Ternary phase heat treatment pdf free download

In , Gray et al. This globular structure is a stable morphology. Generally, many secondary phases e. A discussion of these four morphologies follows. When a high Cr region forms, the depleted Cr region is also formed and leads to a decrease in the corrosion resistance at the same time. Consequently, this decreases the activation energy barrier to form a coherent interface. The minimum deviation angle for the sigma phase formation decreases with increasing annealing time.

Villanueva et al. Konosu et al. The growth of hot cracking cannot be neglected as it is very significant during the welding. Reis et al. Hence, pitting corrosion always happens at low Cr content points. Generally, the austenitic boundary is a preferential site for pitting corrosion because the austenite has a low Cr content. Consequently, the corrosion potent is decreased.

However, the interstitial elements C and N are neglected in this prediction formula. This equation has been widely used because it takes into account many alloy elements. Gill et al.

In recent years, Ni has been used to replace N and decrease the N addition because the price of the Ni in steel continues to improve. Lin et al. Brandis et al. Smuk et al. This thermodynamic simulation only needs the input of the element contents and experimental temperatures to produce the phase diagrams.

Erneman et al. The series of simulation results were shown in Figures 12 a — 12 f. By adding 1. By adding 0. By continuing to add 0. Similarly, by adding 0. The cooling rates of 0. Hong and Han [ 52 ] conducted a high-temperature tensile test in superduplex stainless steel FeCr-7Ni-3Mo This was because the controlled grain boundaries slip-strain induced the grain growth [ 53 , 54 ] during the super-plasticity.

Abe et al. Duhaj et al. This recrystallized reacting force is due to the difference of the dislocation density from two sides of the recrystallized boundaries. Koutsoukis et al. Hsieh et al. They are also obligated to thank Prof. Weite Wu and Prof. Dong-Yih Lin for their scientific writing guidance about this review paper. 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.

Article of the Year Award: Outstanding research contributions of , as selected by our Chief Editors. Read the winning articles. Academic Editor: M. Received 14 Dec Accepted 19 Jan Published 08 Mar Table 1. Figure 1. Figure 2. Figure 3. Figure 4. Figure 5. Figure 6. Figure 7. Figure 8. Figure 9. Figure Table 2. References W. Treitschke and G. View at: Google Scholar E. Bain and W. Jett and F. View at: Google Scholar K.

Yano and K. View at: Google Scholar B. Hattersley and W. Hall and S. View at: Google Scholar P. Duhaj, J. Ivan, and E. View at: Google Scholar M. Wilms, V. Gadgil, J. Krougman, and F. View at: Google Scholar C. Souza, H. Abreu, S. Tavares, and J. Lee, I. Kim, and A. View at: Google Scholar D. Peckner and I. View at: Google Scholar F. Waanders, S. Vorster, and H. Shinohara, T. Download Free PDF. The ternary system Al—Ni—Ti Part II: thermodynamic assessment and experimental investigation of polythermal phase equilibria Intermetallics, Peter Rogl.

A short summary of this paper. The ternary system Al—Ni—Ti Part II: thermodynamic assessment and experimental investigation of polythermal phase equilibria.

Intermetallics, Elsevier, , 7 12 , pp. Zeng a, R. Huneau a,b,c, P. Rogl b, J. The thermodynamic modeling is based on an experimental investigation of the phase equilibria in the composition range of 0. Alloys were prepared by argon-arc or vacuum-electron beam melting of elemental powder blends. The present assessment covers the entire composition range. Keywords: A. Aluminides, miscellaneous; A. Laves phases; A. Titanium aluminides, based on Ti3Al; B. Phase diagram; E. Phase diagram prediction 1.

The thermodynamic descriptions optimized by composition range of 0. Experimental data [3,4,5]. The Greek notations of the phases temperatures in contrast to earlier assessments [3] see employed in the review by Budberg [3] will be used Table 2 and Fig.

These values. Based on the 3. Summary of modeling of binary boundary systems experimental results in Refs. The phases The modeling done by Saunders [8] in the framework and their compositions were based on the experimental of the COST project is used. Although some important experi- The phase diagram has been well characterized with mental results were published since then, such as the good overall agreement among the phase diagram stu- Refs.

The thermodynamics of the system show assessments [9,10] the data by Saunders [11] have been some inconsistencies, though. The calculated phase diagram using Saunders' The sublattice model was used by Ansara et al. The calculated phase diagram and the thermodynamic Fig. SEM micrograph of the alloy This is still consistent al.

They have been taken from previously assessed binary A thermodynamic model for phases with several sub- systems, i. For one mole of formula unit of Eq. The colons separate 3. They were referred to the standard state Dupin [1] has been adopted.

SER of the elements see Section 3. For comparison, the atom distributions in 3. The sublattice formula used For practical reasons, the number of sublattices can be for this phase by Dupin [1] was Ti,Ni,Al 2 Ti,Ni,Al 1, decreased by putting the sublattices of the same or but the calculated homogeneity range is almost totally similar coordination numbers CN with the same out of the experimental region measured by us [2], occupation of atoms into one sublattice as shown in the showing a much smaller Al-content.