A new first principles approach to calculate phonon spectra of disordered alloys

A new first principles approach to calculate phonon spectra of disordered alloys

Oscar Grånäs, Biswanath Dutta, Subhradip Ghosh and Biplab Sanyal Department of Physics and Astronomy, Uppsala University, Box-516, SE-75120 Uppsala, Sweden Department of Physics, Indian Institute of Technology Guwahati, Guwahati-781039,India biplab.sanyal@physics.uu.se
July 20, 2019

The lattice dynamics in substitutional disordered alloys with constituents having large size differences is driven by strong disorder in masses, inter-atomic force constants and local environments. In this letter, a new first-principles approach based on special quasi random structures and itinerant coherent potential approximation to compute the phonon spectra of such alloys is proposed and applied to NiPt alloy. The agreement between our results with the experiments is found to be much better than for previous models of disorder due to an accurate treatment of the interplay of inter-atomic forces among various pairs of chemical species. This new formalism serves as a potential solution to the longstanding problem of a proper microscopic understanding of lattice dynamical behavior of disordered alloys.

63.20.dk, 63.50.Gh, 71.20.Be
: J. Phys.: Condens. Matter

The energy dispersion of lattice waves in ordered intermetallics and disordered alloys has recently gained significant importance due to its role in stabilizing a particular structural phase by contributing towards the system’s entropy and in pinpointing the fundamental mechanism behind the behavior of materials, which are important in technological applications. Examples include the connection between martensitic transformations in shape-memory alloys and the anomalous behavior of their phonon spectra [1], anomalously low thermal-expansion coefficients in Fe-based Invar alloys and the unusual behavior of phonon frequencies under external pressure [2], and the dramatic alteration of relative stabilities of different precipitates in Al-Cu system due to vibrational entropy [3].

Theoretical investigation on lattice dynamics in disordered metallic alloys is one of the challenging areas in the state of the art materials science research. Most of the theoretical studies have been done on the alloy compounds although a wealth of neutron-scattering data is available for various disordered alloys with arbitrary compositions. The dearth of theoretical works is due to the lack of a suitable self-consistent, analytical methodology to carry out the averaging over the random configurations, taking into account the disorder due to the fluctuations in mass, force constant and local environment around an atom. The most widely used method is the single-site coherent potential approximation (SCPA) [4], which being a single-site theory, is unable to handle the non-local fluctuations. The recently developed itinerant coherent potential approximation (ICPA) [5], is a successful generalization of the SCPA in handling disordered alloys with large mass as well as force constant disorder. While the ICPA stands as a self-consistent, analytic, site-translational invariant tool for computing the phonon spectra in disordered alloys, a missing key component in establishing it as an accurate and reliable formalism, is its integration with a tractable structural model for positional disorder which can closely mimic the fluctuations in the inter-atomic force constants in a random alloy. Moreover, due to the presence of short-range order, the phonon spectra of such systems would be affected due to the dominant vibrations of unlike species pairs. Initially, attempts were made in the form of first-principles computation of inter-atomic force constants from selected ordered structures and use them in a random alloy environment [6, 7]. This is not a proper remedy as the force constants are not directly transferable across the environments [8, 9].

In this letter, we present a new first-principles based formalism to compute the lattice dynamics of substitutional disordered alloys which incorporates the effects of disorder in mass, force constant and environment. We demonstrate the formalism by computing the phonon dispersion spectra of NiPt alloy. This alloy is chosen as its constituents have large mass differences(Pt being 3 times heavier than Ni), large size differences ( 11) and large force constant differences (Pt-Pt force constants being 55 larger than the Ni-Ni ones) and thus significant effects of all three kinds of disorder on the lattice dynamics can be expected. Also, the neutron-scattering experiments [10] show anomalous features in the dispersion curves in the form of resonance modes and splitting of dispersion branches. In previous works, neither SCPA [10] nor ICPA [5] with empirical set of force constants could have good quantitative agreement with the experiments, signifying that the inter-atomic interactions have not been modeled accurately.

Our formalism has three important steps: first we generate a structural model of substitutional disorder by special quasirandom structure (SQS) method, then the averaging of the force constant tensor is done to recover the original symmetry of the solid solution followed by the ICPA for performing the averaging over configurations.

(i) Structural model: First principles supercell calculations of disordered alloys involve the direct averaging of the properties obtained from a number of disordered configurations of the alloy. Current computational capabilities limit the size of the supercell necessary to describe each configuration, as well as the number of configurations sampled. Zunger et. al. developed a computationally tractable approach to model the disorder through the introduction of SQS method [11], an -atom per cell periodic structure designed so that their distinct correlation functions best match the ensemble-averaged correlation-functions of the random alloy. Here corresponds to the figure defined by the number of of atoms located on its vertices (=2, 3, 4…. are pairs, triangles, tetrahedra etc.) with being the order of neighbor distances separating them (=1, 2….are first,second neighbors etc.). As the properties like the equilibrium volume, local density of states and bond lengths around an atom are influenced by the local environment, SQS forms an adequate approximation. The biggest advantage of the SQS over a conventional supercell to model positional disorder is that the former uses the knowledge of the pair-correlation functions, a key property of the random alloys, to decide the positions of the atoms in the unit cell, instead of inserting them randomly as is done in the conventional supercell technique, and thus is guaranteed to provide a better description of the environments in an actual random alloy.

(ii) Averaging procedure: The force constant tensors between a given pair of atoms calculated using the SQS will have nontrivial off-diagonal elements due to low symmetry. Moreover, due to the atomic relaxations in a local environment, a distribution of bond distances for a pair of species gives rise to a distribution in their force constants. To extract the force constant tensors having the symmetry of the underlying crystal structure of the disordered alloy, we average the calculated SQS force-constant matrices for a particular set of displacements of the atoms from their ideal positions in the lattice, related by symmetry that will transform the force constant matrices to one displaying the symmetry of the underlying crystal structure. These averaged force-constant tensors are then used as the inputs to the ICPA for the calculation of the configuration-averaged quantities. Below, we demonstrate the idea for a FCC lattice.

In a FCC lattice, the distances between a given atom and its 12 nearest neighbors are specified by the vectors , and ; being the lattice parameter. The force constant matrix for two atoms separated by the vector is of the form

The other nearest neighbor force constant matrices are of the same form and are related by point group operations. However, when the atoms are allowed to relax, the vector separating a pair of nearest neighbor atoms are modified to and the matrix of force constants corresponding to a given pair of atoms reflects the loss of symmetry, taking the general form


For a particular set of , and , one needs to perform the averaging such that we obtain the following force constant matrix:


To achieve this, one needs to pick up the relevant ones out of the symmetry operations corresponding to the cubic group which transform the force constant matrices to one displaying the symmetry of the FCC structure. To elaborate on this, we provide the following example:

Suppose, two atoms are separated by the separation vector . The force constant matrix obtained from first-principles calculations on the SQS is given by Eq. 1. To recover the symmetry of the FCC force constants, we need to find out the transformations that transform the separation vector to a new separation vector and . These transformations, in this particular case, mimic the nearest neighbor separation for the unrelaxed FCC lattice. They are:


Corresponding to each of these transformation, there is a transformation matrix . We transform the SQS force-constant matrix to the FCC force-constant matrix by performing the operation in each of the 4 cases and then adding them. This simple procedure produces , and . All other off-diagonal elements vanish due to this symmetrization and the FCC symmetry is recovered. This procedure is repeated for all pairs of force constants and an arithmetic average is finally computed.

(iii)The ICPA: The ICPA is a Green’s function based formalism that generalizes the SCPA by considering scattering from more than one site embedded in an effective medium within which the effect of this correlated disorder is built in. The medium is constructed in a self-consistent way so that site translational invariance and analyticity of the Green’s function are ensured. The analyticity of the Green’s function is ensured by using the principles of the traveling cluster approximation [12] which showed that once there are non-diagonal terms in the Green’s function, the self-energy must include itineration of the scatterer through the sample to preserve analyticity. This means that the physical observables would be site translationally invariant. This required translational invariance is ensured by expressing the operators associated with the physical observables in an extended Hilbert space which accounts for the statistical fluctuations in site occupancies due to disorder.

We employ first-principles plane wave projector augmented wave method within generalized gradient approximation (GGA) [13] as implemented in the VASP code [14] for the calculation of the Hellman-Feynman forces on the atoms in a 64-atom SQS cell (4x4x4 supercell of the primitive fcc unit cell) with the optimized lattice parameter of 3.93 Å. Our value of the lattice parameter is slightly larger than the experimental value of 3.78 Ådue to the use of GGA. The SQS generated structure has zero short range order in the first four neighboring shells indicating a homogeneous disorder. The cut-off energy for the electronic wave functions is 400 eV. 432 k-points were used in the irreducible Brillouin zone for the calculations of the force constant matrix. We have tested the convergence of our results with respect to the relevant parameters and have concluded that our choice yields quite accurate results. To obtain the force-constant matrix, first, the equilibrium geometry is obtained by relaxing the atomic positions in the SQS cell until the forces converged to 10 eV/Å. Then each atom in the SQS cell is moved by 0.01 Å from the equilibrium position along three cartesian axes and forces on the atoms are calculated. Due to the lack of any symmetry in the SQS cell, 64 different force constant matrices were generated by using the PHON code [15]. The symmetry averaging procedure is then used to obtain an effective 3x3 force constant matrix to be used in ICPA calculation. In ICPA, the disorder is considered in the nearest-neighbor shell only as the further neighbor force constants have one order of magnitude less. The ICPA calculations are done with a -mesh and 1000 energy points.

Figure 1: (Color online) Dispersion of bond distances for three pairs of atoms computed by the SQS.

In Fig. 1, the variations of the number of nearest neighbors of a given type are plotted as a function of the bond distances. It is observed that the inter-atomic bond distances depend sensitively on the number of unlike atoms, which clearly proves the dependence of the bond distances on local environments. As a result of this, the inter-atomic force constants too undergo variations. The calculated average Ni-Ni (), Ni-Pt () and Pt-Pt () bond distances are 2.64 Å, 2.66 Å and 2.73 Å respectively, indicating a significant dispersion among the three pairs of bonds. A comparison to the unrelaxed alloy bond distances reveal that the relaxed remains the same, is less than smaller and is larger. The force constants for three different models of disorder, viz., SQS-averaged, empirical [5] and SCPA are presented in Table 1. In Ref. [5], it was argued that the Ni-Ni bonds in the alloy are softer compared to those in pure Ni, the Pt-Pt bonds are stiffer compared to those in pure Pt and Ni-Pt bonds are even softer than the Ni-Ni ones because the Ni-Pt bond distances were thought to be the largest. A comparison between the force constants obtained by the SQS-averaged and by this empirical scheme shows that the Ni-Ni force constants computed by the SQS-averaging scheme are softer, the Ni-Pt and the Pt-Pt force constants are and harder on an average. More importantly, the Ni-Pt force constants computed by the SQS-averaging scheme are harder than the Ni-Ni ones, a result in contradiction with the empirical scheme. This difference occurs due to the proper inclusion of environmental disorder in our case. in the alloy as computed by the SQS are about larger than that in pure Ni and thus these bonds suffer most severe dilution in strength, reduces by about compared to that in pure Pt and thus they are harder by about only compared to those in pure Pt. Inspite of nearly same bond distances, the Ni-Pt bonds computed by the SQS are stiffer than the Ni-Ni bonds, due to the following reasons: in case of the Ni-Pt pairs, the Ni atoms find much larger Pt atoms as their nearest neighbors, roughly with the same available space as they get in case of Ni-Ni pairs. As a result, the smaller Ni atoms try to accommodate bigger Pt atoms within the same volume as that available for Ni-Ni pairs, resulting in a hardening of Ni-Pt nearest neighbor interactions compared to the Ni-Ni ones.

  • Pair SQS SCPA Empirical
    Ni-Ni -8231 -19365 -15587
    Ni-Pt -17868 -13855
    Pt-Pt -33494 -28993
    Ni-Ni 525 3255 436
    Ni-Pt 2820 348
    Pt-Pt 6854 7040
    Ni-Ni -9580 -22679 -19100
    Ni-Pt -20740 -15280
    Pt-Pt -39655 -30317
Table 1: Real-space nearest neighbor force constants (in dyn cm) for NiPt obtained by averaging the SQS force constants, the force constant matrix used for SCPA calculations and the empirical force constants [5]. The last column indicates the cartesian components of .
Figure 2: (Color online) Phonon dispersion in NiPt alloy computed by SQS-ICPA (solid line), SCPA(dotted line) and empirical-ICPA [5](red diamonds). The circles indicate the experimental results. The shaded regions indicate the disorder-induced widths calculated by the SQS-ICPA.

In Fig. 2, we present the phonon dispersion curves of NiPt alloy computed using force constants obtained by three models of disorder. The configuration averaging in case of the SQS and the empirical scheme are done by the ICPA. SQS-ICPA shows the best agreement with the experiments as compared to the SCPA and the empirical-ICPA [5].The disorder-induced widths computed by the SQS-ICPA method (the shaded region in Fig. 2) also agree reasonably well with the experiments. The comparisons with the experiments were possible only for the direction because experimental results were not available for other directions. A closer look at Fig. 2 reveals that for the low-frequency branches, the empirical-ICPA and the SQS-ICPA methods are in close agreement while there are significant differences for the high frequency branches. The mass-disorder treated in SCPA, on the other hand, fails to reproduce the experimental features of the dispersion relations both qualitatively and quantitatively. The frequencies of the high frequency branches (both transverse and longitudinal) computed by the SCPA are severely overestimated while the lower frequency branches extend all the way to the zone boundary, thus displaying a split-band behavior in the phonon dispersions which is not observed experimentally.

All these observations can be understood in terms of the inter-atomic force constants (shown in Table I) which are influenced by the fluctuations in the local environments. In the SCPA, the fluctuations in the force constants are completely neglected and hence Ni-Ni, Ni-Pt and Pt-Pt all have the same force constants. In earlier studies [10, 5], the force constants used in the SCPA were those of pure Ni ones obtained experimentally [16]. In this study we have used a more realistic set of force constants for the SCPA calculations which are where are the cartesian directions and is the concentration of Ni. are the SQS-averaged force constants where denote atomic species. Such a choice of force constants has been used to incorporate, in an average way, the effects of alloy environment. The results, nevertheless, suggest that unless the fluctuations in the force constants are incoporated, the results do not even agree qualitatively with the measurements. The frequencies of the upper (lower) branches of longitudinal and transverse modes computed by SCPA are too high (low) as compared to the experiments. Ni-Ni vibrations dominate the higher frequency branches and the average force constants being too high pushes the frequencies away from the ones measured by neutron-scattering while the lower frequency branches being solely due to the Pt-Pt vibrations have lower frequencies due to the underestimation of the Pt-Pt force constants. The empirical-ICPA results on the other hand agree qualitatively with the experiments because there is no split-band like behavior as was seen in the SCPA. This is due to the consideration of the Ni-Pt correlated vibrations which renormalize the spectral weights associated with the contributions from Ni-Ni and Pt-Pt pairs [5]. Moreover, the splitting of the vibrational branches found experimentally around as a signature of the existence of resonance mode, is reproduced and the frequencies of the high-frequency branches are better as compared to the SCPA. The Ni-Ni(Pt-Pt) force constants shown in Table I in the empirical model are softer(harder) as compared to the SCPA ones explaining the reason for better agreement of the phonon frequencies computed by the empirical-ICPA model with the experimental results. However, the overestimation(underestimation) of the Ni-Ni(Pt-Pt) interactions and an incorrect qualitative estimation of the Ni-Pt interactions as compared to the Ni-Ni ones gives rise to significant discrepancies for the high-frequency longitudinal and optical branches. With SQS-ICPA, one can have a much better quantitative agreement between theory and experiments as seen in Fig. 2. The high-frequency branches for both longitudinal and transverse vibrations computed by the SQS-ICPA method agree substantially with the experimental results. The normal mode frequencies for these branches are dominated by the vibrations of the Ni pairs and thus a softening of the Ni-Ni bonds as computed by the SQS pushes the frequencies downwards compared to the empirical model making a better agreement with the experiments. Similarly, the relaxations of the Pt atoms result in the stiffening of the Pt-Pt bonds, thus pushing the frequencies slightly upwards. However, the high-frequency transverse branch computed by the SQS-ICPA model is still overestimated. In the neutron-scattering measurements [10], there were some ambiguities in determining the peak positions of the line shapes for the high-frequency transverse modes and thus the experimental results for this branch had larger uncertainties. Given this fact, the agreement between the theory and the experiment can be considered to be fairly good.

In conclusion, we have developed a reliable first-principles based approach for the calculation of phonon spectra in substitutional disordered alloys to treat mass, force constant and environmental disorder on equal footing. We demonstrate in case of NiPt alloy, the importance of an accurate structural model of disorder taking into account the role of fluctuations in the local environment through atomic relaxations in interpreting the microscopic features of the lattice dynamics for this class of complex alloys. The accurate modeling of the environmental disorder made possible by the SQS paves the way for a reliable description of phonon spectra in alloys with short-range order where the force-constants between a pair of species is dominated by a particular configuration of the nearest neighbor environment around an atom. Our future aim is to calculate the thermodynamic quantities [17] to compare with the experiments. Finally, we conclude that a combination of reliable force constants obtained from ab-initio and ICPA as a self-consistent analytic method for configuration-averaging enables us to solve the longstanding problem of theoretical computation of lattice dynamics in disordered alloys.

BS acknowledges Göran Gustafssons Stiftelse and Swedish Research Council for financial support and SNIC-UPPMAX for granting computer time. BD acknowledges CSIR, India for financial support under the Grant-F. No. 09/731 (0049)/2007-EMR-I. Also, we acknowledge Prof. P. L. Leath, Prof. M. H. Cohen, Dr. J. B. Neaton and Dr. A. H. Antons for useful discussions.



  • [1] Bungaro C and Rabe K M 2003 Phys. Rev. B 68 134104.
  • [2] Noda Y and Endoh Y 1988 J. Phys. Soc. Jpn. 57 4225.
  • [3] Wolverton C and Ozolins V 2001 Phys. Rev. Lett. 86 5518.
  • [4] Taylor D W 1967 Phys. Rev. 156 1017.
  • [5] Ghosh S, Leath P L and Cohen M H 2002 Phys. Rev. B 66 214206.
  • [6] Ghosh S, Neaton J B, Antons A H and Cohen M H 2004 Phys. Rev. B 70 024206.
  • [7] Alam A, Ghosh S and Mookerjee A 2007Phys. Rev. B 75 134202.
  • [8] Sluiter M H F, Weinert M and Kawazoe Y 1999 Phys. Rev. B 59 4100.
  • [9] van de Walle A and Ceder G 2002 Rev. Mod. Phys. 74 11.
  • [10] Tsunoda Y, Kunitomi N, Wakabayashi N, Nicklow R M and Smith H G 1979 Phys. Rev. B 19 2876.
  • [11] Zunger A, Wei S -H, Ferreira L G and Bernard J E 1990 Phys. Rev. Lett. 65 353; Lu Z W, Wei S -H and Zunger A 1991 Phys. Rev. B 44 10470.
  • [12] Mills R and Ratanavararaksha P 1978 Phys. Rev. B 18 5291.
  • [13] Perdew J P, Burke K and Ernzerhof M 1996 Phys. Rev. Lett. 77 3865.
  • [14] Kresse G and Hafner J 1993 Phys. Rev. B 47 RC558; Kresse G and Furthmüller J 1996 Phys. Rev. B 54 11169.
  • [15] Alfé D 2009 Comp. Phys. Comm. 180 2622.
  • [16] Dutton D H 1972 Can. J. Phys. 50 2915.
  • [17] Grabowski B, Hickel T and Neugebauer J 2007 Phys. Rev. B 76 024309.
Comments 0
Request Comment
You are adding the first comment!
How to quickly get a good reply:
  • Give credit where it’s due by listing out the positive aspects of a paper before getting into which changes should be made.
  • Be specific in your critique, and provide supporting evidence with appropriate references to substantiate general statements.
  • Your comment should inspire ideas to flow and help the author improves the paper.

The better we are at sharing our knowledge with each other, the faster we move forward.
The feedback must be of minimum 40 characters and the title a minimum of 5 characters
Add comment
Loading ...
This is a comment super asjknd jkasnjk adsnkj
The feedback must be of minumum 40 characters
The feedback must be of minumum 40 characters

You are asking your first question!
How to quickly get a good answer:
  • Keep your question short and to the point
  • Check for grammar or spelling errors.
  • Phrase it like a question
Test description