# Reciprocal lattice

In crystallography, the **reciprocal lattice** of a Bravais lattice is the set of all vectors **K** such that

- $ e^{i\mathbf{K}\cdot\mathbf{R}}=1 $

for all lattice point position vectors **R**. This reciprocal lattice is itself a Bravais lattice, and the reciprocal of the reciprocal lattice is the original lattice.

For an infinite three dimensional lattice, defined by its primitive vectors $ (\mathbf{a_{1}}, \mathbf{a_{2}}, \mathbf{a_{3}}) $, its reciprocal lattice can be determined by generating its three reciprocal primitive vectors, through the formula,

- $ \mathbf{b_{1}}=2 \pi \frac{\mathbf{a_{2}} \times \mathbf{a_{3}}}{\mathbf{a_{1}} \cdot (\mathbf{a_{2}} \times \mathbf{a_{3}})} $
- $ \mathbf{b_{2}}=2 \pi \frac{\mathbf{a_{3}} \times \mathbf{a_{1}}}{\mathbf{a_{2}} \cdot (\mathbf{a_{3}} \times \mathbf{a_{1}})} $
- $ \mathbf{b_{3}}=2 \pi \frac{\mathbf{a_{1}} \times \mathbf{a_{2}}}{\mathbf{a_{3}} \cdot (\mathbf{a_{1}} \times \mathbf{a_{2}})}. $

Using column vector representation of (reciprocal) primitive vectors, the formula above can be rewritten using matrix inversion:

- $ \left[\mathbf{b_{1}}\mathbf{b_{2}}\mathbf{b_{3}}\right]^T = 2\pi\left[\mathbf{a_{1}}\mathbf{a_{2}}\mathbf{a_{3}}\right]^{-1}. $

This method appeals to the definition, and allows generalization to arbitrary dimensions. Curiously, the cross product formula dominates introductory materials on crystallography.

The above definition is called the "physics" definition, as the factor of $ 2 \pi $ comes naturally from the study of periodic structures. An equivalent definition, the "crystallographer's" definition, comes from defining the reciprocal lattice to be $ e^{2 \pi i\mathbf{K}\cdot\mathbf{R}}=1 $ which changes the definitions of the reciprocal lattice vectors to be

- $ \mathbf{b_{1}}=\frac{\mathbf{a_{2}} \times \mathbf{a_{3}}}{\mathbf{a_{1}} \cdot (\mathbf{a_{2}} \times \mathbf{a_{3}})} $

and so on for the other vectors. The crystallographer's definition has the advantage that the definition of $ \mathbf{b_{1}} $ is just the reciprocal magnitude of $ \mathbf{a_{1}} $ in the direction of $ \mathbf{a_{2}} \times \mathbf{a_{3}} $, dropping the factor of $ 2 \pi $. This can simplify certain mathematical manipulations, and expresses reciprocal lattice dimensions in units of spatial frequency. It is a matter of taste which definition of the lattice is used, as long as the two are not mixed.

Each point (hkl) in the reciprocal lattice corresponds to a set of lattice planes (hkl) in the real space lattice. The direction of the reciprocal lattice vector corresponds to the normal to the real space planes, and the magnitude of the reciprocal lattice vector is equal to the reciprocal of the interplanar spacing of the real space planes.

The reciprocal lattice plays a fundamental role in most analytic studies of periodic structures, particularly in the theory of diffraction. For Bragg reflections in neutron and X-ray diffraction, the momentum difference between incoming and diffracted X-rays of a crystal is a reciprocal lattice vector. The diffraction pattern of a crystal can be used to determine the reciprocal vectors of the lattice. Using this process, one can infer the atomic arrangement of a crystal.

The Brillouin zone is a primitive unit cell of the reciprocal lattice.

## Contents

## Reciprocal lattices of various crystals

Reciprocal lattices for the cubic crystal system are as follows.

### Simple cubic lattice

We find that the simple cubic Bravais lattice, with cubic primitive cell of side $ a $, has for its reciprocal a simple cubic lattice with a cubic primitive cell of side $ \begin{matrix}\frac{2\pi}{a}\end{matrix} $ ($ \begin{matrix}\frac{1}{a}\end{matrix} $ in the crystallographer's definition). The cubic lattice is therefore said to be dual, having its reciprocal lattice being identical (up to a numerical factor).

### Face-centered cubic lattice

The reciprocal lattice to an FCC lattice is the BCC lattice.

#### Finding the reciprocal lattice of a face-centered cubic

Consider an FCC compound unit cell. Locate a primitive unit cell of the FCC--i.e., a unit cell with one lattice point. Now take one of the vertices of the primitive unit cell as the origin. Give the basis vectors of the real lattice. Then from the known formulae you can calculate the basis vectors of the reciprocal lattice. These reciprocal lattice vectors of the FCC represent the basis vectors of a BCC real lattice. Note that the basis vectors of a real BCC lattice and the reciprocal lattice of an FCC resemble each other in direction but not in magnitude.

### Body-centered cubic lattice

The reciprocal lattice to a BCC lattice is the FCC lattice.

It can be easily proven that only the Bravais lattices which have 90 degrees between $ (\mathbf{a_{1}}, \mathbf{a_{2}}, \mathbf{a_{3}}) $ (cubic, tetragonal, orthorhombic) have $ (\mathbf{b_{1}}, \mathbf{b_{2}}, \mathbf{b_{3}}) $ parallel to their real-space vectors.

### Simple hexagonal lattice

The reciprocal to a simple hexagonal Bravais lattice with lattice constants c and a is another simple hexagonal lattice with lattice constants (2*Pi)/c and (4*Pi)/(sqrt(3)*a) rotated through 30° about the c-axis with respect to the direct lattice.

## Arbitrary collection of atoms

One path to the reciprocal lattice of an arbitrary collection of atoms comes from the idea of scattered waves in the Fraunhofer (long-distance or lens back-focal-plane) limit as a Huygens-style sum of amplitudes from all points of scattering (in this case from each individual atom)^{[1]}. This sum is denoted by the complex amplitude F in the equation below, because it is also the Fourier transform (as a function of spatial frequency or reciprocal distance) of an effective scattering potential in direct space:

- $ F[\vec{g}]=\sum_{j=1}^{N}f_j[\vec{g}]e^{2\pi i \vec{g} \cdot \vec{r}_{j}}. $

Here **g** = **q**/(2π) is the scattering vector **q** in crystallogapher units, N is the number of atoms, f_{j}[**g**] is the atomic scattering factor for atom j and scattering vector **g**, while **r**_{j} is the vector position of atom j. Note that the Fourier phase depends on one's choice of coordinate origin.

For the special case of an infinite periodic crystal, the scattered amplitude F = M F_{hkl} from M unit cells (as in the cases above) turns out to be non-zero only for integer values of (hkl), where

- $ F_{hkl}=\sum_{j=1}^{m}f_j[g_{hkl}]e^{2\pi i (h u_j + k v_j + l w_j)} $

when there are j=1,m atoms inside the unit cell whose fractional lattice indices are respectively {u_{j},v_{j},w_{j}}. To consider effects due to finite crystal size, of course, a shape convolution for each point or the equation above for a finite lattice must be used instead.

Whether the array of atoms is finite or infinite, one can also imagine an "intensity reciprocal lattice" I[**g**], which relates to the amplitude lattice F via the usual relation I = F^{*}F where F^{*} is the complex conjugate of F. Since Fourier transformation is reversible, of course, this act of conversion to intensity tosses out "all except 2nd moment" (i.e. the phase) information. For the case of an arbitrary collection of atoms, the intensity reciprocal lattice is therefore:

- $ I[\vec{g}]=\sum_{j=1}^{N}\sum_{k=1}^{N}f_j[\vec{g}]f_k[\vec{g}]e^{2\pi i \vec{g} \cdot \vec{r}_{jk}}. $

Here **r**_{jk} is the vector separation between atom j and atom k. One can also use this to predict the effect of nano-crystallite shape, and subtle changes in beam orientation, on detected diffraction peaks even if in some directions the cluster is only one atom thick. On the down side, scattering calculations using the reciprocal lattice basically consider an incident plane wave. Thus after a first look at reciprocal lattice (kinematic scattering) effects, beam broadening and multiple scattering (i.e. dynamical) effects may be important to consider as well.

## Mathematics of the dual lattice

There are actually two versions in mathematics of the abstract **dual lattice** concept, for a given lattice *L* in a real vector space *V*, of finite dimension.

The first, which generalises directly the reciprocal lattice construction, uses Fourier analysis. It may be stated simply in terms of Pontryagin duality. The dual group *V*^ to *V* is again a real vector space, and its closed subgroup *L*^ dual to *L* turns out to be a lattice in *V*^. Therefore *L*^ is the natural candidate for *dual lattice*, in a different vector space (of the same dimension).

The other aspect is seen in the presence of a quadratic form *Q* on *V*; if it is non-degenerate it allows an identification of the dual space *V*^{*} of *V* with *V*. The relation of *V*^{*} to *V* is not intrinsic; it depends on a choice of Haar measure (volume element) on *V*. But given an identification of the two, which is in any case well-defined up to a scalar, the presence of *Q* allows one to speak to the dual lattice to *L* while staying within *V*.

## See Also

## Footnotes

- ↑ B. E. Warren (1969/1990)
*X-ray diffraction*(Addison-Wesley, Reading MA/Dover, Mineola NY).

## External links

This Jmol-based electron diffraction simulator lets you explore the intersection between reciprocal lattice and Ewald sphere during tilt.de:Reziprokes Gitterhe:סריג הופכי