MICROSTRUCTURE AND CRYSTALLOGRAPHIC TEXTURE OF STRIP-CAST 4.3wt%Si STEEL SHEET

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1 Pergamon Scripta Materialia, Vol. 40, No. 8, pp , 1999 Elsevier Science Ltd Copyright 1999 Acta Metallurgica Inc. Printed in the USA. All rights reserved /99/$ see front matter PII S (99) MICROSTRUCTURE AND CRYSTALLOGRAPHIC TEXTURE OF STRIP-CAST 4.3wt%Si STEEL SHEET Jae Young Park, Kyu Hwan Oh and Hyung Yong Ra Division of Materials Science and Engineering, Seoul National University, Shinrim-dong 56-1, Kwanak-ku, Seoul , Korea (Received October 19, 1998) (Accepted in revised form February 1, 1999) Introduction Since grain oriented silicon steel sheet was invented in 1935 by Goss [1], the material has been of considerable fundamental and technological interest to improve the sharpness of Goss orientation {110} 100 [2] etc. The studies have been focused on the improvement of magnetic properties. Although the manufacturing process has been well estabilished, the process is still complicated [3]. Recently, the progress in strip-casting technology [4] provides a possibility to manufacture silicon steel sheet by a simpler processing than the conventional process, because the strip casting process can supply a silicon steel strip with the same thickness and width as that of hot rolled strip. This offers a possibility to eliminate the continuous casting and hot-rolling processes. Raabe examined the texture of ferritic stainless steel strip by an unequal diameter twin roll process, where the textures of the strip cast steel were nearly random and homogeneous through the strip thickness [5,6]. Choi reported that the texture changes were observed both in roll-width and through the thickness of the vertical type twin roll strip cast AISI430 stainless steel [7]. In the present study, a Fe-4.3wt%Si strip was produced by the vertical type twin roll strip casting process and the microstructure and texture through the thickness direction were studied by optical metallography and quantitative X-ray texture analysis. The inhomogeneity of the texture and microstructure through the thickness direction were investigated. Experimental Procedure Table 1 shows the chemical composition of the silicon steel used in this study. Strip casting of Fe-4.3wt%Si silicon steel were carried out by the twin-roll strip caster with internally water-cooled steel rolls of 200mm diameter and 100mm width. Fig. 1 shows a schematic diagram of twin roll strip casting process. Hole-type nozzle was positioned at the center of a preheated tundish. The thickness and width of the strip were 1.5mm and 100mm, respectively. Specimens for metallographic examination were etched with 3% Nital and 1% Nital. The texture variation along the thickness direction was inspected. The position through the thickness direction can be used by a parameter s, defined as s 2a/d, where a and d are the distance from the center layer of strip and the thickness of the strip, respectively. The parameter s is called the normalized thickness. The crystallographic texture was quantitatively examined by measuring the three incomplete pole figures {110}, {200}, {211} in the range of the polar angle 881

2 882 TEXTURE Vol. 40, No. 8 TABLE 1 Chemical Composition of Steel Strip (wt.%) C Si Mn P S Cu N Fe bal. from 0 to 70 with Co K 1 radiation in a Seifert D3000 PTS gniometer. Samples for pole figure measurement were etched at room temperature in a solution of 90ml H 2 O 2 and 10ml HF. From the measured pole figures, the orientation distribution function (ODF) was computed by the WIMV method [8]. Microstructure Results and Discussion Fig. 2 shows the micrograph of the strip cast 4.3wt%Si silicon steel at longitudinal section. The strip cast silicon steel sheet shows an inhomogeneous microstructure through the thickness of the strip, which can be divided into three parts. Near surface regions (s ), the grains of about 200 m size are observed, which were presumably formed due to the rapid cooling [4]. In the region of s , the dendrites grew from the surface to the center of the strip. In the center layer (s ), the equiaxed grains of about 10 m size were observed. The microstructures of three parts are similar to those of the well known chill, dendritic and equiaxed zone in the metal mold casting. Fig. 3 shows the optical micrograph of near surface zone (s ) and Fig. 4 shows the subgrains inside a grain in the subsurface layer. In the subsurface layer (s ), inclined lines are shown inside grains and, in the surface layer (s ), the inclined lines are not shown inside grains. The formation of inclined lines in the subsurface layer will be discussed in the next section. Texture Fig. 5 shows the ODF from the measured pole figures at various thickness of the strip cast 4.3wt%Si steel strip. In the surface layer of s 1.0, {100} 0vw fiber components are evolved as shown in Fig. 5 (a). In the subsurface layer of s 0.8, 0.6, the Goss {110} 001 component shows the maximum ODF value as shown in Fig. 5(b), (c). In the layer of s 0.4, the intensity of {110} 001 component becomes weaker. In the center region of s 0.2, 0.0, the {100} 0vw fiber components, and fiber are evolved as shown in Fig. 5(e), (f). The {100} 0vw fiber components are the typical Figure 1. Schematic diagram for twin roll strip casting process.

3 Vol. 40, No. 8 TEXTURE 883 Figure 2. Microstructure of as-cast strip, longitudinal section (3% Nital etching). solidification texture [7]. The {110} 001 component is the typical shear texture of BCC metals. and - fiber are the typical rolling texture according to plane strain deformation [11]. In a twin roll casting of Bessemer-Type, the two-dimensional temperature field in the liquid and solid regions was calculated using a finite differential method by Schimitz et al. [12] and McLaren calculated the distributions of temperature, equivalent strain, and Zener-Hollomon parameter through the thickness of the slab during hot rolling by an Eulerian finite element model [13]. Fig. 6 shows the typical calculated profiles of temperature, as predicted by Schmitz and McLaren, through thickness direction during strip casting [12] and hot rolling process [13]. During the strip casting, the rapidly cooled surface Figure 3. Microstructure of as-cast strip near-surface layer (1% Nital etching).

4 884 TEXTURE Vol. 40, No. 8 Figure 4. Subgrains inside a grain in the subsurface layer. layer of the strip (s ) had the larger yield strength than the inner layer (s 0.9) with the higher temperature. The surface layer maintained the solidification texture without deformation and the subsurface layer was deformed by shear. The shear deformation in strip casting process is similar to that in hot rolling. In case of hot rolled steel sheets, the maximum of these shear components is frequently located at s , and the center layer is deformed by the plane strain condition [5]. During hot rolling, the inhomogenity of texture is due to the inhomogenity of deformation i.e.; shear deformation in the subsurface layer and the plane strain compression in the center layer [14,15]. This inhomogenity of deformation results from the inhomogenity of strength due to the inhomogenity of temperature. During strip casting, the temperature profile is very similar to that of hot rolling and the temperature gradient near surface zone (s ) gives rise to the strength gradient and finally the large shear Figure 5. 1 sections of ODF in various thickness layers of a strip cast 4.3wt%Si steel strip.

5 Vol. 40, No. 8 TEXTURE 885 Figure 6. Typical calculated profiles of temperature through thickness in the strip casting [12] and hot rolling process [13]. deformation as shown in Fig. 3 and 4. The inclined lines in Fig. 3 were appeared by the shear deformation of the subgrains inside grains in the subsurface layer (Fig. 4). The related shear texture component is shown in Fig. 5(b) and (c). In the center layer of strip, the major rolling fiber are due to the plane strain compression from the solidification end point to the roll nip point, which is similar to the evolution of rolling fiber during hot rolling. The minor {100} 0vw components are the typical solidification texture. Thus, in the vertical type twin roll strip casting process, the texture of cast steel sheet composed of the solidification texture {100} fiber texture at surface, the shear {110} 001 in the subsurface and the combination of major plane strain compression texture and minor solidification texture in the center layer. Conclusion The texture and microstructure distribution through the thickness of strip cast 4.3wt%Si steel have been examined. The inhomogenity of texture and microstructure through the sample thickness resulted from the temperature profile through the thickness during strip casting. Especially between subsurface layer (s 0.8) and the midplane (s 0.6), Goss texture, {110} 001 component, was developed by the shear deformation, and major rolling texture and minor solidification texture appeared in the center layer. References 1. N. P. Goss, Trans. Am. Soc. Metals. 23, 511 (1935). 2. R. M. Bozorth, Trans. Am. Soc. Metals. 23, 1107 (1935). 3. S. Taguchi, A. Sakakura, and H. Takashima, U.S. Patent 3,287,183 (1966). 4. H. Litterscheidt, R. Hammer, C. Schneider, R. W. Simon, D. Senk, R. Kopp, and B. Hehl, Stahl Eisen. 111, 61 (1991). 5. D. Raabe, Mater. Sci. Technol. 11, 461 (1995). 6. D. Raabe, F. Reher, M. Hölscher, and K. Lücke, Scripta Metall. 29, 113 (1993). 7. J. T. Choi, Y. H. Kim, C. H. Choi, K. H. Oh, and H. Y. Ra, In Melt Spinning, Strip Casting and Slab Casting, ed. E. F. Matthys and W. G.Truckner, p. 43, The Mineral, Metals and Materials Society, Anaheim, CA (1996). 8. S. Matthies and G. W. Vinel, Phys. Stat. Sol. 112, 111 (1982). 9. J. Grewen, J. Huber, and M. Hatherly, Metal. Forum. 12, 115 (1978). 10. K. Kawasaki and M. Matsuo, Tetsu-to-Hagané. 70, 18 (1984). 11. D. Raabe and K. Lücke, Scripta Metall. 26, 1221 (1992). 12. J. W. Schmitz and A. R. Büchner, Stahl Eisen. 111(2), 69 (1991). 13. A. J. McLaren and C. M. Sellars, Mater. Sci. Technol. 8, 1090 (1992). 14. Y. Shimizu, Y. Ito, and Y. Iida, Metall. Trans. 17A, 1323 (1986). 15. D. Raabe and K. Lücke, Mater. Sci. Technol. 9, 302 (1993).

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