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Journal of Nanomaterials
Volume 2014, Article ID 138750, 7 pages
http://dx.doi.org/10.1155/2014/138750
Research Article

Inclusions and Microstructure of Steel Weld Deposits with Nanosize Titanium Oxide Addition

School of Materials Science and Engineering, Hebei University of Technology, Tianjin 300130, China

Received 1 November 2013; Accepted 13 February 2014; Published 18 March 2014

Academic Editor: Weichao Song

Copyright © 2014 Cuixin Chen et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

Abstract

Nanosize TiO2 particles were added directly into welding molten pool through electrode for the difficulty of accurate control of oxygen potential and production processing parameters. The characteristics of phase transformation and thermal behavior of inclusions for Fe-C-Mn-Si-Ti-O system and Fe-C-Mn-Si-TiO2 system were analyzed. Results show that the added TiO2 particles are more helpful for the formation of Mn-Ti-O complex inclusion and can induce the decrease of phase transformation temperature of austenite to ferrite. Intragranular ferrite can be obtained under the condition of continuous cooling transformation with cooling rate of 293 K/s–373 K/s. The inclusions in steel welds are spherical in shape and mainly composed of TiO2, Ti3O5, Ti2O3, MnO, and SiO2. The mean size of inclusions is 0.67 μm. These complex inclusions can supply a large number of nucleating cores for their precipitation at higher temperature, which will disturb the growth of columnar crystal during solidification. Moreover, Mn-containing titanium oxides will promote the transformation of austenite to intragranular ferrite for the formation of manganese depleted zones in steel welds around oxides. So it can be concluded that nanosize titanium oxide added directly in welding molten pool can be effectively used to control phase transformation and achieve fine and favorable microstructure.

1. Introduction

Titanium is one of the most effective alloying elements to improve the mechanical properties of materials in steelmaking and welding metallurgy. This is because Ti-containing phases, such as TiC, TiN, Ti(CN), TiOx, and MnTiOx, can inhibit grain growth by Zener pinning effect resulting in grain refinement and can also act as the nucleation sites of acicular ferrite [14].Among these phases, the complex inclusions containing titanium oxide have been recognized as one of the most effective ones [5, 6]. Titanium oxides such as TiO, TiO2, Ti2O3, and Ti3O5 are all the potent nucleation cores during solidification and solid phase transformation for their high melting point and high stability. They have a relatively low misfit with ferrite in certain orientations and their presence in steels may therefore be expected to encourage substantial intragranular ferrite formation through lattice coherency [7]. In addition, the effectiveness of TiO for intragranular nucleation on inclusion is suggested to be due to a small disregistry with appropriately oriented ferrite [8] and that of TiO2 is suggested to be due to releasing oxygen to decarburize adjacent steel matrix, which is advantageous for ferrite nucleation [9]. In case of Ti2O3, the development of local manganese depleted zones (MDZs) around particles has been the most influential hypothesis [5, 10].

It should be noted that the size, shape, chemical composition, and distribution of inclusions containing titanium oxides have an evident effect on microstructure and properties of steel production. The suitable size and number of inclusions which can promote the formation of intragranular ferrite are, respectively, 0.25 μm–0.8 μm and 1.07–1.06 mm−3 [8, 11]. So, the required oxygen content is 0.0015–0.008% in titanium deoxidation steel [12]. Hiroki et al. studied the effect of oxygen content and cooling condition on microstructure. The results showed that more inclusions will be obtained with the increase of oxygen content and cooling rate [13]. Moreover, the higher the cooling rate, the finer the inclusions [14]. So, titanium content and oxygen potential as well as production parameters are crucial to the size and quantity of inclusions. However, it is difficult to control these parameters. So, an alternative method in which oxide was added directly into molten welding pool through electrode coating was adopted in this study.

The purpose of this study is to analyze the effect of oxide addition on the thermodynamics and kinetics behavior of inclusions and phase transformation for low alloy high strength steel welds.

2. Experimental Work

A low alloy rolling steel with compositions of 0.12% C, 1.5% Mn, and 0.5% Si was adopted in the experiment. To avoid the quantitative control of oxygen potential and welding parameters, 0.2% TiO2 particles with the mean size of 50–100 nm were added directly in welding pool through electrode coating. For the agglomeration characteristics of nanomaterials, titanium oxides were pretreated with nanocoating and ultrasonic technology, which can ensure the uniform transition of oxide and improve the transfer coefficient.

The weld joints were prepared with the welding parameters of welding current of 120 A, welding voltage of 30 V, and welding speed of 3 mm/s. The dimension of base metal was 200 m00 m0 mm. The adopted welding machine was THERMALARC-MASTER 351.

Phase transformation of steel welds with Fe-Mn-Si-Ti-O system and Fe-Mn-Si-TiO2 system under continuous cooling condition was analyzed by thermal simulating technology. The cooling rate in simulating test was 293 K/s–373 K/s. This test was performed by Formastor IV digital automatic dilatometer.

For the detailed analysis of inclusions, acid dissolution method was adopted to collect inclusions in weld metal bases on ASTM E194290. Nuclepore polycarbonate membrane with the diameter of 47 mm and the pore diameter of 0.08 μm was used in this test. First, three grams of weld metal was dissolved in 100 mL of hydrochloric acid at 353 K. Then, the solution was filtered by polycarbonate membrane and the inclusions were filtered out followed by acid washing and rinsing by deionized water. Finally, the membrane with inclusions was dried.

GX-51 Olympus optical microscopy was employed to analyze microstructure. PHILIPS-XL30 scanning electron microscopy (SEM) with energy dispersive spectrometer (EDS) and JEM2010 transmission electron microscopy (TEM) were used to analyze the morphology and chemical composition of complex inclusions.

3. Thermodynamics Behaviors

When titanium is added in liquid steel under certain oxygen content, the reactions are as follows [15]: where is the standard Gibbs free energy change, J/moL.

Researches indicated that Ti3O5 is the most stable phase and then Ti2O3 under the same temperature and oxygen content condition. When oxygen content is lower, TiO and TiO2 cannot be found in steel liquid [15]. For the steel with 0.015% Ti and 0.0018%–0.0077% O, the reaction product is Ti2O3 rather than TiO2 at 1873 K [16]. Only when the oxygen content is higher, TiO2 can form. The same results were also obtained by Zhuo et al. They indicated that when the oxygen activity is 0−5, the most stable titanium oxide is Ti2O3 [17].

In addition, manganese in steel can affect the chemical composition of reaction products. If manganese exists, the reaction will be [15, 17]

For the steel with 1.65% Mn and 0.01% Ti, when the oxygen content is 0.003%, Mn-Ti-O complex inclusion will form during solidification. But when the oxygen content drops to 0.001%, only titanium oxide can be found in steel [16]. So, the more stable inclusions forming in Fe-Mn-Ti-O melt were Ti3O5, Ti2O3, and MnTiO3 and MnTiO3-Ti2O3 can only be obtained with higher oxygen content.

When TiO2 was added directly in liquid steel, TiO2 with Ti4+ will be decomposed to titanium subchlorides and the reaction between Mn and titanium oxides can occur. The reactions are [6, 17] So, the inclusions are mainly composed of Ti3O5, Ti2O3, TiO2, and MnTi2O5.

For further understanding the characteristics of phase transformation and thermal behaviors of inclusions, the thermodynamics equilibrium calculation was carried out (as shown in Figures 1 and 2 and Table 1). The solution phases forming in Fe-Mn-Si-Ti-O system and Fe-Mn-Si-TiO2 are as follows: slag Ti2O3-TiO2-MnO, Allmeniter (ILME) Ti2O3-MnTiO3, Pseudobrookite (PSEU) Ti3O5-MnTi2O5, Titania-Spinel (TiSp) MnTi2O4, and Rhodonite (Rhod) MnSiO3.

tab1
Table 1: The calculating transformation temperature of steel in Fe-Mn-Si-Ti-O system and Fe-Mn-Si-TiO2 system.
fig1
Figure 1: Phase transformation and inclusions of Fe-Mn-Si-Ti-O system (a) phase transformation, (b) solid solution, (c) slag, and (d) ILMEA.
fig2
Figure 2: Phase transformation and inclusions of Fe-Mn-Si-TiO2 system (a) phase transformation, (b) solid solution, (c) slag, and (d) PSEU.

For Fe-Mn-Si-Ti-O system, slag precipitates at 2042.8 K. It is composed of 55.3% Ti2O3, 32.8% TiO2, 7.3% MnO, and a little quantity of other oxides (as shown in Figure 1(c)). With the decrease of temperature, PSEU formed at 1640 K–1940 K and then transformed into ILMEA at temperature lower than 1640 K (as shown in Figure 1(b)). In contrast to Fe-Mn-Si-Ti-O system, slag precipitates at higher temperature (2437.5 K) for Fe-Mn-Si-TiO2 system. It mainly consists in 53.1% Ti2O3, 29.1% TiO2, 6.7% MnO, and 13.1% other oxides (as shown in Figure 2(c)). Moreover, the solid solution is mainly composed of PSEU and Rhod (as shown in Figure 2(b)). This indicated that TiO2 in liquid can promote the formation of Ti3O5 and MnTi2O5.

From Table 1, it can be seen that the temperature of solidification and phase transformation of for Fe-Mn-Si-TiO2 system is higher than that of Fe-Mn-Si-Ti-O system. This is because there are more solid solutions (about 0.21% PSEU and 0.03% slag) at 1750 K–1800 K in TiO2 added liquid. But only 0.023% PSEU exists in Fe-Mn-Si-Ti-O system. The existing particles in liquid can act as heterogeneous nuclei to decrease the critical nucleation energy resulting in the increase of temperature. In addition, the austenite in Fe-Mn-Si-TiO2 system has higher stability. The starting temperature of is lower but the finishing temperature is higher. The results show that TiO2 added system is helpful for the formation of intermediate microstructure.

At about 1100 K ( transformation temperature), the inclusions in TiO2 added system are Ti3O5 and MnTi2O5 (as shown in Figures 2(b) and 2(d)). However, the inclusions in Fe-Mn-Si-Ti-O system are ILMEA which mainly consist in Ti2O3. Ti3O5 is the most stable phase. Moreover, MnO-TiOx complex inclusions have been recognized as one of the effective inclusions for grain refinement and the nucleation of intragranular ferrite [1821]. This is because titanium oxide can absorb some elements from substrate due to the existence of a large number of cation vacancies [5, 9]. In addition, manganese with the ion radius of 0.070 nm has similar crystal structure to titanium (Ti+2 0.090 nm, Ti3+ 0.076 nm, and Ti4+ 0.068 nm), which induce that manganese atoms are quite soluble in this structure. Therefore, it is reasonable to believe that the absorption of manganese from the steel matrix into titanium oxide particles dispersed in the steels is a probably thermodynamic process [18]. It has been known that the diffusivity of manganese in austenite between 1300 K and 1600 K is in the order of 10−14 m2/s and the solubility of manganese in cation site of titanium oxide phase is above 10 at % at 1473 K [19, 20]. Such a limited diffusivity of manganese in austenite and a large solubility of manganese in titanium oxide might contribute to forming and maintaining MDZs around titanium oxide. Figure 3 further confirms the result.

138750.fig.003
Figure 3: Manganese content change in FCC, PSEU, and Rhod.

4. Results and Discussion

4.1. Continuous Cooling Transformation Characteristics

Table 2 shows the dilatometer test results. Under the cooling rate of 373 K/s, phase transformation temperature is in the range of 989 K to 584 K for Ti-O system and 951 K to 718 K for 0.2% TiO2 added case. In addition, the microstructure of Ti-O system is composed of martensite, bainite, and proeutectoid ferrite (as shown in Figure 4(b)). However, only intragranular ferrite forms in TiO2 added system (as shown in Figure 4(a)). The similar phenomenon occurs for the case with cooling rate of 293 K/s. The results indicate that, in nonequilibrium condition, TiO2 is favorable for the formation of intermediate temperature microstructure, especially for the case of rapid welding cooling condition.

tab2
Table 2: Microstructure and phase transformation temperature of weld metal with different cooling rate.
fig4
Figure 4: Microstructure of weld metal: (a) 0.2% TiO2 added weld metal with 373 K/s and (b) 0.05% Ti-0.008% O added weld metal with 373 K/s.
4.2. Inclusions in Weld Metal

Figure 4 shows the morphology and chemical composition of inclusion in 0.2% TiO2 added weld metal. Most of inclusions are spherical (as shown in Figure 5(a)) and the main chemical composition is Ti, Si, O, Mn, and S (as shown in Figure 5(b)). The complex inclusion has a black core with white surrounding (as shown in Figure 6). Chemical composition analysis shows that the core is titanium oxide and the outer layer is manganese oxides and silicon oxide. In addition, the complex Ti-Mn-Si-O inclusions have the mean size of 0.67 μm, which can act as nucleating sites to promote the solid phase transformation of . The results are consistent with calculated results.

fig5
Figure 5: Morphology of inclusions (a) and the responding EDS results (b).
138750.fig.006
Figure 6: Inclusion in weld metal.
4.3. Microstructure of Weld Metal

Figure 7 gives the microstructure of weld metal. From the results of 3 and 4.2, it can be seen that, during solidification, many suspending particles of Mn-Ti-O complex inclusions exist in liquid which can supply a large number of effective heterogeneous nucleation cores resulting in refining crystal microstructure by disturbing the growing direction of columnar crystal (as shown in Figure 7(b)). In subsequence cooling process, fine intragranular ferrite can be obtained in TiO2 added steel weld, as shown in Figures 7(a) and 8.

fig7
Figure 7: Crystal microstructure of weld metal: (a) 0.2% TiO2 added and (b) 0.05% Ti-0.008% O added.
138750.fig.008
Figure 8: Intragranular ferrite.

The inclusions in TiO2 added steel weld are mainly composed of Ti2O3, Ti3O5, and MnTi2O5. With the temperature dropping, the content of MnTi2O5 increases. The manganese content increases from 6.43% at starting temperature (1105.9 K) to 6.86% at at finishing temperature (956.9 K). EDS results show that the manganese content in weld metal surrounding the inclusion in Figure 8 is 1.45% which is lower than that (1.63%) in weld metal far away from inclusions. So, MDZs are well developed around the particles dispersed in the steel weld matrix which will make nucleating driving force high and promote the formation of intragranular ferrite. Byun et al. indicate that the area fraction of intragranular ferrite has been related to Mn content in MDZs [6, 22]. The lower the manganese content is, the higher the content of intragranular ferrite will be. So, the complex inclusions are favorable for the nucleation of intragranular ferrite, because they lead to elements redistribution.

5. Conclusions

The effects of TiO2 added directly in steel liquid on inclusions and phase transformation were studied. Thermodynamic calculation results show that TiO2 in liquid can promote the formation of stable solid solutions, Ti3O5 and MnTi2O5. In addition, the stability of austenite in Fe-Mn-Si-TiO2 system is higher. The starting temperature of is lower but the finishing temperature is higher which is helpful for the formation of intermediate microstructure.

Under continuous cooling condition, only intragranular ferrite is found in TiO2 added steel welds with the cooling rate of 273 K/s–373 K/s. The inclusions in steel welds are spherical and composed of TiO2, Ti3O5, MnO, SiO2, and MnS. The mean size is 0.67 μm. Moreover, the lower the temperature is, the more content of manganese is in complex inclusion. So, besides supplying nucleating sites, the complex inclusions can lead to the formation of MDZs in the border of inclusion due to the absorption of titanium oxide to manganese and cause deletion of austenite stabilizing elements in the matrix adjacent to the inclusions. Therefore, during transformation, there is an increased thermodynamic driving force for intragranular ferrite formation in TiO2 added steel weld.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

Acknowledgments

This research is financially supported by the National Natural Science Foundation (no. 51304059) and the Natural Science Foundation of Hebei Province (no. E2011202113). The authors would like to thank Professor X. Y. Song (Beijing University of Technology) and Professor K. Hack (GTT-Technologies, Herzogenrath, Germany) for their valuable discussions during the present study.

References

  1. Y. W. Cho, J. S. Byun, and J. H. Shim, “Effect of Ti addition on mixed microstructure of allotriomorphic and bainitic ferrite in wrought C-Mn steels,” Materials Science Forum, vol. 426–432, no. 2, pp. 1511–1516, 2003. View at Google Scholar · View at Scopus
  2. S. Hossein Nedjad and A. Farzaneh, “Formation of fine intragranular ferrite in cast plain carbon steel inoculated by titanium oxide nanopowder,” Scripta Materialia, vol. 57, no. 10, pp. 937–940, 2007. View at Publisher · View at Google Scholar · View at Scopus
  3. Z. B. Yang, F. Wang, S. Wang, and B. Song, “Intragranular ferrite formation mechanism and mechanical properties of non-quenched-and-tempered medium carbon steels,” Steel Research International, vol. 79, no. 5, pp. 390–395, 2008. View at Publisher · View at Google Scholar · View at Scopus
  4. T. Pan, Z. G. Yang, C. Zhang, B. Z. Bai, and H. S. Fang, “Kinetics and mechanisms of intragranular ferrite nucleation on non-metallic inclusions in low carbon steels,” Materials Science and Engineering A, vol. 438–440, pp. 1128–1132, 2006. View at Publisher · View at Google Scholar · View at Scopus
  5. J. H. Shim, Y. W. Cho, S. H. Chung, J. D. Shim, and D. N. Lee, “Nucleation of intragranular ferrite at Ti2O3 particle in low carbon steel,” Acta Materialia, vol. 47, no. 9, pp. 2751–2760, 1999. View at Publisher · View at Google Scholar · View at Scopus
  6. X. J. Zhuo, X. H. Wang, W. J. Wang, and H. G. Lee, “Thermodynamic calculations and experiments on inclusions to be nucleation sites for intragranular ferrite in Si-Mn-Ti deoxidized steel,” Journal of University of Science and Technology, vol. 14, no. 1, pp. 14–21, 2007. View at Publisher · View at Google Scholar · View at Scopus
  7. T. Koseki and G. Thewlis, “Inclusion assisted microstructure control in C-Mn and low alloy steel welds,” Materials Science and Technology, vol. 21, no. 8, pp. 867–879, 2005. View at Publisher · View at Google Scholar · View at Scopus
  8. S. St-Laurent and L. G. Esperance, “Effects of chemistry, density and size distribution of inclusions on the nucleation of acicular ferrite of CMn steel shielded-metal-arc-welding weldments,” Materials Science and Engineering A, vol. 149, no. 2, pp. 203–216, 1992. View at Google Scholar · View at Scopus
  9. J. M. Gregg and H. K. D. H. Bhadeshia, “Titanium-rich mineral phases and the nucleation of bainite,” Metallurgical and Materials Transactions A, vol. 25, no. 8, pp. 1603–1611, 1994. View at Publisher · View at Google Scholar · View at Scopus
  10. J. H. Shim, J. S. Byun, Y. W. Cho, Y. J. Oh, J. D. Shim, and D. N. Lee, “Hot deformation and acicular ferrite microstructure in C-Mn steel containing Ti2O3 inclusions,” ISIJ International, vol. 40, no. 8, pp. 819–823, 2000. View at Google Scholar · View at Scopus
  11. F. J. Barbaro, P. Krauklis, and K. E. Easterling, “Formation of acicular ferrite at oxide particles in steels,” Materials Science and Technology, vol. 5, no. 11, pp. 1057–1067, 1989. View at Google Scholar · View at Scopus
  12. M. G. Li, S. B. Zheng, and Q. Zheng, “Oxides metallurgy,” Shanghai Metal, vol. 27, pp. 55–60, 2005. View at Google Scholar
  13. G. Hiroki, M. Kenichi, and T. Kazuaki, “Effect of oxygen content on size distribution of oxides in steel,” ISIJ International, vol. 35, no. 3, pp. 286–291, 1995. View at Google Scholar
  14. G. Hiroki, M. Kenichi, and T. Kazuaki, “Effect of Cooling rate on oxide precipitation during solidification of low carbon steels,” ISIJ International, vol. 34, no. 5, pp. 414–419, 1994. View at Google Scholar
  15. H. G. Li, C. F. Wu, D. Zhao, S. B. Zheng, and Q. J. Zhai, “Thermodynamic analysis of ultra fine Ti oxide inclusion precipitation during steel solidification,” Shanghai Metal, vol. 33, no. 2, pp. 36–39, 2011. View at Google Scholar
  16. W. Y. Xia, Y. C. Wang, M. L. Wang, and S. T. Qiu, “Behavior of oxide precipitation in solidification process for alumium-titaniuni deoxidized steels,” Journal of Iron and Steel Research, vol. 23, no. 8, pp. 11–15, 2011. View at Google Scholar · View at Scopus
  17. X. J. Zhuo, X. H. Wang, W. J. Wang, and H. G. Lee, “Thermodynamic calculations and MnS solubility of Mn-Ti oxide formation in Si-Mn-Ti deoxidized steel,” Journal of Iron and Steel Research, vol. 17, no. 2, pp. 10–17, 2010. View at Google Scholar
  18. J. H. Shim, J. S. Byun, Y. W. Cho, Y. J. Oh, J. D. Shim, and D. N. Lee, “Mn absorption characteristics of Ti2O2 inclusions in low carbon steels,” Scripta Materialia, vol. 44, no. 1, pp. 49–54, 2001. View at Publisher · View at Google Scholar · View at Scopus
  19. W. C. Leslie, The Physical Metallurgy of Steels, MCGraw-Hill, New York, NY, USA, 1981.
  20. I. E. Grey, C. Li, and A. F. Reid, “Phase equilibria in the system MnO-TiO2-Ti2O3 at 1473K,” Journal of Solid State Chemistry, vol. 17, no. 4, pp. 343–352, 1976. View at Google Scholar · View at Scopus
  21. Y. B. Kang, I. H. Jung, and H. G. Lee, “Critical thermodynamic evaluation and optimization of the MnO-SiO2-TiO2-Ti2O3 system,” Computer Coupling of Phase Diagrams and Thermochemistry, vol. 30, no. 3, pp. 226–234, 2006. View at Publisher · View at Google Scholar · View at Scopus
  22. J. S. Byun, J. H. Shim, Y. W. Cho, and D. N. Lee, “Non-metallic inclusion and intragranular nucleation of ferrite in Ti-killed C-Mn steel,” Acta Materialia, vol. 51, no. 6, pp. 1593–1606, 2003. View at Publisher · View at Google Scholar · View at Scopus