-1. The latter value is close to that for Si diffusion in Al (124 kJ mol-1) and that of Mg diffusion in Al (131 kJ mol-1). It can be concluded that the precipitation of β' particles might be characterised by both the diffusion of Mg and Si atoms in Al to form β' precipitates

The effect of temperature on the sequence of the hardening precipitates in Al-1·1 wt-%Mg2Si balanced alloy has been investigated by means of differential scanning calorimetry, scanning electron microscopy and hardness measurements. The non-isothermal DSC thermograms exhibited seven reaction peaks. Out of these seven peaks, five are exothermic (representing precipitation) and two are endothermic (representing dissolution). The activation energy associated with the individual precipitates is calculated. The activation energy of nucleation of GP zones (54·3 kJ mol-1) is close to the migration energy of Si in Al (52·7 kJ mol-1). The activation energy associated with the precipitation of p" is determined as 77·6 kJ mol-1 and that for the formation of β' precipitates is 145·3 kJ mol-1. The latter value is close to that for Si diffusion in Al (124 kJ mol-1) and that of Mg diffusion in Al (131 kJ mol-1). It can be concluded that the precipitation of β' particles might be characterised by both the diffusion of Mg and Si atoms in Al to form β' precipitates

The effect of temperature on the sequence of the hardening precipitates in Al-1·1 wt-%Mg2Si balanced alloy has been investigated by means of differential scanning calorimetry, scanning electron microscopy and hardness measurements. The non-isothermal DSC thermograms exhibited seven reaction peaks. Out of these seven peaks, five are exothermic (representing precipitation) and two are endothermic (representing dissolution). The activation energy associated with the individual precipitates is calculated. The activation energy of nucleation of GP zones (54·3 kJ mol-1) is close to the migration energy of Si in Al (52·7 kJ mol-1). The activation energy associated with the precipitation of p" is determined as 77·6 kJ mol-1 and that for the formation of β' precipitates is 145·3 kJ mol-1. The latter value is close to that for Si diffusion in Al (124 kJ mol-1) and that of Mg diffusion in Al (131 kJ mol-1). It can be concluded that the precipitation of β' particles might be characterised by both the diffusion of Mg and Si atoms in Al to form β' precipitates

The present work reports, for the first time, a direct experimental observation of the critical phenomenon associated with the B2–A2 order–disorder transition of Al–Fe binary alloys. Transmission electron microscopy and energy dispersion spectroscopy are employed to span the morphological changes through the transition line from the ordered B2 phase to the disordered A2 phase. Dark field images of the microstructure around the transition line for samples aged at 973 and 1073 K for various times show an interface roughening for the 100 antiphase domain boundaries in body-centered cubic binary alloys having the B2 structure. This observation confirms theory about the instability of the second-order transition in such alloys. This behaviour occurs for compositions with Al-content slightly higher (by 4 at.% Al) than that of the critical point of the equilibrium order–disorder transition. In addition, roughness-induced wetting transition is also observed for alloys having compositions ranging from 1.3 to 1.5 at.% Al above the transition line. The interface roughening transition is thought to be unstable second-order while the wetting transition is suggested to be a stable first-order one

The present work reports, for the first time, a direct experimental observation of the critical phenomenon associated with the B2–A2 order–disorder transition of Al–Fe binary alloys. Transmission electron microscopy and energy dispersion spectroscopy are employed to span the morphological changes through the transition line from the ordered B2 phase to the disordered A2 phase. Dark field images of the microstructure around the transition line for samples aged at 973 and 1073 K for various times show an interface roughening for the 100 antiphase domain boundaries in body-centered cubic binary alloys having the B2 structure. This observation confirms theory about the instability of the second-order transition in such alloys. This behaviour occurs for compositions with Al-content slightly higher (by 4 at.% Al) than that of the critical point of the equilibrium order–disorder transition. In addition, roughness-induced wetting transition is also observed for alloys having compositions ranging from 1.3 to 1.5 at.% Al above the transition line. The interface roughening transition is thought to be unstable second-order while the wetting transition is suggested to be a stable first-order one

The present work reports, for the first time, a direct experimental observation of the critical phenomenon associated with the B2–A2 order–disorder transition of Al–Fe binary alloys. Transmission electron microscopy and energy dispersion spectroscopy are employed to span the morphological changes through the transition line from the ordered B2 phase to the disordered A2 phase. Dark field images of the microstructure around the transition line for samples aged at 973 and 1073 K for various times show an interface roughening for the 100 antiphase domain boundaries in body-centered cubic binary alloys having the B2 structure. This observation confirms theory about the instability of the second-order transition in such alloys. This behaviour occurs for compositions with Al-content slightly higher (by 4 at.% Al) than that of the critical point of the equilibrium order–disorder transition. In addition, roughness-induced wetting transition is also observed for alloys having compositions ranging from 1.3 to 1.5 at.% Al above the transition line. The interface roughening transition is thought to be unstable second-order while the wetting transition is suggested to be a stable first-order one