Quenching in cold water

Glassy Sb Sci alloys (x < 0.05) were prepared by conventional melt quenching. Cleaned silica tubes containing a mixture of the appropriate amount of constituents Sb and Se were evacuated to lO Torr and sealed. The contents of the tubes were melted in a furnace and continuously agitated for 10 h to ensure good homogeneity. The melt was rapidly quenched in cold water from 800 K, and the cooling rate was estimated to be 200 K/s. 

The sodium aluminate and appropriate amounts of surfactants/templates were dissolved in water using C(/Cl4 ratios of 85%/15% and 75%/25%, respectively, and the mixture was aged over night (16-20 hours) according to ref [6]. Subsequently, the usual gel preparation described earlier [4] were followed with no further changes, then the gels were transferred to PTFE-lined autoclaves and heated at 150-175°C for 6 days, quenched in cold water, washed 3-4 times in liberal amounts of water, decanted, filtered and dried overnight in ambient air. 

The crucible with the glass is quenched in cold water, a rubber stopper is put on the crucible and the glass is loosened from the inner wall by softy knocking with a small hammer on the outer wall. In this way the glass can be taken out of the crucible quantitatively. 

One more ternary compound has been observed and studied by Mozharivskyj and Kuz ma (1996) from the arc melted, annealed at 1070 K for 400 h, and finally quenched in cold water alloys. It crystallizes with theMo5B2Si type structure, a = 0.7662, c = 1.3502 (X-ray powder diffraction). The starting metals were Y, not less than 99.8 wt.%, Ni and Sb 99.9 wt.%. 

From a room temperature X-ray powder diffraction analysis LaeCo Sb was found to crystallize with the ordered La6ConGa3, i.e., the Nd6Fei3Si type structure, a = 0.8097, c = 2.3289 (Weitzer et al., 1993). An alloy was synthesized from ingots and compacted powders of the constituting elements (99.9% pure) by arc-melting, followed by annealing at 1073 for 5 days and quenched in cold water. 

Weitzer et al., 1993). An alloy was synthesized from ingots and compacted powders of the constituent elements 99.9% pure by arc melting followed by annealing at 1073 for 3 days and quenched in cold water. 

This precipitate is not suitable for a pigment until it is filtered, dried, crushed, heated to a high temperature, and quenched in cold water. The second heating in a muffle furnace at 725°C produces crystals of the right optical size. 

Exploratory syntheses were accomplished in 15 ml Teflon-lined autoclaves which were statically heated at autogenous pressure in forced convection ovens. Larger autoclaves (300 ml, 600 ml, and above) have also been successfully employed. At specified times, the autoclaves were removed from the oven, quenched in cold water, and the pH of the contents measured. Product VPI-5 was recovered by slurrying the autoclave contents in water, decanting the supernatant liquid, filtering the white solid, and drying the crystals in ambient air. 

NR was added mixing continued for 4 min when DCP was added, and the system was mixed for additional 2 min. The blends were sheeted using a laboratory mill at 1.25-mm nip setting. The sheets were cut into small pieces and re-mixed at 150°C for 1 min and sheeted out again in the laboratory mill. The blended sheets were compression-molded into the dumbbell specimens (2 0.2 mm) in an electrically heated hydraulic press at 150°C for 3 min. The specimens under compression were quenched in cold water (which should keep the crystallinity at a low level). The irradiations were done at T = 25°C, in the y-chamber-900 at BARC, Mumbai. 

II. The preparation from stoichiometric quantities of commercial FegOa and reduced iron can also be recommended. The mixture and a few drops of water are sealed into a preevacuated quartz tube, heated for about three days at 900°C, and quenched in cold water. 

Fine Co powder is mixed with the stoichiometric quantity of fine S powder and heated at 650°C for 2-3 days in an evacuated, sealed quartz tube. The tube is then quenched in cold water. 

Blocks of rubber 150 mm in diameter and 25 mm thick were compression molded at temperatures from 120 to 180°C for different lengths of time, and quenched in cold water. To obtain the cure distribution through the thickness of the slab obtained under the conditions of temperature and time, a cylindrical plug 20 mm in diameter was taken from the center of each block when cold, and this plug was mounted on a lathe and cut into sections 1 mm thick. These sections were swollen in toluene in order to determine the degree of cure. 

Sobolev et al. (1971) determined the phase equilibria within an isothermal section of the system Y-Cr-Si at 800°C based on metallographic and X-ray powder analysis of 80 alloy specimens. Samples were prepared by arc melting and subsequent annealing for 500 h at 800°C, and finally quenched in cold water. Starting... 

The microfibril reinforced polymer-polymer composites are prepared as follows, as shown in Figure 12.1. First, the two thermoplastics with different melt temperatures are melt-mixed in a single-screw extruder with a slit die to ensure uniform deformation. The extrudate is then hot stretched by a take-up device with two pinching rolls to facilitate the microfibril formation. Different hot stretch ratios (HSR, i.e., the area of the transverse section of the die to that of the transverse of the extrudate) are obtained by adjusting the speed of the take-up device. Subsequently, the extrudate is immediately quenched in cold water (20 °C) after stretching to preserve the formed microfibrils, and finally a thin ribbon is obtained. 

Phase equilibria in the Nd-Ru-Ge system have been derived by Salamakha et al. (1996e) by means of powder X-ray analysis of samples prepared by direct arc melting of high-purity components (Nd 99.85 mass%, Ru 99.9mass%, Ge 99.99 mass%), annealed at 870 K for two weeks in evacuated quartz ampoules and quenched in cold water. The isothermal section is shown in fig. 66. The phase relations are characterized by the existence of seven ternary neodymium-ruthenium germanides. Mutual solid solubilities of the binary compoimds were observed to be negligible. 

Phase equilibria have been established in the ternary Nd-Ag-Ge system over the whole concentration region for the isothermal sections at 870 K and 1070 K by Salamakha et al. (1996f) and Zaplatynsky et al. (1996) (figs. 67a,b). The existence of four and five ternary compounds respectively have been observed. Samples were melted from pieces of high purity components (Nd 99.85 mass%, Ag 99.99 mass%, Ge 99.99 mass%) under argon atmosphere in an arc furnace with water-cooled copper hearth. The ingots were subsequently annealed at 870 K (1070 K) and quenched in cold water. The isothermal sections were constructed using X-ray powder diflraction film data obtained by the Debye-Scherrer technique with non-filtered CrK radiation. 

According to Belan (1988), the EuPdGe crystallizes with the EuNiGe type, a = 0.6132, i = 0.7934, c = 0.7441, y= 132.64° (X-ray powder diffraction data). The alloy was obtained by arc melting the proper amoimts of pure components (Eu 99,81 mass% Pd 99.99 mass%, Ge 99.99 mass%) followed by annealing in an evacuated quartz tube at 670 K for 300 hours and finally quenching in cold water. 

Figure 95 represents the isothermal section of the Ho-Ni-Ge phase diagram at 870 K, which was studied by Aslan (1990). The isothermal section was constructed by means of X-ray powder and partly microstructural analyses of 158 alloys which were arc melted, subsequently annealed in evacuated silica tubes for 720 h at 870 K, and finally quenched in cold water. The starting materials were Ho 99.9mass%, Ni 99.98 mass%, and Ge 99.99 mass%. 

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