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1
Chemical and magnetic imaging with x-ray
photoemission electron microscopy (XPEEM)
Andrea Locatelli
Elettra – Sincrotrone Trieste, Italy
9/23/2013 1
9/23/2013 2
Why do we need photoelectron microscopy?
• To combine SPECTROSCOPY and MICROSCOPY to characterise the structural, chemical and magnetic properties of surfaces, interfaces and thin films
• Applications in diverse fields such as surface science, catalysis, material science, magnetism but also geology, soil sciences, biology and medicine.
BiologyMagnetismSurface Science
2
Outline
• Synchrotron radiation and x-ray spectro-microscopy: basics
• Cathode lens microscopy: methods
• Applications
– Chemical imaging: reactivity, characterization of nano-and micro- structured materials
– microXPS, microARPES: examples in Graphene research.
– Biology
– Magnetism
– Time-resolved XPEEM
9/23/2013 3
Why does PEEM need synchrotron radiation?
• High intensity of SR makes measurements faster
• Tuneability – very broad and continuous spectral range from IR to hard X-Rays
• Narrow angular collimation
• Coherence!
• High degree of polarization
• Pulsed time structure of SR – This adds time resolution to photoelectron spectroscopy!
• Quantitative control on SR parameters allows spectroscopy:• Absorption Spectroscopy (XAS and variants)
• Photoemission Spectroscopies (XPS, UPS, ARPES, ARUPS)
9/23/2013 4
),,,;,,,(ee
e
kinEhfJ ϕθσεν ΦΘ=
3
X-ray Absorption Spectroscopy
9/23/2013 5
)(ˆˆ42
2fffi
Er ρψεψωαπµ ⋅= h
The measurement of the absorption warrants:
� Elemental sensitivity.
� Sensitivity to final state
� Sensitivity to valence state, bondorientation, nearest-neighbour
� Magnetic sensitivity
� Buried layer and interfaces accessible
• SR-PEEM can easily implement XAS and its variants (NEXAFS, XMC/LD) by measuring the secondary electron yield as a function of the varying photon energy or photon helicity.
• NO ENERGY FILTER IS NEEDED IN PEEM
Resonances arise from transitions from core levels into unoccupied valence states via excitation processes occurring during the filling of the core hole.
X-ray Photoelectron Spectroscopy
9/23/2013 6
Φ−−= Bk EhE ν
The absorption of a photon ionizes the system, exciting one of the electrons into a free state in the continuum. The transition probability from the initial state to the final is proportional to:
)2
(ˆˆ4222
2
m
kEere
i
jkr
iik
hhh −+⋅∝ ωδψωαπτ
We measure the energy distribution of the photoelectrons emitted from the specimen.
EB is the binding energy of the initial state. EB is a unique fingerprint that allows determining the composition and chemical state of the specimen surface. This is the founding principle of ESCA and XPS (K. Siegbahn’s Nobel prize).
Main features: Elemental and chemical sensitivity (surface core level shifts), sensitivity to the electronic structure, sensitivity to local structure (micro-XPD), highest surface sensitivity
XPS mode: hv consthv in / e- out
Energy filter required!
4
Angle-Resolved Photoelectron Spectroscopy
9/23/2013 7
if
if
kk
hEE
≈+= ν
Another method, also possible using many XPEEM instruments, is that of measuring the momentum of the initial state. The electron analyzer allows us to measure both E and k of the final state, and thus to fully determine the initial state k.
When escaping into vacuum, the k component parallel to the surface is conserved.
2/2 hkinkinf
ikin
mEkk
hEE
==
Φ−+= ν
if kGk ////// =+
Φ−−=−−= ⊥⊥
kinb
kin
EhE
GWEmk
ν
20 /)(2 h
Φ−−=−=
kinb
ekin
EhE
WEmk
νθsin/)(2 2
0// h
3D ordered crystalline system 2D ordered crystalline system
In normal emission k// = 0
Examples
The two main approaches of x-ray microscopy
• Scanning: sequantial indirect imaging
• Lateral resolution determined by X-ray (diffractive) optics: 20-30 nm.
• Combination with TXM
• Excellent spectroscopic ability
• High pressure variants do exisits
• Rough surfaces
9/23/2013 8
e-
sample hv
electron opticswith energy filter
detector
hv
x-ray optics
sample scanning
stage
x-raydetector
electron analyzer
Scanning photoemission electron microscopy (SPEM)
X-ray photoemission electron microscopy (XPEEM)
• Direct imaging, parallel detection
• Lateral resolution determined by electron optics: with AC, few nm possible
• Combination with LEEM/LEED
• Intermediate spectroscopic ability
• Pmax < 5·10-5 mbar
• Flat surfaces
5
The probing depth is tuned by the electron energy
Inelastic mean free path (“universal curve”)
9/23/2013 9
By measuring
secondary Electrons
we probe thin films and buried interfaces to a maximum depth of several nm. This is the case of X-ray absorption spectro-scopy and its variants (NEXAFS, XMCD, XMLD).
By measuring Photoelectrons
emitted from core levels or the
valence band (XPS, ARPES, UPS, ARUPS) we achieve sensitivity to the topmost surface layers, especially when the K. E. Is in the range 50to 150 eV.
SR tuneability & photoionization cross sections
9/23/2013 10
Choosing the best photon energy for the experiment is of crucial importance to maximize surface / elemental sensitivity as well as obtaining favourable acquisition times
Graphene / Ru(0001)
Yeh and Lindau, Atomic Data and Nuclear
Data Tables 32, l-l 55 (1985)
6
Synchrotron Radiation basics
Beamline design
9/23/2013 11
Photon Sources at synchrotrons: undulators
9/23/2013 12
Insertion devices at the Elettra Synchrotron: Courtesy: B. Diviacco( ) nN
BBmc
e
n
uu
n
/1/
polesof numberN with ,N Intensity
1K [T];[cm]934.02
K
E(GeV)1957
)2
K1(
2
2
222
20
=∆=∝
<==
⋅=
++⋅=
λλ
λλπ
γ
θγγλλ
� High flux and wide energy range
� Horizontal, vertical and elliptocal polarization available
a period array of dipole magnets with alternating field direction normal to the plane of the ring;
γα /1<
7
Undulator spectrum
9/23/2013 13
An XPEEM Beamline layout: Nanospectroscopy
9/23/2013 14
Main concept: medium energy resolution, high flux beamline (1012-1013 ph/sec)
Highest flux density on the sample, micro-focus on sample!
Monochromator VLS grating design allows versatility, covering a wide photon enery range with few gratings.
8
Refocusing Optics
• Requirements
– Independent horizontal and vertical focusing
– Homogeneous micro spot
• Solution: Bendable Mirrors
– Adaptive mirrors (or “bendable” mirrors): a plane (or spherical) surface is bent to form an elliptical surface by applying unqeual moments to the mirror ends.
– Kirkpatric-Baez configuration
– Spot size: 2x6 μm2 HxV
9/23/2013 15
horizontal + verticalfocalization
P
Q
Kirkpatrick-Baez
A. Bianco, G. Sostero, and D. Cocco:Proc. SPIE 4782, 74 (2002).
Cathode lens microscopy methods
PEEM, LEEM, SPELEEM, AC-PEEM/LEEM
9/23/2013 16
9
PEEM basics: operating principle
9/23/2013 17
PEEM is a full-field, direct imaging technique. The microscope images a restricted portion of the specimen area illuminated by x-ray beam. Photoemitted electrons are collected at
the same time by the optics setup, which produces a magnified image of the surface. The key element of the microscope is the objective lens, also known as cathode or
immersion lens, of which the sample is part
dDiffdSP
dCH
The cathode lens
9/23/2013 18
1. In emission microscopy θ (emission angle) is large. Electron lenses can accept only small θ because of large chromatic and spherical aberrations
2. Solution of problem: accelerate electrons to high energy before lens → Immersion objective lens or cathode lens
Example for E = 20000 eV:E0 2 eV 200 eV
α for α0 = 45o 0.4o 4.5o
αααα 0 αααα
E
n sinθ = constn ∼ √E
θ → αsin α/sin α0 = √ E0/E
3. The aberrations of the objective lens and the contrast aperture size determine the lateral resolution
d = √ dSP2 + dCH
2 + dD2
dD = 0.6 λ/ rA
10
The different types of PEEM measurements
PEEM Probe Measurement
• threshold microscopy Hg lamp photoelectrons
• Laterally resolved XPS, micro-spectroscopy X-ray core levels or VB ph.el.
• Laterally resolved UPS, microprobe ARUPS and ARPESX-rays, He lamp VB photoelectrons
• Auger Spectroscopy X-ray, or electrons secondary electrons
• XAS-PEEM (XMC/LD-PEEM) X rays secondary electrons
9/23/2013 19
Require
energy filter
Simple PEEM instruments
9/23/2013 20
11
PEEM instrments with energy filter: NanoESCA
9/23/2013 21
9/23/2013 22
Low energy electron microscopy
LEEM is a cathode lens microscopy technique which probes surfaces and interfaces with low energy electrons, using the elastically backscattered beam for imaging. LEEM is particularly well suited to monitor dynamic processes, such as surface reconstructions, epitaxial growth, step dynamics, self-organization
E. Bauer: Low Energy Electron Microscopy, Rep. Prog. Phys. 57 (1994) 895-938.
12
Which properties does LEEM allow to probe?
9/23/2013 23
Different contrast mechanisms are available in LEEM for strucutre characterization
geometricphase contrast
STEP MORPHOLOGY
Mo(110)
quantum sizecontrast
d
FILM THICKNESS
Co/W(110)
diffractioncontrast
sample
contrastaperture
objective
[0,0]
[h,j]
SURFACE STRUCTURE
)
Imaging dynamic processes at surfaces
[001]
very favourable backscattering cross section at low electron energy!
Ni growth on W(110): formation of a striped phase above 1 ps ML Ni
Ni growth on W(110): step flow and completion of ps ML
540 < T < 750 C
13
sample
separator
analyzer
e-gun
SPEL
EEM
inst
rum
en
t o
n N
ano
spe
ctro
scop
y, e
lett
raLo
cate
lli e
t al
, Su
rf. I
nte
rfa
ce A
na
l. 3
8, 1
554
(20
06).
LEEM (low energy electron microscopy) Structure sensitivity
SPELEEM microscope (XPEEM + LEEM)
XPEEM (x-ray photoemission electron microscopy) Chemical and electronic structure sensitivity
Graphene formation on Ir(100)• Growth: large crystals for T > 800 C,
P=2·10-8 mbar ethylene.
• lattice gas � (1x5) lifted � enucleation of graphene islands
• Upon cooling a second distinct phase forms, appearing at about 520 °C.
9/23/2013 26
Fov 10 um, S.V. 6 eV, then 13 eV
Fov 4 um, S.V. 13 eV
14
Spectroscopic Photoemission and low energy Electron Microscope
9/23/2013 27
microprobe-diffraction
ARPES / LEED
microprobe-spectroscopy
XPS
Spectroscopic imaging
XPEEM / LEEM
Microprobe measurements are limited to surface areas of 2 microns in diameter!
Spectroscopic Photoemission and low energy Electron Microscope
9/23/2013 28
Performance: lateral resolution in imaging: 10nm (LEEM)
30 nm (XPEEM)
energy resolution: 0.3 eV (0.2 in microprobe spectroscopy)
Key feature: multi-method instrument to the study of surfaces and
interfaces, based on imaging and diffraction techniques.
Probe: low energy electrons (0-500 eV) structure sensitivi ty
soft X-rays (50-1000 eV) chemical state, magnetic s tate
electronic structure
Applications: characterization of materials at microscopic level
magnetic imaging of microstrucutres
dynamical processes
15
Correction of spherical and chromatic aberrations
9/23/2013 29
focalpoint
focalpoint
Round convex lenses
Chromatic aberration
Spherical aberration
Round concave lenses
Light optics
Correction of spherical and chromatic aberrations
9/23/2013 30
focalpoint
focalpoint
Round convex lenses
Chromatic aberration
Spherical aberration
Round concave lenses
Electron optics
V.K. Zworykin et al, Electron Optics and the Electron Microscope, John Wiley, New York 1945
Electron Mirror
16
9/23/2013 31
Resolution limit without correction
with correction
Spherical α3 + … α5
Chromatic ∆E α + … ∆E α2
+ ∆E2 α
Diffraction 1/α 1/α
ααααd
D. Preikszas, H. Rose, J. Electr. Micr. 1 (1997) 1Th. Schmidt, D. Preikszas, H. Rose et al., Surf.Rev.Lett 9 (2002) 223
Improvement with mirror corrector
Simultaneous improvement in
Transmission and Resolution!!!
9/23/2013 32
XPEEM-LEEM with aberration correction: SMART
17
9/23/2013 33
First results of the SMART microscope @BESSY
Courtesy of Th. Schmidt et al.; 5th Int. Conf. LEEM/PEEM, Himeji, 15.-19. Oct. 2006
50 nm
-2 0 -15 -1 0 -5 0 5 1 0 15 2 0
170
180
190
200
210
220
230
240
250
inte
nsity
d ista nce (nm)
3.1 nm
Atomic steps on Au(111), LEEM 16 eV, FoV = 444 nm x 444 nm
(18.09.06)
Lateral resolution limitations: space charge
9/23/2013 34
XPEEM: photocurrent
estimate for Au
440 bunches
rev. frequency: 1.157 MHz
bunch length: 42 ps (2GeV)
• 1 1013 ph./s on sample =
= 20000 ph./bunch
• Total photoionization yield: about 2% photons result in a photoemission event
• I peak ≈ 400 e-/ 42 ps
≈ 1.5µA vs 20 nA (LEEM)
13 pA/μm2 versus 20 nA/μm2
1. Image blur can be observed with SR, but only under very high photon fluxes. Keep into account in beamline design.
2. Both the lateral and energy resolution are strongly degraded by Boersch and Loeffler effects occurring in the first part of optical path.
Ultramicroscopy 111, 1447 (2011).
18
Space charge in XPEEM and microXPS with FEL radiation
SiO2/Si
patterns
FEL-PEEM
X-PEEM
5 µm16
14
12
10
8
6
4
2
0
1086420-2
kinetic energy (eV)
exit slit 80 µm exit slit 40 µm exit slit 20 µm
liner polarizationgap1 = 23.56gap2 = 41.4phase1 = 0phase2 = 0energy: 9.1 eV
circular
0.7
0.6
0.5
0.4
0.3
0.2
0.1
0.0
1086420
kinetic energy (eV)
x30
Ag/W(110)
X-PEEM
CHG-PEEM
Inte
nsity
(arb
. uni
ts)
L. Gregoratti, T.O. Mentes, A. Locatelli, M. Kiskinova,
J. Electron Spectrosc. Relat. Phenom. 170, 13-18 (2009) .
XPEEM Applications
Chemical imaging
9/23/2013 36
19
Au/TiO2(110): controlling growth by substr. stoichiometry
9/23/2013 37
Creation of ordered oxygen vacancies
MEMWork Function
(1x1) (1x2)
Stochiometric Irradiated
µ-LEEDstructure
Condens. Matter 19, 082202 (2007); Phys. Rev. B 76, 155413 (2007).
Collaboration with A. Kijena and T. Pabisiack (Wroclaw)
Irradiation at 720 K13 pA/μm2
Structure of the (1x2) TiO2
micro-LEED/IV
ongoing collaboration wih G. Held and Z.V. Zheleva
University of Reading
Au growth on TiO2(110)
1x2
1 ML
1x1 XPEEM@ Au 4f
µ-XPS
9/23/2013
Surface Oxygen on Ag : e-beam “Lithography”
Ful l oxidation of Ag using NO2 does not occur:
Low T: NOad stays , prevents oxidation.
High T: NOad desorbs,
but Ag2O unstable.
LEED reveqas path towards Ag2O under e-beam
S. Günther et al., Chem. Phys. Chem. 2010.
Ins tead: e-beam (60 eV) stimulated desorption of NOad works at RT!
S. Günther et al., App. Phys. Lett. 93, 233117 (2008).
A: metallic Ag
B: Ag2O
NO2 � NOad+Oad
20
9/23/2013
Surface Oxygen on Ag : photon-beam “Lithography”
S. Günther et al., Chem. Phys. Chem. 2010.
hv = 40 eV
(a) Start of NO2 adsorption, t = 0 s,
(b) t = 210 s, p(NO2) =1.8×10-7 mbar, 17 L NO2,
(c) t = 540 s, p(NO2) =2.5×10-7 mbar, 67 L NO2.
-9 eV 4 eV
MEM 28 μm x 350 μm; after 130 L NO2;
39
9/23/2013 40
Reactivity and electron confinement in Mg thin films
Thickness dependent reactivity? Film oxidation
inte
nsity
(a.u
.)
8 6 4 2 0binding energy (eV)
clean
~ 4.5L
~ 9L
~ 11L
~ 13L
valence band9ML Mg/W(110)
hν ν ν ν = 56 eV
Oxy
gen
dose
Inte
nsity
(a.
u.)
-4 -3 -2 -1 0 1E-EF (eV)
-6-4-2
E-E
F
5
6/7
8
9
10
11
12
EF
Γ Α Γ
SS
QWSQWSQWS
atomiclayers:
L. Aballe et al., Phys. Rev. Lett. 93, 196103 (2004)
Inte
nsi
ty (
Arb
. Un
its)
Inte
nsi
ty (
Arb
. Un
its)
Binding Energy (eV)
21
9/23/2013 41
Quantitative characterization of film oxidation
Iox/I tot
inte
nsi
ty (
a.u
.)
-54 -52 -50 -48 E-EF (eV)
-54 -52 -50 -48
Mg2phνννν = 112 eV
clean
~ 6L
~ 9L
~ 11L
~ 13L
7 ML 9 ML
O2e
xpo
sure
13
109
56
77
7
5 6
7
8
9
8
9
9
10
11
87
912
11
1310
12
15
10
9
11
12
11
14
10
7/8
9
12
9 10
LEEM reveals morphology
atomic thickness
1 µm
oxide component imaged by XPEEMreveals chemistry!
109
65
5
7 7
6
7
7 - 8
108-9
9
11
1012
7
89
6-8
7
11
13
13
12
15-14 12
9-10
11
6-812
9-10
8
L. Aballe et al., Phys. Rev. Lett. 93, 196103 (2004)
9/23/2013 42
Oxidation of Mg film and QWR
FACTS
� Strong variations in the oxidation extent are correleted to thickness and to the density of states at EF
� XPEEM is a powerful technique for correlating chemistry and electronic structure information
SIGNIFICANCE OF THE EXPERIMENTS
� Control on film thickness enables modifying the molecule-surface interaction
� Theoretical explanation: Decay length of QWS into vacuum is critical: it reproduces peak of reactivity in experimental data. See Binggeli and M. Altarelli, Phys.Rev.Lett. 96, 036805 (2005)
oxi
dat
ion
ext
en
tD
OS
at E
F
L. Aballe et al., Phys. Rev. Lett. 93, 196103 (2004)
22
9/23/2013 43
Spatio-temporal patterns in surface chemical reactions
Pattern formation
in surface chemical reactions
Jakubith et al., PRL 65, 3013 (1990)
rotating spirals
standing fronts
target waves
Belousov-Zabatinski reaction
(solution of, acidified bromate,
malonic acid, ceric salt)
See also: W. Engel, et al., Ultramicroscopy 36, 148–153 (1991).
9/23/2013 44
Reaction diffusion patterns: NO+H2 /Rh(110)
• First quantitative measurement of concentration profiles
Schaak et al Phys. Rev. Lett. 83, 1882 (1999)
O 1s
N 1s Rh 3d5/2
WF
Th. Schmidt et al.,
Chem. Phys. Lett. 318, 549 (2000)
(LEEM, micro-LEED )
23
9/23/2013 45
Reaction diffusion patterns: NO+H2 /Rh(110)
Structure + composition
(LEEM, micro-LEED )
Reactive phase separation processes
9/23/2013 46
F. Lovis et al., J. Phys. Chem. C 115, 19149 (2011)
Spectroscopic determination of the oxidation state
LEEM XPEEM Au 4f 7/2
2µm85.0 84 .0 83.0 82.0binding energy (eV)
Spectroscopic determination of reaction inducedredistribution
Au/Rh(110) during water formation reaction V/Rh(110) during water formation reaction
24
XPEEM Applications
Graphene and ARPES
9/23/2013 47
Micro-XPS mode - an example: C lattice-gas on Ru
9/23/2013 48
LEEM: changes in reflectivity allow to determine C lattice gas concentration
E. Loginova et al., N.J.Phys. 10, 093026 (2008)
XPEEM: direct measurement of C 1s spectrum
Guenther, Locatelli, Mentes; unpublished
Different BE for C 1s in Gr and C adatoms
Quantitative analysis!
25
Microprobe ARPES: Gr/Pt(111)
9/23/2013 49
Weak coupling! No hybridization of graphene’s π band with substrate d
states
Only Pt
Single layer Graphene on
Pt
Sutter et al., Phys Rev. B 80, 245411 (2009)
Micro-LEED
LEEM ARPES
microprobe-LEED
Graphene/Ir(100): existence of two distict phases
9/23/2013 50
–(b)
BrightfieldLEEM
IrBG FG
max
0
<010>
<001>
1 µm darkfieldLEEM
BG
FG
FG: flat graphene
BG: buckled graphene
A. Locatelli et al; ACS Nano, ACS Nano, 7, 6955–6963 (2013)
26
Graphene/Ir(100): existence of two distict phases
9/23/2013 51
BrightfieldLEEM
IrBG FG
max
0
<010>
<001>
1 µm darkfieldLEEM
BG
STM
FG
FG: flat graphene
BG: buckled graphene
A. Locatelli et al; ACS Nano, ACS Nano, 7, 6955–6963 (2013)
Ab-initio results: buckled graphene
9/23/2013 52
<100>
<010>
buckled graphene unit cell
Buckled Graphene
Exceptionally large buckling
GGA:
� Min Ir-C distance of 1.9 Å
� Max Ir-C distance of 4.0 Å
DFT-D:
� Min Ir-C distance of 2.1 Å
� Max Ir-C distance of 1.7 Å
� 18 atoms over 160 (i.e. 11%) are chemisorbed, the others are physisorbed
5.5 Ir units = 21.12 Å
5 Ir
uni
ts =
1.9
2 Å
A. Locatelli et al; ACS Nano, ACS Nano, 7, 6955–6963 (2013)
27
Laterally resolved XPS
9/23/2013 53
STM (200x200) RT
<001>
C 1s spectro-microscopy
chemisorbed
physisorbed
89%
284.82 eV
283.95 eV
11%
� Excellent agreement with theory, which predicts that 18 atoms over 160 (i.e. 11%) are chemisorbed!
� XPS says that the chemisorbed phase is present in small amount in FG (not resolved by LEEM, but in STM)
A. Locatelli et al; ACS Nano, ACS Nano, 7, 6955–6963 (2013)
Electronic structure by ARPES
9/23/2013 54
Issues: what i s the difference in electronic s tructure between FG and BG?
do they both show the same Dirac-like dispersion?
Diffraction Imaging microprobe-ARPES at EF
µ – ARPES
Γ
K
M
Experimental value of 0.42 eV
A. Locatelli et al; ACS Nano, ACS Nano, 7, 6955–6963 (2013)
28
Dark-field PEEM
9/23/2013 55
Menteş and Locatelli, J. El. Spec. Relat. Phenomena 2012.
Dark-field PEEM: DOS at the Fermi level point K
9/23/2013 56
� DF-PEEM maps the emission from the π band at K allowing us to quantify the local DOS of flat and buckled graphene phases.
� DF-PEEM images at EF clearly indicate that only FG shows high DOS at K. BG shows a much reduced DOS and inversion of contrast in the image at Γ. This points to strong hybridization, and thus to metallicity.
� Microprobe-ARPES data are thus representative of the FG phase, not the BG one!
µ – ARPES
Γ
M
XPEEM at Γ, EF
max
min
K
df-XPEEM at K, EF
FG
BG
Ir
A. Locatelli et al; ACS Nano, ACS Nano, 7, 6955–6963 (2013)
29
Application to life sciences
Biomineralization
9/23/2013 57
9/23/2013 58
Applications of XAS in biology: biomineralization
• Bio-mineralization resulting from microbal activity
• X-PEEM images of (A) non mineralized fibrils from the cloudy water above the biofilm (scale bar, 5 um)
• (B) mineralized filaments and a sheath from the biofilm (scale bar, 1 um); (bottom)
• X-PEEM Fe L-edge XANES spectra of the FeOOH mineralized looped filament shown in (B), compared with iron oxyhydroxide standards, arranged (bottom to top) in order of decreasing crystallinity.
P.U.P.A Gilbert et al. (ALS group),
Science 303 1656-1658, 2004.
30
Nano-scale architecture of Nacre
9/23/2013 59
Contrast is observed between adjacent individual nacre tablets, arising because different tablets have different crystal orientations with respect to the radiation’s polarization vector.
The 290.3 eV peak corresponds to the C 1s � Pi* transition of the CO bond. Synchrotron radiation is linearly polarized in the orbit plane. Under such illumination, the
intensity of the peak depends on the crystallographic orientation of each nacre tablet with respect to the polarization. This was the first observation of x-ray linear dichroism in a bio-mineral.
R.A. Metzler et al., Phys.Rev.Lett. 98, 268102 (2007)
Oxygen K-edge XAS image
Carbon K-edge XANESCarbon K-edge image
Absorption intensity at resonance
Magnietic imaging
XMCD and XMLD PEEM
9/23/2013 60
31
Magnetic imaging: XMCD
9/23/2013 61
X-ray magnetic circular dichroism (XMCD) is the dependence of x-ray absorption on the relative orientation of the local magnetization and the polarization vector of the circularly polarized light
�Element sensitive technique
� Secondary imaging with PEEM determine large probing depth (10 nm), buried interfaces.
�sum rules allows measuring orbital and spin moments
At resonance, the secondary electron yield is proportional to the dot product between the magnetization direction and the photon helicity vector, which is parallel or anti-parallel to the beam propagation direction according to the handedness of the circular polarizationhv
MnAs/GaAs Magnetic domain imaging SPELEEM microscopehv
FM
PM
16°
Owing to the illumination
geometry, we are sensitive to
the in plane component of M
XMCD principles
9/23/2013 62
– The spin moment is given by the
imbalance of spin-up and spin-down
electrons (holes).
– By using circularly polarized radiation, the
angular momentum of the photon can be
transferred in part to the spin through the spin-orbit coupling. Photoelectrons
with opposite spins are created in the
cases of left and right handed
polarization. Spin polarization is opposite
also for p3/2 (L3) and p1/2 (L2) levels.
– The spin-split valence shell is thus a detector for the spin of the excited
photoelectron. The size of the dichroism
effect scales like cosθ, where θ is the
angle between the photon spin and the
magnetization direction.
– Refs: IBM. J . Res. Develop. 42, 73 (1998) and J. Magn. Magn. Mater. 200, 470
(1999).
• We PROBE 3d elements by exciting 2p into
unfilled 3d states
Dominant channel: 2p � 3d
White line intensity of the L3 and L2 resonances
with the number N of empty d states (holes). So 3d
electrons determine the magnetic properties.
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Image algebra
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The size of the dichroism effect scales like cosθ, where θ is the angle between the photon spin and the magnetization direction. Hence the maximum dichroism effect (typically 20%) is observed if the photon spin and the magnetization directions are parallel and anti-parallel.
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Nano-characterization by XMCD-PEEM (imaging)
MAGNETIC STATE using XMCD & XMLD
Co nanodots on Si -Ge
A. Mulders et al,
Phys. Rev. B 71,
214422 (2005).
patterned s tructures
1.6 µmhv
M. Klaeui et al,
PRL , PRB 2003 - 2010
pulse injection
Laufemberg et al,
APL 88, 232507(2006).
domain wall motion induced by spin currents
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Spin configturations in Heusler alloys
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Co2FeAl 0.4Si0.6 rings
C.A.S. Vaz et al
Appl. Phys. Lett. 99, 182510 (2011)
Multi-domain to flux-closure states (favored by the shape anisotropy) with decreasing element size, with a thickness-dependent crossover at the micrometer scale.
La 0.7Sr0.3MnO3
J. Rhensius et al
Appl. Phys. Lett. 99, 062508 (2011)
Magnetic Imaging – present capability
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I Kowalik, D. Arvanitis, M.A. Niño et al.,
in preparation
Fe L3 edge (chemical) Fe L3 edge (XMCD)
nano-magnetism of (Ga,Fe)N films Magnetization in NiPd nanostructures
J.-Y. Chauleau, Phys. Rev. B 84, 094416 (2011)
34
Magnetic imaging basics: XMLD
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In the presence of spin order the spin-orbit coupling leads to preferential charge order relative to the spin direction, which is exploited to determine spin axis in antiferromagnetic systems.
�Element sensitive technique
� Secondary imaging with PEEM determine large probing depth (10 nm), buried interfaces.
�Applied in AFM systems (oxides such as NiO)
Absorption intensity at resonance SPELEEM microscopehv
16°
Linear vertical and linear
horizontal polarization of the
photon beam
1st term: quadrupole moment, i.e.electronic charge (not magnetic!)
2nd term determines XMLD effect; Ө is the angle between E and
magnetic axis A; XMLD max for E || A; M reflects long range
magnetic order
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Applications of XMCD and XMLD
Nature, 405 (2000), 767.
770 775 780 785 790 795 800
Photon Energy (eV)
705 710 715 720 725 730
Nor
mal
ized
Int
ensi
ty (
a.u.
)
Photon Energy (eV)
2 µm
LaFeO3 layerXMLD Fe L3
Co layerXMCD Co L3/L2
ferromagnet/antiferromagnet Co/LaFeO3
bilayer, demonstrating interface exchange
coupling between the two materials
35
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Limited probing depth of XMCD: MnAs/GaAs
180 nm MnAsExperiment: Straight walls; Head to head domains
Simulation: Cross sectional cut: diamond s tate R. Engel-Herbert et al, J. Magn. Magn. Mater. 305 (2006) 457
Adding the time domain to PEEM
TR-PEEM methods
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Time-resolved PEEM: the stroboscopic approach
Stroboscopic experiments combine high lateral resolution of PEEM with high time resolution, taking advantage of pulsed nature of synchrotron radiation
Choe et al., Science 304, 420 (2004)
Detector gating
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A. Locatelli et al., in preparation
37
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Time resolved XMCD-PEEM: applications
• Switching processes (magnetisation reversal) in magnetic elements ( in spin va lves, tunnel junction)
– Nucleation, DW propagation or both?– Effect of surface topography, morphology crystalline structure
etc.
– Domain dynamics in Landau flux closure s tructures.
• response of vortices, domains, domain walls in Landau closure domains in the precessional regime
• Stroboscopic technique:
– only reversible processes can be s tudied by pump – probe experiments
– Measurements are quantitative
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Magnetic excitations in LFC structures
xmcd
ti-t0
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Summary
• XPEEM is a versatile full-field imaging technique. Combined with SR it allows us to implement laterally resolved versions of the most popular x-ray spectroscopies taking advantage of high flux of 3rd generation SR light sources.
• In particular, XAS-PEEM combines element sensitivity with chemical sensitivity (e.g. valence), and, more importantly, magnetic sensitivity. Magnetic imaging has been the most successful application of PEEM (next tutorial lecture!).
• XPEEM or energy-filtered PEEM adds true chemical sensitivity to PEEM. Modern instruments allow to combine chemistry with electronic structure using ARUPS.
• XPEEM can be complemented by LEEM, which adds structure sensitivity and capability to monitor dynamic processes.
• Lateral resolution will approach the nm range as AC instruments become available. Limitations due to space charge are not yet clear
• Novel application field are being approached, such as biology, geology and earth sciences. HAXPES will increase our capabilities to probe buried structures (bulk).
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Review works
Some reviews and topical papers on x-ray spectromicroscopy and XPEEM• S. Guenther, B. Kaulich, L.Gregoratti, M. Kiskinova, Prog. Surf. Sci. 70, 187–260 (2002).
• E. Bauer, Ultramicroscopy 119, 18–23 (2012).
• E. Bauer, J. Electron. Spectrosc. Relat. Phenom. (2012): http://dx.doi.org/10.1016/j.elspec.2012.08.001
• G. Margaritondo, J. Electron. Spectrosc. Relat. Phenom. 178–179, 273–291 (2010) .
• A. Locatelli, E. Bauer, J. Phys.: Condens. Matter 20, 093002 (2008) .
• G. Schönhense et al., in “Adv. Imaging Electron Phys.”, vol. 142, Elsevier, Amsterdam, P. Hawkes (Ed.), 2006, pp. 159–323.
• G. Schönhense, J. Electron. Spectrosc. Relat. Phenom. 137–140, 769 (2004) .
• C.M. Schneider, G. Schönhense, Rep. Prog. Phys. 65, R1785–R1839 (2002) .
• W. Kuch, in “Magnetism: A Synchrotron Radiation Approach”, Springer, Berlin, E. Beaurepaire et al. (Eds.), 2006, pp. 275–320.
• J. Feng, A. Scholl, in P.W. Hawkes, “Science of Microscopy”, Springer, New York, J.C.H. Spence (Eds.), 2007, pp. 657–695.
• E. Bauer and Th. Schmidt, in “High Resolution Imaging and Spectroscopy of Ma-terials”, Springer, Berlin, Heidelberg, F. Ernst and M. Ruehle (Eds.), 2002, pp. 363-390.
• E. Bauer, J. Electron Spectrosc. Relat. Phenom. 114-116, 976-987 (2002).
• E. Bauer, J. Phys.: Condens. Matter 13, 11391-11405 (2001).