Frank Kasper phases

Unit cell of the A15 phases of Nb3Sn
Unit cell of Laves phase with MgZn2 structure (Mg atoms are green).

Frank-Kasper (FK) phases or topologically close-packed phases are one of the largest groups of intermetallic compounds, known for their complex crystallographic structure and physical properties. Owing to their combination of periodic and aperiodic structure, FK phases belong to the class of quasicrystals. Applications of FK phases as high-temperature structural and superconducting materials have been highlighted; however, they have not yet been sufficiently investigated for details of their physical properties. Also, their complex and often non-stoichiometric structure makes them good subjects for theoretical calculations.

History

In 1958, Frank and Kasper, in their original work investigating many complex alloy structures, showed that non-icosahedral environments form an open-end network which they called the major skeleton, and is now identified as the declination locus. They came up with the methodology to pack asymmetric icosahedra into crystals using other polyhedra with larger coordination number and atoms. These coordination polyhedra were constructed to maintain topological close packing (TCP).[1]

Unit-cell geometries classification

Based on the tetrahedral units, FK crystallographic structures are classified into low and high polyhedral groups denoted by their coordination numbers (CN) referring to the number of atom centering the polyhedron. Some atoms have an icosahedral structure with low coordination, labeled CN12. Some others have higher coordination numbers of 14, 15 and 16, labeled CN14, CN15 and CN16, respectively. These atoms with higher coordination numbers form uninterrupted networks connected along the directions where the five-fold icosahedral symmetry is replaced by six-fold local symmetry.[2]

Classic FK phases

The most common members of a FK-phases family are: A15, Laves phases, σ, μ, M, P, and R. A15 phases are intermetallic alloys with an average coordination number (ACN) of 13.5 and eight A3B stoichiometry atoms per unit cell. Where two B atoms are surrounded by CN12 polyhedral (icosahedra), and six A atoms are surrounded by CN14 polyhedral. Nb3Ge is a superconductor with A15 structure. Laves phases are intermetallic compounds composed of CN12 and CN16 polyhedrons with AB2 stoichiometry, commonly seen in binary metal systems like MgZn2. Due to the small Solubility of AB2 structures, Laves phases are almost line compounds.

The sigma (σ) phase is an AB stoichiometric intermetallic compound formed at the electron/atom ratio range of 6.2 to 7. CrFe is a typical alloy crystallizing in the σ phase at the equiatomic composition. With physical properties adjustable based on its structural components, or its chemical composition provided a given structure. The μ phase has an ideal A6B7 stoichiometry, with its prototype W6Fe7, containing rhombohedra cell with 13 atoms. While many other Frank Kasper alloy types have been identified, more continue to be found. The alloy Nb10Ni9Al3 is the prototype for the M phase. It has orthorhombic space group with 52 atoms per unit cell. The alloy Cr9Mo21Ni20 is the prototype for the P-phase. It has a primitive orthorhombic cell with 56 atoms. The alloy Co5Cr2Mo3 is the prototype for the R-phase which belongs to the rhombohedral space group with 53 atoms per cell.[3][4]

Applications

FK phase materials have been pointed out for their high-temperature structure and as superconducting materials. Their complex and often non-stoichiometric structure makes them good subjects for theoretical calculations. A15, Laves and σ are the most applicable FK structures with interesting fundamental properties.The A15 compounds are forming important intermetallic superconductor with major applications in materials used in wires for superconducting such as: Nb3Sn, Nb3Zr and Nb3Ti. A majority of superconducting magnets are constructed out of Nb3Ti alloy.[5] Small extents of σ phase considerably decreases the flexibility and impairment in erosion resistance. While addition of refractory elements like W, Mo or Re to FK phases helps to enhance the thermal properties in such alloys as steels or nickel-based superalloys, it increases the risk of unwanted precipitation in intermetallic compounds.[6]

References

  1. ↑ Joubert, J. M.; Crivello, J. C. (2012). "Non-Stoichiometry and Calphad Modeling of Frank-Kasper Phases". Applied Sciences 2 (4): 669. doi:10.3390/app2030669.
  2. ↑ Berne, C.; Sluiter, M.; Pasturel, A. (2002). "Theoretical approach of phase selection in refractory metals and alloys". Journal of Alloys and Compounds 334: 27. doi:10.1016/S0925-8388(01)01773-X.
  3. ↑ Graef, M.D.; Henry, M.E. (2007) Structure of materials, An introduction to crystallography, diffraction and symmetry. Cambridge University Press. ISBN 1107005876. pp. 518–536
  4. ↑ Frank, F. C.; Kasper, J. S. (1958). "Complex alloy structures regarded as sphere packings. I. Definitions and basic principles". Acta Crystallographica 11 (3): 184. doi:10.1107/S0365110X58000487.
  5. ↑ Sadoc, J.F.; Mosseri, R. (1999) Geometrical Frustration. Cambridge University Press. ISBN 9780511599934. pp. 159–162
  6. ↑ Crivello, J. C.; Breidi, A; Joubert, J. M. (2013). "Χ and σ phases in binary rhenium-transition metal systems: A systematic first-principles investigation". Inorganic Chemistry 52 (7): 3674–86. doi:10.1021/ic302142w. PMID 23477863.
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