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Transmission electron microscopy in
materials science
Humboldt-Universität zu Berlin,
Institut für Physik, AG Kristallographie
Newtonstrasse 15, D-12489 Berlin
Telefon 030 2093 7868, Fax 030 20937760
E-mail: [email protected]
Web: http://crysta.physik.hu-berlin.de/ag_tem/
Raum 2‘403
A. Mogilatenko, H. Kirmse
pdf-Dateien der Vorlesungen unter:
http://crysta.physik.hu-
berlin.de/~kirmse/
Teaching
„Inorganic Materials"
Vorlesungen zur
Elektronenmikroskopie:
Teil 1, Teil 2
First TEM built in 1931 by
Max Knoll and Ernst Ruska
in Berlin
Nobel Prize in Physics 1986
First transmission electron microscope
1931: magnification 17
resolution > light microscope
1933: magnification 12.000
resolution < light microscope
Ray diagram in light microscopy and
TEM
lamp electrons
glass lens
glass lens
glass lens
eye
ocular
illumination
condensor lens
specimen
objective lens
projective lens
final image
first image
electromagnetic
lens
electromagnetic
lens
electromagnetic
lens
eye
fluorescent
screen
Ernst Abbe:
1840-1905
1866 - starts working with Carl Zeiss
1873 - theoretical description of
resolution limit
Theory of image formation and resolution
limit
sin2nd
: wavelength
n : refractive index of medium
between object and objective
: opening angle of rays originating
from object and collected by objective
„… it is poor comfort to hope that human ingenuity will find ways and
means of overcoming this limit.“
Resolution: Light Microscopy
no lens imperfections =>
resolution is limited by diffraction at edges of lens system
: wavelength
n: refractive index of medium
between object and objective
: opening angle of rays originating from object
and collected by objective
Light optics:
400 .. 800 nm
1 .. 1.5 (air .. immersion system)
70°
=> d ~ 250 nm
! To get a better resolution –
decrease the wave length! sin2n
d
Wave-Particle Duality Louis de Broglie, 1924
2
0
0
0
212
2
cm
eVeVm
h
eVm
h
p
h
V: acceleration voltage, m0: electron mass
e: electron charge, c: velocity of light
with 100 keV electrons travell
at about 1/2c!
!
Wave-Particle Duality
wave particle
imaging,
high resolution imaging,
diffraction
spectrometry
elastic ↔ inelastic coherent ↔ incoherent
Electron wavelength
V = 300kV => = 1.97 pm => resolution only ~ 0.1 nm ?
„magnetic lenses of TEMs have similar quality as
bottom of bottle of champagne would have for light microscope“
V / kV
/ p
m
How can I focus electron beam?
electric field E
electron charge e => force F
F = -e*E
force in opposite direction of electric field
magnetic induction B
electron velocity v => Lorentz force
F = -e(v x B)
force perpendicular to magnetic field and electron
velocity direction
E
B
Williams & Carter
Wine glass
with water =
optical lens with
huge aberrations
“if the lens in your own eyes would be as bad as
electromagnetic lenses, then you would be legally blind“
Electron lenses are
bad lenses too!!!
Magnetic electron round lens
optic
axis
lens
object
back focal
plane
image
plane
d1
d2
Brennebene Bildebene
optische
Achse
Ray diagram
Perfect imaging by a round lens
Objective lens Image plane
the same focus for all rays
Object
marginal ray
paraxial ray
Spherical aberration (Öffnungsfehler) - off-axis rays
are focused stronger!
Objective lens Image plane
marginal ray
paraxial ray
A point object is imaged as a disk of finite size –
limits the resolution!
marginal focus
paraxial focus
disk of least
confusion
Problems / disadvantages in TEM
damage dose:
living objects: 10-4 – 1 e/nm²
bio molecules: 103 – 105 e/nm²
anorganic substances: 106 – 1011 e/nm²
• time consuming specimen preparation is required
• only small sample regions can be investigated
(~ 1 nm…some µm)
• electron beam damage
Rose equation: links resolution d and contrast c c * d > 5/n0.5
n: number of electrons per unit area
example: c = 5 %; d = 0.3 nm => n > 105 e/nm²
Smeeton et al., Appl. Phys. Lett. 83 (2003) 5419
Electron beam induced segregation effects
Electron beam damage in InGaN QWs - In-clustering
thin crystalline specimen
primary electrons
elastically and inelastically scattered electrons
backscattered electrons
secondary electrons
X-rays
Electron Energy Loss Spectrometer
High-Angle Annular Dark-Field
Detector
Energy-Dispersive X-ray
Spectrometer
Electron Diffraction, Conventional imaging,
High resolution imaging
direct
beam
diffracted
beam
10…200 nm
100…400 keV
Electron forward scattering from thin specimen
thin specimen
coherent
incident beam
direct beam
coherent
elastic scattered
electrons
(1…10°)
incoherent
inelastic scattered
electrons
(< 1°)
incoherent
elastic
scattered
electrons
(> ~10°)
• single scattering
• plural scattering (>1)
• multiple scattering (>20)
Full width at
half maximum
Scattering of electrons
1 nm
Bulk material
12 nm
200 nm
50 nm
TEM specimen
Monte-Carlo Simulation of the paths
of electrons (acceleration voltage: 100 kV)
trough Silicon of different thicknesses
50 µm
Full width at
half maximum
IMAGING DIFFRACTION SPECTROSCOPY
Amplitude
contrast (diffraction
contrast)
Phase
contrast (high-
resolution
imaging)
Selected
area
diffraction
Energy
dispersive
X-ray
spectroscopy
Electron
energy loss
spectroscopy
Electron
holography
Z-contrast
imaging
Convergent
beam
diffraction
Micro-/
nano-
diffraction
Energy-filtered
TEM (EFTEM)
X-ray
mapping
TEM/STEM
Lorenz
microscopy Tomography
Why sample preparation for Transmission Electron
Microscopy
• Electrons with properties of particles and waves
• Strong interaction between electrons of the
beam and atoms of the samples scattering
• Sufficient intensity/number of transmitted
electrons only for small thickness (about 100 nm)
• Essential thickness depends on, e.g.,
materials properties, acceleration voltage, and
requirements of individual investigation method
Demands on sample preparation
• No change of materials properties including:
– Structure (amorphous, polycrystalline,
crystalline)
– Chemistry (composition of the bulk material,
of surfaces, and of interfaces)
• But:
Artifacts inherent in every preparation
method!
• Criterion of appropriate preparation technique:
Influence on structural and chemical
properties as small as possible!
Shape of the sample
• TEM sample holders
• Limits of sample size:
– Diameter: 3 mm
due to the furnace
of the TEM sample
holder
– Maximum
thickness of
sample edge: ca.
100 µm
Type of sample
• Structural properties
– size distribution of
entities
– area density
– structural defects
• Chemical properties
– composition
– modification
– interface sharpness
• Electronic properties
• Magnetic properties
• Particles
• Bulk material
• Epitaxial structures
Materials properties
• Hardness
• Sensitivity for
chemical solutions
Preparation strategy
Aim of investigation
TEM preparation of small particles
• Dispersion in a non
dissolving liquid (e.g.:
methanol, water, etc.) in an
ultrasonic bath
• Transfer to a carbon film
supported by a copper grid
Dipping Evaporation of a droplet
CaF2 with Pd particles (after reaction)
transmission electron microscopy bright-field image
Humboldt-Universität zu Berlin,
Institut für Physik (AG Kristallographie), Institut für Chemie (AG Festkörperchemie)
Pd-CaF_HF25_slotB2; hrtem01_particel01_ovw_3kx
Matrix (after reaction)
high-resolution transmission electron microscopy imaging
Humboldt-Universität zu Berlin,
Institut für Physik (AG Kristallographie), Institut für Chemie (AG Festkörperchemie)
Pd-CaF_HF25_slotB2; hrtem01_particle03_25kx
0.24 nm
Lattice plane distances d (nm)
CaF2 Pd PdF2 PdO
0.31541 0.22458 0.30756 0.30431
0.27315 0.19451 0.26868 0.26680
0.19314 0.13754 0.23832 0.26430
0.16472 0.11730 0.21748 0.21521
0.15770 0.11230 0.18834 0.20060
0.13657 0.09725 0.17757 0.16751
0.12533 0.08925 0.16061 0.15358
0.12216 0.08699 0.15378 0.15215
0.16 nm
0.27 nm
0.27 nm
0.16 nm
Plan-view and cross-sectional TEM
preparation
Ultrasonic disc cutting
Gluing of dummies
Mechanical thinning
Ion-beam milling
Dimpling
Gluing in a cylinder and sawing
face-to-face gluing
Formatting
Cross section (XTEM)
Thinning of substrate
Cutting of a disc
Dimpling
Ion-beam milling
Initial sample
Plan view (PVTEM)
Region 1
Region 2
Region 3
Beilby layer: change of chemical composition, strong deformation, amorphisation
~ 100 nm
macro-deformed layer:
tilt of grains,
increased dislocation density
micro-deformed layer:
weak tilt of grains,
dislocation density as grown
Situation after sawing
Next preparation step has to remove the damage!
Mechanical thinning damage
Principles of dimpling technique
Dimple grinding
Dimpler grinder of Gatan
sample
Detail of a dimple grinder
thickness in the
center ~ 20 µm
Ion-beam milling
Ion gun arrangement for milling of
both sides of the sample;
possible ions: Ar+, Xe+, I+, ...
acceleration voltage: 1...5 kV
usual angle : < 10°
Layout of a vacuum
chamber with two ion guns
sample
HRTEM of Ga(Sb,As) QD on (In,Ga)As seed QD TU#5294cs/2, links: qdot4_012c.jpg, rechts: qdot5_012c.jpg
Humboldt-Universität zu Berlin, Institut für Physik, AG Kristallographie
Forschungszentrum Jülich GmbH, Institut für Festkörperforschung
TEM Philips CM200 FEG cS, GaAs spacer thickness: 4.5 nm
Ga(Sb,As)
GaAs
GaAs
GaAs
(In,Ga)As
most important in
HRTEM most
important for
amorphous samples
most important
for crystalline samples
Contrast in TEM
Amplitude contrast: mass-thickness contrast total cross section Qtot for scattering from sample (thickness t):
Thicker and /or higher mass (Z) areas
will scatter more electrons and appear
darker in the image
! product is called „mass thickness“ t A
N Q tot
tot
t) 0 t
Avogadro number density
atomic weight of atoms total scattering cross section
of an isolated atom
Amplitude contrast: diffraction contrast
Bragg’s law: n·λ = 2·d·sinθ
Two beam conditions:
Tilting the specimen unitl direct
beam and one diffracted beam are
strong!
primary beam
sample
objective aperture
imaging plane
intermediate lenses projective lenses
objective lens
Phase contrast: high resolution TEM
multiple-beam
condition
2-beam
condition primary beam
sample
objective aperture
imaging plane
intermediate lenses projective lenses
objective lens
Phase shift due to the inner potential of
specimen
Path through the vacuum:
Eem2
Eem – Plancks constant
– electron mass
– electron charge
– electron energy
zyxVEme ,,2'
zyxV ,, – inner potential
energy
Path through the specimen:
d
Electron beam
Phase shift due to the inner potential of
specimen
x
local charge energy
atomic nucleus
mean inner potential
Plane wave
tr ,0
trObject ,
object exit wave
Plane wave
zyxV ,,
t
t dzzyxVyxV0
,,,projected potential:
(thin sample)
Phase shift due to the inner potential of
specimen
Phase shift:
zyxVdzdz
d ,,'
22
Ewith (interaction constant)
Total phase shift:
yxVdzzyxVd t ,,,
d
Electron beam
z
! phase change depends on potential V
which electrons see, as they pass
through sample
Role of optical system
transfer of each point in specimen into region in final image
f(x,y): specimen (transmission) function describes specimen
g(x,y): extended region of point x,y in image
h(r-r`): weighting term: point spread function
'''' rrtrfdrrrhrfrg
optical system
image g(x,y)=g(r)
f(x,y) point
disc
2 points
each point in final image has contributions
from many points in specimen
point
resolution
information
limit
u, [nm-1]
χ(u)uE sinuE
HRTEM: contrast transfer function
! opposite sign of T(u) - oposite contribution to
contrast
u < point resolution:
images are directly
interpretable
u > point resolution: no
direct interpretation is
possible
T(u)
No simple correspondence between the image
intensity and the atom column positions!
Additional calculations are necessary!
f - defocus
- wave length
Cs - spherical aberration
u - spatial frequency
432
2
1uCufu s
Example: HRTEM simulation for GaAs
projected
potential
by courtesy of Prof. Kerstin Volz
same thickness,
only defocus
change