Abstract

The widespread adoption of Ti alloys in various engineering fields, where they would provide significant benefits,is still primarily hindered by their high cost. This study examined the synchronous expansion of modest alloying components (for example Cu and Fe) planning to evaluate the properties of amazing failure cost ternary Ti-Cu-Fe composites got through powder metallurgy. Powder blends are found to be less compressible when alloying elements are added, but relative density values comparable to those of other powder metallurgy Ti alloys can be achieved. Alloys with a lamellar microstructure are formed when Cu and Fe are added. The alloy's specific chemistry determines the prior grain size, morphology, interlamellar spacing, and formation of an eutectoid substructure. Thus, the disfigurement and disappointment of the sintered ternary Ti-xCu-xFe composites are represented by a similar system however the strength, hardness, malleability, and strain solidifying rate are combination subordinate.

For ultrahigh strength steel MS1300, a laser-assisted robotic roller forming (LRRF) process and apparatus were  developed to bend a plate into a straight channel. An integrated thermo-metallurgical-mechanical finite element simulation that took into account the heat source, phase transformation, and material constitutive models was developed because the thermal processing that occurs during roller forming has an effect on the steel's microstructure and mechanical behavior. A new surface heat source model was proposed and confirmed, and a rectangular laser source was created to uniformize the temperature around the bending corner. The stage change model representing the austenitization cycle, austenite decay, and treating was implanted in the limited component model through selfcreated client subroutines. The phase distribution and predicted progression of the microstructure were in line with the experimental characterization of the microstructure. In particular, tempering dominates at the inner layer of the bend, resulting in two distinct phases—the original martensitic phase and the tempered martensitic phase—after the LRRF process. The external layer of the curve, notwithstanding, goes through austenitization, extinguishing,and treating processes, bringing about a mix of new martensite, a limited quantity of tempered martensite and held austenite stages.