Low Thermal Expansion Glass Ceramics by Wolfgang Pannhorst (auth.), Dr. Hans Bach (eds.)

By Wolfgang Pannhorst (auth.), Dr. Hans Bach (eds.)

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Therefore, there is no straightforward process for finding the correct glass composition and its ceramization conditions to meet specific requirements but there exist always several solutions simultaneously; it is up to the intuition of the developer which solution is finally proposed. The development of a glass ceramic composition always starts with a base glass composition taken from the area indicated in Fig. 20. The upper amounts of Si0 2 and Al 20 3 or the sum of both components are often determined by the refractoriness of these components.

S. is preferred here. The thermodynamic stability of the high-quartz-type and, particularly, the keatite-type alumino-silicates is much reduced if part of the Li ions is replaced by the divalent ions Mg or Zn. 14]. Cordierite, Mg 2A1 4Si 50 18, and the very stable spinel phases, MgAlz0 4 and ZnAI 20 4, are formed instead. Consequently, no fields of stability are found for high-quartz-type or keatite-type aluminosilicates in the systems MgAlz04-Si02 or ZnAlz0 4-Si0 2. S. phases occurs readily from strongly supercooled liquids in the whole compositional range (Li, Mg O.

11. Time-temperaturetransformation (TTT) diagram of nucleation showing several crystal density lines (p) Knowledge of the TTT diagram and, particularly, of the p = 1 density line is of great importance for the forming and hot working pro ces ses of glasses with a strong tendency towards nucleation. From this diagram, schedules can be derived which avoid nucleation. For the forming process of the parent glass the main interest is in the upper limit of nucleation. EspeciaHy during casting the temperature should not fall below this limit.

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