Abstract:Al-Cu-Co single quasicrystals were studied by the reflective X-ray topography. It was found that on the surfaces of the single quasicrystals, which were parallel to (00001) decagonal plane, the contrast associated with screw dislocation occurs. In the topograms taken from other surfaces of the single quasicrystals the bands of contrast appear. This contrast comes from the antiphase domains and depends on the conditions of the single quasicrystals growth process.
“…To explain these trends, higher order kinetics deserves consideration since the degree of supersaturation is nearly uniform around the QC. According to a study 61 of an Al-Cu-Co single decagonal quasicrystal by X-ray topography, contrast associated with a screw dislocation appears in the {00001} plane. This suggests that growth along <00001> occurs via second order kinetics wherein the interfacial velocity is related to the square of the driving force (i.e., equation ( 2 ) with n = 2).…”
How does a quasicrystal grow? Despite the decades of research that have been dedicated to this area of study, it remains one of the fundamental puzzles in the field of crystal growth. Although there has been no lack of theoretical studies on quasicrystal growth, there have been very few experimental investigations with which to test their various hypotheses. In particular, evidence of the in situ and three-dimensional (3D) growth of a quasicrystal from a parent liquid phase is lacking. To fill-in-the-gaps in our understanding of the solidification and melting pathways of quasicrystals, we performed synchrotron-based X-ray imaging experiments on a decagonal phase with composition of Al-15at%Ni-15at%Co. High-flux X-ray tomography enabled us to observe both growth and melting morphologies of the 3D quasicrystal at temperature. We determined that there is no time-reversal symmetry upon growth and melting of the decagonal quasicrystal. While quasicrystal growth is predominantly dominated by the attachment kinetics of atomic clusters in the liquid phase, melting is instead barrier-less and limited by buoyancy-driven convection. These experimental results provide the much-needed benchmark data that can be used to validate simulations of phase transformations involving this unique phase of matter.
“…To explain these trends, higher order kinetics deserves consideration since the degree of supersaturation is nearly uniform around the QC. According to a study 61 of an Al-Cu-Co single decagonal quasicrystal by X-ray topography, contrast associated with a screw dislocation appears in the {00001} plane. This suggests that growth along <00001> occurs via second order kinetics wherein the interfacial velocity is related to the square of the driving force (i.e., equation ( 2 ) with n = 2).…”
How does a quasicrystal grow? Despite the decades of research that have been dedicated to this area of study, it remains one of the fundamental puzzles in the field of crystal growth. Although there has been no lack of theoretical studies on quasicrystal growth, there have been very few experimental investigations with which to test their various hypotheses. In particular, evidence of the in situ and three-dimensional (3D) growth of a quasicrystal from a parent liquid phase is lacking. To fill-in-the-gaps in our understanding of the solidification and melting pathways of quasicrystals, we performed synchrotron-based X-ray imaging experiments on a decagonal phase with composition of Al-15at%Ni-15at%Co. High-flux X-ray tomography enabled us to observe both growth and melting morphologies of the 3D quasicrystal at temperature. We determined that there is no time-reversal symmetry upon growth and melting of the decagonal quasicrystal. While quasicrystal growth is predominantly dominated by the attachment kinetics of atomic clusters in the liquid phase, melting is instead barrier-less and limited by buoyancy-driven convection. These experimental results provide the much-needed benchmark data that can be used to validate simulations of phase transformations involving this unique phase of matter.
“…For this five-indices labeling of the diffraction reflections is often used (see e.g. [1,2,16,18,21]), four indices being related to a plain quasilattice and the fifth one being referred to the direction of periodicity. Six-indices labeling of the diffraction reflections of the decagonal quasicrystals was used by [15,22].…”
Modelling of lattices of two-diMensional Quasi-crystals We propose the method for modelling of quasi-periodic structures based on an algorithm being a geometrical interpretation of the Fibonacci-type numerical sequences. The modelling consists in a recurrent multiplication of basis groups of the sites, which possess the 10-th, 8-th or 12-th order rotational symmetry. The advantage of the proposed method consists in an ability to operate with only two-dimensional space coordinates rather than with hypothetical spaces of dimension more than three. The correspondence between the method of projection of quasi-periodic lattices and the method of recurrent multiplication of basis-site groups is shown. As established, the six-dimensional reciprocal lattice for decagonal quasi-crystals can be obtained from orthogonal six-dimensional lattice for icosahedral quasi-crystals by changing the scale along one of the basis vectors and prohibiting the projection of sites, for which the sum of five indices (corresponding to other basis vectors) is not equal to zero. It is shown the sufficiency of using only three indices for describing diffraction patterns from quasi-crystals with 10-th, 8-th and 12-th order symmetry axes. original algorithm enables direct obtaining of information about intensity of diffraction reflexes from the quantity of self-overlaps of sites in course of construction of reciprocal lattices of quasi-crystals.
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