Past exam of the materials science course of the University of Cambridge / 2017 / Paper 1 / 7

A heat engine must reject some absorbed heat to a colder reservoir. For heat addition and rejection at absolute temperatures $T_h$ and $T_c$, the Carnot bound isAt fixed $T_c$, increasing $T_h$ increases this upper limit and can increase useful specific work in an appropriately designed gas-turbine cycle. Thus a higher hot-side temperature permits more efficient conversion of heat to work, rather than merely heating the exhaust. Real combustion occurs over a temperature range, and actual efficiency also depends on pressure ratio, losses and cycle design: peak temperature alone does not determine it. The materials incentive is to sustain higher turbine inlet temperatures while maintaining strength, oxidation resistance and acceptable creep life.

At turbine operating temperatures, grain boundaries provide paths for rapid diffusion, grain-boundary sliding and cavity formation, encouraging creep rupture. A single-crystal turbine blade removes these boundaries, especially boundaries unfavourably oriented across the tensile load. It retains dislocations and can still creep; eliminating boundaries is useful in this high-temperature regime even though fine crystal grains can strengthen other materials at lower temperatures.

Use directional solidification of the cast alloy through a controlled thermal gradient. A suitably oriented seed or a narrow grain selector lets one crystal survive and grow into the blade mould while suppressing competing nucleation. A spiral selector is a common way to exclude competing crystal grains. The blade is generally oriented near a $⟨001⟩$ axis for the intended anisotropic properties. crystal grain selection is experimentally verified by orientation mapping, rather than assuming a directionally elongated casting is automatically a single crystal.^[ref]

The nickel-rich $\gamma$ matrix is a disordered substitutional solid solution on a face-centered cubic lattice. The ordered ${\gamma }^{\prime }$ phase has the L12 structure, approximately $\mathrm{N}{\mathrm{i}}_3\mathrm{Al}$: aluminium occupies cube corners and nickel occupies face centres. Its occupied-site geometry is often called ordered FCC, but its chemically labelled Bravais lattice is primitive cubic, with a four-atom basis. A face-centre translation exchanges chemical sublattices and is not a symmetry of the ordered crystal.

Each Al atom has twelve nearest-neighbour Ni atoms at Euclidean distance $a/\sqrt{2}$. Each Ni atom has twelve nearest neighbours too, but these are four Al and eight Ni. The chemical distinction matters for slip. In disordered $\gamma$, the shortest perfect Burgers vector isFor the ordered primitive cubic translation lattice, the shortest order-preserving perfect vector isThis does not imply that $⟨100⟩$ slip must dominate. A vector must lie in a favourable glide plane and have an accessible core structure and activation stress. Matrix dislocations commonly glide on $\{111\}⟨110⟩$ systems. A single $a⟨110⟩/2$ passage through ${\gamma }^{\prime }$ leaves an antiphase boundary; a second matching passage restores order, giving total vector $a⟨110⟩$. Such a superdislocation has a longer total vector than $a⟨100⟩$, yet its constituent dislocations can move on the favourable close-packed planes and interact with the matrix. Paired motion balances line and antiphase-boundary energies, so the shortest abstract lattice translation alone does not select the active slip system.^[ref]

The main strengthening architecture is a high volume fraction of fine, thermally stable ordered gamma prime phase precipitates in the ductile nickel-rich matrix. Their nearly matching crystal parameters allow coherent crystal interfaces, but coherence does not make them transparent to a moving dislocation: cutting disrupts chemical order and costs antiphase-boundary energy. Pairing of cutting dislocations and their interactions with narrow matrix channels raise the stress needed for deformation. For particles that are bypassed, bowing and high-temperature climb are also impeded by the precipitate spacing and interface dislocation structures.

coherency strain and differences in elastic response provide additional obstacles. Refractory substitutional solutes contribute solid-solution strengthening and can slow diffusion-controlled deformation. Single-crystal manufacture suppresses grain-boundary creep and grain-boundary cavitation. Together these mechanisms permit useful strength at temperatures where an unstrengthened nickel matrix would deform much faster. Protective oxide scales and coatings preserve load-bearing material against environmental attack; they complement, rather than replace, the internal strengthening mechanisms.

A concrete microscopic observation is the paired dislocation loops around fine precipitates in the Cambridge C263 creep micrograph: the observed defect structure supports the importance of precipitate–dislocation interactions, though one image does not by itself separate every strengthening contribution.^[ref] In-situ diffraction during stress-jump tests of a rafted AM1 single crystal also resolves evolving load partition and deformation in matrix channels, demonstrating why channel width and interface interactions matter.^[ref] Long exposure can coarsen or change the precipitate morphology and alter channel widths, so high strength is conditional on temperature, time and microstructural stability.