Coherent diffraction imaging

From Wikipedia, the free encyclopedia
Jump to navigation Jump to search
A diffraction pattern of a gold nanocrystal formed from using a nano area beam of coherent X-rays. This reciprocal space diffraction image was taken by Ian Robinson's Group to be used in the reconstruction of a real space coherent x-ray diffraction image in 2007.

Coherent diffractive imaging (CDI) is a "lensless" technique for 2D or 3D reconstruction of the image of nanoscale structures such as nanotubes,[1] nanocrystals,[2] porous nanocrystalline layers,[3] defects,[4] potentially proteins,[5] and more.[5] In CDI, a highly coherent beam of x-rays, electrons or other wavelike particle or photon is incident on an object.

The beam scattered by the object produces a diffraction pattern downstream which is then collected by a detector. This recorded pattern is then used to reconstruct an image via an iterative feedback algorithm. Effectively, the objective lens in a typical microscope is replaced with software to convert from the reciprocal space diffraction pattern into a real space image. The advantage in using no lenses is that the final image is aberration–free and so resolution is only diffraction and dose limited (dependent on wavelength, aperture size and exposure). Applying a simple inverse Fourier transform to information with only intensities is insufficient for creating an image from the diffraction pattern due to the missing phase information. This is called the phase problem.

The phase problem[edit]

There are two relevant parameters for diffracted waves: amplitude and phase. In typical microscopy using lenses there is no phase problem, as phase information is retained when waves are refracted. When a diffraction pattern is collected, the data is described in terms of absolute counts of photons or electrons, a measurement which describes amplitudes but loses phase information. This results in an ill-posed inverse problem as any phase could be assigned to the amplitudes prior to an inverse Fourier transform to real space.

Three ideas developed that enabled the reconstruction of real space images from diffraction patterns.[5] The first idea was the realization by Sayre in 1952 that Bragg diffraction under-samples diffracted intensity relative to Shannon's theorem.[6] If the diffraction pattern is sampled at twice the Nyquist frequency (inverse of sample size) or denser it can yield a unique real space image.[2] The second was an increase in computing power in the 1980s which enabled iterative hybrid input output (HIO) algorithm for phase retrieval to optimize and extract phase information using adequately sampled intensity data with feedback. This method was introduced[4] by Fienup in the 1980s.[7] Finally, the development of "phase recovery" algorithms led to the first demonstration of CDI in 1999 by Miao using a secondary image to provide low resolution information.[8] Reconstruction methods were later developed that could remove the need for a secondary image.

A simulated double wall nanotube (n1,m1)(n2,m2) can be used to test a CDI algorithm. First, a simulated nanotube is created (left) given the chiral numbers, (26,24)(35,25) in this case. Then a diffraction pattern is created by using the power spectrum function in Digital Micrograph software (middle). Finally, the algorithm is tested by reconstructing a final image (right). This work was performed by Ji Li and Jian-Min Zuo in 2007.


In a typical reconstruction[2] the first step is to generate random phases and combine them with the amplitude information from the reciprocal space pattern. Then a Fourier transform is applied back and forth to move between real space and reciprocal space with the modulus squared of the diffracted wave field set equal to the measured diffraction intensities in each cycle. By applying various constraints in real and reciprocal space the pattern evolves into an image after enough iterations of the HIO process. To ensure reproducibility the process is typically repeated with new sets of random phases with each run having typically hundreds to thousands of cycles.[2][9][10][11] The constraints imposed in real and reciprocal space typically depend on the experimental setup and the sample to be imaged. The real space constraint is to restrict the imaged object to a confined region called the "support". For example, the object to be imaged can be initially assumed to reside in a region no larger than roughly the beam size. In some cases this constraint may be more restrictive, such as in a periodic support region for a uniformly spaced array of quantum dots.[2] Other researchers have investigated imaging extended objects, that is, objects that are larger than the beam size, by applying other constraints.[12][13][14]

In most cases the support constraint imposed is a priori in that it is modified by the researcher based on the evolving image. In theory this is not necessarily required and algorithms have been developed[15] which impose an evolving support based on the image alone using an auto-correlation function. This eliminates the need for a secondary image (support) thus making the reconstruction autonomic.

The diffraction pattern of a perfect crystal is symmetric so the inverse Fourier transform of that pattern is entirely real valued. The introduction of defects in the crystal leads to an asymmetric diffraction pattern with a complex valued inverse Fourier transform. It has been shown[16] that the crystal density can be represented as a complex function where its magnitude is electron density and its phase is the "projection of the local deformations of the crystal lattice onto the reciprocal lattice vector Q of the Bragg peak about which the diffraction is measured".[4] Therefore, it is possible to image the strain fields associated with crystal defects in 3D using CDI and it has been reported[4] in one case. Unfortunately, the imaging of complex-valued functions (which for brevity represents the strained field in crystals) is accompanied by complementary problems namely, the uniqueness of the solutions, stagnation of the algorithm etc. However, recent developments that overcame these problems (particularly for patterned structures) were addressed.[17][18] On the other hand, if the diffraction geometry is insensitive to strain, such as in GISAXS, the electron density will be real valued and positive.[2] This provides another constraint for the HIO process, thus increasing the efficiency of the algorithm and the amount of information that can be extracted from the diffraction pattern.


Clearly a highly coherent beam of waves is required for CDI to work since the technique requires interference of diffracted waves. Coherent waves must be generated at the source (synchrotron, field emitter, etc.) and must maintain coherence until diffraction. It has been shown[9] that the coherence width of the incident beam needs to be approximately twice the lateral width of the object to be imaged. However determining the size of the coherent patch to decide whether the object does or does not meet the criterion is subject to debate.[19] As the coherence width is decreased, the size of the Bragg peaks in reciprocal space grows and they begin to overlap leading to decreased image resolution.

Energy sources[edit]


Coherent x-ray diffraction imaging (CXDI or CXD) uses x-rays (typically .5-4keV)[5] to form a diffraction pattern which may be more attractive for 3D applications than electron diffraction since x-rays typically have better penetration. For imaging surfaces, the penetration of X-rays may be undesirable, in which case a glancing angle geometry may be used such as GISAXS.[2] A typical x-ray CCD is used to record the diffraction pattern. If the sample is rotated about an axis perpendicular to the beam a 3-Dimensional image may be reconstructed.[10]

Due to radiation damage,[5] resolution is limited (for continuous illumination set-ups) to about 10 nm for frozen-hydrated biological samples but resolutions of as high as 1 to 2 nm should be possible for inorganic materials less sensitive to damage (using modern synchrotron sources). It has been proposed[5] that radiation damage may be avoided by using ultra short pulses of x-rays where the time scale of the destruction mechanism is longer than the pulse duration. This may enable higher energy and therefore higher resolution CXDI of organic materials such as proteins. However, without the loss of information "the linear number of detector pixels fixes the energy spread needed in the beam"[9] which becomes increasingly difficult to control at higher energies.

In a 2006 report,[4] resolution was 40 nm using the Advanced Photon Source (APS) but the authors suggest this could be improved with higher power and more coherent X-ray sources such as the X-ray free electron laser.

Simulated single wall carbon nanotube (left) is used to generate a diffraction pattern (middle) for reconstruction (right) algorithm testing. The top and bottom are different chirality tubes. This work was performed by Ji Li and Jian-Min Zuo in 2007.


Coherent electron diffraction imaging works the same as CXDI in principle only electrons are the diffracted waves and an imaging plate is used to detect electrons rather than a CCD. In one published report[1] a double walled carbon nanotube (DWCNT) was imaged using nano area electron diffraction (NAED) with atomic resolution. In principle, electron diffraction imaging should yield a higher resolution image because the wavelength of electrons can be much smaller than photons without going to very high energies. Electrons also have much weaker penetration so they are more surface sensitive than X-rays. However, typically electron beams are more damaging than x-rays so this technique may be limited to inorganic materials.

In Zuo's approach,[1] a low resolution electron image is used to locate a nanotube. A field emission electron gun generates a beam with high coherence and high intensity. The beam size is limited to nano area with the condenser aperture in order to ensure scattering from only a section of the nanotube of interest. The diffraction pattern is recorded in the far field using electron imaging plates to a resolution of 0.0025 1/Å. Using a typical HIO reconstruction method an image is produced with Å resolution in which the DWCNT chirality (lattice structure) can be directly observed. Zuo found that it is possible to start with non-random phases based on a low resolution image from a TEM to improve the final image quality.

LEFT Volume representation of a particle formed by a collection of octahedral Si nanoparticles, RIGHT The central slice showing the high degree of porosity.[3]

In 2007, Podorov et al.[20] proposed an exact analytical solution of CDXI problem for particular cases.

In 2016 using the coherent diffraction imaging (CXDI) beamline at ESRF (Grenoble, France), the researchers quantified the porosity of large faceted nanocrystalline layers at the origin of photoluminescence emission band in the infrared.[3] It has been shown that phonons can be confined in sub-micron structures, which could help enhance the output of photonic and photovoltaic (PV) applications.

Related techniques[edit]

Ptychography is a technique which is closely related to coherent diffraction imaging. Instead of recording just one coherent diffraction pattern, several – and sometimes hundreds or thousands – of diffraction patterns are recorded from the same object. Each pattern is recorded from a different area of the object, although the areas must partially overlap with one another. Ptychography is only applicable to specimens that can survive irradiation in the illuminating beam for these multiple exposures. However, it has the advantage that a large field of view can be imaged. The extra translational diversity in the data also means the reconstruction procedure can be faster and ambiguities in the solution space are reduced.

See also[edit]


  1. ^ a b c JM Zuo; I Vartanyants; M Gao; R Zhang; LA Nagahara (2003). "Atomic Resolution Imaging of a Carbon Nanotube from Diffraction Intensities". Science. 300 (5624): 1419–1421. Bibcode:2003Sci...300.1419Z. doi:10.1126/science.1083887. PMID 12775837. S2CID 37965247.
  2. ^ a b c d e f g IA Vartanyants; IK Robinson; JD Onken; MA Pfeifer; GJ Williams; F Pfeiffer; H Metzger; Z Zhong; G Bauer (2005). "Coherent x-ray diffraction from Quantum dots". Phys. Rev. B. 71 (24): 245302. arXiv:cond-mat/0408590. Bibcode:2005PhRvB..71c5302P. doi:10.1103/PhysRevB.71.245302.
  3. ^ a b c E. M. L. D. de Jong; G. Mannino; A. Alberti; R. Ruggeri; M. Italia; F. Zontone; Y. Chushkin; A. R. Pennisi; T. Gregorkiewicz & G. Faraci (24 May 2016). "Strong infrared photoluminescence in highly porous layers of large faceted Si crystalline nanoparticles". Scientific Reports. 6: 25664. Bibcode:2016NatSR...625664D. doi:10.1038/srep25664. PMC 4877587. PMID 27216452.
  4. ^ a b c d e M Pfeifer; GJ Williams; IA Vartanyants; R Harder; IK Robinson (2006). "Three-dimensional mapping of a deformation field inside a nanocrystal" (PDF). Nature Letters. 442 (7098): 63–66. Bibcode:2006Natur.442...63P. doi:10.1038/nature04867. PMID 16823449. S2CID 4428089.
  5. ^ a b c d e f S. Marchesini; HN Chapman; SP Hau-Riege; RA London; A. Szoke; H. He; MR Howells; H. Padmore; R. Rosen; JCH Spence; U Weierstall (2003). "Coherent X-ray diffractive imaging: applications and limitations". Optics Express. 11 (19): 2344–53. arXiv:physics/0308064. Bibcode:2003OExpr..11.2344M. doi:10.1364/OE.11.002344. PMID 19471343. S2CID 36312297.
  6. ^ D Sayre (1952). "Some implications of a theorem due to Shannon". Acta Crystallogr. 5 (6): 843. doi:10.1107/s0365110x52002276.
  7. ^ JR Fienup (1987). "Reconstruction of a complex-valued object from the modulous of its Fourier transform using a support constraint". J. Opt. Soc. Am. A. 4: 118–123. Bibcode:1987JOSAA...4..118Y. doi:10.1364/JOSAA.4.000118.
  8. ^ J Miao; P Charalambous; J Kirz; D Sayre (1999). "Extending the methodology of x-ray crystallography to allow imaging of micromere-sized non-crystalline specimens". Nature. 400 (6742): 342–344. Bibcode:1999Natur.400..342M. doi:10.1038/22498. S2CID 4327928.
  9. ^ a b c JCH Spence; U Weierstall; M Howells (2004). "Coherence and sampling requirements for diffractive imaging". Ultramicroscopy. 101 (2–4): 149–152. doi:10.1016/j.ultramic.2004.05.005. PMID 15450660.
  10. ^ a b H. N. Chapman; A. Barty; S. Marchesini; A. Noy; C. Cui; M. R. Howells; R. Rosen; H. He; J. C. H. Spence; U. Weierstall; T. Beetz; C. Jacobsen; D. Shapiro (2006). "High-resolution ab initio three-dimensional x-ray diffraction microscopy". J. Opt. Soc. Am. A. 23 (5): 1179–1200. arXiv:physics/0509066. Bibcode:2006JOSAA..23.1179C. doi:10.1364/JOSAA.23.001179. PMID 16642197. S2CID 8632057.
  11. ^ S. Marchesini; H. N. Chapman; A. Barty; C. Cui; M. R. Howells; J. C. H. Spence; U. Weierstall; A. M. Minor (2005). "Phase Aberrations in Diffraction Microscopy". IPAP Conference Series. 7: 380–382. arXiv:physics/0510033. Bibcode:2005physics..10033M.
  12. ^ S Marchesini (2008). "Ab Initio Undersampled Phase Retrieval". Microscopy and Microanalysis. 15 (Supplement S2): 742–743. arXiv:0809.2006. Bibcode:2009MiMic..15..742M. doi:10.1017/S1431927609099620. S2CID 15607793.
  13. ^ Leili Baghaei; Ali Rad; Bing Dai; Diling Zhu; Andreas Scherz; Jun Ye; Piero Pianetta; R. Fabian W. Pease (2008). "X-ray diffraction microscopy: Reconstruction with partial magnitude and spatial a priori information". J. Vac. Sci. Technol. B. 26 (6): 2362–2366. Bibcode:2008JVSTB..26.2362B. doi:10.1116/1.3002487.
  14. ^ Baghaei, Leili; Rad, Ali; Dai, Bing; Pianetta, Piero; Miao, Jianwei; Pease, R. Fabian W. (2009). "Iterative phase recovery using wavelet domain constraints". J. Vac. Sci. Technol. B. 27 (6): 3192. Bibcode:2009JVSTB..27.3192B. doi:10.1116/1.3258632. S2CID 10278767.
  15. ^ S. Marchesini; H. He; H. N. Chapman; S. P. Hau-Riege; A. Noy; M. R. Howells; U. Weierstall; J.C.H. Spence (2003). "X-ray image reconstruction from a diffraction pattern alone". Physical Review Letters. 68 (14): 140101(R). arXiv:physics/0306174. Bibcode:2003PhRvB..68n0101M. doi:10.1103/PhysRevB.68.140101. S2CID 14224319.
  16. ^ IA Vartanyants; IK Robinson (2001). "Partial coherence effects on the imaging of small crystals using coherent X-ray diffraction". J. Phys.: Condens. Matter. 13 (47): 10593–10611. Bibcode:2001JPCM...1310593V. doi:10.1088/0953-8984/13/47/305.
  17. ^ A. A. Minkevich; M. Gailhanou; J.-S. Micha; B. Charlet; V. Chamard; O. Thomas (2007). "Inversion of the diffraction pattern from an inhomogeneously strained crystal using an iterative algorithm". Phys. Rev. B. 76 (10): 104106. arXiv:cond-mat/0609162. Bibcode:2007PhRvB..76j4106M. doi:10.1103/PhysRevB.76.104106. S2CID 119441851.
  18. ^ A. A. Minkevich; T. Baumbach; M. Gailhanou; O. Thomas (2008). "Applicability of an iterative inversion algorithm to the diffraction patterns from inhomogeneously strained crystals". Phys. Rev. B. 78 (17): 174110. Bibcode:2008PhRvB..78b4110M. doi:10.1103/PhysRevB.78.174110.
  19. ^ Keith A Nugent (2010). "Coherent methods in the X-ray sciences". Advances in Physics. 59 (4): 1–99. arXiv:0908.3064. Bibcode:2010AdPhy..59....1N. doi:10.1080/00018730903270926. S2CID 118519311.
  20. ^ S. G. Podorov; K. M. Pavlov; D. M. Paganin (2007). "A non-iterative reconstruction method for direct and unambiguous coherent diffractive imaging". Optics Express. 15 (16): 9954–9962. Bibcode:2007OExpr..15.9954P. doi:10.1364/OE.15.009954. PMID 19547345.

External links[edit]