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Duncan Alexander: Imaging with Diffraction Contrast
Imaging with Diffraction Contrast
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Duncan AlexanderEPFL-CIME
Duncan Alexander: Imaging with Diffraction Contrast
Introduction
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When you study crystalline samples TEM image contrast is dominated by diffraction contrast.
An objective aperture to select either the direct beam for a bright-field image,or diffracted beam(s) for a dark-field image.
The TEM image effectively maps spatially the intensity in this beam.
Changes in intensity are given by:- general crystal orientation relative to the electron beam, and crystal phase
- local changes in crystal orientation from crystal defects and bending- sample thickness changes.
These effects combine to give the diffraction contrast that are your TEM data.
Inherent connection to diffraction pattern of your specimen.
Duncan Alexander: Imaging with Diffraction Contrast
• Possible interactions of beam with specimen
• Only some lead to contrast in TEM image
Specimen
Inc
ide
nt
be
am
Auger electrons
Backscattered electronsBSE
secondary electronsSE Characteristic
X-rays
visible light
“absorbed” electrons electron-hole pairs
elastically scatteredelectrons
dire
ct
be
am
inelasticallyscattered electrons
BremsstrahlungX-rays
1-100 nm
Diffraction contrast?
Duncan Alexander: Imaging with Diffraction Contrast
Diffraction contrast?
Specimen
Inc
ide
nt
be
amBackscattered electrons
BSE
“absorbed” electrons
elastically scatteredelectrons
1-100 nm
dire
ct
be
am
inelasticallyscattered electrons
• Biological specimen with heavy metal stain: majority of contrast from “absorption of electrons.
• Sample of interest biologically, but physics of scattering are boring.
Duncan Alexander: Imaging with Diffraction Contrast
• Materials science specimen: CVD-grown ZnO thin film. Elastic scattering of the electrons (i.e. diffraction) by crystal is major contribution to contrast.
• Changes in crystal orientation from grain to grain or within grains at defects change the diffraction condition and hence the contrast.
Diffraction contrast?
Specimen
Inc
ide
nt
be
amBackscattered electrons
BSE
“absorbed” electrons
elastically scatteredelectrons
1-100 nm
dire
ct
be
am
inelasticallyscattered electrons
Duncan Alexander: Imaging with Diffraction Contrast
TEM imaging/diffraction modes recap
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Diffractionmode
Imagemode
Duncan Alexander: Imaging with Diffraction Contrast
Bright-field image vs dark-field image
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Bright-field image=
select direct beamwith objective aperture
Dark-field image=
select diffracted beamwith objective aperture
Duncan Alexander: Imaging with Diffraction Contrast
Nanocrystalline sample image/diffraction
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Image modeDiffraction mode
Bright field image setup - select direct beam with objective aperture
Contrast from different crystals according to diffraction condition
Duncan Alexander: Imaging with Diffraction Contrast
Nanocrystalline sample image/diffraction
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Image mode
Dark field image setup - select some transmitted beams with objective aperture
Diffraction mode
Only crystals diffracting strongly into objective aperture give bright contrast in image
Duncan Alexander: Imaging with Diffraction Contrast
Nanocrystalline sample image/diffraction
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Image mode
Dark field image setup - select some transmitted beams with objective aperture
Diffraction mode
Only crystals diffracting strongly into objective aperture give bright contrast in image
Duncan Alexander: Imaging with Diffraction Contrast
Nanocrystalline sample image/diffraction
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BF
DF A
DF B
DF images allow us to pick out individual grains
Duncan Alexander: Imaging with Diffraction Contrast
Diffraction contrast on/off zone axis
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In bright-field imaging, zone axis condition => more scattering to diffracted beamsTherefore intensity in direct beam goes down and bright-field image has strong contrast
Duncan Alexander: Imaging with Diffraction Contrast
Diffraction contrast on/off zone axis
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In bright-field imaging, zone axis condition => more scattering to diffracted beamsTherefore intensity in direct beam goes down and bright-field image has strong contrast
Example: GaN nanowire
Off zone axis
On zone axis
CBED SADP BF
CBED SADP BF
Duncan Alexander: Imaging with Diffraction Contrast 14
Diffraction contrast on/off zone axisIn bright-field imaging, zone axis condition => more scattering to diffracted beams
Therefore intensity in direct beam goes down and bright-field image has strong contrast
Example: GaN nanowire
BF off zone axis BF on zone axis
Duncan Alexander: Imaging with Diffraction Contrast
Image delocalization
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TEM image with no objective aperture. Image formed from direct beam and diffracted beams. Dark-field images from diffracted beams delocalize from bright-field image of
direct beam. Gives shadow images that move with objective focus (mostly result from Cs).
Duncan Alexander: Imaging with Diffraction Contrast 16
Image delocalization
Image of same nanowires but with objective aperture to make bright-field image. No diffracted beams => no shadow images.This is how you should take your TEM data!
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Image delocalizationTEM (multi-beam) image Bright-field image
Direction of delocalization depends on direction of diffracted beam in diffraction pattern
Duncan Alexander: Imaging with Diffraction Contrast
Dark-field imaging:displaced aperture vs beam tilt
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Duncan Alexander: Imaging with Diffraction Contrast
Bend contours
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From Williams & Carter Transmission Electron Microscopy
Duncan Alexander: Imaging with Diffraction Contrast 20
Bend contoursExample: electropolished Ni3Al superalloy
Sample at lower magnification.
Duncan Alexander: Imaging with Diffraction Contrast 21
Bend contoursExample: electropolished Ni3Al superalloy
Bright-field images. Same region at different sample tilts.See bend contours interacting with dislocations.
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Bend contoursExample: mechanically polished and ion beam milled silicon
Duncan Alexander: Imaging with Diffraction Contrast
Thickness fringes
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Thickness fringesDynamical scattering in the dark-field image –
=> Intensity zero for thicknesses t = nξg (integer n)
Composition changes in quantum wells=> extinction at different thickness compared to substrate
See effect as dark “thickness fringes” on wedge-shaped sample:
Duncan Alexander: Imaging with Diffraction Contrast
Phase contrast
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Example: electropolished Ni3Al superalloySimple cubic γ’ precipitates in FCC γ matrix
SADP simple cubic γ’ SADP FCC γ
0 0 01 0 0
2 0 0
0 0 0
2 0 0
Duncan Alexander: Imaging with Diffraction Contrast 25
Example: electropolished Ni3Al superalloySimple cubic γ’ precipitates in FCC γ matrix
SADP simple cubic γ’ Bright-field image
0 0 01 0 0
2 0 0
Phase contrast
Duncan Alexander: Imaging with Diffraction Contrast 26
Example: electropolished Ni3Al superalloySimple cubic γ’ precipitates in FCC γ matrix
SADP simple cubic γ’ Dark-field image g = 1 0 0
0 0 01 0 0
2 0 0
Phase contrast
Duncan Alexander: Imaging with Diffraction Contrast 27
Example: electropolished Ni3Al superalloySimple cubic γ’ precipitates in FCC γ matrix
SADP simple cubic γ’ Dark-field image g = 2 0 0
0 0 01 0 0
2 0 0
Phase contrast
Duncan Alexander: Imaging with Diffraction Contrast
Crystal defects: dislocations
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Burgers vector for edge (top right) and screw (bottom right) dislocations
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Crystal defects: dislocationsLocal bending of crystal planes around the dislocation change their diffraction condition
This produces a contrast in the image => g.b analysis for Burgers vector
From Williams & Carter Transmission Electron Microscopy
Duncan Alexander: Imaging with Diffraction Contrast
Crystal defects: dislocations - g.b analysis
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Invisibility criterion!
Duncan Alexander: Imaging with Diffraction Contrast
Crystal defects: dislocations - g.b analysis
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Sakai et al. APL 71 (1997) 2259
Example: threading dislocations in GaN
From visibility in for images a) to c) and near invisibility in d), dislocation B found to have:
b = ±1/3[2 -1 -1 3]or b = ±1/3[1 -2 -1 3]
Duncan Alexander: Imaging with Diffraction Contrast
Planar defects – stacking faults
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Similarly to Burgers vector analysis, stacking faults with displacement vector Rare invisible for g.R = 0
Example: analysis of basal plane stacking faults in ZnO
SADP on [1 1 00] zone axis Bright-field g = 1 -1 0 0 Dark-field g = 1 -1 0 0
g g
g parallel to R: stacking faults visible
Duncan Alexander: Imaging with Diffraction Contrast
Planar defects – stacking faults
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Similarly to Burgers vector analysis, stacking faults with displacement vector Rare invisible for g.R = 0
Example: analysis of basal plane stacking faults in ZnO
SADP on [1 1 00] zone axis Bright-field g = 0 0 0 2 Dark-field g = 0 0 0 2
g perpendicular to R: stacking faults invisible
g g
Duncan Alexander: Imaging with Diffraction Contrast
Amorphous? Or low diffraction contrast?
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Bright-field image of Al-Cr-N-O thin film
• Some regions show clear diffraction contrast, so obviously crystalline.
• Other regions did not. Combined with contrast from probable amorphous surface layer, looked amorphous.
• However CBED proved crystalline, just in low diffraction contrast condition.
Duncan Alexander: Imaging with Diffraction Contrast
Phase contrast, grain boundaries, bend contours, dislocations in one image
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Duncan Alexander: Imaging with Diffraction Contrast
Summary
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When imaging crystalline samples in the TEM, any change in the crystal will change the elastic scattering diffraction condition and hence intensity and contrast in the resulting image. This can be
from:- crystal orientation relative to the electron beam and deviations from bending
- defects in the crystal- changes in phase (e.g. precipitates)
- changes in thickness (dynamical scattering).
Using an objective aperture to select the direct beam (bright-field image) or diffracted beam (dark-field image) combined with carefully selected diffraction conditions gives many possibilities for
analysing and understanding your specimen.
Even without pursuing this you still have to learn to live with diffraction contrast and how it can unhelpfully affect your TEM data (e.g. bend contours). In this way TEM is not like other types of
microscopy!
No objective aperture => ill-defined diffraction condition and image delocalization!