A superalloy, or high-performance alloy, is an
alloythat exhibits excellent mechanical strength and creep resistance at high temperatures, good surface stability, and corrosion and oxidation resistance. Superalloys typically have an austenitic face-centered cubiccrystal structure. A superalloy's base alloying element is usually nickel, cobalt, or nickel- iron. Superalloy development has relied heavily on both chemical and process innovations and has been driven primarily by the aerospace and power industries. Typical applications are in the aerospace, industrial gas turbine and marine turbine industry, e.g. for turbineblades for hot sections of jet engines.
Examples of superalloys are
Hastelloy, Inconel, Waspaloy, Rene alloys (e.g. Rene 41, Rene 80, Rene 95), Haynes alloys, Incoloy, MP98T, TMS alloys, and CMSX single crystal alloys.
metallic materials for service at high temperatures, particularly in the hot zones of gas turbines. Such materials allow the turbine to operate more efficiently by withstanding higher temperatures. Turbine Inlet Temperature (TIT), which is a direct indicator of the efficiency of a gas turbine engine, depends on the temperature capability of 1st stage high pressure turbine blade made of Ni base superalloys exclusively.
One of the most important superalloy properties is high temperature creep resistance. Other crucial material properties are fatigue life, phase stability, as well as
Superalloys develop high temperature strength through
solid solution strengthening. Oxidation and corrosion resistance is provided by the formation of a protective oxide layer which is formed when the metal is exposed to oxygen and encapsulates the material, and thus protecting the rest of the component. Oxidation or corrosion resistance is provided by elements such as aluminiumand chromium. By far the most important strengthening mechanism is through the formation of secondary phase precipitates such as gamma prime and carbides through precipitation strengthening.
Creep resistance is dependent on slowing the speed of
dislocations within the crystal structure. The gamma prime phase [Ni3(Al,Ti)] present in nickel and nickel-iron superalloys presents a barrier to dislocations. Chemical additions such as aluminum and titaniumpromote the creation of the gamma prime phase. The gamma prime phase size can be precisely controlled by careful precipitation hardening heat treatments. Cobalt base superalloys do not have a strengthening secondary phase like gamma prime. Many other elements, both common and exotic, (including not only metals, but also metalloids and nonmetals) can be present; chromium, cobalt, molybdenum, tungsten, tantalum, aluminium, titanium, zirconium, niobium, rhenium, carbon, boronor hafniumare just a few examples.
The historical developments in superalloy processing have brought about considerable increases in superalloy operating temperatures. Superalloys were originally iron based and cold wrought prior to the 1940s. In the 1940s
investment castingof cobalt base alloys significantly raised operating temperatures. The development of vacuum melting in the 1950s allowed for very fine control of the chemical composition of superalloys and reduction in contamination and in turn led to a revolution in processing techniques such as directional solidificationof alloys and single crystal superalloys.
Single-crystal superalloys (SC superalloys) are formed as a
single crystalusing a modified version of the directional solidification technique, so there are no grain boundaries in the material. The mechanical properties of most other alloys depend on the presence of grain boundaries, but at high temperatures, they would participate in creep and must be replaced by other mechanisms. In many such alloys, islands of an ordered intermetallic phase sit in a matrix of disordered phase, all with the same crystalline lattice. This approximates the dislocation-pinning behavior of grain boundaries, without introducing any amorphous solidinto the structure.
Superalloys are used where there is a need for high temperature strength and corrosion/oxidation resistance.
The largest applications of superalloys are the following: aircraft and industrial
gas turbines; rocket engines; space vehicles; submarines; nuclear reactors; military electric motors, chemical processing vessels, and heat exchanger tubing.
Many of the industrial nickel-based superalloys contain alloying elements, including
chromium, aluminium, and titanium, also molybdenum, tungsten, niobium, tantalumand cobalt.
Metallurgy of superalloys
The superalloys of the first generation were intended for operation up to 700 °C (973 K). The up-to-date superalloys of the fourth generation are used as single or
Monocrystals and are extra alloyed, especially with ruthenium. They can operate up to 1100 °C (1373 K).
The structure of most precipitation strengthened nickel-base superalloys consists of the gamma matrix, and of intermetallic γ' precipitates. The γ-phase is a solid solution with a face-centered crystal lattice and randomly distributed different species of atoms.
By contrast, the γ'-phase has an ordered crystalline lattice of type L12. In pure Ni3Al phase
atomsof aluminium are placed at the vertices of the cubic cell and form the sublattice A. Atoms of nickel are located at centers of the faces and form the sublattice B. The phase is not strictly stoichiometric. There may exist an excess of vacancies in one of the sublattices, which leads to deviations from stoichiometry. Sublattices A and B of the γ'-phase can solute a considerable proportion of other elements. The alloying elements are dissolved in the γ-phase as well. The γ'-phase hardens the alloy through an unusual mechanism called the yield stressanomaly. Dislocations dissociate in the γ'-phase, leading to the formation of an anti-phase boundary. It turns out that at elevated temperature, the free energy associated with the anti-phase boundary (APB) is considerably reduced if it lies on a particular plane, which by coincidence is not a permitted slip plane. One set of partial dislocations bounding the APB cross-slips so that the APB lies on the low-energy plane, and, since this low-energy plane is not a permitted slip plane, the dissociated dislocation is now effectively locked. By this mechanism, the yield strength of γ'-phase Ni3Al actually "increases" with temperature up to about 1000 °C, giving superalloys their currently unrivalled high-temperature strength.
In addition, it is often beneficial for a grain boundary containing nickel-base alloy to contain carbides for improvements in creep strength. Where the carbides (e.g. MC where M is a metal and C is a carbon atom) are precipitated at the grain boundaries, they act to pin the grain boundaries and improve the resistance to sliding and migration that would occur during creep diffusion. However if they precipitate within a grain, or if they form as a continuous grain boundary film, the fracture toughness of the alloy is reduced, together with the ductility and rupture strength.
Coating of superalloys
Superalloy products that are subjected to high working temperatures and corrosive atmosphere (like first stages of
jet engine turbine blades) are coated with various kinds of coating. Mainly two kinds of coating process are applied: pack cementation process and gas phase coating. Both are a type of CVD. In most cases, after the coating process near-surface regions of parts are enriched with aluminium, the matrix of the coating being nickel aluminide.
Pack cementation process
The pack cementation process is carried out at lower temperatures, about 750°C). The parts are loaded into boxes that contain a mixture of powders: active coating material, containing
aluminium, activator( chlorideor fluoride), and thermal ballast, like aluminum oxide). At high temperatures the gaseous aluminium chloride (or fluoride) is transferred to the surface of the part and diffuses inside (mostly inward diffusion). After the end of the process the so-called "green coating" is produced, which is too thin and brittle for direct use. A subsequent diffusion heat treatment (several hours at temperatures about 1080°C) leads to further inward diffusion and formation of the desired coating.
Gas phase coating
This process is carried out at higher temperatures, about 1080°C. The coating material is usually loaded onto special trays without physical contact with the parts to be coated. The coating mixture contains active coating material and activator, but usually does not contain thermal ballast. As in the pack cementation process, the gaseous aluminium chloride (or fluoride) is transferred to the surface of the part. However, in this case the diffusion is outwards. This kind of coating also requires diffusion heat treatment.
uperalloys in the future
The availability of superalloys during past decades has led to a steady increase in the turbine entry temperatures and the trend is expected to continue.
Sandia National Laboratoriesis studying a new method for making superalloys, known as radiolysis. It introduces an entirely new area of research into creating alloys and superalloys through nanoparticlesynthesis. “This process holds promise as a universal method of nanoparticleformation. By developing our understanding of the basic material sciencebehind these nanoparticle formations, we’ll then be able to expand our research into other aspects of superalloys, like nickel-based alloys.” Tina Nenoff says.
* cite book
last = Sims
first = Chester T.
coauthors = Stolloff, Norman S., Hagel, William C.
title = Superalloys II: High Temperature Materials for Aerospace and Industrial Power
origdate = 1987
publisher = John Wiley & Sons
* [http://www.msm.cam.ac.uk/phase-trans/2003/nickel.html Extensive resource on Superalloys, Cambridge University]
* [http://www.sandia.gov/news/resources/releases/2007/nanopart.html Sandia news release on superalloys]
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