PSI - Issue 14

P. Rama Rao et al. / Procedia Structural Integrity 14 (2019) 322–329 P R Rao et al/ Structural Integrity Procedia 00 (2018) 000–000

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7

Ti 20 Zr 20 Cu 50 Ni 10

1000 1200 1400

200 400 600 800

NiTi2 & Cu51Zr14 Ni4Ti3 Ni2Ti

Intensity(arb.units)

10 20 30 40 50 60 70 80 90 0

2  /°

Fig.7. The Ti 20 Zr 20 Cu 50 Ni 10 metallic glass ribbon annealed at 753 K for a period of 30 min, and the corresponding XRD spectrum. These results e.g., figure 3(c) and Table 3 corroborated with the corresponding XRD data shown in figure 7. Figure 3(a) and figure 3(b) confirmed the homogeneous distribution of the various nanocrystalline phases in the amorphous matrix, Zhai, Q.Y., Xu, J.F. and Cui, J. (2013). The existence of these nanocrystallie phases were confirmed from both the XRD data figure 7 and the compositional analysis data obtained from the TEM studies Table 3. The XRD spectra shown in Figure 7 confirmed that annealing at 753 K for 30 min produced the crystalline phases Ni 4 Ti 3 ( 122), Cu 51 Zr 14 (316), Ni 2 Ti(101) and NiTi 2 (511) in the Ti 20 Zr 20 Cu 50 Ni 10 metallic glass ribbon. 4. Conclusions Microstructural evolution of the clad Ti 20 Zr 20 Cu 50 Ni 10 metallic brazed CP-Ti alloy have been investigated composite joint brazed at 990 K for a period of 30 min. By using X-RD, FESEM and TEM.It is observed that the joint is dominated by primary β-Ti and coarse eutectic of (Ti,Zr) 2 Ni, Ti 2 Cu, and α-Ti during brazing. The primary β-Ti is transformed to fine lamellar eutectoid of (Ti,Zr) 2 Ni, Ti 2 Cu, Ti 2 Ni, and α-Ti upon the subsequent cooling cycle of brazing.The loss of Cu, Ni,andZr from the braze melt results in isothermal solidification of molten braze, and the β-Ti grains dominate the entire joint at the brazing temperature. The β-Ti alloyed with Cu, Ni, and Zr is subsequently transformed to fine eutectoid of (Ti,Zr) 2 Ni, Ti 2 Cu, Ti 2 Ni, and α-Ti. Acknowledgements P. Rama Rao gratefully acknowledges the partial support of this research by the University Grants Commission, through Rajiv Gandhi National Fellowship (UGC-RGNF) while I was at University of Hyderabad, India. AKB Thanks Indian National Science Academy, New Delhi (India) for support through its Senior Scientist scheme. References R. Roger, E.W. Collings, and G. Walsh., 1993. Materials Properties Hand book, Titanium Alloys, ASM International, Materials Park, Oh, pp, 1-3. J.L. Walter, M.R. Jackson, and C.T. Sims, 1988.Titanium and Its Alloys, Principles of Alloying Titanium, ASM, International, Materials Park, Oh, pp, 23-33. J.R. Davis: ASM, Handbook, Volume 2, 1990. Properties and Selection, Nonferrous Alloys and Special Purpose Materials, ASM, International, Materials Park, Oh, pp, 592-633. W.F. Smith, 1993. Structure and Properties of Engineering Alloys, Mcgraw-Hill Inc., New York, pp. 433-484 C.T. Chang, Y.C. Du, R.K. Shiue, and C.S. Chang: 2006. Mater. Sci. Eng., Vol. 420a, pp. 155-164. C.T. Chang, Z.Y. Wu, R.K. Shiue, and C.S. Chang: 2007. Mater. Lett, Vol. 61(3), pp. 842-845. C.T. Chang, R.K. Shiue, and C.S. Chang, 2006. Scripta Mater., Vol. 54, pp. 853-858. T.B. Massalski: 1990. Binary Alloy Phase Diagrams, ASM International, Materials Park, Oh, pp. 1494. M.K. Lee, J.G. Lee, 2013. Mechanical and corrosion properties of Ti–6Al–4V alloy joints brazed with a low-melting-point 62.7Zr–11.0Ti– 13.2Cu–9.8Ni–3.3 be amorphous filler metal, Mater. Characterization. 81, 19-27. S.J. Lee, S.K. Wu, R.Y. Lin, 1998.Infrared joining of Ti-Al intermetallic using Ti–15Cu–15Ni foil-II. The microstructure evolution at high temperature, Acta Mater. 46, 1297–1305. E.W. Colhngs, 1984. The Physical Metallurgy of Titanium Alloys, ASM Metal Park, Oh. L. Li, X.Q. Li, K. Hu, S.G. Qu, C. Yang, Z.F. Li, 2015. Effects of brazing temperature and testing temperature on the microstructure and shear strength of γ-TiAl joints, Mater. Sci. Eng. A 63, 491-498.