High-resolution transmission electron microscopy

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High-resolution transmission electron microscopy (HRTEM) or (HREM) is an imaging mode of the transmission electron microscope (TEM) that allows for direct imaging of the atomic structure of the sample.[1][2] HRTEM is a powerful tool to study properties of materials on the atomic scale, such as semiconductors, metals, nanoparticles and sp2-bonded carbon (e.g., graphene, C nanotubes). While HRTEM is often also used to refer to high resolution scanning TEM (STEM, mostly in high angle annular dark field mode), this article describes mainly the imaging of an object by recording the 2D spatial wave amplitude distribution in the image plane, in analogy to a "classic" light microscope. For disambiguation, the technique is also often referred to as phase contrast TEM. At present, the highest point resolution realised in phase contrast TEM is around 0.5 ångströms (0.050 nm).[3] At these small scales, individual atoms of a crystal and its defects can be resolved. For 3-dimensional crystals, it may be necessary to combine several views, taken from different angles, into a 3D map. This technique is called electron crystallography.

One of the difficulties with HRTEM is that image formation relies on phase contrast. In phase-contrast imaging, contrast is not necessarily intuitively interpretable, as the image is influenced by aberrations of the imaging lenses in the microscope. The largest contributions for uncorrected instruments typically come from defocus and astigmatism. The latter can be estimated from the so-called Thon ring pattern appearing in the Fourier transform modulus of an image of a thin amorphous film.

Image contrast and interpretation[edit]

Simulated HREM images for GaN[0001]

The contrast of a HRTEM image arises from the interference in the image plane of the electron wave with itself. Due to our inability to record the phase of an electron wave, only the amplitude in the image plane is recorded. However, a large part of the structure information of the sample is contained in the phase of the electron wave. In order to detect it, the aberrations of the microscope (like defocus) have to be tuned in a way that converts the phase of the wave at the specimen exit plane into amplitudes in the image plane.

The interaction of the electron wave with the crystallographic structure of the sample is complex, but a qualitative idea of the interaction can readily be obtained. Each imaging electron interacts independently with the sample. Above the sample, the wave of an electron can be approximated as a plane wave incident on the sample surface. As it penetrates the sample, it is attracted by the positive atomic potentials of the atom cores, and channels along the atom columns of the crystallographic lattice (s-state model[4]). At the same time, the interaction between the electron wave in different atom columns leads to Bragg diffraction. The exact description of dynamical scattering of electrons in a sample not satisfying the weak phase object approximation (WPOA), which is almost all real samples, still remains the holy grail of electron microscopy. However, the physics of electron scattering and electron microscope image formation are sufficiently well known to allow accurate simulation of electron microscope images.[5]

As a result of the interaction with a crystalline sample, the electron exit wave right below the sample φe(x,u) as a function of the spatial coordinate x is a superposition of a plane wave and a multitude of diffracted beams with different in plane spatial frequencies u (spatial frequencies correspond to scattering angles, or distances of rays from the optical axis in a diffraction plane). The phase change φe(x,u) relative to the incident wave peaks at the location of the atom columns. The exit wave now passes through the imaging system of the microscope where it undergoes further phase change and interferes as the image wave in the imaging plane (mostly a digital pixel detector like a CCD camera). It is important to realize, that the recorded image is NOT a direct representation of the samples crystallographic structure. For instance, high intensity might or might not indicate the presence of an atom column in that precise location (see simulation). The relationship between the exit wave and the image wave is a highly nonlinear one and is a function of the aberrations of the microscope. It is described by the contrast transfer function.

The phase contrast transfer function[edit]

The phase contrast transfer function (CTF) is a function of limiting apertures and aberrations in the imaging lenses of a microscope. It describes their effect on the phase of the exit wave φe(x,u) and propagates it to the image wave. Following Williams and Carter,[6] if we assume the WPOA holds (thin sample) the CTF becomes

where A(u) is the aperture function, E(u) describes the attenuation of the wave for higher spatial frequency u, also called envelope function. χ(u) is a function of the aberrations of the electron optical system.

The last, sinusoidal term of the CTF will determine the sign with which components of frequency u will enter contrast in the final image. If one takes into account only spherical aberration to third order and defocus, χ is rotationally symmetric about the optical axis of the microscope and thus only depends on the modulus u = |u|, given by

where Cs is the spherical aberration coefficient, λ is the electron wavelength, and Δf is the defocus. In TEM, defocus can easily be controlled and measured to high precision. Thus one can easily alter the shape of the CTF by defocusing the sample. Contrary to optical applications, defocusing can actually increase the precision and interpretability of the micrographs.

The aperture function cuts off beams scattered above a certain critical angle (given by the objective pole piece for ex), thus effectively limiting the attainable resolution. However it is the envelope function E(u) which usually dampens the signal of beams scattered at high angles, and imposes a maximum to the transmitted spatial frequency. This maximum determines the highest resolution attainable with a microscope and is known as the information limit. E(u) can be described as a product of single envelopes:

due to

Es(u): angular spread of the source
Ec(u): chromatic aberration
Ed(u): specimen drift
Ev(u): specimen vibration
ED(u): detector

Specimen drift and vibration can be minimized in a stable environment. It is usually the spherical aberration Cs that limits spatial coherency and defines Es(u) and the chromatic aberration Cc, together with current and voltage instabilities that define the temporal coherency in Ec(u). These two envelopes determine the information limit by damping the signal transfer in Fourier space with increasing spatial frequency u

where α is the semiangle of the pencil of rays illuminating the sample. Clearly, if the wave aberration ('here represented by Cs and Δf) vanished, this envelope function would be a constant one. In case of an uncorrected TEM with fixed Cs, the damping due to this envelope function can be minimized by optimizing the defocus at which the image is recorded (Lichte defocus).

The temporal envelope function can be expressed as


Here, δ is the focal spread with the chromatic aberration Cc as the parameter:

The terms and represent instabilities in of the total current in the magnetic lenses and the acceleration voltage. is the energy spread of electrons emitted by the source.

The information limit of current state-of-the-art TEMs is well below 1 Å. The TEAM project at Lawrence Berkeley National Laboratory resultet in the first TEM to reach an information limit of <0.5 Å in 2009 [7] by the use of a highly stable mechanical and electrical environment, an ultra-bright, monochromated electron source and double-hexapole aberration correctors.

Optimum defocus in HRTEM[edit]

CTF of the OAM microscope

Choosing the optimum defocus is crucial to fully exploit the capabilities of an electron microscope in HRTEM mode. However, there is no simple answer as to which one is the best.

In Gaussian focus one sets the defocus to zero, the sample is in focus. As a consequence contrast in the image plane gets its image components from the minimal area of the sample, the contrast is localized (no blurring and information overlap from other parts of the sample). The CTF now becomes a function that oscillates quickly with Csu4. What this means is that for certain diffracted beams with a given spatial frequency u the contribution to contrast in the recorded image will be reversed, thus making interpretation of the image difficult.

Scherzer defocus[edit]

In Scherzer defocus, one aims to counter the term in u4 with the parabolic term Δfu2 of χ(u). Thus by choosing the right defocus value Δf one flattens χ(u) and creates a wide band where low spatial frequencies u are transferred into image intensity with a similar phase. In 1949, Scherzer found that the optimum defocus depends on microscope properties like the spherical aberration Cs and the accelerating voltage (through λ) in the following way:

where the factor 1.2 defines the extended Scherzer defocus. For the CM300 at NCEM, Cs = 0.6mm and an accelerating voltage of 300keV (λ = 1.97 pm) (Wavelength calculation) result in ΔfScherzer = -41.25 nm.

The point resolution of a microscope is defined as the spatial frequency ures where the CTF crosses the abscissa for the first time. At Scherzer defocus this value is maximized:

which corresponds to 6.1 nm−1 on the CM300. Contributions with a spatial frequency higher than the point resolution can be filtered out with an appropriate aperture leading to easily interpretable images at the cost of a lot of information lost.

Gabor defocus[edit]

Gabor defocus is used in electron holography where both amplitude and phase of the image wave are recorded. One thus wants to minimize crosstalk between the two. The Gabor defocus can be expressed as a function of the Scherzer defocus as

Lichte defocus[edit]

To exploit all beams transmitted through the microscope up to the information limit, one relies on a complex method called exit wave reconstruction which consists in mathematically reversing the effect of the CTF to recover the original exit wave φe(x,u). To maximize the information throughput, Hannes Lichte proposed in 1991 a defocus of a fundamentally different nature than the Scherzer defocus: because the dampening of the envelope function scales with the first derivative of χ(u), Lichte proposed a focus minimizing the modulus of dχ(u)/du[8]

where umax is the maximum transmitted spatial frequency. For the CM300 with an information limit of 0.8 Å Lichte defocus lies at −272 nm.

Exit wave reconstruction[edit]

Exit wave reconstruction through focal series

To calculate back to φe(x,u) the wave in the image plane is back propagated numerically to the sample. If all properties of the microscope are well known, it is possible to recover the real exit wave with very high accuracy.

First however, both phase and amplitude of the electron wave in the image plane must be measured. As our instruments only record amplitudes, an alternative method to recover the phase has to be used. There are two methods in use today:

  • Holography, which was developed by Gabor expressly for TEM applications, uses a prism to split the beam into a reference beam and a second one passing through the sample. Phase changes between the two are then translated in small shifts of the interference pattern, which allows recovering both phase and amplitude of the interfering wave.
  • Through focal series method takes advantage of the fact that the CTF is focus dependent. A series of about 20 pictures is shot under the same imaging conditions with the exception of the focus which is incremented between each take. Together with exact knowledge of the CTF the series allows for computation of φe(x,u) (see figure).

Both methods extend the point resolution of the microscope the information limit, which is the highest possible resolution achievable on a given machine. The ideal defocus value for this type of imaging is known as Lichte defocus and is usually several hundred nanometers negative.

See also[edit]

External links[edit]



  1. ^ Spence, John C. H (1988) [1980]. Experimental high-resolution electron microscopy. New York: Oxford U. Press. ISBN 0-19-505405-9. 
  2. ^ Spence, J. C. H.; et al. (2006). "Imaging dislocation cores - the way forward". Philos. Mag. 86: 4781–4796. Bibcode:2006PMag...86.4781S. doi:10.1080/14786430600776322. 
  3. ^ C. Kisielowski; B. Freitag; M. Bischoff; H. van Lin; S. Lazar; G. Knippels; P. Tiemeijer; M. van der Stam; S. von Harrach; M. Stekelenburg; M. Haider; H. Muller; P. Hartel; B. Kabius; D. Miller; I. Petrov; E. Olson; T. Donchev; E. A. Kenik; A. Lupini; J. Bentley; S. Pennycook; A. M. Minor; A. K. Schmid; T. Duden; V. Radmilovic; Q. Ramasse; R. Erni; M. Watanabe; E. Stach; P. Denes; U. Dahmen (2008). "Detection of single atoms and buried defects in three dimensions by aberration-corrected electron microscopy with 0.5 Å information limit". Microscopy and Microanalysis 14: 469–477. doi:10.1017/S1431927608080902. 
  4. ^ Geuens, P; van Dyck, D (Dec 2002). "The S-state model: a work horse for HRTEM.". Ultramicroscopy 3–4: 179–98. doi:10.1016/s0304-3991(02)00276-0. 
  5. ^ O'Keefe, M. A., Buseck, P. R. and S. Iijima (1978). "Computed crystal structure images for high resolution electron microscopy". Nature. nature (Nature (journal)) 274 (5669): 322–324. Bibcode:1978Natur.274..322O. doi:10.1038/274322a0. 
  6. ^ Williams, David B.; Carter, C. Barry (1996). Transmission electron microscopy: A textbook for materials science. New York: Plenum Press. ISBN 0-306-45324-X. 
  7. ^ "TEAM project web page". Retrieved 8 August 2013. 
  8. ^ Lichte, Hannes (1991). "Optimum focus for taking electron holograms". Ultramicroscopy 38 (1): 13–22. doi:10.1016/0304-3991(91)90105-F.