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Nickel base superalloys are hi-tech materials intended for high temperature applications. This property owns a complex microstructure formed by matrix of Ni and variety of precipitates. The type, form and the amount of these phases significantly affect the resulting properties of these alloys. At sufficiently long exposure to high temperatures, the transformation phase can occur, which can lead to degradation of properties of these alloys. A cyclic plastic deformation can accelerate these changes, and they could occur at significantly lower temperatures or in shorter time of exposure. The aim of this study is to describe phase transformation, which can occur by a cyclic plastic deformation at high temperatures in nickel base superalloy Inconel 718. KeywordsNickel base superalloy Inconel 718 phase transformations high temperature fatigue

The contribution describes influence of the age-hardening consist of solution treatment at 515 °C with holding time 4 hours, water quenching at 40 °C and artificial aging at different temperature 150 °C, 170 °C and 190 °C with different holding time 2, 4, 8, 16 and 32 hours on mechanical properties (tensile strength and Brinell hardness) and changes in morphology of eutectic Si, Fe-rich and Cu-rich intermetallic phases in secondary (recycled) AlSi9Cu3 cast alloy. A combination of different analytical techniques (light microscopy upon black-white and colour etching, scanning electron microscopy (SEM) upon deep etching and energy dispersive X-ray analysis (EDX)) were therefore been used for the identification of the various phases. Quantitative study of changes in morphology of eutectic Si, Cu-rich and Fe-rich phases was carried out using Image Analyzer software NIS-Elements. Mechanical properties were measured in line with EN ISO. Age-hardening led to changes in microstructure include the spheroidization and coarsening of eutectic silicon, gradual disintegration, shortening and thinning of Fe- rich intermetallic phases, the dissolution of precipitates and the precipitation of finer hardening phase (Al₂Cu) further increase in the hardness and tensile strength in the alloy.

DOI: http://dx.doi.org/10.5755/j01.ms.18.3.2430

In the present study, microstructure and porosity of AlSi7Mg0.3 cast alloy including various amounts (0.123; 0.454 and 0.655 wt. %) of iron were investigated. The alloys were produced as secondary (scrap-based -recycled IntroductionAutomotive -chassis, bodies, engine blocks, radiators, hubcaps, and etc. driven by consumer needs and increasingly tight regulations, the automobile industry has made ample recourse to aluminium. A European car today contains on average 100 kg of aluminium, taking advantage of multiple properties of the materials: lightness (a 100 kg loss of weight reduces fuel consumption by 0.6 litres/100 km and greenhouse gases by 20 %), resistance (improved road-handling, absorption of kinetic energy, shorter braking distance) and recycling (95 % of the aluminium contained in autos is collected and recycled, and represents over 50 % of the vehicle's total end-of-life value). Aluminium coming from recycling can allow 95 % energy savings and 85 % less CO 2 emissions compared to primary aluminium production. Recycling -aluminium can be recycled indefinitely without losing any of its intrinsic qualities. This is a considerable advantage in modern metallurgical industry. For the past 20 years the proportion of metal consumed that is recycled has grown steadily and today stands at something like 30 % of primary metal production (European Aluminium Association; Schlesinger, 2014;Hurtalová et al., 2013).The Fig. 1 shows the fraction of world aluminium production from primary and secondary (recycled) sources. About one-third of the aluminium produced in the world is now obtained from secondary sources and in some countries the percentage is much higher. The process used for recycling aluminium scrap is very much different from those used to produce primary metal but in many ways follow the same general sequence. This sequence begins with mining ore, followed by mineral processing and thermal pre-treatment and then a melting step. The metal is then refined, cast into ingots and sent to customers. Aluminium alloys recyclers also face similar challenges to the producers of primary aluminium; there is need to produce a consistent alloy with the required chemistry, reduce the amount of waste generated, minimize energy usage and manufacture the highest-quality product at the lowest possible cost from raw materials of uncertain chemistry and condition (Mc Millan et al., 2012;Schlesinger, 2014).Commercial Al-alloys always contain Fe, often as undesirable impurity and occasionally as a useful minor alloying

Secondary-cast aluminum alloys have increasing industrial applications. Their biggest deficiency is their impurity content, especially Fe, which has low solubility in Al and almost all the content creates intermetallic phases. This work examines the effect of higher Fe content on the microstructure and properties of A356.0 alloy. At the same time, no other possibility existed to affecting the brittleness of the formation of the β phases. The calculation of Fecrit, ratio of Mn/Fe, quantitative and computed tomography analysis of porosity and Fe plate-like phases, measurement of mechanical and fatigue properties, and fractography analysis were performed in this study. The results show that gravity die casting into a sand mold, and the non-usage of Mn addition or heat treatment, do not have a negative effect on increasing the size of the Fe-rich plate-like phases. The longest Fe-rich phases have limited the pore growth and ratios, but their higher thickness led to greater porosity formation. The mechanical and fatigue properties correlate with the Fecrit level and the highest were for the experimental alloy with 0.454 wt.% of Fe. The experimental results confirmed the fact that if the Fe plate-like phases have a length of up to 50 µm, the fatigue properties depend more on the size of porosity. If the length of the Fe needles is more than 50 µm, then the properties are mainly affected by the length of these Fe phases.

A polycrystalline alpha-beta TiAl6V4 alloy in the annealed condition was used for the three-point bending fatigue test at frequency f∼100 Hz. The static preload Fstat. = −15 kN and variable dynamic force Fdyn. = −7 kN to −13.5 kN were set as fatigue test loading parameters. The fatigue life S-N curve presented the stress amplitude σa as a function of a number of cycles to fracture Nf. A limiting number of cycles to run out of 2.0 × 107 cycles were chosen for the 3-point fatigue tests of rectangular specimens. In addition, the Smith diagram was used to predict the fatigue life. The alpha lamellae width has a significant influence on fatigue life. It is assumed that the increasing width of alpha lamellae decreases fatigue life. A comparison of fatigue results with given alpha lamellae width in our material to the results of other researchers was performed. The SEM fractography was performed with an accent to reveal the initiation sites of crack at low and high load stresses and mechanism of crack propagation for the fatigue part of fracture.

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The Inconel’s alloy IN 718 has been developed by International Nickel Company in early 50-ties of 20thcentury. It is high-strength; corrosion-resistant nickel chromium material used at temperature range from-250°C up to 705°C. In this study, the high cycle fatigue (HCF) and very high cycle fatigue (VHCF) properties of IN718 superalloy with given chemical composition were investigated under push-pull high frequency fatigue test at room temperature. A S – N curve was obtained after testing. With the help of scanning electron microscope (SEM), fractography analyses were performed to disclose the fracture features of specimens in different life ranges.