Tellurite And Fluorotellurite Glasses For Active And Passive
Tellurite And Fluorotellurite Glasses For Active And Passive Tellurite And Fluorotellurite Glasses For Active And Passive
Refractive index, n , at 632.8 nm 6. Optical properties; MDO 223 1.97 1.96 1.95 1.94 1.93 1.92 1.91 1.90 1.89 1.88 y = 0.06371x + 1.89170 R 2 = 0.90430 0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.8 0.9 1.0 Fraction oxide Fig. (6.49): Variation of refractive index at 633 nm with increasing oxide to fluoride ratio of glasses in the series 65TeO2-(25-x)ZnF2-xZnO-10Na2O mol. %, for 5 ≤ x ≤ 25 mol. % (MOF009 to 013). Glass MOF001 (65TeO2-25ZnF2-10Na2O mol. %) used for oxide / fluoride = 0. It can be seen that refractive index increased with increasing ZnO content, however variation was greater than the series shown in fig. (6.48). 6.3. Discussion The results presented in the previous section (6.2) are discussed here in the same order, starting with the infrared absorption spectra of oxide tellurite and fluorotellurite glasses. These are followed by the emission spectra of heat treated Er +3 -doped fluorotellurite glasses. Refractive indices of oxide tellurite and fluorotellurite glasses are then discussed. To conclude, a core / clad pair is selected for fibre drawing, based on properties discussed in this chapter, and chapter 4.
6. Optical properties; MDO 224 6.3.1. Infrared spectroscopy 6.31.1. Infrared spectroscopy of oxide tellurite glasses Infrared spectroscopy of glasses of the series (80-x)TeO2-10Na2O-10ZnO-xMO, where MO is PbO or GeO2 Fig. (6.6) shows infrared spectra of glasses in the series (80-x)TeO2-10Na2O-10ZnO- xMO, where MO is PbO or GeO2, for MOD006 (x = 3 mol. % PbO), MOD010 (x = 5 mol. % PbO) and MOD012 (x = 5 mol. % GeO2). Fig. (6.7) shows the multiphonon edge of these glasses. The 3 and 5 mol. % PbO glasses had approximately the same multiphonon edge (the edge of the 3 mol. % glass was at a slightly higher wavenumber). The edge for the GeO2 containing glass was found to be at a higher wavenumber than the PbO glasses. This is probably due to a combination of: (i) Ge is of a lower atomic mass than Pb, and (ii) the Pb-O bond (382.0 kJ.mol -1 ) is weaker than the Ge-O bond (659.4 kJ.mol -1 ) [6]. Applying the Szigeti equation (2.8), the multiphonon edge will tend to be shifted to a higher wavenumber if GeO2 is substituted for PbO, as µ (reduced mass) will decrease, and k (related to bond strength) will increase. The edge will also tend to shift to higher wavenumbers from 5 to 3 mol. % PbO, as PbO was substituted for TeO2, and is much heavier (Z = 82 and 52, respectively). Using the Szigeti equation (2.8), µ will decrease with decreasing PbO content, which will tend to shift the multiphonon edge to higher frequencies.
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Refractive index, n , at 632.8 nm<br />
6. Optical properties; MDO 223<br />
1.97<br />
1.96<br />
1.95<br />
1.94<br />
1.93<br />
1.92<br />
1.91<br />
1.90<br />
1.89<br />
1.88<br />
y = 0.06371x + 1.89170<br />
R 2 = 0.90430<br />
0.0 0.1 0.2 0.3 0.4 0.5 0.6 0.7 0.8 0.9 1.0<br />
Fraction oxide<br />
Fig. (6.49): Variation of refractive index at 633 nm with increasing oxide to fluoride ratio<br />
of glasses in the series 65TeO2-(25-x)ZnF2-xZnO-10Na2O mol. %, for 5 ≤ x ≤ 25 mol. %<br />
(MOF009 to 013). Glass MOF001 (65TeO2-25ZnF2-10Na2O mol. %) used for oxide /<br />
fluoride = 0.<br />
It can be seen that refractive index increased with increasing ZnO content, however<br />
variation was greater than the series shown in fig. (6.48).<br />
6.3. Discussion<br />
The results presented in the previous section (6.2) are discussed here in the same order,<br />
starting with the infrared absorption spectra of oxide tellurite and fluorotellurite glasses.<br />
These are followed by the emission spectra of heat treated Er +3 -doped fluorotellurite<br />
glasses. Refractive indices of oxide tellurite and fluorotellurite glasses are then discussed.<br />
To conclude, a core / clad pair is selected for fibre drawing, based on properties discussed<br />
in this chapter, and chapter 4.