Tellurite And Fluorotellurite Glasses For Active And Passive
Tellurite And Fluorotellurite Glasses For Active And Passive Tellurite And Fluorotellurite Glasses For Active And Passive
8. Fibre drawing; MDO 359 β-relaxation which occurs mainly below Tg, possibly due to non-cooperative atom movements. The Vicker’s hardness of fragile glasses such as TeO2- and Bi2O3-based systems, was shown to decrease rapidly at around T/Tg = 0.9 to 1.0 (i.e. just below Tg). For stronger glass formers based on P2O5 and SiO2, this behaviour was observed at T/Tg = 1.0 to 1.1 (i.e. just above Tg). This is thought to be due to β-relaxation processes playing a grater role in the rheological properties of fragile glasses, whereas α-relaxation is more prominent in the stronger glasses [24]. The slope at any point of fig. (8.16) is equal to the activation energy for viscous flow [25]. Fig. (8.17) shows the differential curve of the fragility plot of glass MOF001 (25 mol. % ZnF2). d[log 10 (ηη)] / d(T g /T) / Pa.s 22 20 18 16 14 12 10 8 6 4 0.0 0.2 0.4 0.6 0.8 1.0 T g /T Fig. (8.17): Differential of fragility plot for glass MOF001 (25 mol. % ZnF2).
8. Fibre drawing; MDO 360 It can be seen the activation energy for viscous flow generally increases as Tg is approached, as expected. Braglia et al. [6] showed TeO2-Na2O-ZnO glasses behave in a Newtownian manner (i.e. viscosity-temperature behaviour independent of the applied force). This is advantageous for fibre drawing, as the viscosity will only depend on temperature, rather than also draw speed, as seen with fluorozirconates and chalcogenides. 8.3.3. ESEM of crystallised fibres Fig. (8.7) shows an electron micrograph of triangular shaped crystals near the surface (10 to 20 µm) of the glass fibre of composition MOF005ii (70TeO2-10Na2O-20ZnF2 mol. %), mounted length-ways in epoxy resin, and cross-sectioned. These crystals have grown close to the fibre surface, and are around 2 µm in diameter. This surface crystallisation, could be due to degradation of the fibre surface during heating in the fibre drawing tower. The nitrogen atmosphere in the fibre drawing furnace was not passed through a liquid nitrogen dewar for preform MOF005ii. Therefore, there could have been sufficient water vapour present in the atmosphere to attack and degrade the surface of the fibre, and provide sites for crystal nucleation. OH groups lower the local viscosity of the glass [26], increasing the likelihood of atomic rearrangement, and crystallisation. Physical volatilisation from the fibre surface, could have changed the surface composition, destabilising the glass and causing local crystallisation. Organic contaminants (from the internal surface of the brass mould or preform handling) also could have been present on
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8. Fibre drawing; MDO 359<br />
β-relaxation which occurs mainly below Tg, possibly due to non-cooperative atom<br />
movements. The Vicker’s hardness of fragile glasses such as TeO2- and Bi2O3-based<br />
systems, was shown to decrease rapidly at around T/Tg = 0.9 to 1.0 (i.e. just below Tg).<br />
<strong>For</strong> stronger glass formers based on P2O5 and SiO2, this behaviour was observed at T/Tg =<br />
1.0 to 1.1 (i.e. just above Tg). This is thought to be due to β-relaxation processes playing a<br />
grater role in the rheological properties of fragile glasses, whereas α-relaxation is more<br />
prominent in the stronger glasses [24].<br />
The slope at any point of fig. (8.16) is equal to the activation energy for viscous flow<br />
[25]. Fig. (8.17) shows the differential curve of the fragility plot of glass MOF001 (25<br />
mol. % ZnF2).<br />
d[log 10 (ηη)] / d(T g /T) / Pa.s<br />
22<br />
20<br />
18<br />
16<br />
14<br />
12<br />
10<br />
8<br />
6<br />
4<br />
0.0 0.2 0.4 0.6 0.8 1.0<br />
T g /T<br />
Fig. (8.17): Differential of fragility plot for glass MOF001 (25 mol. % ZnF2).