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Oxide dispersion strengthened (ODS) steels are being developed as promising core component structural materials for future generation fast breeder and fusion reactors because of their better high temperature thermal stability and neutron irradiation void swelling resistance as compared to currently used austenitic steels. The type of oxide dispersoids, their size distribution in metallic matrix and stability at adverse service conditions (such as high temperature along with fast neutron irradiation) governs the physical and mechanical properties of the steel. Yttria (Y₂O₃), is the most preferred oxide dispersoid being used in the ODS steels, because of its superior thermal and neutron irradiation stability. However there are reports that show that these oxides either dissolve or dissociate or even become amorphous during mechanical milling and reprecipitate as coarse particles during high temperature consolidation process, in absence of Ti in a model Fe-15Y₂O₃ system [1]. It is believed that Ti can inhibit the growth of nano-dispersoid during annealing by formation of Y-Ti-O complex oxides such as Y₂Ti₂O₇ or Y₂TiO₅ or YTiO₃ [2]. The Y₂O₃ to Ti weight ratio in the alloy is critical in determining the chemical composition of the dispersoid and the Y₂Ti₂O₇ oxides are finer and most stable oxide among all combinations of Y-Ti-O complex oxides whose size which varies in the range of 2-15 nm in ODS steel. Synchrotron XRD is used to characterize the dispersoids in the ODS steel, with 0.35 wt% of yttria and 0.2 wt% of Ti, due to the low volume fraction. TEM has been found more suitable for complete characterization of the nano-sized (~2-5 nm) dispersoids w.r.t size, distribution, morphology, chemical composition and crystal structure. However, characterisation of samples prepared by conventional methods for TEM studies continues to be difficult owing to magnetic nature of ferritic steel. Hence FIB was employed to extract electron transparent samples which are of micrometer dimensions. In order to understand the structural evolution of the Y₂Ti₂O₇ oxide in ODS steel, a concentrated alloys of 5, 10, 15) were synthesized by mechanical milling and subsequently annealed. Figure 1(a) and (b) represents the typical bright field (BF) TEM micrographs of Fe-15wt%Y₂O₃-15wt%Ti model ODS after 60h of milling and subsequent annealing at 1273K respectively, the corresponding SAD patterns are shown as inset. The analysis of SADP reveals amorphisation of yttria upon milling and recrystallisation of Y₂Ti₂O₇, in annealed alloy powder. Interestingly, it was observed when the Y₂O₃ to Ti weight ratio is 1:1, the oxide phase formed upon annealing is only Y₂Ti₂O₇ and are very finer in size (varies in the range of 2-30 nm). Details of these studies will be presented in the paper.

Multiprincipal elemental alloys commonly referred to as High Entropy Alloys (HEA) are a relatively new class of materials gaining large interest in recent times due to their new microstructures and excellent mechanical and corrosion properties. An equiatomic high entropy Cr-Fe-Ni-Nb-V alloy synthesized by multiple vacuum arc melting. Though the formation of BCC solid solution was predicted by considering the thermodynamic parameters like entropy and enthalpy of mixing, atomic size differences, valence electron concentration and electronegativity [1], analysis of XRD pattern of the as cast alloy, showed the presence of a major HCP Laves phase of CrNiNb type and minor tetragonal and BCC phases. The lattice parameters of these phases calculated by Rietveld refinement are as follows: (i) HCP Laves phase: a=0.485 ± 0.003 & c= 0.790 ± 0.009 nm (ii) BCC phase: a=0.327 ± 0.001 nm (iii) Tetragonal phase: a= 0.895 ± 0.002 & c= 0.462 ± 0.002 nm. Microstructural and microchemical analysis through Transmission Electron Microscopy confirmed that the HCP Laves phase is Nb rich, while the tetragonal and BCC phases are lean w.r.t Nb and enriched with Cr and V. The microstructure of the alloy was found to be stable upto 1100°C. Bright field TEM image of the Laves phase of this alloy aged at 1100°C along with the Selected Area Diffraction Pattern along [-11.0] zone axis from the Laves phase is shown in the figure below. The formation of HCP Laves phase in contrast to the theoretical predictions was understood based on the calculation of average d orbital energy level, which decides the formation of topological close packed phases in superalloys containing transition elements [2]. Since HEAs also contains transition elements, this concept is extended to these novel alloys. For the current alloy, the average d-orbital energy level was calculated to be 1.46, which is well above the threshold value of 1.09 for formation of intermetallic phases. This dictates the formation of intermetallic Laves phases in this system. Detailed analysis regarding the crystallographic aspects of this Laves phase using Rietveld refinement and Precession Electron Diffraction (PED) technique is under progress, results of which will be presented in the paper.