Materials Transactions, Vol. 52, No. 2 (2011) pp. 139 to 141 #2011 The Japan Institute of Metals Effect of a High Magnetic Field on Carbon Diffusion in -Iron Shou-Jing Wang1;2 , Yan Wu1 , Xiang Zhao1; * and Liang Zuo1 1 Key Laboratory for Anisotropy and Texture of Materials (Ministry of Education), Northeastern University, Shenyang 110004, Liaoning Province, P. R. China 2 Mechanical Engineering Institute, Liaoning Shihua University, Fushun 113001, Liaoning Province, P. R. China The effect of 12-Tesla high magnetic field on carbon diffusion in -Fe at 1273 K has been investigated using a diffusion couple made by pure Fe and high purity Fe-0.76%C alloy. The results show that the high magnetic field obviously hinders carbon diffusion in the direction perpendicular to the magnetic field direction; while it only slightly enhances the carbon diffusion in the direction parallel/antiparallel to the magnetic field direction. [doi:10.2320/matertrans.M2010327] (Received September 17, 2010; Accepted November 11, 2010; Published January 25, 2011) Keywords: high magnetic field, carbon, diffusion, iron-carbon alloys 1. Introduction The diffusion is a very important process in diffusional transformations in steels, but so far, only a few papers have been published to show the effects of a magnetic field on diffusion in metallic materials. Youdelis et al.1) reported that a 3 T magnetic field retarded the diffusion of copper in aluminium. Nakajima et al.2) observed no magnetic effects on the diffusion of nickel in titanium. Pokoev et al.3,4) measured the diffusivity of nickel in -Fe and Fe-1.94%Si alloy and the magnetic effect on diffusivity were not monotonic as a function of applied magnetic field. Nakamichi et al.5) studied the effects of magnetic field and magnetic field gradient on the diffusion of carbon and titanium in -Fe and found that the carbon diffusion in -Fe was retarded by the application of a 6 T magnetic field. However, the diffusion of carbon in -Fe can be enhanced in a magnetic field gradient when carbon atoms move towards the direction with a higher magnetic field strength. The higher the magnetic field gradient strength becomes, the more the carbon diffusion is enhanced. Nevertheless, a magnetic field gradient causes a decrease in diffusivity of carbon in -Fe when the opposite magnetic field gradient is applied. Ohtsuka6,7) studied the influence of 10 T magnetic field on carbon diffusion by using a diffusion couple made by pure Fe and Fe-0.8C alloy. The results showed that the high magnetic field retarded the carbon diffusion along the magnetic field direction after isothermal annealing at 1073 K for 24 h. While after isothermal annealing at 1203 K for 5 h, the influence of high magnetic field on carbon diffusion is unnoticeable. The above two studies have great importance on elucidating the mechanism and the influence rule of high magnetic field on carbon diffusion in Fe-C alloy. However, till now, the study about the carbon diffusion in the direction perpendicular to the magnetic field direction is rarely mentioned. In this study, we further studied the effect of high magnetic field on carbon diffusion in -Fe using a diffusion couple made by pure Fe and high purity Fe-0.76%C alloy. *Corresponding author, E-mail: zhaox@mail.neu.edu.cn 2. Experiment The diffusion couple used in this study was made by pure Fe (99.99%) and high-purity Fe-0.76C alloy (Besides Fe and C, the total content of other elements is below 0.01%), they were subjected to isothermal annealing at 1273 K for 5 h with and without a 12 T magnetic field, and then cooled to 473 K with a cooling rate of 20 K/min. The vacuum degree during the heat treatment is 103 Pa. During the magnetic field annealing, the magnetic field was applied in the direction parallel and perpendicular to the interface between pure Fe and high-purity Fe-0.76C alloy, respectively. Specimen was fixed at the center of the applied field, therefore the magnetic field gradient and the magnetic force to the specimens are negligible. 3. Results and Discussion Figure 1 shows the microstructures of the specimens at room temperature after isothermal annealing at 1273 K for 5 h with and without high magnetic field. The line between the pure Fe in the right part and the Fe-0.76C alloy in the left part is the diffusion interface. In the figure, Jc presents the carbon diffusion direction, and H presents the magnetic field direction, both of them are shown by the white arrows. Figure 1(a) shows the microstructure of the specimen annealed without magnetic field. And Fig. 1(b)(c)(d) show the microstructures of specimens annealed with magnetic field. In the left region of pure Fe, there are some phase transition product formed in the cooling process—pearlite (black regions) and Widmanstaten structure ferrite like needle and plate (white regions). Along the carbon diffusion direction, with the increase of the distance to the diffusion interface, the area percentage of black pearlite of per unit area reduces gradually; and the carbon content decreases gradually, too. The far right side where carbon didn’t diffuse is the equiaxed ferrite grains. As shown in Fig. 1(d), when the direction of carbon diffusion perpendicular to the magnetic field direction, the few transformation amount of the black pearlite in the right side of the interface indirectly indicates that the number of the carbon atoms passed through the unit S.-J. Wang, Y. Wu, X. Zhao and L. Zuo (a) 0T Fe-0.76C Jc Pure Fe (b) 12T H Jc Fe-0.76C Pure Fe (c) 12T Fe-0.76C H Jc Pure Fe (d) 12T H Fe-0.76C Jc Pure Fe 200µm Fig. 1 Microstructures of the specimens isothermally annealed at 1273 K for 5 h: (a) 0 T; (b) 12 T, Jc parallel to H; (c) 12 T, Jc antiparallel to H; (d) 12 T, Jc perpendicular to H. diffusion interface area is smaller, and the carbon diffusion distance is short. But, when the carbon diffusion direction parallel/antiparallel to the magnetic field direction, the high magnetic field only slightly promotes the carbon diffusion, compared to the non-field annealed specimen. Figure 2 shows the carbon diffusion distance in specimens annealed with and without the high magnetic field. The measurement of the carbon diffusion distance is as follows: when measuring the area percentage of pearlite, the measurement starts from the point 1500 mm away from the diffusion interface on the side of pure Fe along the direction opposite to Jc with a step size of 5 mm (The measuring width perpendicular to Jc is 1000 mm). When the measured area percentage of the pearlite is greater than 1%, the distance between this point to the diffusion interface is defined as ‘‘carbon diffusion distance’’. It can be seen from Fig. 2 that, in the direction perpendicular to the magnetic field, the carbon diffusion distance is the shortest, which is far below the carbon diffusion distance in the non-field annealed specimen. While in the direction parallel and antiparallel to the magnetic field, the carbon diffusion distance is a bit longer, which is slightly higher than that of the non-field annealed one. Among them, the carbon diffusion distance of the field annealed specimen with the carbon diffusion direction parallel to the magnetic field direction is the longest. Ohtsuka6,7) attributed the retardation of diffusivity of carbon in a magnetic field to two factors, (1) retardation of carbon diffusivity and (2) shift of Fe-C diagram. Concerning (1), it is known that the Arrhenius plot of the self-diffusion coefficients in ferromagnetic -Fe below the Curie temperature deviates downwards from the extrapolated Arrhenius plots from the paramagnetic state above the Curie temper- Carbon Diffusion Distance (µm) 140 1600 1400 1200 0T 12T Jc parallel to H 12T Jc antiparallel to H 12T Jc perpendicular to H 1000 800 600 400 200 0 Fig. 2 Carbon diffusion distance in annealed specimens with and without the magnetic field. ature. Therefore it is expected that the carbon diffusion is retarded in a the magnetic field. As for (2), the A3 line of an Fe-C phase diagram is shifted to higher temperature and higher carbon content in a magnetic field. That is, at the same temperature, the carbon content of = phase equilibrium point is increased by the high magnetic field, resulting in the decline of carbon diffusion driving force. The above theories successfully explain the mechanism of high magnetic field on carbon diffusion in = two-phase coexistence temperature range. When in single-phase region, Ohtsuka observed that the high magnetic field almost had no effect on carbon diffusion, but he didn’t give clear theory explanation, since in this region there is not only no slope change of Arrhenius plots but also no carbon content change of the = phase equilibrium point. From Fig. 1 and Fig. 2, it can be seen that, compared with the carbon diffusion in the non-field annealed specimen, the 12 T high magnetic field obviously hinders the carbon diffusion in the direction perpendicular to the magnetic field; while it only slightly enhances the carbon diffusion in the direction parallel/antiparallel to the magnetic field. The above experimental phenomena adequately demonstrate that the high magnetic field has strong anisotropic effect on the carbon diffusion in -Fe. Ono et al.8) measured the magnetic susceptibility curve of -Fe with different carbon content in 2 T magnetic field at high temperature, the results showed that at the same temperature, the magnetic susceptibility of -Fe increased with the increasing of its carbon content. According to the experimental results of Ono et al.,8) we extrapolated the magnetic susceptibility of Fe-0.76C and pure iron at 1273 K, and they are about 0:38 106 Kg/m3 and 0:35 106 Kg/m3 , respectively. The magnetic susceptibility is the intrinsic properties of materials, while the change of magnetic free energy GM ðT; HÞ of paramagnetic materials under the magnetic field can be shown as 1 GM ðT; HÞ ¼ H 2 2 ð1Þ Where H is the magnetic field intensity, is the magnetic susceptibility. Then we can calculate that the change of the magnetic free energy of Fe-0.76C is 0.215 J/m3 , and that of Fe is 0.198 J/m3 . The magnetic free energy difference of Fe-0.76C and Fe is about 0.017 J/m3 . Effect of a High Magnetic Field on Carbon Diffusion in -Iron (a) (b) Fig. 3 (a) Schemati of the alignment of atomic magnetic moments under the magnetic field applied; (b) Position between two neighboring atomic moments correlated in a coordinate system.9) Therefore, it can be inferred that the magnetic free energy of -Fe with higher carbon content formed by the Fe-0.76C alloy in diffusion couple decreased much more than the magnetic free energy of -Fe with lower carbon content formed by the pure Fe in diffusion couple at 1273 K in 12 T magnetic field. That is, the magnetic free energy of Fe-0.76C alloy side is lower in the diffusion couple, and it is more stable in the high magnetic field, which inhibits the carbon diffusion to some extent. However, the magnetic free energy of the austenite lowered by the field is dependent on its carbon content, and there is no relationship with the diffusion direction. On the other hand, under the 12 T magnetic field, the atomic magnetic moment of iron atoms in paramagnetic -Fe tend to align along the magnetic field direction, as schematically illustrated in Fig. 3(a). Then there exists a dipolar interaction between neighbouring atoms. Let the magnetic moment of each atom be m and the distance between two neighbouring atoms r. The magnetic moments align along the magnetic field direction, as shown in Fig. 3(b). The dipolar interaction energy ED between neighboring atoms can be expressed as:9) ED ¼ 0 m2 3 cos2 1 r3 4 ð2Þ where 0 is the vacuum magnetic permeability and is the included angle between r and magnetic field direction. It can be seen that when ¼ 0 or 180 , i.e., the pairs of moments 2 0m aligned are parallel to the field direction, ED ¼ 2r 3 , ED is negative; when ¼ 90 or 270 , i.e., the pairs of moments aligned are perpendicular to the magnetic field direction, 2 0m ED ¼ 4r 3 , ED is positive. Therefore, the atoms attract each other along the magnetic field direction, but repel each other in the direction perpendicular to the magnetic field direction. Correlatively, the distance between neighbouring atoms tends to decrease along the magnetic field direction and increase in the direction perpendicular to the magnetic field. So, the carbon diffusion activation energy in the direction perpendicular to the magnetic field direction increases, which results in the decrease of the carbon diffusion coefficient, while the carbon diffusion activation energy in the magnetic field direction decreases, which results in the increase of the carbon diffusion coefficient. 141 So, in the direction perpendicular to the magnetic field, the joint action of the above two field effects result in the obvious retardation of carbon diffusion in the magnetic field. In the direction parallel/antiparallel to the magnetic field, the counteraction of the above two field effects result in the slightly promotion of the carbon diffusion in the magnetic field, compared with that of the non-field annealed diffusion couple. Besides, the effect of high magnetic field on atomic magnetic moment of the diamagnetic carbon atoms may be one reason that attribute to the different carbon diffusion distance in the direction parallel/antiparallel to the magnetic field. 4. Conclusion The high magnetic field obviously hinders the carbon diffusion in the direction perpendicular to the magnetic field direction; while it only slightly enhances the carbon diffusion in the direction parallel/antiparallel to the magnetic field. This may be attributed to two field effects. One is that the magnetic free energy of the austenite lowered by the magnetic field is dependent on its carbon content and the other one is that the intensities of the magnetic dipolar interaction between iron atoms in the magnetic field direction and in the direction perpendicular to the magnetic field is different. The joint influence of the two effect results in the anisotropy of the carbon diffusion coefficient in these directions. Acknowledgements Acknowledegments to the Projects 50801010, 50971034 and 50911130365 supported by NSFC, Program for Changjiang Scholars and Innovative Research Team in University (Grant No. IRT0713), and the ‘‘111’’ Project (Grant No. B07015). The authors would like to express appreciation to the High Magnetic Field Laboratory of Northeastern University for providing the facilities. REFERENCES 1) W. V. Youdelis, D. R. Colton and J. Cahoon: Can. J. Phys. 42 (1964) 2217–2237. 2) H. Nakajima, S. Maekawa, Y. Aoki and M. Koiwa: Trans. Jpn. Inst. Met. 26 (1985) 1–6. 3) A. V. Pokoev, D. I. Stepanov, I. S. Trofimov and V. F. Mazanko: Phys. Stat. Sol. (a) 137 (1993) K1–K3. 4) A. V. Pokoev and D. I. Stepanov: Defect Diffusion Forum 143–147 (1997) 419–424. 5) S. Nakamichi, S. Tsurekawa, Y. Morizono, T. Watanabe, M. Nishida and A. Chiba: J. Mater. Sci. 40 (2005) 3191–3198. 6) H. Ohtsuka: CAMP-ISIJ 19 (2006) 791. 7) H. Ohtsuka and X. J. Hao: 5th Int. Symp. on EPM, (2006) pp. 648–651. 8) T. Ono, K. Sassa, K. Iwai, H. Ohtsuka and S. Asai: Research Report for Structural Control of Steels through Phase Transformations in High Magnetic Fields, (2006) pp. 37–43. 9) Y. D. Zhang, C. Esling, J. S. Lecomte, C. S. He, X. Zhao and L. Zuo: Acta Mater. 53 (2005) 5213–5221.