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��Materials Science and Engineering A273 275 (1999) 471 474 www.elsevier.com/locate/msea Study of the temperature dependence of the bainitic transformation rate in a multiphase TRIP-assisted steel a, b a a a E. Girault *, P. Jacques , P. Ratchev , J. Van Humbeeck , B. Verlinden , a E. Aernoudt a Department of Metallurgy and Materials Engineering, K.U. Leu en, de Croylaan 2, B-3001 Leu en, Belgium b D�partement des Sciences des Mat�riaux et des Proc�d�s, Uni ersit� Catholique de Lou ain, PCIM, Place Sainte Barbe 2, B-1348 Lou ain-la-Neu e, Belgium Abstract A prerequisite to the development of multiphase TRIP-assisted steels is a good understanding of the bainitic transformation that takes place during the related thermo-mechanical processing. In this framework, the present paper proposes to investigate the formation of bainite when originating from intercritical austenite in a Si bearing steel. The experimental results suggest the contribution of a martensitic type mechanism to the transformation process. Yet, the overall bainitic reaction rates are found to strongly depend on the holding temperature. This original kinetics is correlated with the typical microstructure the steel exhibits after the intercritical annealing stage. To this extent, the crucial role of the adjacent development of bainitic ferrite for the observed temperature dependence is discussed. � 1999 Elsevier Science S.A. All rights reserved. Keywords: Bainite; Multiphase steels; TRIP steels TRIP-assisted steels, for which intercritical annealing 1. Introduction leads to an original duplex ferrite/austenite microstruc- ture. The purpose of this work is to contribute to the The microstructure of multiphase TRIP-assisted understanding of the bainite formation originating steels typically consists of a fine dispersion of from intercritical austenite. The investigation was car- metastable retained austenite islands in a ferritic base ried out on a Si bearing steel, so that carbide precipita- matrix. This multiphase microstructure is usually gener- tion is substantially retarded and does not interfere ated by a standard two stage heat-treatment [1]. The with the progress of the bainitic transformation [2]. A material is first intercritically annealed in the ferrite/ strong temperature dependence of the bainitic reaction austenite coexistence domain during which the austenite rate is evidenced and interpreted by means of the is created. Next, isothermal holding in the bainite for- microstructural features of multiphase TRIP-assisted mation domain is performed in order to stabilize the steels. remaining austenite and to permit its presence at room temperature. Since the accomplishment of the last step is crucial for the retention of austenite and, thereby, the control of the mechanical properties, a good under- 2. Material and experimental procedures standing of the associated bainitic reaction seems neces- The investigation was carried out on an Fe 0.11C sary. However, it appears that emphasis has been 1.50Si 1.53Mn steel previously hot and cold-rolled drawn so far on the study of bainite formation when down to 0.8mm thickness following classical processing originating from a fully austenitic microstructure. This routes. The desired multiphase microstructure is ob- appreciably differs from the processing of multiphase tained as follows. The cold-rolled material is first inter- critically annealed in the ( + ) region at 750�C. It was * Corresponding author. Tel.: +32-16-32-1780; fax: +32-16-32- then rapidly cooled and held at an intermediate temper- 1990. E-mail address: etienne.girault@mtm.kuleuven.ac.be (E. Girault) ature where upper bainite formation can take place, 0921-5093/99/$ - see front matter � 1999 Elsevier Science S.A. All rights reserved. PII: S0921-5093(99)00330-5 472 E. Girault et al. / Materials Science and Engineering A273 275 (1999) 471 474 namely between 375 and 450�C. The heat-treatment was eventually interrupted by fast quenching down to room temperature. The thermal simulations were con- ducted under vacuum in a Theta dilatometer using 15�4�0.8 mm flat specimens cut out by spark-ero- sion. The length change of the samples was continu- ously monitored during the holding stage to study the rate of bainite formation. The microstructural evolution along the isothermal holding was studied on specimens whose treatment was interrupted by quenching. Partic- ular sample preparation [3] was carried out prior to scanning electron microscopy (SEM) observations. Transmission electron microscopy (TEM) examinations were also performed on specimens electropolished by using a solution composed of 80% methanol and 20% perchloric acid. The carbon content of the retained austenite was estimated from the lattice parameter a0 Fig. 2. Comparison of ultimate austenite carbon content (dots) determined by XRD with calculated T0 and Ae3 curves (solid lines). measured from the (220) X-ray diffraction peak, using the base relationship a0 (A)=3.578+0.033 (wt.%C) avoid any presence of martensite at room temperature. [4]. Since the steel studied contained Mn and Si, the This means that all the residual austenite is effectively latter formula was appropriately modified with the stabilised and thus the carbon content measured at respective factors [4,5] to take these elements into room temperature is also relevant to the state just account. before cooling. Fig. 2 shows the austenite carbon content reached at the termination of the bainitic transformation together 3. Results and discussion with the T0 and the Ae3 curves. T0 is the temperature at which austenite and ferrite of identical composition Fig. 1 shows the rate at which bainite forms at 375, have equal free Gibbs energy, whereas Ae3 refers to the 416 and 450�C, as determined by dilatometry. It ap- + / paraequilibrium temperature (i.e. with no sub- pears clearly that the overall reaction rate of the stitutional partitioning). The T0 and the Ae3 lines were bainitic transformation is strongly dependent on the calculated using the PARROT [6] module of the holding temperature. Moreover, for the three tempera- Thermo-Calc [7] data-bank system. In this module it is tures under consideration, bainite formation is found to possible to do a calculation corresponding to the condi- cease well before the whole consumption of austenite, tion that defines respectively the T0 and Ae3 tempera- exhibiting thereby a transformation stasis . At that tures. The experimental values of the carbon content of stage, it is found that the austenite carbon enrichment austenite prove to fall fairly well on the T0 locus. This accompanying the bainite formation is sufficient to suggests the contribution to the investigated bainite growth of a martensitic type mechanism where carbon diffusion is prohibited. Accordingly, the bainitic reac- tion is observed to proceed until the Gibbs energy of the parent phase (the residual austenite) and the product phase (the supersaturated ferrite) of the same composition are identical. The large gap between the measured values and the T0 curve on one hand and the Ae3 locus on the other hand seems to rule out the occurrence of bainite growth under carbon diffusion control. Note finally that the fact that the T0 tempera- ture is a decreasing function of the carbon concentra- tion is effectively consistent with the increase of the degree of transformation to bainite as temperature is reduced, visible on Fig. 1. The dilatometric experiments reveal that the overall rate of the bainitic reaction strongly depends on the holding temperature, a trend that has also been recently Fig. 1. Kinetics of the bainitic reaction between 375 and 450�C, as determined by dilatometry. observed by the present authors in other multiphase E. Girault et al. / Materials Science and Engineering A273 275 (1999) 471 474 473 TRIP-assisted steels [8]. It must be emphasised that the manifestation of this temperature dependence is new, given that bainite formation kinetics of austenitized Si bearing steels are usually reported to be hardly depen- dent on temperature, e.g. Ref. [9]. In order to better understand this new issue, comparative TEM observa- tions were carried out on specimens isothermally trans- formed until cessation of the bainitic reaction. In accordance with other studies [10,11], Fig. 3 shows that a bainite unit is composed of a set of parallel ferrite laths. However, for the multiphase TRIP-assisted steel studied, the prior austenite grains from which bainite originates are small (i.e. about 1 m in size) because they were formed in the intercritical domain. Due to these geometrical restrictions, one lath only suffices to cross a parent austenite grain. Therefore, a bainite unit appears to consist of an adjacent pile up of laths, whose typical arrangement can be seen in Fig. 3. Further microscopy examination showed that the nucleation process of the laths is heterogeneous and, when thermodynamically allowed, favoured at the / boundaries [12]. Since the experimental results pre- sented in Fig. 2 suggest that the growth of bainitic ferrite laths is diffusionless, an interpretation of the kinetics observed is rather to be found in the nucleation process of these laths. After a lath is martensitically formed, the carbon in supersaturation in the product ferrite tends to be rapidly released into the surrounding austenite [13], which leads to the carbon enrichment measured. The development of the following lath will Fig. 4. TEM micrographs of an intercritical austenite grain partly transformed to bainite at 375�C. (a) Bright field image, showing the depend to a large extent on the effectiveness of the parent austenite (in black) together with three adjacent bainitic ferrite carbon previously ejected to disperse and uniformly laths. (b) The corresponding dark field image revealing the presence spread in the austenite. The growth of a lath is indeed of residual austenite between the laths. The specimen was isother- energetically favoured in a low carbon concentration mally held for 30 min. environment, where the chemical driving force is higher. It has been shown in the present study that because of the small size of the parent austenite grains, the bainitic ferrite laths can only develop side by side. Yet, the adjacent carbon evacuation through the long edges of a lath is likely to provoke a rapid build-up of carbon concentration in austenite domains near the interface, especially at moderate temperatures. Evidence of this tendency is seen in Fig. 4 which shows the bright (a) and corresponding dark (b) field images of a repre- sentative austenite grain partially transformed to bainite at 375�C. It is clear that a large amount of residual austenite (i.e. the illuminated phase in the dark field conditions) is retained between the laths of bainitic ferrite. This austenite retention can only be interpreted by the initial presence of zones highly enriched in carbon, a source of stabilisation. For a transformation Fig. 3. TEM micrograph of an intercritical austenite grain partly temperature of 450�C interlath austenite is almost ab- transformed to bainite at 375�C ( r, retained austenite; b, bainitic sent. Substantial carbon heterogeneities are, therefore, ferrite). The bainite unit is clearly composed of an adjacent pile-up of observed to emerge in the residual austenite near the individual ferrite laths. The specimen was isothermally held for 30 min. long edge of the laths as the holding temperature 474 E. Girault et al. / Materials Science and Engineering A273 275 (1999) 471 474 decreases. The presence and persistence of the observed sary. This transformation process is indeed observed to domains of high carbon content are believed to sub- easily cause a build-up of carbon in the austenite near stantially increase the delay between the adjacent for- the interface, which significantly persists at low temper- mation of two successive laths. As a consequence, the ature and hinders the progress of the reaction. (3) overall rate of formation of a bainite unit is markedly Hence, the kinetics of bainite formation that is seen in reduced at low temperatures, leading to the kinetics of this study differs from that reported on fully austeni- Fig. 1. tized grades and seems to be typical of multiphase In view of the above results, it appears that the TRIP-assisted steels. observed bainitic transformation kinetics is typical of multiphase TRIP-assisted steels. Thus, due to the small Acknowledgements size of the intercritical austenite grains, the develop- ment of the bainite laths is constrained to proceed in an EG is indebted to Dr K.C. Hari Kumar for the adjacent way. The increasing difficulty of carbon to calculation of the T0 and Ae3 curves. The continuous transversally disperse as the temperature decreases ac- support of OCAS (Research Centre of the Sidmar counts for a corresponding slowing in the progress of Group) is greatly appreciated. The authors are grateful the reaction. This justification is not inconsistent with to the Laboratory for Iron and Steelmaking and Physi- the fact that the rate of the bainitic reaction after full cal Metallurgy of Ghent for providing the steel. This austenitisation is reported to hardly depend on the study was partly supported by the Belgian State, Prime holding temperature. Austenitization indeed gives rise Minister s Office, Federal Office for Scientific, Techni- to coarse austenite grains, in which the adjacent devel- cal and Cultural Affairs, under contract P4/33 of the opment of the laths is no longer required. Conse- Interuniversity Poles of Attraction Programme. JVH quently, carbon dispersion may take place in a larger acknowledges the FWO (Fonds voor Wetenschappelijk volume of diffusion around the laths, so that carbon Onderzoek). heterogeneities can be rapidly dissipated and do not significantly affect the transformation kinetics. References [1] O. Matsumura, Y. Sakuma, H. Takeshi, Trans. ISIJ 27 (1987) 4. Conclusions 570. [2] H.K.D.H. Bhadeshia, Bainite in Steels, The Institute of Materi- The present investigation carried out on an intercriti- als, London, 1992, p. 72. [3] E. Girault, P. Jacques, P. Harlet, et al., Mater. Charact. 40 cally annealed and isothermally held Fe 0.11C (1998) 111. 1.50Si 1.53Mn steel showed the following points. (1) [4] D.J. Dyson, B. Holmes, J. Iron Steel Inst. 208 (1970) 469. The bainitic transformation that takes place during [5] R.C. Ruhl, M. Cohen, Trans. TMS-AIME 245 (1969) 241. isothermal holding ceases well before the complete con- [6] B. Jansson, PhD Thesis, Division of Physical Metallurgy, Royal sumption of the residual austenite, exhibiting, thereby, Institute of Technology, Stockholm, Sweden, 1984. [7] B. Sundman, B. Jansson, J.-O. Andersson, Calphad 9 (1985) 153. an incomplete reaction phenomenon. The carbon con- [8] P. Jacques, E. Girault, T. Catlin, N. Geerlofs, Th. Kop, S. van centration of untransformed austenite measured at the der Zwaag, F. Delannay, Mater. Sci. Eng. A (accepted). cessation of bainite formation proves to correlate fairly [9] N.A. Chester, H.K.D.H. Bhadeshia, J. Phys. (Fr.) IV 7 (1997) well with the calculated T0 line. This suggests the C5 41. contribution of a diffusionless mechanism to the con- [10] H.K.D.H. Bhadeshia, J. Phys. (Fr.) IV 7 (1997) C5 367. [11] G. Papadimitriou, G. Fourlaris, J. Phys. (Fr.) IV 7 (1997) sidered bainitic transformation. (2) However, the over- C5 131. all rate at which bainite forms is found to depend on [12] E. Girault, PhD Thesis, Department of Metallurgy and Materi- the transformation temperature. This is due to the fact als Engineering, K.U. Leuven, Belgium, March 1999. that, inside the small intercritical austenite grains, adja- [13] H.K.D.H. Bhadeshia, Bainite in Steels, The Institute of Materi- cent development of the bainitic ferrite laths is neces- als, London, 1992, p. 156. .

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