International
Tables for Crystallography Volume F Crystallography of biological macromolecules Edited by M. G. Rossmann and E. Arnold © International Union of Crystallography 2006 
International Tables for Crystallography (2006). Vol. F, ch. 9.1, pp. 179183
Section 9.1.6. Basis of the rotation method^{a}National Cancer Institute, Brookhaven National Laboratory, NSLS, Building 725AX9, Upton, NY 11973, USA, and ^{b}Structural Biology Laboratory, Department of Chemistry, University of York, York YO10 5DD, England 
The physical process of diffraction from a crystal involves the interference of Xrays scattered from the electron clouds around the atomic centres. The ordered repetition of atomic positions in all unit cells leads to discrete peaks in the diffraction pattern. The geometry of this process can alternatively be described as resulting from the reflection of Xrays from a set of hypothetical planes in the crystal. This is explained by the Ewald construction (Fig. 9.1.6.1), which provides a visualization of Bragg's law. Monochromatic radiation is represented by a sphere of radius , and the crystal by a reciprocal lattice. The lattice consists of points lying at the end of vectors normal to reflecting planes, with a length inversely proportional to the interplanar spacing, . In the rotation method, the crystal is rotated about a single axis, with the rotation angle defined as ϕ. A seminal work giving an excellent background to this field by a number of contributors was edited by Arndt & Wonacott (1977).
For a stationary crystal in any particular orientation (a socalled `still' exposure), only a fraction of the total number of Bragg reflections will satisfy the diffracting condition. The number of reflections will be very limited for a smallmolecule crystal, possibly zero in some orientations. Macromolecules have large unit cells, of the order of 100 Å, compared with the wavelength of the radiation, which is about 1.0 Å. In geometric terms, the reciprocal space is densely populated by points in relation to the size of the Ewald sphere. Thus, more reflections diffract simultaneously but at different angles, since many reciprocallattice points (reflections) lie simultaneously on the surface of the Ewald sphere in any crystal orientation. This is the great advantage of 2D detectors for large cell dimensions.
The real crystal is a regular and ordered array of unit cells. This means that reciprocal space is made up of a set of points organized in regular planes. For a still exposure, any particular plane of points in the reciprocal lattice intersects the surface of the Ewald sphere in the form of a circle. The corresponding diffracted rays, originating from the centre of the Ewald sphere, form a cone that intersects the sphere on the circle formed by the set of points. In most experiments, the detector is placed perpendicular to the direct beam and the cone of diffracted rays forms an ellipse of spots on its surface (Fig. 9.1.6.2). If a major axis of the crystal lies nearly parallel to the beam, then the ellipses will approximate a set of circles around the centre of the detector. All reflections within each circle will have one index in common, corresponding to the unitcell axis lying along the beam. For noncentred unit cells, the index will increase by one in successive circles. The gaps between the circles depend on the spacing between the set of reciprocallattice planes and are inversely proportional to the real cell dimension related to these planes.

The plane of reflections in the reciprocal sphere that is approximately perpendicular to the Xray beam gives rise to an ellipse of reflections on the detector. 
Still exposures were used extensively in the early applications of the rotation method for estimation of crystal alignment. The geometric location of the spots with respect to the origin allows accurate determination of the unitcell parameters and the crystal orientation. This approach has been superseded in modern software packages by autoindexing algorithms using real rotation images instead of stills.
The Ewaldsphere construction assumes an ideal source with a totally parallel Xray beam and an ideal crystal with all unit cells having identical relative orientation, resulting in infinitely sharp Bragg reflections. These assumptions lead to a sphere of radius attached rigidly to the beam and with the crystal in a particular orientation as a reciprocal lattice consisting of mathematical points. A real experiment deviates from this in three respects. Firstly, the incident beam is not strictly parallel. On a conventional rotatinganode source the beam can only be focused and collimated to be parallel within a small angle, with a divergence of about 0.2° (with mirror optics) and 0.4° (with a monochromator). On SR sources, a much smaller beam divergence can be achieved, and, indeed, beamlines on thirdgeneration SR sources approach the ideal ever more closely. The horizontal and vertical beam divergence may differ, and this must be taken into account. The Ewald sphere now has two limiting orientations which result in a nonzero active width. Secondly, the Xradiation is only monochromatic within a defined wavelength bandpass, , of the order 0.0002–0.001 at synchrotron lines, but considerably more for laboratory sources. The wavelength bandpass, in effect, thickens the surface of the Ewald sphere. Thirdly, real crystals are made up from small mosaic blocks imperfectly oriented relative to one another, increasing the total rocking curve. At room temperature, protein crystals often show a mosaic spread less than 0.05°, but for some samples this may be much larger. However, flash freezing of crystals in many cases leads to substantial increase of mosaicity to sometimes more than 1°. In the reciprocal lattice, the effect of this is to give a finite dimension to each of the lattice points.
These effects are schematically illustrated in Fig. 9.1.6.3. The combined result is that the diffraction of a particular reflection is spread over a range of crystal rotation.
Using monochromatic radiation, in order to measure the remaining reflections that do not lie on the surface of the sphere, the crystal must be rotated to bring the reflections into the diffracting condition. If the crystal is rotated about a single axis during sequential exposures, this is known as the rotation method. The rotation axis is, in practice, chosen to be perpendicular to the beam to preserve the symmetry between the two halves of the complete pattern. This is the most commonly applied method of data collection for macromolecular crystals (Arndt & Wonacott, 1977).
If the crystal is rotated during exposure, the ellipses observed on a still image change their position on the detector. In effect, all reflections diffracting during one exposure will be contained within lunes formed between the two limiting positions of each ellipse at the start and end of the given rotation. The width of the lunes in the direction of the crystal rotation, perpendicular to the rotation axis, is proportional to the rotation range per exposure. In contrast, along the rotation axis the width of the lunes is very small, since the intersection of the reciprocallattice plane with the Ewald sphere does not change significantly. For crystals of small molecules, the lunes are not pronounced, owing to the sparse population of reciprocal space, but for crystals with large cell dimensions, the lunes are densely populated by diffraction spots and often exhibit clear and well pronounced edges. At high resolution, the mapping of the reciprocal lattice within each lune is distorted, and rows of reflections form hyperbolas. At low diffraction angles, where the surface of the Ewald sphere is approximately flat, this distortion is minimal, and the lunes look like fragments of precession photographs.
The rotation method gives rise to lunes of data between the ellipses that relate to the start and the end of the rotation range used for the exposure. The data are complete if the Ewald sphere has been crossed by all reflections in the asymmetric part of the reciprocal lattice, which means that the crystal has to be rotated by a substantial angle. However, it is impossible to record all the data in a single exposure with such a wide rotation, owing to overlapping of the diffraction spots.
In practical applications to macromolecules, the total rotation is divided into a series of narrow individual rotations of width Δϕ. In each of these, the crystal is exposed for a specified time or Xray dose per angular unit. Each reflection diffracts over a defined crystal rotation and hence time interval, owing to the finite value of the rocking curve or angular spread, here referred to as ξ, the combined effect of beam divergence (δ) and crystal mosaicity (η). Provided ξ is less than Δϕ, some reflections will start and finish crossing the Ewald sphere and hence diffract within one exposure. Their full intensity will be recorded on a single image, and these are referred to as fully recorded reflections, or fullys.
Other reflections will start to diffract during one exposure, but will still be diffracting at the end of the Δϕ rotation range. The remaining intensity of these reflections will be recorded on subsequent images. There will of course be corresponding reflections at the start of the present image. These reflections are termed partially recorded, or partials. Fig. 9.1.6.4 shows schematically how a lune appears on two consecutive exposures, with partials at each edge. The partials at the bottom edge of each lune contain the rest of the intensity of the partials from the previous exposure. The rest of the intensity of the partials at the top of the lune will appear on the next exposure. Superposition of two successive images will reveal some spots common to both: they are the partials shared between the two. If the angular spread ξ is small compared to the rotation range Δϕ then most reflections will be fully recorded. As ξ increases, the proportion of partials will rise, and when it reaches or exceeds Δϕ in magnitude there will be no fully recorded reflections. If the rotation range per image is small compared with the rocking curve, individual reflections can be spread over several images.

A single lune on two consecutive exposures. The partial reflections appear on both images and their intensity is distributed over both. 
As ξ increases, the lunes become wider (Fig. 9.1.6.5), since there are more partial reflections crossing the Ewald sphere at any one time. The appearance of the lunes can be used to estimate the mosaicity of the crystal. If the edges are sharply defined, then the mosaicity is low. In contrast, if the intensities at the edges gradually fade away, then the mosaicity must be high. Indeed, this phenomenon can be exploited by the integration software to provide accurate definition of the orientation parameters and of the mosaicity.

Appearance of a lune for (a) a crystal of low mosaicity and (b) a highly mosaic crystal. Characteristically, the width of the lune along the rotation axis is wider if the mosaicity is high. 
A key characteristic of high mosaicity is that all lunes are wide in the region along the rotation axis. On still exposures, the width of the rings is proportional to the angular spread. The width of lunes is expected to be very small along the rotation axis. If they are wide in this region, this is especially indicative of high mosaic spread. While highly ordered crystals with low mosaicity are preferable and often lead to data of the highest quality, high mosaic spread is not a prohibitive factor in accurate intensity estimation, provided it is properly taken into account in estimating the data collection and integration parameters, such as individual rotation ranges.
An important variable in the rotation method is the width of the rotation ranges per individual exposure. The two basic approaches can be termed wide and fine ϕ slicing and differ in the relation between the angular spread and the rotation range per exposure. The two methods are applicable under different experimental constraints.
Fine ϕ slicing requires that the individual intensities are divided over several consecutive images, i.e. Δϕ should be substantially less than ξ (Kabsch, 1988). This approach possesses two very positive features. Firstly, it minimizes the background by integrating intensities only over a ϕ range equivalent to the rocking curve of the crystal. Secondly, it allows the fitting of 3D profiles to the pixels that compose a reflection, the first two dimensions being the xy plane of the detector, and the third the ϕ rotation. In combination, these should provide an optimum signaltonoise ratio for the measured intensities and would appear to be the method of choice for data collection.
However, this involves a very large number of images, which can pose logistical problems in terms of data handling. Only if the readout time is negligible in comparison with the exposure time can fine slicing be applied. If the detector readout is slow, fine slicing becomes totally impractical. Multiwire chambers allow fine ϕ slicing, but unfortunately their disadvantages in terms of effective dynamic range preclude their use on highintensity sources. Imaging plates are generally too slow for this approach.
The fineslicing method is undergoing a resurgence of interest with the introduction of fast readout CCD detectors. Solidstate pixel detectors would be even more ideally matched to these needs.
The object of the wideslicing approach is to acquire the data on as small a number of individual exposures as possible. It involves large Δϕ values per image, usually in the order of 0.5° or more, which exceed the angular spread. Each image contains a considerable proportion of fully recorded reflections. Originally, wide slicing was used to minimize the large numbers of Xray films to be processed. Only the wideslicing approach is tractable for detector systems where the readout time is relatively slow in relation to exposure, e.g. imaging plates with readout times of 20 seconds to minutes.
Wide slicing has two drawbacks. Firstly, during integration of the intensity data, only 2D profiles are fitted for each individual spot in the wide slicing. Secondly, each reflection profile overlaps a background which accumulates throughout the whole time and angular range of the exposure, even when the reflection concerned is not diffracting.
The aim is to use the maximum acceptable rotation range per image. The lunes on an image have finite width proportional to the rotation range. This width restricts the allowed angular range per image, as overlap of spots resulting from overlap of adjacent lunes must be avoided if the intensities are to be successfully integrated (Fig. 9.1.6.6). Several factors affect the degree of overlap and will be discussed in the rest of this section. A simple formula (Fig. 9.1.6.7) can be used to estimate the maximum permitted rotation range per image: where the factor converts radians to degrees, ξ is the angular spread of the reflection, d is the highresolution limit and a is the length of the primitive cell dimension along the direction of the Xray beam. However, this simplistic equation can be somewhat misleading. It most strictly applies when the lunes are densely packed with reflections, for an orthogonal cell rotated about a major axis. If this is not the case, then often rows of reflections from one lune fit between rows in the adjacent lune without overlap. For example, for a trigonal crystal with its a axis along the beam and rotating about its c axis, even and odd lunes contain rows of reflections that lie between one another on the detector (Fig. 9.1.6.8).

The width of the lunes is proportional to the rotation range per image, Δϕ, which increases from (a) to (c). If the rotation range is large, the lunes overlap at high resolution. 

The largest allowed rotation range per exposure depends on the dimension of the primitive unit cell oriented along the Xray beam; this is diminished by high mosaicity. 

If the crystal lattice is centred or if its orientation is nonaxial, the reflections do not overlap in spite of overlapping lunes. 
It can be extremely hard to record data from samples with a very long cell dimension. If the long axis lies along the Xray beam, then it will restrict Δϕ considerably to very low values. This is exacerbated if the mosaicity is substantial. It is therefore beneficial to have the longest axis oriented roughly along the spindle axis, as it can then never lie parallel to the beam. This can be a problem with cryogenic samples mounted in loops, where the preferred orientation is hard to dictate, and this is an example where a κgoniostat is an advantage, allowing reorientation of the crystal.
The degree of overlap also depends on pixel size, beam cross section, crystal size and mosaicity, and crystaltodetector distance. In view of the limited applicability of the above equation and these additional parameters, it is in practice better to employ the integration software, first to interpret the diffraction pattern and then to simulate predicted patterns heuristically by adjusting the datacollection parameters, including Δϕ. Most modern packages have such strategy features, and it is vital to employ them before collecting data.
To avoid the overlap of reflections on adjacent lunes and allow much larger rotation ranges per image, up to 5–10°, the Weissenberg camera was reintroduced (Sakabe, 1991). This minimized the number of exposures for a data set, which fitted well with some imagingplate detectors with large size and slow readout. In the Weissenberg method, the detector is translated along the axis of rotation at a rate directly coupled to the rate of rotation. The method required a finely collimated and parallel SR beam so that the spot size on the detector was small. Rows of spots in a particular lune then lay between those from the previous one. Data could be recorded in a very short time on a series of rapidly exchanged imaging plates, which were subsequently read out offline. Complete data could thus be recorded in a mattter of minutes.
This was an application of screenless Weissenberg geometry, quite different from that originally used for small molecules, with the imagingplate translation being small, sufficient only to offset the spots from adjacent lunes. The speed of the system was especially useful for looking at shortlived states, with a lifetime of minutes to hours. However, there are severe limitations, the first of which is that the background is relatively high, as it is recorded over the whole of the large rotation range. This substantially degrades the signaltonoise ratio for the integrated intensities. In addition, the prediction of crystal orientation and hence reflection position, and of optimum rotation ranges, is less straightforward than for the rotation method. Finally, the handling of the imaging plates offline leads to limitations in the subsequent processing and analysis, already a problem in the initial orientation and evaluation of the sample.
Recent developments at the ESRF involve the use of a robot in changing and reading the plates (Wakatsuki et al., 1998), but this system has not been in operation long enough to lead to a sound judgement of its impact. In general, the Weissenberg method is at present not as widely used as the simpler rotation geometry.
References
Arndt, U. W. & Wonacott, A. J. (1977). Editors. The rotation method in crystallography. Amsterdam: North Holland.Kabsch, W. (1988). Evaluation of singlecrystal Xray diffraction data from a positionsensitive detector. J. Appl. Cryst. 21, 916–924.
Sakabe, N. (1991). Xray diffraction data collection system for modern protein crystallography with a Weissenberg camera and an imaging plate using synchrotron radiation. Nucl. Instrum. Methods A, 303, 448–463.
Wakatsuki, S., Belrhali, H., Mitchell, E. P., Burmeister, W. P., McSweeney, S. M., Kahn, R., Bourgeois, D., Yao, M., Tomizaki, T. & Theveneau, P. (1998). ID14 `Quadriga', a beamline for protein crystallography at the ESRF. J. Synchrotron Rad. 5, 215–221.