Tellurite And Fluorotellurite Glasses For Active And Passive
Tellurite And Fluorotellurite Glasses For Active And Passive Tellurite And Fluorotellurite Glasses For Active And Passive
6. Optical properties; MDO 229 a change in the multiphonon edge. Tellurium also has a higher charge than zinc, therefore also has a higher lattice energy. Using equation (2.8), addition of zinc will result in a decrease in µ (reduced mass), causing the edge to shift to higher frequencies. Fig. (6.13) shows the multiphonon edges of glass of composition 80TeO2-10Na2O- 20ZnO mol. % (MOD013) with thickness viz. 2.98, 0.50 and 0.20 mm. The multiphonon edge was enhanced with decreasing thickness due to an increasing amount of signal reaching the detector. Ernsberger [14] has shown that by using very thin silicate glass samples it was possible to ‘extend the useful spectrum [of silicates] to ≈ 1,300cm -1 ’ i.e. enable us to see more clearly bands that were indistinguishable before. This is also true for tellurite glasses as fig. (6.14) and (6.15) show [5]. In the spectrum of thin (0.20 mm) glass, of composition 80TeO2.10ZnO.10Na2O (mol. %), the higher wavenumber shoulder of the 3060 cm -1 band can be more clearly discerned than in the spectra of the longer optical pathlength specimens (fig. (6.15)), and at least four bands thought to be related to structural units in the glass network (see below) can be seen within the multi-phonon absorption edge (fig. (6.14)). Fig. (6.16) to (6.17) show the Gaussian deconvolution of these OH bands in the longer optical pathlength samples. Scholze [17] identified a band around 3500 cm -1 for alkali metal silicate glasses and attributed this to the stretching mode of the free Si-OH groups. Ryskin [22, 23] also identified a band around 3500 cm -1 for hydrated crystalline silicates and attributed this to a stretching mode of the water molecule. It is therefore proposed that the band around 3300 cm -1 in fig. (6.17) (which is a shoulder of the 3060 cm -1 band) be attributed to free Te-OH groups or molecular water (or a combination of both) [5]. By exposing thin glass films to a high a vapour pressure of water (i.e. steam) Ernsberger [14] entrapped
6. Optical properties; MDO 230 molecular water in alkali-silicate glasses, evidenced by the characteristic absorption band at 1600 cm -1 (fundamental H-O-H bending mode) and a broader band around 3600 cm -1 which occurred for the water vapour treated glasses. Two equilibria must be taken into account when considering hydrolysis of a glass melt [20] (where R is the main glass forming cation e.g. Si 4+ or Te 4+ ): (i) Water vapour entering the melt as molecular water (i.e. [H2O]vapour ↔ [H2O]melt). (ii) Molecular water in the melt hydrolysing the molten network (i.e. [R-O-R]melt + [H2O]melt ↔ 2[R-OH]melt). Therefore the coexistence of these two equilibria in the melt seems to suggest the probable non-zero concentration of molecular water in any glass with a non-zero water content [20]. Scholze [17] identified a band around 2800 cm -1 for alkali metal silicate glasses and attributed this to the stretching mode of the Si-OH group that forms the weaker hydrogen bonding with the non-bridging oxygens (NBO’s) of the Q 2 or Q 3 tetrahedron (where Q n is a SiO4 tetrahedron with n bridging oxygen bonds to the surrounding network). Ryskin [22, 23] also identified a stretching mode of the hydrogen-bonded Si-OH groups around 2800 cm -1 in crystalline hydrated silicates. It is proposed in the current study that the band, which occurs around 3060 cm -1 for tellurite and fluorotellurite glasses (fig. (6.17)) be attributed to the stretching mode of the weakly hydrogen-bonded Te-OH groups [5].
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6. Optical properties; MDO 230<br />
molecular water in alkali-silicate glasses, evidenced by the characteristic absorption band<br />
at 1600 cm -1 (fundamental H-O-H bending mode) and a broader band around 3600 cm -1<br />
which occurred for the water vapour treated glasses. Two equilibria must be taken into<br />
account when considering hydrolysis of a glass melt [20] (where R is the main glass<br />
forming cation e.g. Si 4+ or Te 4+ ):<br />
(i) Water vapour entering the melt as molecular water (i.e. [H2O]vapour ↔<br />
[H2O]melt).<br />
(ii) Molecular water in the melt hydrolysing the molten network (i.e. [R-O-R]melt<br />
+ [H2O]melt ↔ 2[R-OH]melt).<br />
Therefore the coexistence of these two equilibria in the melt seems to suggest the<br />
probable non-zero concentration of molecular water in any glass with a non-zero water<br />
content [20].<br />
Scholze [17] identified a band around 2800 cm -1 for alkali metal silicate glasses and<br />
attributed this to the stretching mode of the Si-OH group that forms the weaker hydrogen<br />
bonding with the non-bridging oxygens (NBO’s) of the Q 2 or Q 3 tetrahedron (where Q n is<br />
a SiO4 tetrahedron with n bridging oxygen bonds to the surrounding network). Ryskin<br />
[22, 23] also identified a stretching mode of the hydrogen-bonded Si-OH groups around<br />
2800 cm -1 in crystalline hydrated silicates. It is proposed in the current study that the<br />
band, which occurs around 3060 cm -1 for tellurite and fluorotellurite glasses (fig. (6.17))<br />
be attributed to the stretching mode of the weakly hydrogen-bonded Te-OH groups [5].