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New scaling relations to compute atom-in-material polarizabilities and dispersion coefficients: part 1. Cite this: RSC Adv.,2019,9, 19297 Theory and accuracy†
Thomas A. Manz, *a Taoyi Chen, a Daniel J. Cole, b Nidia Gabaldon Limasa and Benjamin Fiszbeina
Polarizabilities and London dispersion forces are important to many chemical processes. Force fields for classical
atomistic simulations can be constructed using atom-in-material polarizabilities and Cn (n ¼ 6, 8, 9, 10.) dispersion coefficients. This article addresses the key question of how to efficiently assign these parameters to constituent atoms in a material so that properties of the whole material are better reproduced. We develop a new set of scaling laws and computational algorithms (called MCLF) to do this in an accurate and computationally efficient manner across diverse material types. We introduce a conduction limit upper bound and m-scaling to describe the different behaviors of surface and buried atoms. We validate MCLF by comparing
Creative Commons Attribution 3.0 Unported Licence. results to high-level benchmarks for isolated neutral and charged atoms, diverse diatomic molecules, various polyatomic molecules (e.g., polyacenes, fullerenes, and small organic and inorganic molecules), and dense solids (including metallic, covalent, and ionic). We also present results for the HIV reverse transcriptase enzyme complexed with an inhibitor molecule. MCLF provides the non-directionally screened polarizabilities required to construct force fields, the directionally-screened static polarizability tensor components and eigenvalues, and
environmentally screened C6 coefficients. Overall, MCLF has improved accuracy compared to the TS-SCS Received 23rd April 2019 method.ForTS-SCS,wecomparedchargepartitioning methods and show DDEC6 partitioning yields more Accepted 3rd June 2019 accurate results than Hirshfeld partitioning. MCLF also gives approximations for C8,C9,andC10 dispersion DOI: 10.1039/c9ra03003d coefficients and quantum Drude oscillator parameters. This method should find widespread applications to This article is licensed under a rsc.li/rsc-advances parameterize classical force fields and density functional theory (DFT) + dispersion methods.
3,9–12 ff Open Access Article. Published on 19 June 2019. Downloaded 6/24/2019 3:33:38 PM. 1. Introduction eld design. Polarization e ects are especially important for simulating materials containing ions.13–20 When considered along- When combined with large-scale density functional theory (DFT) side the importance of accurate theoretical methods to study van der calculations, the DDEC method has been shown to be suitable for Waals interactions at the nanoscale,21 it is clear that a crucial feature assigning atom-centered point charges for exible molecular of new methods to compute these important quantities is the ability 1–8 mechanics force-eld design. The assignment of C6 coefficients to scale to large system sizes in reasonable computational time. and atomic polarizabilities is another active area of research in force In this article, we develop new scaling laws and an associated method to compute polarizabilities and dispersion coefficients for atoms-in-materials (AIMs). These new scaling laws and a Department of Chemical & Materials Engineering, New Mexico State University, Las computational method give good results for isolated atoms, Cruces, New Mexico, 88003-8001, USA. E-mail: [email protected] diatomic molecules, polyatomic molecules, nanostructured bSchool of Natural and Environmental Sciences, Newcastle University, Newcastle upon Tyne NE1 7RU, UK materials, solids, and other materials. This new method is † Electronic supplementary information (ESI) available: A pdf le containing: abbreviated MCLF according to the authors' last name initials damping radii denition (S1); def2QZVPPDD basis set denition (S2); m scaling (where the C is both for Chen and Cole). We performed tests on formula for wp (S3); and plot of the smooth cutoff function (S4). A 7-zip format isolated neutral and charged atoms, small molecules, fullerenes, archive containing: isolated atoms reference data and regression results and their polyatomic molecules, solids, and a large biomolecule with extrapolation up to element 109; def2QZVPPDD.gbs and def2QZVPPDD.pseudo les containing the full basis set and RECP parameter tabulations, respectively; MCLF. The results were compared with experimental data, high HIV reverse transcriptase complex geometry, ONETEP input les, and tabulated level CCSD calculations, time-dependent DFT (TD-DFT) calcula- MCLF and TS-SCS results for every atom in the material; MCLF and TS-SCS input tions, or published force-eld parameters. and output les for the CH2Br2 example showing symmetric (MCLF) and As discussed in several recent reviews and perspectives, the asymmetric (TS-SCS) atom-in-material polarizability tensors; C8,A and C10,A models dispersion interaction is a long-range, non-local interaction for isolated atoms; and detailed MCLF and TS-SCS results for each material in the following test sets: diatomic molecules, small molecules and molecule pairs, caused by uctuating multipoles between atoms in mate- 22–26 solids, polyacenes and fullerenes. See DOI: 10.1039/c9ra03003d rials. It is especially important in (i) condensed phases
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including liquids, supercritical uids, solids, and colloids, (ii) geometry-based method to calculate C6,C8, and C9 dispersion nanostructure binding such as the graphene layers forming coefficients and dispersion energies, but this method does not graphite, and (iii) the formation of noble gas dimers. The yield polarizability tensors.11 The recently formulated D4 dispersion interaction is closely related to AIM polarizabilities. models are geometry-based methods that extend the D3 The dispersion energy can be described by an expansion series. formalism by including atomic-charge dependence.35–37 The The leading term is inversely proportional to R6, where R is the exchange-dipole model (XDM) is an orbital-dependent distance between two atoms. The coefficient of this term is approach that yields AIM dipole, quadrupole, and octupole 38–42 called the C6 dispersion coefficient, and this term quanties polarizabilities and C6,C8, and C10 dispersion coefficients. uctuating dipole–dipole interactions between two atoms. The Several density-dependent XDM variants have been formu- ffi 43,44 ffl intermolecular C6 coe cient is given by the sum of all inter- lated. In 2009, Tkatchenko and Sche er introduced the TS ffi 12 atomic contributions method for isotropic AIM polarizabilities and C6 coe cients. X X mol Both the XDM and TS methods yielded isotropic AIM polariz- C ¼ C ; (1) 6 6 AB abilities rather than molecular polarizability tensors.12,38–44 In A˛M1B˛M2 both the XDM and TS methods, the AIM unscreened polariz- where M1 and M2 refer to the rst and the second molecules. ability is given by Higher-order terms represent different interactions.27 For AIM hr3i example, the eighth-order (C8) term describes the uctuating TS ¼ ref a a ref (2) dipole–quadrupole interaction between two atoms. The ninth- hr3i order (C ) term describes the uctuating dipole–dipole–dipole 9 where “ref” refers to the reference value for an isolated neutral interaction between three atoms. The tenth-order (C ) term 10 atom of the same chemical element, “AIM” refers to the parti- describes the uctuating quadrupole–quadrupole and dipole– tioned atom-in-material value, and hr3i refers to the r-cubed octupole interaction between two atoms. radial moment. Both the XDM and TS methods originally used ffi Methods for computing polarizabilities and dispersion coe - 45 3 AIM 12,42 Creative Commons Attribution 3.0 Unported Licence. Hirshfeld partitioning to compute the hr i values. cients can be divided into two broad classes: (A) quantum chem- In 2012, Tkatchenko et al. introduced self-consistent istry methods that explicitly compute the system response to an screening (TS-SCS) via the dipole interaction tensor to yield electric eld (e.g., TD-DFT, CCSD perturbation response theory, ffi the molecular polarizability tensor and screened C6 coe - etc.) and (B) AIM models. Class A methods can be highly accurate cients.46 The TS-SCS dipole interaction tensor uses a quantum for computing polarizabilities and dispersion coefficients of harmonic oscillator (QHO) model similar to that used by Mayer a whole molecule, but they do not provide AIM properties. but extended over imaginary frequencies and omitting charge– Therefore, class A methods cannot be regarded as more accurate dipole and charge–charge terms.33,34,46 That same article also versions of class B methods. Parameterizing a molecular used a multibody dispersion (MBD46,47) energy model based on This article is licensed under a mechanics force-eld from quantum mechanics requires an AIM a coupled uctuating dipole model (CFDM47,48). The TS-SCS (i.e., class B) model. Our goal here is not merely to develop screened static polarizability and characteristic frequency for a computationally cheaper method than TD-DFT or CCSD each atom are fed into the CFDM model to obtain the MBD
Open Access Article. Published on 19 June 2019. Downloaded 6/24/2019 3:33:38 PM. perturbation response theory to compute accurate system polar- energy.46 The TS-SCS approach has advantages of yielding izabilities and dispersion coefficients, but rather to exceed the a molecular polarizability tensor and AIM screened polariz- capabilities of both of those methods by providing accurate AIM abilities and AIM screened C6 coefficients using only the properties for force-eld parameterization. system's electron density distribution as input.46 One must distinguish the polarizability due to electron cloud The TS-SCS method has several key limitations. Two key distortion from the polarization due to molecular orientation assumptions of the TS-SCS method are: (i) for a specic (and other geometry changes) such as occurs in ferroelectric chemical element, the unscreened atomic polarizability is materials. Herein, we are solely interested in the polarizability proportional to the atom's hr3i moment, and (ii) for a specic that occurs due to electron cloud distortions. Electric polariza- ffi chemical element, the unscreened C6 coe cient is propor- tion due to molecular orientation and other geometric changes tional to the atom's polarizability squared.12,46 However, in can be described by a geometric quantum phase.28–30 their work these hypotheses were not directly tested.12,46 Later, There are several existing frameworks for calculating AIM Gould tested these two assumptions and found them inaccu- polarizabilities and/or dispersion coefficients. Applequist et al. rate for describing isolated neutral atoms placed in a conne- 31 introduced a formalism that represents the molecular polar- ment potential.49 Hirshfeld partitioning was used in the TS- izability tensor in terms of AIM polarizabilities via the dipole SCS method12,46 to compute the hr3iAIM. Because Hirshfeld interaction tensor. Thole32 rened this formalism by replacing partitioning uses isolated neutral atoms as references,45 the atomic point dipoles with shape functions to avoid innite Hirshfeldmethodtypicallyseverely underestimates net atomic interaction energies between adjacent atoms. Applequist's and – charge magnitudes.50 53 The TS-SCS method assumes Thole's methods use empirical atomic polarizability tting to a constant unscreened polarizability-to-hr3i ratio and constant reproduce observed polarizability tensors of small mole- characteristic frequency (wp) for all charge states of a chemical cules.31,32 Mayer et al. added charge–charge and dipole–charge element,46 but these assumptions are not realistic. Due to interaction terms to calculate more accurate polarizabilities of these assumptions, the TS and TS-SCS methods are inaccurate conducting materials.33,34 Grimme et al. presented the D3
19298 | RSC Adv.,2019,9, 19297–19324 This journal is © The Royal Society of Chemistry 2019 View Article Online Paper RSC Advances
for systems with charged atoms.54–57 Bucko et al. showed the TS to provide accurate net atomic charges (NACs), atomic volumes, and TS-SCS methods severely overestimate polarizabilities for and radial moments as inputs. Our method has new scaling dense solids.57 The TS-SCS method has also not been opti- laws for the unscreened atomic polarizabilities, characteristic ffi ff mizedtoworkwithconductingmaterials,andweshowin frequency (wp), and C6 dispersion coe cients. The di erent Section 5.2 below the TS and TS-SCS methods sometimes scaling behaviors of surface and buried atoms are included via predict erroneous polarizabilities even greater than for m-scaling. Our approach accurately handles the variability in a perfect conductor. As discussed in Sections 4 and 5 below, polarizability-to-hr3i moment ratio for charged surface atoms the TS-SCS method overestimates directional alignment of while only requiring reference atomic polarizabilities, reference
uctuating dipoles at large interatomic distances. We also C6 coefficients, and reference radial moments for isolated show the TS-SCS method sometimes gives asymmetric AIM neutral atoms. It uses a new self-consistent screening procedure ffi polarizability tensors and unphysical negative AIM to compute screened polarizability tensors and C6 coe cients. polarizabilities. Our approach separates non-directional screening from direc- Several research groups developed improvements to the TS- tional screening of the dipole interaction tensor. This allows SCS method. Ambrosetti et al. introduced range separation to a conduction limit upper bound to be applied between non- avoid double counting the long-range interactions in TS-SCS directional and directional screening to ensure buried atoms followed by MBD (aka MBD@rsSCS).58 MBD@rsSCS improves do not have a screened polarizability above the conduction the accuracy of describing directional alignments of uctu- limit. Our method yields three different types of dipole polar- ating dipoles at large interatomic distances.58 Bucko et al. used izabilities: (a) induced static polarizabilities corresponding to Iterative Hirshfeld (IH51) partitioning in place of Hirshfeld a uniform applied external electric eld, (b) isotropic screened partitioning to compute hr3iAIM.55,57 While this was an polarizabilities suitable as input into polarizable force-elds, improvement, it did not address several problems mentioned and (c) uctuating polarizabilities that are used to compute
above. For example, the TS-SCS/IH method still unrealistically C6 dispersion coefficients via the Casimir–Polder integral. h 3i ffi
Creative Commons Attribution 3.0 Unported Licence. assumed the unscreened polarizability-to- r ratio is the same When computing C6 dispersion coe cients, we use multi-body for various charge states of a chemical element.55,57 This screening to taper off the dipole directional alignment at large assumption was removed in the subsequent Fractionally Ionic interatomic distances. The self-consistent screening is applied (FI) method.54 However, the FI approach requires separate incrementally. Richardson extrapolation provides high numeric ffi reference polarizabilities and C6 dispersion coe cients for all precision. Through quantum Drude oscillator (QDO) parame- charge states of a chemical element.54 This is extremely terization, our method also yields higher-order polarizabilities problematic, because some anions that exist in condensed (e.g., quadrupolar, octupolar, etc.) and higher-order dispersion 2 59 materials (e.g.,O ) have unbound electrons in isolation. coefficients (e.g.,C8,C9,C10, etc.) for AIMs. Other important Although methods to compute charge-compensated reference improvements include: improved damping radii, proportional
This article is licensed under a ion densities have been developed,53,55,59–64 those methods do partitioning of shared polarizability components to avoid not presently extend to computing charge-compensated negative AIM polarizabilities, iterative update of the spherical ffi polarizabilities and C6 coe cients of ions. Thus, several Gaussian dipole width, and AIM polarizabilities are symmetric
Open Access Article. Published on 19 June 2019. Downloaded 6/24/2019 3:33:38 PM. problems with the TS-SCS approach have not been satisfacto- tensors. rily resolved in the prior literature. Our method was designed to satisfy the following criteria: In Gould et al.'s FI method, reference free atom polarizabil- (1) The method should require only the system's electron ities were computed for various whole numbers of electrons and and spin density distributions as input; interpolated to nd fractionally charged free atom reference (2) The method should work for materials with 0, 1, 2, or 3 polarizabilities.54 This yields different polarizability-to-hr3i ratios periodic boundary conditions; for different charge states of the same chemical element.54 Due to (3) The method should give accurate results for charged atoms the instability of highly charged anions, the 1 states of halogens in materials while only requiring reference polarizabilities and 54,65 ffi were the only anions Gould et al. computed self-consistently. reference C6 coe cients for neutral free atoms; (In this context, ffi For other anions, Gould and Bucko resorted to using DFT orbitals reference polarizabilities and reference C6 coe cients refer to from the neutral atoms to build non-self-consistent anions for those polarizabilities and C6 coefficients stored within the so- 65 polarizability and C6 calculations, but this severely underesti- ware program that are used during application of the method.) mates the diffuseness of anions (i.e., underestimates their (4) The method should give accurate results for diverse mate-
polarizabilities and C6 coefficients). Unfortunately, this problem rials types: isolated atoms; small and large molecules; nano- cannot be easily resolved by performing self-consistent calcula- structured materials; ionic, covalent, and metallic solids, etc.; tions for all charged states, because some highly charged anions (5) The method should give accurate results for both surface (e.g.,O2 )59 contain unbound electrons. This makes the FI and buried atoms; method problematic for materials containing highly charged (6) The method should yield both static polarizability tensors anions. Because FI was not included in VASP version 6b that we and polarizabilities suitable for constructing molecular currently have access to, we did not perform FI calculations for mechanics force-elds; comparison in this work. (7) The method should accurately describe both short- and
In this article, we develop a new approach that resolves these long-range ordering of dipole polarizabilities and C6 issues. Our method uses DDEC6 (ref. 61 and 66–68) partitioning coefficients;
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(8) The method should have less than approximately 10% 3L h2ðnÞ 1 m2 aðnÞ¼ ffi 2 (3) average unsigned error on C6 coe cients and dipole polariz- 4p h ðnÞþ2 3kBT abilities for the benchmark sets studied here; h m (9) The method should include estimates for higher-order where is the refractive index, is the dipole moment magni- L AIM polarizabilities (e.g., quadrupolar, octupolar, etc.) and tude, T is absolute temperature, is the volume per molecule, 70 and kB is Boltzmann's constant. (The last term in eqn (3) dispersion coefficients (e.g.,C8,C9,C10, etc.); (10) The method should have low computational cost for accounts for orientational polarizability.) Static or low-frequency k both small and large systems. dielectric constants were obtained by measuring the ratio of the There are two main applications for this MCLF method. First, capacitance of a set of electrodes with the sample material in- the polarizabilities and dispersion coefficients can be used to between to the capacitance of the same electrodes with vacuum 72 partially parameterize molecular mechanics force-elds. In addi- in-between. The polarizability of a gas-phase sample can then ffi be calculated using the Clausius–Mossotti relation:73 tion to polarizabilities and C6 dispersion coe cients, those force- elds would also need to include net atomic charges (NACs), 3L k 1 a ¼ (4) exibility parameters (e.g., bond, angle, and torsion terms), 4p k þ 2 exchange–repulsion parameters, (optionally) charge penetration parameters, and optionally other parameters. Second, the disper- ffi Reference C6 coe cients for the atom/molecule pairs sion coefficients can be used to partially parameterize DFT + (Section 5.4) were taken from the experimentally extracted dispersion methods.23 In addition to the C dispersion coefficients, 6 dipole oscillator strength distribution (DOSD) data of Meath an accurate DFT + dispersion method should also include higher- and co-workers74,75 as tabulated by Bucko et al.55 order dispersion (e.g.,C,C,and/orC terms) or multi-body 8 9 10 Time-dependent DFT (TD-DFT) and time-dependent Hartree– dispersion (MBD) combined with an accurate damping func- Fock (TD-HF) can be used to compute benchmark polarizabilities tion.22,23 (Partially analogous to the MBD@rsSCS method,58 range and dispersion coefficients. The Casimir–Polder integral is used
Creative Commons Attribution 3.0 Unported Licence. separation would be required to avoid double counting dispersion ffi to calculate C6 coe cients from polarizabilities at imaginary interactions when combining a MCLF variant with a MBD 76 frequencies (imfreqs). For polyacenes (Section 5.5), reference C6 Hamiltonian.) Because DFT and molecular mechanics are widely coefficients and isotropic static polarizabilities are from the TD- used in computational chemistry, our new method can have DFT calculations of Marques et al.77 For selected polyacenes, widespread applications. static polarizability tensor components were available as refer- The remainder of this article is organized as follows. ence from Jiemchooroj et al.'s TD-DFT calculations.78 Jiem- Section 2 contains the background information. Section 3 chooroj et al. found their TD-DFT results were similar to TD-HF, contains the new isolated atom scaling laws developed for experimental (where available), and CCSD (where available) MCLF. Section 4 describes the theory of the MCLF method. ffi results. For fullerenes (Section 5.5), the reference C6 coe cients This article is licensed under a Section 5 contains calculation results of C coefficients and 6 and isotropic static polarizabilities are from the TD-HF calcula- polarizabilities and comparisons to benchmark data. Section 6 tions of Kauczor et al.116 Kauczor et al. also obtained similar is the conclusions. results using TD-DFT.116 Open Access Article. Published on 19 June 2019. Downloaded 6/24/2019 3:33:38 PM.
2. Background information 2.2 Notation 2.1 Benchmarking methods A system may have either 0, 1, 2, or 3 periodic boundary condi- Experimental data and high-level quantum chemistry calcula- tions. In periodic materials, the term ‘image’ refers to a translated tions were used as references in this work. Section 3.1 below image of the reference unit cell. Each image is designated by describes reference polarizabilities and dispersion coefficients translation integers (L1, L2, L3) that quantify the unit cell trans- (C6,C8, and C10) for the isolated atoms. For diatomic molecules lation along the lattice vectors. The reference unit cell is the image in Section 5.1, we computed static polarizability tensors using designated by (L1, L2, L3) ¼ (0, 0, 0). N # Li # N along a periodic CCSD calculations combined with the “polar” keyword in direction. Li ¼ 0 along a non-periodic direction. Similar to the Gaussian09 (ref. 69). As explained in Section 5.2 below, we set notation previously used in the bond order article,67 a capital letter the reference static polarizability for dense solids to the lesser of (A, B,.) designates an atom in the reference unit cell and – the Clausius Mossotti relation value and the conduction limit alowercaseletter(a,b,.) designates an image atom. For example, upper bound based on the experimental crystal structure ¼ b (B, L1, L2, L3) denotes a translated image of atom B. geometry and dielectric constant. ~ Let RB represent the nuclear position of atom B in the refer- For the small molecules in Section 5.3, reference static polar- ence unit cell. Then, the nuclear position of a translated image is izabilities were obtained from published experiments. Experi- ~ ~ (1) (2) (3) mental isotropic polarizabilities were extracted from dielectric Rb ¼ RB + L1~v + L2~v + L3~v (5) constant or refractive index measurements having approximately 0.5% or less error.70 Refractive index can be measured by passing where ~v(1), ~v(2), and ~v(3) are the lattice vectors. The distance a light ray through a gas-phase sample.71 The polarizability a(n)of between the nuclear position of atom A and the translated thesampleatfrequencyn canthenbecalculatedusing image of atom B is
19300 | RSC Adv.,2019,9, 19297–19324 This journal is © The Royal Society of Chemistry 2019 View Article Online Paper RSC Advances
AB,L ~ ~ ‘ ’ dAb ¼ r ¼kRb RAk (6) followed by / followed by the charge partitioning method. For example, TS-SCS/IH indicates the TS-SCS dispersion- Cartesian components (s ¼ x, y, z) of the vector from atom A's polarization model using IH charge partitioning. Where our nuclear position to image b's nuclear position are represented by computed data are simply labeled ‘TS-SCS’, the DDEC6 charge partitioning method was used. Since all of the MCLF results rAB,L ¼ R~ R~ s b A (7) reported in this paper used DDEC6 charge partitioning, we used the less precise but shorter term ‘MCLF’ in place of the full ~r is the vector from the image of atom A's nuclear position to A ‘MCLF/DDEC6’ designation. More generally, the MCLF the spatial position ~r: dispersion-polarization model could potentially be combined (1) (2) (3) ~ with other charge partitioning methods (e.g., MCLF/IH), but ~rA ¼ ~r L1~v L2~v L3~v RA (8) that is beyond the scope of the present study. ffi The length of this vector is represented by Calculating dispersion coe cients involves integrating polarizabilities over imfreqs. This is inconvenient in two
rA ¼k~rAk (9) respects. First, it is easier to deal with real-valued variables rather than imaginary-valued ones. Second, numeric integra- A stockholder partitioning method assigns a set of atomic tion from zero to innite imaginary frequency is inconvenient, ~ electron densities {rA(rA)} in proportion to atomic weighting because innity cannot be readily divided into nite intervals factors {wA(rA)} for numeric integration. Letting u represent an imaginary frequency magnitude, we used the following variable trans- ~r ¼ ~r w r W ~r rA( A) r( ) A( A)/ ( ) (10) formation to solve these two problems: Nimfreqs Nimfreqs so that all sum to the total electron density u ¼ ; uðuÞ¼ 1 (15) X 1 þ u u
Creative Commons Attribution 3.0 Unported Licence. r ~r ¼ r ~r (11) A A u ¼ N A;L This conveniently transforms integration limits [0, ) into u ¼ [Nimfreqs, 0), which upon changing the integrand's sign X gives integration limits u ¼ (0, Nimfreqs]. As shown in the W ~r ¼ wAðrAÞ (12) A;L companion article, this allows convenient Rhomberg integra- tion using integration points u ¼ 1, 2,. Nimfreqs.79 In this where summation over A, L means summation over all atoms in article, a(u) denotes the polarizability at the imaginary the material. The number of electrons NA and net atomic charge frequency whose magnitude equals u(u). (qA) assigned to atom A are
This article is licensed under a Þ 3 2.3 Details of the TS-SCS methodology NA ¼ rA(~rA)d ~rA ¼ QA qA (13) Fig. 1 is a ow diagram of the TS-SCS method. Bucko et al.56 gave where QA is the atomic number for atom A. As discussed in the step-by-step calculation of the self-consistent screening
Open Access Article. Published on 19 June 2019. Downloaded 6/24/2019 3:33:38 PM. ff Section 2.4 below, di erent ways of de ning {wA(rA)} produce process. Here, we follow the presentation of Bucko et al., except different stockholder methods. The AIM radial moment of using the variable substitution of eqn (15). For atoms A and B, order f is they dene a many-body polarizability matrix P, with its inverse Þ Q having the form f f 3 h(rA) i¼ (rA) rA(~rA)d ~rA (14) AB 1 AB Q ¼ dABdst þ s (16) 2 3 4 2 3 4 st aunscreened st hr i, hr i, and hr i are shorthand for h(rA) i, h(rA) i, and h(rA) i, A respectively. where s, t designate Cartesian components. Square matrices P Since a particular dispersion-polarization model can be and Q have x, y, and z spatial indices for every atom to give ff combined with di erent charge partitioning methods, we a total of 3Natoms rows. The last term on the right-hand side is indicate the combination by the dispersion-polarization model the dipole interaction tensor which has the form