Effect of Impurities on the Secondary Recrystallization in Silicon Iron Takashi MATSUOKA Synopsis: An investigation has been made on the effects:of im
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1 Effect of Impurities on the Secondary Recrystallization in Silicon Iron Takashi MATSUOKA Synopsis: An investigation has been made on the effects:of impurities on the development of (110) [001] secondary recrystallization texture in silicon iron. While dispersed inclusions, TiC, VN, NbC, and A1N, were observed to have the ability to promote secondary recrystallization, BN and ZrC, have not. Necessary amounts of impurity elements were found to be 0.04% Ti, 0.07% V, and 0.02% Nb, respectively. The solubility products or [%M] [%N] (M: impurity element) of effective inclusions were estimated to be from 10-5 at the secondary recrystallization temperature. Inclusions of the order of 0.1 micron in size were observed to be dispersed more densely than 1012 particles/cm3 in final gauge strips in which secondary recrystallization occurred appreciably. (Received 29, 1966 Nov.) normal grain growth
2 Table 1. Chemical composition of heats (wt%). Fig. 1. Manufacturing process.
3 Fig.2. Maximum torque of a (110) [001] single crystal of silicon iron. (after SAGEL16)) Table 2. Per cent (110) [001] texture developed in the final gauge strips by annealing for 6hr. Ti-containg heat.
4 Table 3. Per cent (110) [001] texture developed in the final gauge strips by annealing for 6ht. V-containing heat. Table 4. Per cent (110) [001] texture developed in the final gauge strips by annealing for 6hr. Nb-containing heat.
5 Table 5. Percent (110) [001] texture developed in the final gauge strips by annealing for 6hr. Al-containing heat. Table 6. Per cent (110) [001] texture developed in the final gauge by annealing for 6hr at 1000 Ž in hydrogen atmosphere. Zr- and B- containing heats.
6 Photo. 1. Macrostructures of final gauge strips of heat T4 annealed for 6hr at 1000 Ž. Temperature and duration of heat-treatment of hot-rolled bands are indicated.
7 Photo. 2. Microstructures of hot-rolled bands of heat T15, (a) as-rolled, (b)heat-treated for 50 min at 650 Ž and cooled in air, (c)ditto 800 Ž, (d)ditto 950 Ž, (e)ditto 1000 Ž, and (f) ditto 1100 Ž. Photo. 3. Electron micrographs and diffraction patterns showing TiC. Hot-rolled band of heat T 15.
8 Table 7. Interplanar spacings of TiC in hotrolled band. Photo. 8. Interplanar spacings of VN and VC in hot-rolled band. Photo.. 4. Electron micrographs and diffraction patterns showing VN. Hot-rolled band of heat V 8. Table 9. Interplanar spacings of NbC in hot-rolled band. Photo. 5. Electron micrographs and diffraction patterns showing NbC. Hot-rolled band of heat NC 3a. Table 10. Interplanar spacings of AIN in final gauge strip.
9 Table 11. Interplanar spacings of ZrC in final gauge strip. Table 12. Interplanar spacings of BN in final gauge strip. Table 13. Dispersion density of inclusions in final gauge strips. The strips were processed from the hot-rolled bands which were annealed for 50 min at the indicated temperatures. (unit, 1012 particles/cm3)
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13 Photo. 12. Variation in disperion of NbC in final gauge strips of heat NC 3a. The treatments given to the hot-rolled bands were as follows : (a) none (as-rolled), (b) heat-treated for 50 min at 650 Ž, (c) ditto 800 Ž, (d) ditto 950 Ž, (e) ditto 1000 Ž, and (f) ditto 1100 Ž. Fig. 3. Relationship between per cent (110) [001] texture and content of acid-soluble AI in final gauge strips.
14 Table 14. Estimated content of inclusions necessary for the development of (110) [001]secondary recrystallization texture. Fig. 4. Solubility products estimated for various inclusions in iron. Solid lines (subscripted with a or 6) are extrapolation of data for either ƒ - or 6- phase, while broken lines are based on ƒá- phase data. Data for TiCa, TiCO, VNa, 6, AINa, ANO, ZrCƒÂ, ZrNƒ, ƒâ, and TiNƒ, ƒâ are due to SAWAMURA and MORI18)19), for VNƒ to FOUNTAIN and CHIpman20)21); NbCƒÁ et al24); AINƒÁ to DARKEN et al25), and MnS to AINSLIE and SEYBOLL27). and NbNƒÁ to SIMTH22)23); NbCƒÁ to MORI
15 Table 15. Solubility of nitrogen in silicon iron in equilibrium with Si3N4. (after FRYXELL et a129))
16 1) John E. MAY and David TURNBULL: Trans. Met. Soc., Amer. Inst. Min., Met. & Pet.Eng., 212 (1958), p. 769 `781 2) John E. MAY and David TURNBULL: J. Appl. Phys., 30 (1959), 210S `212S 3) H. C. FIEDLER: Trans. Met. Soc., Amer. Inst. Min., Met. & Pet. Eng., 221 (1961), p ) H. C. FIEDLER : ibid, 227 (1963), p. 776 ` ) H. C. FIEDLER and R. H. PRY: U. S. Patent 2,939,810 15) E. V. WALKER and J. HOWARD: J. Iron and Steel Inst. (U K.), 194 (1960), p. 96-,400 16) Konrad SAGEL: Arch, Eisenhutenw., 32 (1961), p. 153-, ) H. J. GOLDSCHMIDT: J. Iron and Steel Inst.
17 (U.K.), 160 (1948), p. 345 `362 27) Norman G. AINSLIE and Alan U. SEYBOLT : J. Iron and Steel Inst. (U.K.), 194 (1960), p. 20) R. W. FOUNTAIN and John CHIPMAN : Trans. 341 `350 Met. Soc., Amer. Inst. Min., Met. & Pet. Eng., 28) J. D. FAST: Philips Res. Rep., 11 (1956), 212 (1958), p. 737 `748 p. 490 `491 21) R. W. FOUNTAIN and John CHIPMAN: ibid ) R. E. FRYXELL, N. GALITZINE and F. S. GARD- (1962), p. 59 `606 NER : J. Iron and Steel Inst. (U.K.), ) Rodney P. SMITH: ibid, 224 (1962), p. 190 `191 (1958), p ) Rodney P. SMITH: ibid, 236 (1966), p. 220 `221 30) M. MARKUSZEWICZ, J. GROYECKI, J. LASSOTA and ZAWADA: Trans. Met. Soc., Amer. Inst. p `2033 Min., Met. & Pet. Eng., 236 (1966), p. 196 ` 25) L. S. DARKEN, R. P. SMITH and E. W. FILER: 200 Trans. Met. Soc., Amer. Inst. Min., Met. & 31) K. DETERT : Metall, 12 (1958), p. 817 `821 Pet. Eng., 191 (1951), P. 1174
9) H. SCHMCLZRIED: Z. Elektrochem. 66 (l%1) p ) W. D. KINGERY et al.: J. Am. Chem. Soc., 42 (1959), p ) F. HUND: Z. Phys. Chem., 199 (195
9) H. SCHMCLZRIED: Z. Elektrochem. 66 (l%1) p. 572 10) W. D. KINGERY et al.: J. Am. Chem. Soc., 42 (1959), p.394 11) F. HUND: Z. Phys. Chem., 199 (1952), p. 142 12) J. F. ELLIOTT and M. GLEISER: " Thermochemistry
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