Frank–Kasper phases

Topologically close pack (TCP) phases, also known as Frank-Kasper (FK) 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, some TCP phases belong to the class of quasicrystals. Applications of TCP 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.

Unit cell of Laves phase with MgZn₂ structure (Mg atoms are green).

History

In 1958, Frederick C. Frank and John S. Kasper, in their original work investigating many complex alloy structures,^[1]^[2] 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 numbers. These coordination polyhedra were constructed to maintain topological close packing (TCP).^[3]

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.^[4] The sites of 12-coordination are called minor sites and those with more than 12-fold coordination are major sites.^[1]

Classic FK phases

The most common members of a FK-phases family are: A15, Laves phases, σ, μ, M, P, and R.

A15 phases

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

The three Laves phases are intermetallic compounds composed of CN12 and CN16 polyhedra 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, though sometimes they can have a wide homogeneity region.

σ, μ, M, P, and R phases

The sigma (σ) phase is an intermetallic compound known as the one without definite stoichiometric composition and formed at the electron/atom ratio range of 6.2 to 7. It has a primitive tetragonal unit cell with 30 atoms. 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 rhombohedral 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.^[5]^[1]

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 include important intermetallic superconductors such as: Nb₃Sn, Nb₃Al, and V₃Ga with applications including wires for high-field superconducting magnets.^[6] Nb₃Sn is also being investigated as a potential material for fabricating superconducting radio frequency cavities.

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.^[7]

References

^ ^a ^b ^c Frank, F. C.; Kasper, J. S. (1958-03-10). "Complex alloy structures regarded as sphere packings. I. Definitions and basic principles". Acta Crystallographica. 11 (3). International Union of Crystallography (IUCr): 184–190. doi:10.1107/s0365110x58000487. ISSN 0365-110X.
^ Frank, F. C.; Kasper, J. S. (1959-07-10). "Complex alloy structures regarded as sphere packings. II. Analysis and classification of representative structures". Acta Crystallographica. 12 (7). International Union of Crystallography (IUCr): 483–499. doi:10.1107/s0365110x59001499. ISSN 0365-110X.
^ 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.
^ Berne, C.; Sluiter, M.; Pasturel, A. (2002). "Theoretical approach of phase selection in refractory metals and alloys". Journal of Alloys and Compounds. 334 (1–2): 27–33. doi:10.1016/S0925-8388(01)01773-X.
^ 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
^ Stewart, G.R. (July 2015). "Superconductivity in the A15 structure". Physica C: Superconductivity and Its Applications. 514: 28–35. arXiv:1505.06393. doi:10.1016/j.physc.2015.02.013.
^ 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.

[FK_1958-1] Frank, F. C.; Kasper, J. S. (1958-03-10). "Complex alloy structures regarded as sphere packings. I. Definitions and basic principles". Acta Crystallographica. 11 (3). International Union of Crystallography (IUCr): 184–190. doi:10.1107/s0365110x58000487. ISSN 0365-110X.

[2] Frank, F. C.; Kasper, J. S. (1959-07-10). "Complex alloy structures regarded as sphere packings. II. Analysis and classification of representative structures". Acta Crystallographica. 12 (7). International Union of Crystallography (IUCr): 483–499. doi:10.1107/s0365110x59001499. ISSN 0365-110X.

[3] 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.

[4] Berne, C.; Sluiter, M.; Pasturel, A. (2002). "Theoretical approach of phase selection in refractory metals and alloys". Journal of Alloys and Compounds. 334 (1–2): 27–33. doi:10.1016/S0925-8388(01)01773-X.

[5] 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

[6] Stewart, G.R. (July 2015). "Superconductivity in the A15 structure". Physica C: Superconductivity and Its Applications. 514: 28–35. arXiv:1505.06393. doi:10.1016/j.physc.2015.02.013.

[7] 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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