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Electronic structure changes in cobalt phthalocyanine due to nanotube
encapsulation probed using resonant inelastic X-ray scattering
Janine C. Swarbrick,*a Tsu-Chien Weng,a Karina Schulte,b Andrei N. Khlobystovc
and Pieter Glatzela
Received 10th February 2010, Accepted 15th April 2010
DOI: 10.1039/c002501a
The electronic structure of cobalt phthalocyanine (CoPc) changes upon encapsulation inside
multi-walled carbon nanotubes (CoPc@MWNT), as detected in this research using Co-K-edge
X-ray absorption near-edge structure spectroscopy (XANES) and Co-Ka1 resonant inelasticX-ray scattering (RIXS). The CoPc molecules are no longer planar once inside the nanotubes,
and the molecular symmetry is found to change upon encapsulation from D4h to C4v symmetry.
This change of symmetry increases the amount of p–d orbital mixing, which is seen in the spectra
as a change in peak intensity. Energy shifts are also seen between CoPc and CoPc@MWNT,
showing that Co in the encapsulated species is more oxidized due to electron donation from the
phthalocyanine molecule to the surrounding nanotube. Trends seen in the spectra between CoPc
and CoPc@MWNT can be calculated using density functional theory (DFT), which shows the
molecular orbitals involved in different spectral features.
1. Introduction
Phthalocyanines (Pcs) are metalloorganic macrocyclic molecules
with a readily tunable central metal atom. They have received
much attention due to their wide-ranging applicability in
cancer treatments,1 sensors2 and organic electronics3,4 amongst
other areas of research. Cobalt phthalocyanine (CoPc) (Fig. 1a)
is currently being studied in such fields as biosensors5 and
organic photovoltaics.6 The central Co2+ ion has an unpaired
3d electron, which also makes CoPc an interesting candidate
for magnetic applications.
The ability to encapsulate molecules, such as fullerenes,
phthalocyanines and rare earth compounds inside carbon
nanotubes has been achieved recently,7–9 producing a new
class of nanomaterials. The encapsulation of CoPc inside
multi-walled carbon nanotubes (CoPc@MWNT, Fig. 1) has
been performed,7 limiting the molecules to one-dimensional
arrangements and raising interesting possibilities for controlling
molecular arrays with magnetic character10,11 and optical
properties.12 Understanding the electronic properties of such
systems is vital for potential applications. This article describes
a hard X-ray absorption near-edge structure spectroscopy
(XANES) and resonant inelastic X-ray scattering (RIXS)
study of CoPc and CoPc@MWNT. Due to their size, CoPc
molecules can only be encapsulated in larger inner diameter
nanotubes, which are multi-walled (usually between two and
five carbon layers). Hard X-rays are a bulk sensitive probe and
as such the ‘buried’ Co atoms can be accessed without
significant signal attenuation.
XANES spectroscopy at the Co-K edge can be used to
determine the local coordination and oxidation state of the Co
atoms. The post edge peaks arise from 1s–4p and 1s–continuum
transitions.13,14 In systems with inversion symmetry, the pre-edge
arises from 1s–3d quadrupolar transitions; lower symmetry
causes p–d orbital mixing to occur.
To further investigate the electronic structure of the CoPc
systems, an X-ray emission spectrometer was used to record
RIXS planes. In this study the Co-K edge absorption features
were recorded over the Co-Ka1 emission line to give 1s–2p3/2RIXS planes. The incident energy can be tuned, as can the
detected emitted energy, to plot a 2-D RIXS plane. Here the
RIXS data is plotted against incident energy and energy
transfer (incident minus emission energy).
From the RIXS map, a line scan may be extracted along the
diagonal as shown in Fig. 3 which is the so-called high energy
resolution fluorescence detected (HERFD) absorption spectrum.
This HERFD spectrum shows essentially the same features as
the total fluorescence yield (TFY) XANES spectrum, but with
higher resolution due to the apparent reduction in the core-hole
lifetime broadening.15–17 The increase in the spectral resolution
obtained over TFY XANES, combined with a zero back-
ground count level due to detection using an avalanche
photodiode (APD) allow the pre-edge peaks to be more clearly
recorded and the spectral features to appear sharper.
2. Method
2.1 Experimental
The experiments were performed on the high brilliance X-ray
beamline ID26 at the European Synchrotron Radiation Facility
(ESRF). The electron energy was 6.0 GeV with a ring current
of 170–200 mA. A monochromator employing a pair of
Sih311i single crystals was used to choose the incident energy
for access to the Co edge at 7709 eV. Higher harmonics were
suppressed using two Si mirrors at 2.5 mrad. The beam size
was approximately 0.3 mm vertically � 0.9 mm horizontally.
a European Synchrotron Radiation Facility (ESRF), BP 220,F-38043, Grenoble Cedex 9, France. E-mail: [email protected]
b Lund University, MAX-lab, P.O. Box 188, SE-221 00 Lund, Swedenc School of Chemistry, University of Nottingham, University Park,Nottingham, NG7 2RD, UK
This journal is �c the Owner Societies 2010 Phys. Chem. Chem. Phys., 2010, 12, 9693–9699 | 9693
PAPER www.rsc.org/pccp | Physical Chemistry Chemical Physics
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The Co-Ka1 emission line at 6931 eV was measured using a
vertical Rowland circle spectrometer using the (531) reflection
of a spherically bent Si Bragg crystal analyzer of 1 m bending
radius crystal. The Bragg angle was 771. Co-Ka1 RIXS
spectra were measured by recording the Co-K absorption edge
between 7707 and 7720 eV over the Co-Ka1 emission line. The
standard TFY XANES was also recorded with a photodiode.
Emitted photons were detected in the emission spectrometer
using a 100 mm APD. The emission spectrometer energy
bandwidth was found to be 0.6 eV taken from the full width
at half maximum (FHWM) of the elastic peak taken at
7700 eV.
Radiation damage studies were performed at room
temperature by measuring rapid (5 s) XANES spectra at the
pre-edge region and monitoring any shift in the pre-edge peak
shape and intensity, and any shift of the edge. For all samples,
no change was observed over 30 min and all measurements
were taken on sample spots exposed for less than 30 min.
Energy calibration of the monochromator was performed by
recording the XANES spectrum of a Co metal foil.
2.2 Synthesis
CoPc (97% purity) was purchased from Sigma Aldrich and
used without further purification for the CoPc samples. Thin
multi-walled carbon nanotubes (MWNT) were obtained from
Nanocyl, having an average outer diameter of 7–10 nm.
Purified carbon nanotubes were first oxidized in air at
400 1C for 40 min, resulting in a weight loss of around 40%.
This thermal treatment opens the nanotube caps and also
partly removes amorphous carbon from the surface of the
tubes. They were then mixed with an excess of sublimation
purified CoPc in a quartz tube, sealed in a vacuum of 10�6 Torr
and heated at 375 1C for three days. CoPc that had settled on
the outside of the nanotubes was successfully removed
by repeated rinsing with a mixture of chloroform and 1%
trifluoroacetic acid. A control sample was also prepared by
mixing the nanotubes and CoPc only with no encapsulation
treatment. The resulting powder samples were prepared for
study using X-rays by being pressed into pellets.
2.3 Calculations
Density functional theory (DFT) calculations were performed
in the ORCA code18 to model the transitions seen in the
XANES spectra. The input structure is that proposed in
ref. 19. The BP86 method was employed with a TZVP basis
set. A finer grid was used over the Co atom, as was a CP(PPP)
basis set. Quadrupolar transitions were included. A broadening
of 1 eV was applied to the calculated transitions.
3. Results and discussion
3.1 TFY XANES
Co-K edge TFY XANES for CoPc, a CoPc/MWNT mixture
and CoPc@MWNT are shown in Fig. 2. The Co-K edge
shows the unoccupied states close to the Fermi level. The
spectra have been normalised using the edge jump of the
EXAFS region. The count rates obtained were similar for all
samples, thus the signal from Co in the CoPc@MWNT and
CoPc/MWNT mixture samples was not significantly attenuated
due to the surrounding C atoms, which can be problematic in
surface-sensitive soft X-ray studies. The spectra are very
similar for all compounds, demonstrating that the molecular
structure has not been changed significantly upon mixing or
encapsulation (to the extent that the molecule has broken up
or become destroyed). Here the pre-edge peaks (between
7706–7712 eV) and the edge peak, which is characteristic of
Pc molecules (between 7714–7717 eV),14 are discussed. The
largest edge peak intensity at 7715.5 eV is observed for the
CoPc reference sample, with the CoPc@MWNT having the
lowest intensity edge peak. It is difficult to see changes in the
pre-edge region as these peaks are very low intensity and are
not well resolved. Co-Ka1 RIXS plots (vide infra) are used to
show spectral details in the pre-edge region.
The differences in relative peak intensity should be discussed
in relation to self-absorption effects. The samples are concen-
trated bulk powders and as such the spectra may appear
artificially flattened at higher energy due to self-absorption.
However self-absorption would affect the spectral intensity
above the edge more than the pre-edge, which has a lower
absorption cross-section. Self-absorption effects would also be
expected to affect the spectrum of CoPc the most as it has the
highest proportion of Co, which is the strongest absorber in
these samples. However, the CoPc sample shows the strongest
edge peak, so these relative intensity differences do not originate
from self-absorption, but are real spectroscopic changes.
Fig. 1 Schematic diagram of (a) the CoPc molecule and (b) schematic structure of CoPc@MWNT (only one NT layer is shown).
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3.2 Co-Ka1 RIXS planes
To obtain further information on the transitions being probed,
the Co-Ka1 RIXS planes were recorded for the three samples.
Fig. 3(a) shows a schematic with the electronic transitions
involved in recording a Ka RIXS plane. In the Ka RIXS
process a 1s core electron is excited into the localized unoccupied
states just above the Fermi level. A 2p electron relaxes to fill
the core-hole (the relaxation of the 2p3/2(2p1/2) electron gives
the Ka1(Ka2) line). The overall energy transferred to the
system is the incident energy O minus the emitted energy o.In this study we only measure transitions over the stronger
Ka1 emission line.
The Co-Ka1 RIXS plane for CoPc is shown in Fig. 3(b). The
pre-edge peaks are seen in the 7706–7712 eV incident energy
range and 779–784 eV energy transfer range. The edge peak is
seen between 7714–7717 eV incident energy and 785–789 eV
energy transfer. Above 7718 eV incident energy and 789 eV
energy transfer the intensity arises from transitions to the
continuum (post-edge). The diagonal line along the maximum
intensity of the edge peak and continuum features represents
the cut along which a HERFD spectrum can be extracted.
In the RIXS plane (and the extracted HERFD line scan), the
pre-edge transitions are clearer due to the higher resolution
compared with TFY XANES. Thus we will focus on this
region of the RIXS plane to obtain information on the
pre-edge, and hence on the unoccupied electronic levels just
above the Fermi level.
3.3 Co-Ka1 RIXS over the Co-K pre-edge
The Co-Ka1 RIXS planes over the pre-edge peak region are
shown for the three samples in Fig. 4. It can be seen that the
pre-edge peaks are similar for CoPc and a CoPc/MWNT
mixture, which is expected as most of the CoPc in the mixture
sample is still in the bulk phase since no special treatment was
used. The two main pre-edge peaks are at the same energy for
both samples, and have similar intensities. The main difference
between the two can be seen as a broadening of the second
pre-edge peak in a CoPc/MWNT mixture around 7710.5 eV
incident energy, but the main features are the same. The pre-edge
for CoPc@MWNT, however, is very different with two
pre-edge peaks rather than three. The CoPc@MWNT Ka1RIXS shows a strong pre-edge peak at 7709.8 eV incident
energy. The lower energy pre-edge peak around 7708 eV for
CoPc and a CoPc/MWNT mixture is shifted to higher energy
in CoPc@MWNT to 7708.4 eV, a shift of 0.4 � 0.1 eV. This
shift is revisited in the HERFD spectral analysis later.
If HERFD spectra are to be used for detailed analysis it is
important to ensure the equivalence of the features measured
in the HERFD spectra compared with those measured in TFY
XANES. The full RIXS plane should be recorded to understand
the energy position and shape of the peaks. In these RIXS
planes it can be seen that the pre-edge peaks are not aligned
along the HERFD diagonal. The diagonal is positioned along
the maxima of the post-edge and edge peak as shown in
Fig. 3(b). The HERFD diagonal passes through the center
Fig. 2 TFY XANES spectra for the three CoPc samples.
Fig. 3 (a) Schematic of the electronic excitations involved in measuring
Co-Ka RIXS planes. O in the incident energy and o is the emitted
energy. (b) Co-Ka1 RIXS plane for CoPc. The diagonal dashed line
shows the cut which gives a HERFD spectrum. The dotted line box
indicates the pre-edge region shown in detail in Fig. 4.
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of the first pre-edge peak but is below the second peak in the
energy transfer direction. Firstly, this shows that the HERFD
spectra are not simply a higher resolution version of the TFY
XANES scan since the full intensity of the second pre-edge
peak is not recorded in the HERFD line scans. The second
peak is at higher energy transfer, which relates to final state
interactions, electron-electron interactions and core-hole effects.
3.4 HERFD line scans
The HERFD line scans over the pre-edge and edge peak,
extracted from the Co-Ka1 RIXS planes, are shown in Fig. 5
alongside the equivalent TFY XANES spectra. The increase in
resolution is apparent in the HERFD spectrum. Also shown is
the first pre-edge peak extracted from the RIXS planes by
integrating over the final states in the range 778.8–780.7 eV
(see Fig. 4). This peak can be used as an indicator of the shift
in incident energy between the samples.15 Using the method in
ref. 20 for estimating the overall spectral broadening from
core-hole lifetimes and experimental considerations (using a
monochromator with resolving power 35 000 and an emission
spectrometer energy bandwidth of 0.6 eV), the overall
HERFD peak broadening using the Co-Ka1 line was calculatedto be 0.42 eV.
Differences in resolution in the pre-edge region between the
TFY XANES and HERFD spectra are clear. The main edge
and edge peak at 7715.5 eV follow the same trend in both TFY
XANES and HERFD. Using the HERFD technique the
pre-edge peak is better separated from the main edge and
facilitates peak identification.13 As seen in the Co-Ka1 RIXS,
the CoPc/MWNT mixture sample has a more intense second
pre-edge peak which starts to merge with the third peak at
around 7709.6 eV, but the shape is still similar to that of CoPc.
The CoPc@MWNT sample has a differently shaped pre-edge
with two main peaks, of which the second one at 7709.8 eV is
Fig. 4 Co-Ka1 RIXS planes over the pre-edge for (a) CoPc (b) a
CoPc/MWNT mixture and (c) CoPc@MWNT. HERFD diagonal
cuts are shown as in Fig. 3, and the pre-edge peaks are clearly seen.
The horizontal dashed lines mark the upper bound of the region of
integration (778.8–780.7 eV) used to show the energy position of the
first pre-edge peak (see Fig. 5).
Fig. 5 TFY XANES pre-edge and edge region compared to HERFD
spectra taken using the Co-Ka1 emission line for the three CoPc
samples. The pre-edge is magnified �5 to show the peaks more clearly.
Also shown is the integrated intensity over the first pre-edge peak from
the RIXS planes to demonstrate the shift in incident energy between
the samples.
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around twice as intense that the corresponding peak(s) from
CoPc or a CoPc/MWNT mixture.
Considering the edge peak at 7715.5 eV, we see the reverse
trend in intensity to that seen in the pre-edge. The highest peak
intensity is seen for CoPc. A slightly lower peak intensity is
observed for a CoPc/MWNT mixture, and the same peak
measured for CoPc@MWNT has much lower intensity, is
broader, and appears at slightly higher incident energy. The
combination of an increased pre-edge intensity, and a decrease
in the edge peak intensity for CoPc@MWNT shows a change
in the p–d orbital mixing due to encapsulation.
There is a small shift to higher incident energy of the first
pre-edge peak in CoPc@MWNT compared to CoPc or
a CoPc/MWNT mixture, as seen most clearly using the
integrated intensity of the first pre-edge peak taken from
the RIXS planes. This peak is a reliable indicator of the
energy position as it represents the localized Co unoccupied
electronic levels and thus the Co electronic structure. A
clear shift to higher incident energy is seen in this first
pre-edge for CoPc@MWNT compared with the non-encapsulated
samples, which is consistent with a more oxidized Co species
in CoPc@MWNT. Encapsulated molecular species are
found to be more oxidized in previous soft X-ray studies
of CoPc,21 cobaltocene22 and fullerenes.23 Electron density is
donated from the encapsulated species to the surrounding
nanotube.
The peak shifts seen in the CoPc@MWNT data are subtle,
which can be understood in terms of the arrangement of
CoPc inside the nanotubes. From previous studies8 it is
understood that the CoPc molecules arrange inside the
nanotube so as to stack similarly (at least over a short range)
to the packing in the bulk a-phase, shown schematically in
Fig. 1. Thus the Co atom is not located close to the surrounding
nanotube. While the Co atom ‘feels’ the effect of electron
donation to the nanotube, making it more oxidized, the
electron donation is likely to be greatest from the outer
atoms (C and H) of the CoPc, which are closer to the
nanotube. The electron donation affects the central Co atom,
not because the Co atom is close to the nanotube, but because
of the delocalisation of electronic density over the whole
phthalocyanine.
3.5 Symmetry changes upon encapsulation
Previous studies state that the edge peak, characteristic of Pc
molecules, arises from the Co 4pz orbitals.14,24,25 CoPc
molecules in the bulk phase have D4h symmetry, as they are
flat square-planar molecules. To understand the changes in the
pre-edge peak and edge peak intensities between CoPc, a
CoPc/MWNT mixture and CoPc@MWNT, seen in the
Co-Ka1 RIXS and highlighted in HERFD line scans, changes
in the molecular symmetry will be considered. A change in
symmetry would change the p–d hybridisation and therefore
the spectral features.
STM studies of CoPc and modified CoPc monolayers
adsorbed on a gold surface show the molecular plane is
distorted to give C4v symmetry.26 Perfluorinated CuPc on
the Cu(111) and Ag(111) surfaces was found via X-ray standing
wave studies to distort, and the center of the molecule
moved closer to the substrate giving the Pc molecule an
‘‘umbrella-shaped’’ structure.27 Fe, Co and Cu phthalocyanine
molecules absorbed on the Cu (100) surface also show
molecular distortion from four-fold to two-fold symmetry.28
In Fe K-edge XANES studies of FePc absorbed on carbon
electrodes,29 the small pre-edge peak increases and the edge
peak decreases after absorption, and these changes are attributed
to a distortion of the molecular shape, giving rise to lower
symmetry and a higher pre-edge peak.
Firstly the small differences between CoPc and a CoPc/
MWNT mixture are considered. For a CoPc/MWNT mixture,
it is expected that a small fraction of the CoPc molecules are
adsorbed onto the outer surface of the nanotubes, but that
most of the CoPc remains in the bulk crystalline phase. This
adsorption can be thought to change the symmetry of the
molecules by moving the Co atom out of the plane of the
molecule, resulting in a molecule with C4v symmetry rather
than D4h symmetry. If the peak changes seen in the Co K-edge
XANES are due to a small proportion of molecules (since only
a small fraction of the CoPc present in the mixture could be
absorbed on the outer nanotube layer) having lower symmetry,
the changes are expected to be very small.
The trend in changing peak intensity and increased peak
broadening continues from the CoPc/MWNT mixture to
CoPc@MNWT, which agrees with the hypothesis that the
molecular symmetry has changed, since more CoPc molecules
are affected on encapsulation than in the mixture. All the CoPc
present in the CoPc@MWNT sample is encapsulated inside
MWNTs rather than existing in bulk crystals as in CoPc and
the CoPc/MWNT mixture. A lower molecular symmetry
arises due to distortion of the CoPc molecules because of
geometry constraints within the nanotubes. It was previously
shown8 that the CoPc molecules stack inside nanotubes in a
similar way to that seen in the bulk phase; the molecular
geometry may relax by distorting the molecular plane to
ensure the molecules can pack inside the nanotubes in such
a way. The effect of changing the molecular geometry on
the orbitals involved in a XANES/HERFD spectrum was
investigated using DFT.
3.6 DFT modelling
To test the proposal of symmetry breaking to give the spectral
changes seen, DFT calculations were performed to obtain the
transitions contributing to the XANES/HERFD spectrum.
A lower symmetry molecule was modelled by using the atomic
coordinates of a CoPc molecule and moving the Co atom out
of plane by 0.1 and 0.2 A. This is still much less than the
out-of-plane distance found in naturally non-planar phthalo-
cyanines such as SnPc30 or PbPc.31
The calculated spectra for planar and distorted CoPc are
shown in Fig. 6. They have been shifted in incident energy so
that the Fermi level for both calculated and measured spectra
are the same. The calculated spectra are normalised to the
transitions far above the edge where there are fewer differences
between the two molecular conformations. The pre-edge
transitions are not well reproduced in the calculations. The
calculation of the pre-edge peaks and the 3d electronic structure
in CoPc and other Co systems depends on several factors,
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including multiplet effects due to interatomic electron–electron
interactions, and changes in the local environment,13,32 which
at present cannot all be considered in a single theoretical code.
Current theoretical approaches also show that the calculated
3d electronic structures depend on the particular theoretical
model chosen.33 Spectral structures higher than the pre-edge in
molecular systems reflect more delocalized orbitals, thus they
do not strongly depend on multiplet effects and can be more
readily modelled using e.g. DFT, as done here.
The DFT calculations give the transitions present in the
XANES beyond the pre-edge, shown in Fig. 6, and for each
transition the molecular orbital (MO) can be plotted. The edge
peak is formed from two main contributions, labelled I and II,
with the corresponding MOs shown in Fig. 7. It can be seen
that as the Co atom is moved out of the molecular plane, the
overall contribution to the edge peak becomes less intense, and
the two orbitals involved split in energy, consistent with an
increase in orbital hybridisation. The decrease in intensity is
seen in the measured spectra as a smaller edge peak in
CoPc@MWNT compared to CoPc. The increase in splitting
is seen as a broadening of the edge peak.
For planar CoPc, orbital I has Co 4pz character only, and
orbital II has Co 4s hybridized with Co 3dz2 orbitals. The dz2
and s orbitals can mix as they both have A1 symmetry for a
molecule with D4h symmetry, but the pz orbitals have A2u
symmetry and therefore cannot mix. The calculated atomic
orbital compositions are in agreement with previous studies
assigning this peak to an orbital with pz, or more generally, out
of plane orbital character. For the two non-planar CoPc
representations, the molecular symmetry is reduced to C4v,
and the orbitals can mix in a different way than for the planar
molecule. Both orbitals I and II have Co s, Co 4pz and Co 3dz2
character, which all have A1 symmetry in the reduced
symmetry and can thus mix. This mixing of p and d type
orbitals has an effect in the pre-edge also, leading to a broader,
higher intensity second pre-edge peak in CoPc@MWNT. The
fractions of each atomic orbital contributing to the MOs are
shown in Fig. 7. The hybridisation is stronger for the more
distorted molecule. The calculations follow the same trend as
that seen in the experimental spectra.
It may be thought that peak intensity changes are stronger
for CoPc@MWNT than for CoPc mixed with MWNT, due to
the Co atom being positioned further out of the molecular
plane rather than a higher proportion of CoPc atoms being
distorted. However, the proportion of CoPc not in the bulk
structure is known to be much greater for CoPc@MWNT
than for CoPc mixed with MWNT, therefore this is more
likely the reason for a further peak intensity change. A higher
proportion of the molecules are affected in the encapsulated
sample, rather than the effect being greater per molecule.
Fig. 6 (a) TFY XANES spectrum of CoPc compared with DFT
calculations for (b) a planar CoPc molecule, (c) a molecule where the
Co is out of plane by 0.1 A and (d) by 0.2 A. The symmetry change
induces a change in p–d orbital mixing giving a lower intensity edge
peak as seen for CoPc@MWNT compared with CoPc. The two main
MOs contributing to the edge peak (labelled I and II) are shown for
each molecular configuration in Fig. 7.
Fig. 7 Representations of the two MOs involved in the edge peak for
(b) planar CoPc, (c) CoPc with Co out of plane by 0.1 A and (d) by
0.2 A. Orbital mixing changes upon symmetry breaking, and percentage
components of the MOs due to Co are shown. For (c) and (d) the Co is
above the plane.
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4. Conclusions
The general structure of CoPc does not change significantly
upon encapsulation, as the XANES/HERFD spectra do not
change dramatically before and after encapsulation. However,
changes are seen in the pre-edge and edge peaks in the XANES
and Co-Ka1 RIXS spectra for CoPc@MWNT compared with
CoPc and a CoPc/MWNT mixture which indicate a change in
molecular symmetry upon encapsulation.
Co-Ka1 RIXS measurements and the first pre-edge peak
energy position extracted from this RIXS data show, from a
small shift to higher energy of the first pre-edge peak for
CoPc@MWNT compared with CoPc or a CoPc/MWNT
mixture, that electron density is donated from the encapsulated
CoPc to the surrounding nanotube. This is in agreement with
previous photoemission studies. The Co atoms become more
oxidized upon encapsulation, not just the outer ligands which
are in closer proximity to the nanotube, because extensive
molecular orbital delocalisation is present across the whole
CoPc molecule.
Intensity changes in the HERFD pre-edge and edge peaks
between CoPc and CoPc@MWNT have been modelled using
DFT calculations. These results show that the geometry of the
CoPc molecules change upon encapsulation due to the Co
atom moving out of the molecular plane by a fraction of an
Angstrom, and this changes the molecular symmetry from D4h
to C4v. The MOs involved in the edge peak are calculated, and
relate to 4s, 4pz and 3dz2 orbitals, which mix differently
depending on the molecular geometry. A very small change
is seen for CoPc mixed with MWNTs, which is most likely due
to a small proportion of CoPc molecules changing geometry
after adsorption on the outer NT surface. Changes due to
encapsulation relate to conformational changes, so that the
molecules fit inside the nanotubes.
This study shows how the electronic structure of molecules
and nanotube-encapsulated molecules can may be determined
using XANES and Co-Ka1 RIXS spectroscopy. Subtle
changes in electronic and geometric structure can be extracted
and confirmed using DFT modelling to understand the
changes in molecular orbitals. Understanding the properties
of versatile and magnetically interesting nanomaterials such as
CoPc@MWNT are important to realize the potential uses of
these materials.
Acknowledgements
The authors acknowledge C. Lapras of the ESRF for technical
support.
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