High temperature air oxidation behavior of Hastelloy X processed by Electron Beam Melting (EBM) and Selective Laser Melting (SLM)
Introduction
The rapid development of Additive Manufacturing (AM) processes, such as Selective Laser Melting (SLM) or Electron Beam Melting (EBM), is driven by the growing need for manufacturing high performance components with complex geometries and minimum material wastage. AM uses computer-aided design to build objects layer-by-layer in contrast with casting processes where numerous subsequent operations are needed in order to obtain the desire shape object geometry. SLM and EBM are Powder Bed Fusion (PBF) methods involving a local melting and rapid solidification of the powder [1]. The solidification microstructure is governed by the ratio between the temperature gradient, the solidification rate and under-cooling △T [2]. Usually SLM and EBM processes involve fast cooling rates inducing a preferred crystallographic direction for solidification along [100] for face centered and body centered cubic materials and non-equilibrium solidification conditions [1], [3], [4]. For EBM, the build temperature can be modified allowing additional manipulation of the resulting alloy microstructure. However, without understanding of the coupling between alloy metallurgy and AM parameters, different alloy mechanical properties can be obtained. For example, for SLM and EBM alloys, interdentritic precipitation was observed to be detrimental for the mechanical properties of several materials (such as IN718 or Ti-6Al-4V) [5], [6], [7]. Control of AM parameters [8], [9], [10] and post-processing of AM parts (heat treatment, HIP-treatment, polishing) [11], [12], [13], [14], [15], [16] are being studied in order to achieve comparable mechanical properties with the respective wrought materials.
Ni-based alloys are used for their combined corrosion resistance and high temperature strength. They are strengthened by precipitates and/or by elements forming a solid solution. Hastelloy X® is a Ni-based alloy solution and carbide strengthened (presence of Mo-rich carbides) [17], [18], [19] and is widely used in gas turbine engines environments for its high temperature properties. The oxidation behavior of wrought Hastelloy X was studied in the past under isothermal conditions [20], [21], [22] and under cyclic conditions in air between 760 °C and 1150 °C for times up to 10,000 h [23]. The oxidation behavior was also studied in air + 10 % H2O at 950 °C [19] and under carburizing isothermal (650 °C) [24] and cyclic conditions (1000 °C) [25]. In general, at these temperatures, wrought Hastelloy X was observed to form an outer (Ni,Fe,Cr)2O4 or MnCr2O4 spinel, if the alloys contains sufficient Mn, along with an inner protective Cr2O3 scale and partial SiO2 underlayer. In a turbine environment, the alloy is exposed to thermal cycling conditions which can induce the spallation of the protective scale [26].
While studies focused on the mechanical properties and microstructure of AM Hastelloy X [27], [28], [29], [30], [31], [32], the oxidation behavior of AM alloys has received little attention in the literature [33], [34], [35], [36], [37]. One preliminary study was found on the oxidation behavior of Hastelloy X made by EBM and SLM after isothermal and 100 h cyclic exposure in air at 950 °C [38]. Higher oxidation and spallation rates for (Mn, Si)-containing AM materials were found and were associated with the presence of Mo, Si-rich carbides at grain boundaries [38]. Parabolic isothermal oxidation behavior of SLM IN718 after 100 h exposure in still air at 850 °C was observed and increasing spallation of the oxide film with increasing laser volumetric energy density [33]. Similar isothermal oxidation kinetics were observed for SLM and EBM IN 718 after 48 h between 600 and 800 °C in air [37] and after 100 h at 800 °C in air [35]. In [35], roughness of EBM IN 718 was considered to evaluate the oxidation rate constant. Higher oxidation kinetics of as-fabricated IN 718 than wrought IN 718 were measured after 1000 h exposure in air + 10% H2O between 650 and 750 °C due to the formation of Fe-rich oxide nodules on EBM IN 718 [34]. Finally, similar short-term oxidation kinetics were seen between as-fabricated, Hot Isostatic Pressed (HIP) and traditionally hot-rolled Ti-6Al-4V after up to 500 h isothermal exposure at 600 °C [36]. In most of the studies, the combined influence of alloy composition, microstructure and exposure conditions (thermal cycling) on the oxidation behavior were not covered.
The objective of this paper is to evaluate the oxidation behavior of three different AM Hastelloy X materials under isothermal and cyclic oxidation conditions. Thermogravimetric analyses were performed to study the early stage oxidation behavior after 8 and 72 h exposure at 950 °C. Simultaneously, the specimens were thermally cycled with a hold time of 50 h in a furnace at the same temperature for a duration of up to 1000 h to study their cyclic oxidation behavior. The effect of composition (Mn and Si contents) and alloy microstructure on the Cr2O3 scale microstructure and oxidation kinetics will also be discussed.
Section snippets
Materials
The oxidation behavior of three AM Hastelloy X variants: two fabricated by Electron Beam Melting (EBM) with different Si and Mn contents (named henceforth as EBM1 and EBM2) and the other processed with Selective Laser Melting (named henceforth as SLM) were studied. Their oxidation behavior was compared with the commercial wrought Hastelloy X provided by Haynes International. The compositions of the four materials (all within the nominal composition range of Hastelloy X provided by the alloy
Initial microstructure
Etched cross sections of the different materials are reported in Fig. 2 in both transversal and longitudinal directions. The wrought and SLM alloys showed isotropic microstructures (Fig. 2). Equiaxed grains of about 50μm and 60–80μm were formed in the wrought and SLM alloys respectively in both directions. Whereas, for the EBM1 and EBM2 specimens, anisotropic microstructures were observed (aspect ratio of 10 ± 3). As reported for the EBM1 specimen in Figs. 2 and 3 , large elongated grains
Microstructure of additively manufactured alloys
After fabrication, various microstructures were observed for the AM specimens (Fig. 2) as a result of the scanning strategy and the chosen geometry of the build [44], [45]. The grain size in AM alloys is also known to be affected by the cooling rate (cooling rate decreases as the layer height increases or if the bed is pre-heated) [46], [47] and the scanning strategy [8], [9], [10], [48]. Thus, solidification maps (grain size, orientation) can be derived as function of build parameters [3], [10]
Authors’ contributions
Marie Romedenne: Conceptualization, Data curation, Writing – original draft, Review & Editing, Visualization, Investigation. R. Pillai: Conceptualization, Methodology, Writing – Review & Editing, Supervision. M. Kirka: Resources – Provision of study materials, Review. S. Dryepondt: Methodology, Writing – Review & Editing, Funding acquisition, Supervision.
Conflicts of interest
This manuscript has been authored by UT-Battelle, LLC under Contract No. DE-AC05-00OR22725 with the U.S. Department of Energy. The United States Government retains and the publisher, by accepting the article for publication, acknowledges that the United States Government retains a non-exclusive, paid-up, irrevocable, world-wide license to publish or reproduce the published form of this manuscript, or allow others to do so, for United States Government purposes. The Department of Energy will
Acknowledgements
The authors would like to thank T. M. Lowe, T. Jordan, V. Cox, P. Stack and E. Cakmak for their assistance with the experimental work. S.S. Babu, M.P. Brady and B. Pint are acknowledged for their comments on the manuscript. This research was sponsored by the U.S. Department of Energy, Office of Fossil Energy, Crosscutting Research Program.
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