Abstract
High-resolution transmission electron microscopy (HRTEM) comprises techniques of image formation by bright-field phase contrast with the aim of resolving the lattice fringes of a crystal lattice. There is no specific resolution threshold value separating “HR”-TEM from conventional TEM. Instead, the distinction is based on the fact that several diffracted beams are necessary to form the image of crystal planes. HRTEM is most important and powerful for studies of crystal defect structures in real space. For this, the aperture of the objective lens must be large enough to allow the diffracted beams corresponding to the projected crystal planes to pass and the passband of the contrast-transfer function (aberrations and incoherence envelopes) must extend sufficiently far. Many non-equivalent diffracted electron waves then build up an interference pattern in the image plane according to Abbe’s optical microscope theory. Conventional TEM, on the other hand, uses scattering around a single diffracted beam only. An HRTEM image pattern normally mirrors well the atomic geometry and symmetry of the material examined, but not necessarily the atom positions. Visual interpretation is therefore routinely assisted by computer simulations of the experimental image formation process. The image is correctly interpreted in terms of the atomic structure once the simulated and experimental image match sufficiently. For many years, experimental and simulated HRTEM images were compared visually, but recently interest has shifted towards digital and automated interpretation of the micrographs. This trend towards computer-controlled atomic-resolution structure retrieval (as opposed to just verifying or falsifying a few structure models) has three main motivations:
-
1.
Present trends in materials science. The need for accurate knowledge of the structure of crystal defects at atomic resolution has increased rapidly along with the engineering and designing of materials down to the nanometre scale. For example, the semiconductor device industry and fundamental research on quantum confinement rely on the knowledge and control of defect structure, such as interfaces, dislocations and composition fluctuations at the nanometre level. Nanostructured and nanocrystalline metals, alloys, and ceramics, and especially compound materials, thin films, and multilayered coatings likewise depend on atomic scale characterisation and control. Furthermore, the history of the development of “novel materisls” such as carbon nanotubes, high-temperature superconductors, magnetic nanostructures, or metallic quantum wires, was closely linked to their observation in the high-resolution electron microscope.
-
2
Progress in instrumentation. Several important milestones have been passed in the last ten years. Nwe ultra-resolution lens designs combining low spherical aberration with acceptable tilting ranges have been introduced for 200kV–300kV instruments. Field-emission guns now combine very high brightness with high spatial and temporal coherence. The development of very stable and comfortable high-voltage/high-resolution instruments has resulted in a point-resolution of about 1Å thanks to the reduction in wavelength at 1250kV. Finally, the most recent milestone was the demonstration of sub-1.4Å Scherzer-resolution by correcting the spherical aberration at 200kV. See Chap. 6 for more details. All these modern microscope techologies share the common advantage of pushing the information resolution limit (the ultimate detectable spatial frequency, independent of associated aberrations) to regions near or even below 1Å. The information resolution has become a major figure of merit now that image processing allows image evaluation techniques that are less dependent on a Rayleigh-type point resolution limit to be employed. The development of slow-scan CCD cameras and, more recently, the image palte system was another milestone; these complement the conventional photographic film, which can, however, still be reliably used for quantitative work combined with digitisation in a high-quality scanner. The revolutionary increase of CPU power over the last decade can be appreciated from the following numbers: Thecomputing time to convert one small defect structure model into one HRTEM-image on a stata-of-the-art laboratory workstation decreased from 2–3 hours in 1990 (e.g. DEC μ VAX II) to 10–20 seconds in 1999 (e.g. DEC Alpha AXP).
-
3
Progress in modelling of materials. The development of large-scale atomic modelling of defect structures now allows thousands of atomas to be included in a calculation cell, covering whole misfit dislocation networks at heterophase boundaries, for example. Methods of quantum chemistry and solid-state physics thus generate another challenge but also provide an important boost for HRTEM quantification : getting theory and experiment to agree on the Å -scale with accuracy of atom location on the pm-scale.
Access this chapter
Tax calculation will be finalised at checkout
Purchases are for personal use only
Preview
Unable to display preview. Download preview PDF.
References
Spence J.C.H. (1988) Experimental High Resolution Electron Microscopy. Oxford University Press, New York
Ibers J.A., Hamilton W.C. (Eds) (1974) International Tables for X-Ray Crystallography, Vol. IV. Kynoch, Birmingham.
Möbus G., Schweinfest R., Gemming T., Wagner T.,Rühle R. (1998) Iterative structure retrieval techniques: A comparative study and a modular program package. J Microsc, 190, 109–130
Gemming T., Möbus G., Exner M., Rühle M. (1998) Ab-initio high resolution electron microscopy: A case study of sapphire. J Microsc, 190, 89–98
Möbus G., Gemming T., Gumbsch P. (1998) Influence of phonon scattering on HRTEM-images. Acta Cryst A, 54, 83–90
Ishizuka K. (1980) Contrast transfer of crystal images in TEM. Ultramicroscopy, 5, 55–65
Stadelmann P. (1987) EMS a software package for electron diffraction analysis and HREM image simulation in materials science. Ultramicroscopy, 21, 131145
Möbus G., Rühle M. (1994) Structure determination of metal-ceramic interfaces by numerical contrast evaluation of HRTEM-micrographs. Ultramicroscopy, 56, 54–70
Marks L.D. (1985) Image localisation. Ultramicroscopy, 18, 33–38
Coene W., Jansen A.J.E.M. (1992) Image delocalisation in HRTEM. Scann Micr Suppl, 6, 379–403
Lichte H. (1991) Optimum focus for taking holograms. Ultramicroscopy, 38, 13–22
Decaro L., Giuffrida A., Carlino E., Tapfer L. (1995) Elastic stress relaxation in HRTEM specimens of strained semiconductor heterostructures. Microsc Microanal Microstr, 6, 465–472
Hÿtch M.J., Plamann T. (2000) Imaging conditions for reliable measurement of rapidly varying displacement and strain in HREM. Ultramicroscopy, 87, 199–212
Hÿtch M.J., Plamann T. (2000) Effect of the objective lens on the measurement of rapidly varying displacement fields from HRTEM images. Proceed. EUREM Brno, Czechia, 1, 119–120
Bierwolf R., Hohenstein M., Phillipp F., Brandt O., Crook G.E., Ploog K. (1993). Direct measurement of local lattic distortions in strained layer structures by HREM. Ultramicroscopy, 49, 273–285
Seitz H., Ahlborn K., Seibt M., Schröter W. (1998) Sensitivity limits of strain mapping procedures using HREM. J Microscopy, 190, 184–189
Wang S.Q. (1995) Atom: X-windows based software for quantitative analysis of atomic images. J Appl Cryst, 28, 837–839
Hofmann D. and Ernst F. (1994) Quantitative high-resolution transmission electron microscopy of the incoherent J’3(211) boundary in Cu. Ultramicroscopy, 53, 205–221
Kilaas R., Paciornik S., Schwartz A.J., Tanner L.E. (1994) Quantitative analysis of atomic displacements in HRTEM images. J Comp Assist Microsc, 6, 129–138
Bayle P., Thibault J. (1994) Quantitative HREM Study of [001] Au/Ni Multi-layers Proceed. ICEM, Paris, 1, 397–398
Robertson M.D., Currie J.E., Corbett J.M., Webb J.B. (1995) Determination of lattice strains in epitaxial layers in HRTEM. Ultramicroscopy, 58, 175–184
Rosenauer A., Remmele T., Fischer U., Forster A., Gerthsen D. (1997) Strain determination in mismatched semiconductor heterostructures by the digital analysis of lattice images. Inst Phys conf series, Bristol, UK, 157, 39–42
Hÿtch M.J. (1997) Analysis of variations in structure from HREM images by combination of real space and Fourier space information. Microsc Microanal Microstruct, 8, 41–57
C.J.D. Hetherington C.J.D., Dahmen U. (1992) An optical moiré technique for the analysis of displacements in lattice images Scann Microsc Suppl, 6, 405–414
Inkson B.J., Möbus G., Rühle M. (1997) Atomic-resolution electron microscopy of TiB2 precipitates in an industrial TiAl alloy. MRS Symp Proc, Boston, 466, 151–156
Möbus G., Wagner T. (1999) Direct versus iterative structure retrieval for a Cu/Ti misfit dislocation: A comparison of various 1A HREM Technologies. J Microsc, 194, 124–141
Paciornik S., Kilaas R., Dahmen U. (1993) Assessment of specimen noise in HREM images of simple structures. Ultramicroscopy, 50, 255–262
Möbus G., Necker G., Rühle M. (1993) Adaptive Fourier filtering technique for quantitative evaluation of high resolution electron micrographs of interfaces. Ultramicroscopy, 49, 46–65
Paciornik S., Kilaas R., Turner J., Dahmen U. (1996) A pattern recognition technique for the analysis of grain boundary structures by HREM. Ultramicroscopy, 62, 15–27
Kilaas R., Gronsky R. (1985) The effect of amorphous surface layers on imaging of crystals in HRTEM. Ultramicroscopy, 16, 193–201
Kienzle O., Ernst F., Möbus G. (1998) Reliability of atom column positions in a ternary system determined by quantitative HRTEM. J Micros, 190, 144–158
Hillebrand R. (1995) Quantitative analysis of HREM images: Measures of similarity. phys stat sol (a), 150, 65–76
Taupin D. (1988) Probabilities, data reduction and error analysis in the physical sciences. les editions de physique, Les Ulis Cedex, France
Hÿtch M.J., Stobbs W.M. (1994) Quantitative comparison of high resolution TEM images with image simulation. Ultramicroscopy, 53, 191–205
Hÿtch M.J., Stobbs W.M. (1994) Quantitative criteria for the matching of simulations with experimental HREM images. Microsc Microanal Microstruct, 5, 133–151
Boothroyd C.B. (1998) Why don’t high-resolution simulations and images match? J Micros, 190, 99–108
Press W.H. et al. (1992) Numerical Recipes, 2nd ed. Cambridge University Press, Cambridge, UK
Schwefel H-P. (1981) Numerical Optimization of Computer Models. J. Wiley, New York
Bäck T., Schwefel H-P. (1993) An overview of evolutionary algorithms for parameter optimization. Evolutionary Computation, 1, 1–23
Smith A.R., Eyring L. (1982) Calculation, display and comparison of electron microscope images modelled and observed. Ultramicroscopy, 8, 65–78
Barry J.C. (1989) Semiquantitative image matching in HRTEM. In W. Krakow and M. O’Keefe, Eds, Computer Simulation of Electron Microscope Diffraction and Images. The Minerals, Metals and Materials Society, Pennsylvania
Thust A., Urban K. (1992) Quantitative high-speed matching of high-resolution electron microscopy images. Ultramicroscopy, 45, 23–42
King W.E., Campbell G.H. (1993) Determination of thickness and defocus by quantitative comparison of experimental and simulated high-resolution images. Ultramicroscopy, 51, 128–135
Tang D., Kirkland A.I., Jefferson D.A. (1994) Optimization of high-resolution image simulations. Ultramicroscopy, 53, 137–146
Möbus G. (1994) Optimierung der digitalen Kontrastauswertung hochaufgelöster elektronenmikroskopischer Aufnahmen innerer Grenzfiächen. Dissertation, Universität Stuttgart, Germany
Möbus G., Gutekunst G., Mayer J., Rühle M. (1994) High precision iterative digital image matching and limitations of quantitative HRTEM. Proceed 13th Int Congr Electron Microscopy, Paris, France, 1, 373–374
Hofmann D., Möbus G., Ernst F. (1992) Quantitative HRTEM of incoherent twin boundaries in copper. Proceed Xth Europ Congr Electron Microscopy, Granada, Spain, 513–514
King W.E., Campbell G.H. (1993) Quantitative HREM study of the atomic structure of the J(310)/[001] symmetric tilt grain boundary in Nb. MRS Symp Proc, 295, 83–88
King W.E., Campbell G.H. (1994) Quantitative HREM using non-linear least-squares methods. Ultramicroscopy, 56, 46–53
Zhang H., Marks L.D., Wang Y.Y., Zhang H., Dravid V.P., Han P., Payne D.A. (1995) Structure of planar defects in (Sro.9Cao.3)i.1CuO2 infinite-layer superconductors by quantitative high-resolution electron microscopy. Ultra-microscopy, 57, 103–111
Möbus G., Dehm G. (1996) Retrieval of crystal defect structures from HREM images by simulated evolution: II experimental image evaluation. Ultramicroscopy, 65, 217–228
King W.E., Campbell G.H., Foiles S.M., Cohen D., Hanson K.M. (1998) Quantitative HREM observation of the E’11(113)/[110] grain-boundary structure in aluminium and comparison with atomistic simulation. J Microsc, 190, 131–143
Nadarzinski K., Ernst F. (1996) The atomistic structure of a Sigma=3,(111) grain boundary in NiAI studied by quantitative HRTEM. Phil Mag A, 74, 641–664
Höche T., Kenway P.R., Kleebe H-J., Rühle M., Morris P.M. (1994) High-resolution transmission electron microscopy studies of a near all grain boundary in a-alumina. J Amer Ceram Soc, 77, 339–348
Kienzle O., Ernst F., Möbus G. (1998) Reliability of atom column positions in a ternary system determined by high-resolution transmission electron microscopy. J Microsc, 190, 144–158
Schweinfest R., Ernst F., Wagner T., Rühle M. (1998) Quantitative HRTEM at the Al/MgAl2O4 interface. Proceed ICEM-14, Cancun/Mexico (IOP-publ., Bristol, UK), 1, 635–636
Möbus G. (1996) Retrieval of crystal defect structures from HREM images by simulated evolution: I basic technique. Ultramicroscopy, 65, 205–216
Merkle K.L., Csencsits R., Rynes K.L., Withrow J.P., Stadelmann P.A. (1993) The effect of the three-fold astigmatism on measurments of grain boundary volume expansion by HRTEM. J. Microscopy, 190, 204–213
Möbus G., Kienzle O. (1999) Interface structure retrieval by HREM: From entropy maximisation to r-factor fits. In Kiely, C.J., Edt, Proceedings of EMAG 1999, Sheffield, 263–266. IOP, Bristol, UK
Möbus G. (2000) Probability Calculus for quantitative HREM. Part II: Entropy and Likelihood concepts. Ultramicroscopy, 85, 199–213
Skilling J. (1998) Probabilistic data analysis: An introductory guide. J Microsc, 190, 28–36
Jaynes E.T. (1957) Information theory and statistical mechanics. Phys Rev, 106, 620–630
Buck B., Macaulay V.A. (1990) Maximum Entropie in Action. Oxford Science Publications, Oxford, UK
Möbus G., Kienzle O. (2000) Probability Calculus for quantitative HREM. Part I: Monte Carlo and Point Cloud Techniques. Ultramicroscopy, 85, 183–213
Ourmazd A., Baumann F.H., Bode M., Kim Y. (1990) Quantitative chemical lattice imaging: theory and practice. Ultramicroscopy, 34, 237–255
Schwander P., Kisielowski C., Seibt M., Baumann F.H., Kim Y.O., Ourmazd A. (1993) Mapping Projected Potential, Interfacial Roughness, and Composition in General Crystalline Solids by Quantiative Transmission Electron-Microscopy Phys Rev Lett, 71, 4150–4153
Stenkamp D., Jäger W. (1993) Compositional and structural characterization of SixGei_x alloys and heterostructures by HRTEM. Ultramicroscopy, 50, 321–354
Hillebrand R. (1998) Fuzzy logic approaches to the analysis of HREM images of III-V compounds. J Microscopy, 190, 61–72
Stenkamp D. (1998) Detection and quantitative assessment of image aberrations from single HRTEM lattice images. J Microscopy, 190, 194–203
Saxton W.O. (1978) Computer Techniques for Image Processing in Electron Microscopy. Academic Press, New York
Kirkland E.L. (1984) Improved high resolution image processing of bright field electron micrographs. Ultramicroscopy, 15, 151–172
Coene W., Janssen A., Op de Beeck M., Van Dyck D. (1992) Phase Retrieval Through Focus Variation For Ultra-Resolution in Field-Emission Transmission Electron-Microscopy Phys Rev Lett, 69, 3743–3746
Thust A., Coene W.M.J., Op de Beeck M., Van Dyck D. (1996) Focal-series reconstruction in HRTEM: Simulation studies on non-periodic objects. Ultra-microscopy, 64, 211–230
Lichte H. (1986) Electron holography approaching atomic resolution. Ultra-microscopy, 20, 283–304
Lehmann M. (2000) Determination and correction of the coherent wave aberration from a simple off-axis electron hologram by means of a genetic algorithm. Ultramicroscopy, 85, 165–182
Pennycook S.J., Jesson D.E. High-resolution incoherent imaging of crystals. Phys Rev Lett, 64, 938–941
Nellist P., Pennycook S. (1998) Accurate structure determination from image reconstruction in ADF STEM. J Microsc, 190, 159–170
Jansen J., Tang D., Zandbergen H.W., Schenk H. (1998) A least-square procedure for accurate crystal structure refinement from dynamical electron diffraction patterns. Acta Cryst A, 54, 91–101
Zuo J.M, Spence J.C.H. (1991) Automated structure factor refinement from convergent beam patterns. Ultramicroscopy, 35, 185–196
Lentzen M., Urban K. (1996) Reconstruction of the projected crystal potential from a periodic high-resolution electron microscopy exit plane wave function. Ultramicroscopy, 62, 89–102
Scheerschmidt K. (1998) Retrieval of object information by inverse problems in electron diffraction. J microscopy, 190, 238–248
Editor information
Editors and Affiliations
Rights and permissions
Copyright information
© 2003 Springer-Verlag Berlin Heidelberg
About this chapter
Cite this chapter
Möbus, G. (2003). Structure Determination by Quantitative High-Resolution Transmission Electron Microscopy. In: Ernst, F., Rühle, M. (eds) High-Resolution Imaging and Spectrometry of Materials. Springer Series in Materials Science, vol 50. Springer, Berlin, Heidelberg. https://doi.org/10.1007/978-3-662-07766-5_3
Download citation
DOI: https://doi.org/10.1007/978-3-662-07766-5_3
Publisher Name: Springer, Berlin, Heidelberg
Print ISBN: 978-3-642-07525-4
Online ISBN: 978-3-662-07766-5
eBook Packages: Springer Book Archive