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VOLUME 44, NUMBER 17 P H Y S I C A L R E V I E W L E T T E R S 28 APRIL 1980
Tunneling States in Metallic Glasses: A Structural Model
M. Banville Groupe de Recherches en Semiconducteurs et Dielectriques, Departement de Physique,
Universite de Sherbrooke, Sherbrooke, Quebec J1K2R1, Canada
and a(a) R. Harris^'
Physics Department, McGill University, Montreal, Quebec H3A2T8, Canada (Received 20 December 1979)
We analyze the metas table states for individual atoms within a computer-generated structural model of a metallic glass, and discover that their probability of occurrence is a strong function of the degree of relaxation of the model. We propose that the relaxation process simulates closely the annealing of metallic glasses below the glass transition temperature, so that the annealing process should reduce the magnitudes of the various low-temperature anomalies seen in these materials.
PACS numbers: 61.40.Df
The structure of metallic glasses has received considerable recent attention in the literature: A review is given by Car gill.1 In general, some variant of the dense random packing of atomic spheres gives a good account of the structure, reproducing, for example, the characteristic double peak at the next-nearest-neighbor distance in the radial distribution function (RDF) for glasses with only one type of metallic atom.1 In more particular amplications, however, it has been found that the simplest, unconstrained packings of hard spheres differ significantly from the structures of real glasses, and improvements have been achieved through two approaches. In the first of these2 it has been shown that "chemical" constraints can be very significant in those glasses which contain "glass formers" such as P, C, or Si. In the second case,3 '4 more re levant to the present paper, it has been shown that a structural relaxation to equilibrium under the influence of suitable interatomic forces can also materially improve the agreement with experimentally determined RDF's.
More recently, a variety of experimental r e sults have posed more detailed questions about the structure of metallic glasses. Recent low-temperature measurements of the specific heat,5
the thermal conductivity,5'6 and the dispersion6"8
and the attenuation8*9 of ultrasonic waves as well as the low-temperature resistivity anomaly10
have all received explanations in terms of "two-level systems" (TLS's) or "tunneling states" as sociated in some way with the structure. These explanations have all been motivated by the model proposed by Anderson, Halperin, and Varma11
and by Phillips12 to explain analogous phenomena in insulating glasses. In what follows, we pro
pose a mechanism for this model which is particular to metallic glasses, and which leads us to a new assessment of existing data.
In the original papers11 '12 the TLS's were modeled by double-well oscillators, having energy barr iers V between the two wells and an energy difference AE between the two minima. The atoms or groups of atoms represented by this moedl were thus able to tunnel from one well to the other. In order to explain the experimental data, it is necessary to postulate that there be a finite probability of finding both V and AE close to zero. Measurable quantities such as the specific heat, thermal conductivity, and ultrasonic response are then related to the probability density of TLS's having AE equal to zero, a quantity which has a value around 5x l0" 2 e V 1 atom"1 i r respective of the material studies. For the purpose of subsequent discussion, we note also that this value includes only those TLS's with barr i e r s low enough, V<VmaK> that tunneling can occur during the time of the experimental measurement.11
In the insulating glasses, the TLS's have been associated with structural features specific to the glassy state,13 but there is no universal agreement on their precise nature. In the absence of direct experimental evidence, a computer simulation of the structure of a covalently bonded glass was carried out by Smith14 in an attempt to identify possible TLS's. His results were encouraging, although with disappointing statistics in the physically interesting range of parameters. In the metallic glasses, however, there has until now been no attempt, either experimental or theoretical, to associate any particular structural features with the TLS's presumed to be present.
1136 © 1980 The American Physical Society
V O L U M E 44, N U M B E R 17 PHYSICAL REVIEW LETTERS 28 A P R I L 1980
In what follows, we report on our investigations of a computer-generated model which we relaxed to varying degrees suing a standard algorithm which allows each atom in turn to move down the potential energy gradient. Our chosen model comprised the central 1170 atoms of the 8000-atom structure of hard spheres of one size constructed by Bletry,15 and we used a Lennard-Jones potential V(r) =4e[(or/r)12 - (cr/r)6] to relax this structure from its original density (packing fraction) of 0.54.
We chose to estimate the range of appropriate values for € by comparing the activation energy for the diffusion of a three-dimensional t ransition metal atom in a body-centered cubic lattice (typically 0.5 to 5.0 eV) with the corresponding value calculated with our potential. In this way we assign € values in the range from 0.01 to 0.1 eV. Of course, strictly speaking, neither a Lennard-Jones interatomic potential nor the similar Morse potential gives a good description of metallic binding, although for computational reasons they have often been used in other simulation calculations.3 Nevertheless, the highest density achieved in our simulation (0.6320) compares favorably with that measured for a simple MgZn glass.4
Apart from the density, an essential feature of our model structure is the presence of voids, which are somewhat analogous to vacancies in a crystalline material, but which are scarcely large enough to accommodate an extra atom. Although we can make no quantitative comparison between the characteristics of the voids in our low-density model and those in a typical metallic glass, with density around 0.69,1 we believe that there is a qualitative relationship, since the measurement of atomic diffusion in metal-metalloid glasses16 '17 has been interpreted in terms of the "porous" nature of the structure.
The significance of the voids became apparent as , at various stages during the relaxation process , we searched for the simplest TLS's, corresponding to the motion of single atoms. We examined the environments of a limited number of atoms in the center of the model structure, using a detailed analysis of the numbers of common nearest neighbors possessed by pairs of atoms in the structure,18 which enabled us to identify those situations most likely to give rise to TLS's. In particular, we chose as prime candidates those atoms which were the only common neighbor of a given pair of atoms. In each case we then searched for alternate metastable minimum-
energy positions for the single atom in the force field of its neighbors, and, when successful, tabulated the relevant parameters. Detailed analysis revealed that all our TLS's were associated with the voids in the structure, with the tunneling motion consisting of a single atom moving between two or more alternate equilibrium positions within the void. Although we did not simultaneously take account of possible cooperative r e arrangements of the neighbors around the chosen single atom, we verified that such rearrangements were not significant in any interesting cases , in accord with the work of Gibbs19 who examined the stability of vacant sites in a relaxed structure.
Typical results of our analysis are given in Fig. 1, which shows the distribution of TLS parameters AE and V, as defined in the inset, after 325 relaxation steps per atoms, when the density had reached 0.6065. The axes are labeled in units of €, and also in units with c =0.1 eV, approximately representative of a real glass, as discussed earlier.
To estimate the probability density corresponding to the specific heat, we first evaluate the parameter V ^ following Ref. 11. Using a value of 100 a.u. for the mass of a tunneling atom we obtain Fmax^O.OS eV, a value which depends only weakly on the energy of zero-point motion. By projecting the calculated distribution of Fig. 1 onto the AE axis, using only points with V< Vmax,
20
V /units\ Vote )
12
1.0 cV
0 4 AE 8
(units of €)
1.0cV 12
FIG. 1. Probabi l i ty d is t r ibut ion of T I S ' s for the cen t ra l 300 atoms of the model s t r u c t u r e re laxed to densi ty 0.6065. The axes co r respond to the b a r r i e r height V and the energy difference AE, as shown in the inset , m e a s u r e d in units of the LJ e . The p r o b a bil i ty densi ty cor responding to the specific heat is a project ion onto the A E axis of points with V< V m a x
= 0.05.
1137
VOLUME 44, NUMBER 17 PHYSICAL REVIEW LETTERS 28 APRIL 1980
we obtain a histogram for the probability density, from which we can extract the value for AE =0 as required for the specific heat. The appropriate values are -0.02 states eV"1 atom"1 with £ = 0.1 eV and -1 .0 states eV"1 atom"1 with € =0.01 eV, so that, given the large statistical e r ro r s , there is qualitative agreement with the experimental data.
However, a much more significant feature of our results concerns our analysis of the structure when it is relaxed by a further 1520 steps per atom, to a density of 0.6320. At first sight, the changes in the structure, as monitored by the density or the radial distribution function (RDF), are only minor. However, as is clearly shown in Fig. 2, the probability density of TLS's in the interesting range of energies drops by almost an order of magnitude, a result which is consistent with our analyses of other "fully" relaxed structures,20 and which also explains the null result of a search for TLS's by Gibbs.19 This substantial reduction in the probability density might be r e garded as an artifact of our relaxation procedure were it not for considerable evidence that suggests a comparison of the structures of densities 0.61 and 0.63 with those of real metallic glasses before and after annealing below their glass transition temperatures.
Although it has been evident for some time3
that the relaxation procedure qualitatively improves agreement with experimentally determined radial distribution functions (RDF's), it was only recently that energy-dispersive x - r ay -diffraction (EDXD) techniques21 have explicitly demonstrated the changes in the RDF's during an-
/unitsN Uf e ;
12 i~
1.0<2V \~
c ; i : L i L ^
O 4 A ,_ 8 1.0«2V 12 AE
(units of e)
FIG. 2. Probability density of TLS's for the central 300 atoms of the model structure relaxed to density 0.6320. Notation is otherwise the same as in Fig. 1.
1138
nealing. Quite explicitly, the effect of annealing is to enhance the structures seen in the RDF's, or to cause a "transformation towards a more stable amorphous state." This, of course, is precisely the function of any relaxation procedure, and, indeed, our calculations of the RDF are in qualitative agreement with the EDXD data. If we further assume that the annealing is associated with the disappearance of the voids in the structure, an assumption which is consistent with the reduction of the diffusivity by two orders of magnitude upon annealing,17 then we can estimate the corresponding activation energy as £ 20e, which, with e taken as 0.1 eV, is in qualitative agreement with the data.21 '22
Further evidence that the effects of our relaxation actually correspond to the annealing of real glasses is also to be found in a published analysis of low-temperature thermal-conductivity data.6 In this paper it was shown that "mild heat treatment" actually increased the magnitude of the conductivity by some 45%: On the basis of the usual TLS model,11 '12 this was related to a reduction in the probability density of TLS's. Similar evidence relating to the low-temperature anomaly in the electrical resistivity10 can also be found,23 but there have been no published analyses of relevant specific-heat or ultrasonic data.
To summarize, we propose that the TLS's which exist in metallic glasses correspond to the motion of individual atoms within voids in the incompletely relaxed structure. We further propose that the effect of annealing is to eliminate the TLS's by the suppression of the voids, and thus to eliminate the characteristic anomalous properties of these materials which appear at low temperatures. A straightforward test of our ideas would thus be the reevaluation of the effect of annealing on such properties: We suggest that measurement of the dispersion of ultrasound before and after annealing would be very worthwhile. K correct, our ideas offer the prospect of a clearer understanding of the structure of metallic glasses and perhaps, of a resolution of some of the current theoretical problems.10
One of us (M.B.) is grateful to J. P. Gaspard for his hospitality during an extended visit to the University of Liege, for suggesting the configura-tional analysis,18 and for providing the coordinates of the partially relaxed structure of Bletry (Ref. 15). Thanks are also due to our colleagues for useful discussions.
This work was supported in part by the Natural Sciences and Engineering Research Council of
VOLUME 44, NUMBER 17 PHYSICAL REVIEW LETTERS 28 APRIL 1980
Canada (NSERC) and by the Formation de Cher-cheurs et Action Concertee (FCAC) program of the government of Quebec.
( aTo whom all correspondence should be addressed. 1G. S. Cargill, III, in Solid State Physics, edited by
H. Ehrenreich, F. Seitz, and D. Turnbull (Academic, New York, 1975), Vol. 30, p. 227.
2J. F. Sadoc, J. Dixmier, and A. Guinier, J. Non-Cryst. Solids JL2, 46 (1973).
3L. von Heimendahl, J. Phys. F 5, L147 (1975), and 9t 161 (1979); J. A. Barker, J. L. Finney, and M. R. Hoare, Nature (London) 257, 120 (1975); A. Rahman, M. J. Mandell, and J. P. McTague, J. Chem. Phys. 64, 1564 (1976).
4J. Hafner and L. von Heimendahl, Phys. Rev. Lett. 42, 386 (1979).
5J. E. Graebner, B. Golding, R. J. Schutz, F. S. L. Hsu, and H. S. Chen, Phys. Rev. Lett. £9, 1480 (1977).
6J. R. Matey and A. C. Anderson, J. Non-Cryst. Solids 23, 129 (1977), and Phys. Rev. B !L6, 3406 (1977).
7G. Bellessa, P. Doussineau, and A. Levelut, J. Phys. (Paris), Lett. 38, L65 (1977); G. Bellessa, J . Phys. C10, L285 (1977); G. Bellessa and O. Bethoux, Phys. Lett. 62A, 125 (1977).
8B. Golding, J. E. Graebner, A. B. Kane, and J. B. Black, Phys. Rev. Lett. 41, 1487 (1978).
9P. Doussineau, A. Levelut, G. Bellessa, and O. Bethoux, J. Phys. (Paris), Lett. 38, L483 (1977).
10R. W. Cochrane, R. Harris , J . O. Strom-Olsen, and M. J. Zuckermann, Phys. Rev. Lett. 215, 676 (1975).
n P . W. Anderson, B. I. Halperin, and C. M. Varma,
In this Letter we report the first observation of low-energy positron (e*) diffraction (LEPD) from a solid surface, Cu(l l l ) . 1 LEPD offers the possibility of becoming a quantitative tool for the study of surfaces to complement the well-established technique of low-energy electron diffraction (LEED)c The change in the sign of the
Philos. Mag. _25, 1 (1972). 12W. A. Phillips, J. Low Temp. Phys. 1, 351 (1972). 13S. Hunklinger and W. Arnold, in Physical Acoustics,
edited by R. N. Thurston and W. P. Mason (Academic, New York, 1976), Vol. 12, p. 155.
14D. A. Smith, Phys. Rev. Lett. 42, 729 (1979). 15J. Bletry, Z. Naturforch 329, 445 (1977). 16D. Gupta, K. N. Tu, and K. W. Asai, Phys. Rev.
Lett. £5, 706 (1975); H. S. Gill and J. H. Judy, J. Appl. Phys. 50, 1648 (1979).
17H. S. Chen, L. C. Kimerling, J. M. Poate, and W. L. Brown, Appl. Phys. Lett. £2, 461 (1978).
18M. Banville and J. P. Gaspard, to be published. 19S. Gibbs, M.Sc. thesis, McGill University, 1977
(unpublished). 20Our analysis (M. Banville and R. Harris , to be
published) has also been applied to the model structures built by Rahman et al. and by von Heimendahl (see Ref. 3). For the purposes of comparison we note that in terms of the effective time defined by Rahman et al. their simulation ran for 100 units, whereas our final structure had been relaxed for 127 units.
21T. Egami, J. Appl. Phys. J50, 1564 (1979), and J. Mat. Sci. 13, 2587 (1978).
22H. Fujimori, S. Ohta, T. Masumoto, and K. Naka-moto, in Rapidly Quenched Metals Til, edited by B. Cantor (Metals Society, London, 1978), Vol. 2, p. 232; R. Hasegawa and R. C. O'Handley, J. Appl. Phys. 50, 1551 (1979).
23S. Schmid-Marcic and J. A. Mydosh, Solid State Commun. 17, 795 (1975); S. B. Dierker, H. Gudmunds-son, and A. C. Anderson, Solid State Commun. 29, 767(1979).
charge from e~ to e+, the absence of an exchange term in the scattering Hamiltonian, and differences in correlation effects make the interactions of positrons with a surface significantly different from those of electrons. As there is no readily available means for producing large quantities of low-energy positrons, the development of a
Low-Energy Positron Diffraction from a Cu(l l l ) Surface I. J. Rosenberg, A. H. Weiss, and K. F. Canter
Department of Physics, Brandeis University, Waltham, Massachusetts 02254 (Received 25 February 1980)
The first observation of low-energy positron diffraction from a solid surface is r e ported. Slow (20-400-eV) monochromatic positron beams were focused onto a Cu(lll) surface and their elastically scattered distributions detected with a channel electron multiplier. Measurements of the scattered intensity versus angle as a function of incident energy show peaks at the predicted (01) and (02) diffraction angles. Profiles of intensity versus energy at fixed angles exhibit maxima corresponding to the primary Bragg peaks.
PACS numbers: 61.14.Fe, 78.70.Bj, 71.60.+ Z
© 1980 The American Physical Society 1139