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High-entropy alloys (HEAs) were presumed to have a configurational entropy ashigh as that of an ideally mixed solid solution (SS) of multiple elements innear-equal proportions. However, enthalpic interactions inevitably render suchchemically disordered SSs rare and metastable, except at very hightemperatures. Here we highlight a structural feature that sets theseconcentrated SSs apart from traditional solvent-solute ones: the HEAs possess awide variety of (local) chemical ordering (LCO). Our atomistic simulationsemploying an empirical interatomic potential for NiCoCr reveal that the LCO ofthe multi-principal-element SS changes conspicuously with alloy processingconditions, producing a wide range of generalized planar fault energy in termsof both its sample-average and spatial variation. We further demonstrate thatthe LCO heightens the ruggedness of the energy landscape and raises activationbarriers governing dislocation activities. This not only influences theselection of dislocation pathways in slip, faulting, twinning, and martensitictransformation, but also increases the lattice friction to dislocation motionvia a new mechanism of nanoscale segment detrapping that elevates themechanical strength. All these open a vast playground not accessible toground-state SSs or intermetallics, offering rich opportunities to tuneproperties.

Strengthening in multi-principal element alloys with local-chemical-order roughened dislocation pathways