Compacted oxide layer formation under conditions of limited debris retention at the wear interface during high temperature sliding wear of superalloys

The initial part of this study concentrates on sliding speed -- during the current experimental programme, testing was conducted at 0.314 m.s-1 and 0.905 m.s-1, between room temperature and 750°C -- this supplemented previous testing conducted at 0.654 m.s-1. When Nimonic 80A was slid against Stellite 6, lowering sliding speed to 0.314 m.s-1 between 510°C and 750°C lead to the formation of wear protective glaze layers consisting of cobalt and chromium oxides from the Stellite 6, whereas at 0.905 m.s-1 and during previous testing at 0.654 m.s-1, only high wear was encountered with debris consisting of nickel and chromium oxides from the Nimonic 80A. When Incoloy MA956 was slid against Stellite 6 at the same sliding speeds and over the same temperature range, a wear protective layer readily formed regardless of sliding speed. However, the sliding speed was observed to affect the relative contributions to the glaze layer from sample and counterface -- a shift was observed from largely cobalt and chromium oxides from the Stellite 6 at 0.314 m.s-1 to largely iron and chromium oxides from the Incoloy MA956 at 0.905 m.s-1. Also, the use of a higher sliding speed was noted to promote glaze formation at lower temperature, with glaze appearing at 450°C for 0.905 m.s -1, whereas only severe wear was observed for testing at 0.654 m.s -1.;When Incoloy MA956 was worn against Incoloy 800HT, increasing the sliding speed from 0.314 m.s-1 to 0.905 m.s-1 had the opposite affect -- the beginning of glaze formation was suppressed from 630°C to 690°C. Similar results were also observed when Nimonic 80A was slid against Incoloy 800HT, with the beginning of glaze formation suppressed from 570°C to 630°C. Thus whether sliding speed promotes or suppresses glaze formation is highly material dependant. Additionally, both the Incoloy MA956 versus Incoloy 800HT and the Nimonic 80A versus Incoloy 800HT combinations were characterised by high degrees of metallic transfer and especially at room temperature and 270°C, adhesive wear -- with Nimonic 80A versus Incoloy 800HT, the level of transfer, mostly from Incoloy 800HT to Nimonic 80A, was observed to increase with increasing sliding speed.;Further experimental studies concentrating on the sliding of Nimonic 80A versus Stellite 6 at 0.314 m.s-1 and 750°C, indicated extremely rapid formation of glaze from Stellite 6-sourced debris -- this consisted of an initial transfer of material from the harder Stellite 6 to the softer Nimonic 80A, followed by the steady development of a wear resistant glaze layer. The reversal of sample and counterface whilst varying sliding speed demonstrated that direction of transfer was more strongly influenced by material than configuration (i.e. which material was sample and which material was counterface). Finally, the substitution of Nimonic 80A with high purity nickel promoted the formation of glaze at not just 0.314 m.s-1, but also at 0.905 m.s-1 -- this was due to the elimination of chromium oxide (in the form of Cr2O3) from the predominantly nickel oxide (NiO) debris. This result, however, raises a number of queries yet to be answered. Firstly, why were nickel and chromium together readily able to form an oxide glaze with Nimonic 80A worn against Incoloy 800HT, but not so readily with Nimonic 80A worn against Stellite 6? Secondly, why did chromium readily form an oxide glaze with cobalt at 0.314 m.s-1 with the Nimonic 80A versus Stellite 6 combination, but not so readily with nickel at higher sliding speed?;Finally, nano-characterisation studies were carried out on the glaze layers formed on Nimonic 80A samples slid against Stellite 6 at 0.314 m.s -1 and 750°C. These glaze layers were shown to have a nano-scale grain structure, with a grain size of as little as 5 to 15 nm at the very surface of the glaze. A likely route of formation was established, starting with deformation of the surface, intermixing of debris from sample and counterface, oxidation of debris, further mixing and repeated welding and fracture -- these processes are aided by high temperature oxidation and diffusion. The grain size is then refined by the formation of sub-grains, accompanied by increasing mis-orientation to give nano-structured grains - a non-equilibrium state results, with poorly defined and irregular grain boundaries. The presence of a nano-polycrystalline structure implies improved fracture toughness. However, the disorganised nature of the glaze layer suggests the production of a glaze is, overall, an inefficient process. (Abstract shortened by UMI.)...