The tip of a scanning tunnelling microscope is an atomic-scale source of electrons and holes. As the injected charge spreads out, it can induce adsorbed molecules to react. By comparing large-scale ‘before’ and ‘after’ images of an adsorbate covered surface, the spatial extent of the nonlocal manipulation is revealed. Here, we measure the nonlocal manipulation of toluene molecules on the Si(111)-7 × 7 surface at room temperature. Both the range and probability of nonlocal manipulation have a voltage dependence. A region within 5–15 nm of the injection site shows a marked reduction in manipulation. We propose that this region marks the extent of the initial coherent (that is, ballistic) time-dependent evolution of the injected charge carrier. Using scanning tunnelling spectroscopy, we develop a model of this time-dependent expansion of the initially localized hole wavepacket within a particular surface state and deduce a quantum coherence (ballistic) lifetime of ∼10 fs.
During imaging, the scanning tunnelling microscope (STM) injects charge into a surface on average every 1 nanosecond. Less than 1 picosecond after injection a charge carrier will have undergone a hierarchy of scattering events leading to eventual thermalization with the surface. In this interval, a charge carrier may transfer energy to individual atoms and molecules on the surface and induce, for example, bond breaking1 or atomic desorption2. Thus, atomic manipulation is the signature of the underlying dynamics of the charge carriers. Conventional atomic manipulation is restricted to the tunnel junction and the time-scale of the charge dynamics has to be inferred from the complementary calculations3. Conversely, nonlocal manipulation, in which molecules located at some tens of nanometres4,5,6,7,8 away from the tunnelling site respond to charge injection, can expose the ∼200 femto-second (fs) diffusive dynamics of injected electrons9.
Here, we employ the nonlocal manipulation technique at room temperature to probe the ultrafast ballistic dynamics of the injected charge carrier, that is, while it coherently evolves from its original quantum state. We find a coherence length scale of up to 15 nm, and deduce an associated coherence lifetime of ∼10 fs. Recent advances in the ability to construct atomic-scale structures by conventional atomic manipulation have opened the way to atomic architectures that exhibit engineered quantum effects on metals10,11, semiconductors12,13 and even graphene14. Our results indicate the possibility of harnessing such quantum behaviour well above normal 4 K operating temperatures, possibly reaching the more practical room temperature regime.
Nonlocal manipulation of toluene molecules with holes
Figure 1 shows three pairs of 30 × 30 nm STM images taken before and after the injection of holes (negative sample bias) at the location marked ‘X’ at voltages (A,D) −1.6 V, (B,E) −1.9 V and (C,F) −2.2 V. The bright spots are silicon adatoms of the Si(111)-7 × 7 surface and the dark-spots indicate chemisorbed toluene molecules15. Before hole injection, there is a random distribution of toluene molecules (see Supplementary Fig. 1 for full-scale 50 × 50 nm version of Fig. 1a,d), while after injection, there is a markedly lower toluene (dark-spot) coverage surrounding the injection site. We quantify this nonlocal desorption (manipulation) behaviour by identifying the crystallographic location16 relative to the injection site of each molecule before and after the injection. Figure 1g–i show, for each voltage, the radial dependence of the ratio of molecules that are manipulated (that is, leave their initial adsorption site), N(r), to the total number of molecules that were originally at that radial distance, N0(r). Here, we inject into unfaulted-middle (UM) sites of the Si(111)-7 × 7 surface (Fig. 1j,k) and report the behaviour of molecules initially bonded to crystallographically equivalent UM sites (other sites produce similar behaviour—see Supplementary Figs 3–5 and 7–9).
‘Suppression’ of manipulation close to injection site
At radial distances >15 nm, the radial distributions are well described by a one-hole manipulation process coupled to a 2 dimensional (2D) diffusive charge-transport model with a single decay channel, see Supplementary Fig. 2 (ref. 9). (The manipulation of the molecule, that is, induced movement away from the original binding site, could in principle be due either to a phonon emission during this decay or a non-adiabatic decay channel17). The diffusive model parameters are β, the probability per generated hole of inducing a manipulation event, and λ, the range of the diffusive transport. The blue-dashed line in Fig. 1g–i show fits of this model to the data, and Fig. 2a,b show the bias dependence for these parameters. The principal result of this work is that at distances less than 15 nm there is a strongly voltage-dependent ‘suppression’ region R, where the probability of manipulation is far below the predicted value. Furthermore, the probability β of inducing a manipulation event increases monotonically with increasing negative voltage (Fig. 2a), whereas the range R of the suppression region has a saw-tooth behaviour and returns to a minimum value at a voltage of −1.5 V. The same voltage marks a transition between near constant values for the diffusion length scale. (Similar behaviour is found for the other molecular binding sites of the Si(111)-7 × 7 surface unit cell, Supplementary Figs 3–5 and there is evidence of a near identical voltage discontinuity for STM-induced nonlocal desorption of chlorine atoms from the Si(111)-7 × 7 surface by holes18).
Connection between surface states and transport regions
We associate the plateau region of the diffusion length λ with diffusive charge transport through a particular prominent surface state9,19, and identify the threshold voltage corresponding to each plateau region with the onset of particular surface states. This assignment is supported by scanning tunnelling spectroscopy (STS) measurements of UM silicon adatoms (the injection site) shown in Fig. 2d. The nonlocal threshold at −1.2 V corresponds to the onset of the S3 back-bond surface state20, which peaks at −1.6 V in Fig. 2d, and the second threshold at −1.6 V corresponds to the onset of a state that peaks at −2.2 V18, which for consistency we label S4. Thus, the nonlocal manipulation thresholds are matched with the onsets of particular surface states, not their peak-positions. We therefore label the two charge-transport regimes as between −1.2 and −1.5 V and for manipulation between −1.5 and −2.3 V. We find analogous behaviour for the other adsorption sites (Supplementary Figs 3–5).
The discontinuity in the range of the suppression region R with increasing voltage immediately rules out an electric-field effect as the cause of the suppression, since the E-field strength monotonically increases with injection voltage (Supplementary Fig. 6B). It also eliminates E-field induced dangling-bond charging as a possible ‘suppression’ mechanism21. Furthermore, to maintain a constant current as the voltage increases the, STM tip withdraws from the surface (Supplementary Fig. 6A), and so any mechanical, short-range tip-molecule interaction would be reduced (not enhanced) as the voltage increased.
Instead, here we propose that the relative suppression of the molecular manipulation probability close to the STM tip reflects a (counter-intuitive) reduction of the number of charge carriers that interact, either directly through a short-lived ionic state or indirectly as the carrier decays via phonon emission, with the adsorbed molecule at distances close to the injection site: after injection, the probability distribution undergoes rapid ballistic expansion, or ‘inflation’, followed by relatively slow 2D diffusion. The diffusion is therefore initiated at a radius that is distant from the injection site. The solid radial curves in Fig. 1g–i correspond to such a two-step (ballistic-inflation followed by diffusion) model, using the initial conditions for diffusion an annulus of width 2 nm centred on the injection site at a radius R, the range of the suppression region. The excellent fit to the measured data across all length-scales is evident.
Charge injected from the tip of an STM undergoes a series of processes eventually leading to thermalization with the bulk crystal. These follow a hierarchy of time scales: elastic momentum scattering (that is, directional scattering); inelastic scattering within an electronic state to form a quasi-equilibrated distribution (it is during this phase that the nonlocal diffusive transport occurs); inelastic scattering out of the state towards lower lying states where the charge has insufficient energy to induce manipulation (this is the decay channel of the diffusive model). Since the two-step inflation-diffusion model accounts so well for the experimental observation, we conclude that the inflation region is the result of the charge dynamics before quasi-equilibration. Furthermore, since any incoherent scattering, whether elastic or inelastic, would lead to diffusive behaviour, the inflation region must correspond to the dynamics of the injected charge before it undergoes any scattering, while it remains a coherently expanding quantum wavepacket. That is, the inflation region is determined by the positions that the injected charges undergo their first scattering event.
We develop a simple model to connect the range of the inflation region with the band-structure of the surface and hence access the time-scale of the coherent-inflation process. In line with their prominence in our STS measurement, the inflation process is modelled on the initial occupation (by tunnelling) of an electronic surface state. The state is modelled as an azimuthally isotropic 2D state with a tight-binding dispersion . Figure 3 shows the model for the S3 state, with the dispersion shown in Fig. 3a. At a particular injection voltage, we compute the probability of tunnelling with a particular wavevector in the surface plane k|| (Fig. 3b) and use these values to construct a time-dependent cylindrically symmetric wavepacket. Figure 3c shows the radial probability distribution of the initial wavepacket. Figure 3d shows the time evolution of the wavepacket until the end of the inflation time at 10 fs, and Fig. 3e shows the radial extent of the wavepacket at the end of the inflation period. The spread of the wavepacket from the injection site is evident. This radial distribution is used as the starting point for diffusion (Fig. 3f) with an exponential decay (Fig. 3g).
The time-integrated radial distribution provides the total number of charges that can interact with a molecule at a particular distance. Figure 4 shows a series of these curves fitted to voltage-dependent experimental data. Within a transport region each curve has (i) the same diffusive parameters derived from Fig. 2 ( λ=(9.0±0.2) nm (note all errors are s.e.m.), λ=(18.0±0.3) nm); (ii) the same fitting parameter for the inflation time, and (iii) a voltage-dependent amplitude. The excellent global fits of the inflation-diffusion model give inflation times for =(11±1) fs and =(9±1) fs. We also find good global fits for the other three possible molecular binding sites and good correlations with their STS measurements (Supplementary Figs 7–9). We conclude that the nonlocal STM manipulation measurements capture the initial coherent dynamics of the injected charge carriers.
The inflation time represents the coherent or ballistic transport regime. We find no direct comparison in the literature, but the relaxation time of electrons within the dangling bond U1 state has been measured to be ∼40 fs22. This is longer than our ∼10 fs time-scale and, may be due to the U1 state lying within the bulk band-gap unlike our higher-lying states. However, recent calculations for holes in bulk silicon giving relaxation times of ∼10 fs23 have demonstrated the sensitivity to both the identity of the band that the electronic excitation resides in, and to the energy of the electronic excitation within the band. We also note, again for bulk states, that the mean free paths computed for holes in Si are in the tens of nanometres range, mirroring our surface-sensitive measurements.
The STM injects charges with a range of energies, from the bias voltage level to the Fermi level. Figure 3b shows this relationship in terms of parallel momenta. Our experiments are therefore a weighted average over a range of energies and hence, according to Bernardi et al.23, a range of coherent lifetimes. In our simple scheme, we fit a single inflation (coherence) lifetime to each surface state. The site-to-site variation of the lifetimes we obtain may reflect the spatial distribution of the particular surface states within a Si(111)-7 × 7 unit cell giving rise to differing site-to-site coherent propagation. Phonon amplitudes will also vary within the large 7 × 7 unit cell24, so that e-phonon relaxation rates can be expected to be site-specific.
The coherent-inflation time itself most likely has two main components, a temperature-independent coupling to bulk states and a temperature-dependent phonon scattering. Our earlier work with temperature-dependent electron injection found no obvious increase in the inflation region at lower temperatures, suggesting that the measured inflation region is an intrinsic property of the surface state. It therefore offers the possibility (as in the case of C60 (ref. 25) and other molecular overlayers26) of designing a system with reduced coupling to bulk states and hence an increased quantum coherent-inflation range, thereby extending the range over which a possible quantum device could work.
Sample preparation and imaging
All experiments were performed at room temperature with an Omicron STM1 in an ultrahigh vacuum chamber at base pressure 1 × 10−10 mbar. Tungsten tips were electrochemically etched in a 2 M NaOH solution and out-gassed by resistive heating in high vacuum. Pre-cut silicon samples from an n-type phosphorus doped Si(111) wafer (0.001–0.002 Ω cm) were prepared using an automated flashing routine19. Toluene was purified by the freeze-pump-thaw technique with liquid nitrogen and checked for purity with a quadrupole mass spectrometer. Typically, the surface was saturated with a toluene dose of 4 Langmuirs, corresponding to a coverage of 1,500–2,000 molecules in a 50 × 50 nm image. All images were obtained in constant current mode with passive scanning conditions (+1 V and 100 pA)16.
Experiments were performed with a Nanonis SPM control system programmed to inject into user-selected atomic locations. Stability during the injections was provided by in-house developed drift-tracking software, and a feature-locking technique employed to ensure the correct injection position. The individual locations of all molecules adsorbed to the surface before and after an injection experiment with respect to the injection site were determined using an in-house computer analysis suite16. This resulted in a molecule identification accuracy of more than 99%. The results were corrected for thermally induced desorption using the technique outlined in ref. 16. To ensure good statistical results, the total injected charge (number of holes) was varied so that approximately half the molecules at half the distance to the edge of the full image (50 × 50 nm) were manipulated.
The Si(111)-7 × 7 surface presents four distinct adatoms that a toluene molecule can bind to: faulted corner (FC), faulted middle (FM), unfaulted corner (UC) and unfaulted middle (UM) (Fig. 1j,k). Each site has slightly different electronic properties27 and binding energies for a chemisorbed toluene molecule28. To ensure a consistent experimental scenario here, we only inject into clean UM adatom sites (that is, with no adsorbate molecule) and report in the main text the manipulation of toluene molecules initially bonded to UM sites. Other injection and adsorption sites produce qualitatively similar results (Supplementary Figs 3–5 and 6–9), but the trends in the data are clearest for UM injection and adsorption sites. To further ensure the robust nature of the results, we use an automated experimental system allowing many repeats at each set of injection parameters.
2D diffusion model
As derived in ref. 9 the mathematical model for 2D diffusion with a single decay channel gives
where ni is the number of generated holes, D is the diffusion constant of the charge carriers and the combined term β gives the probability (a cross-section per unit time) that an injected hole will induce a manipulation event. Finally K0 is a modified Bessel function of the second kind with argument that includes the parameter λ, which gives the range of the diffusive transport.
Determination of suppression region R
To accurately determine the size of the suppression region, R, the 2D diffusion model was fitted to the data from the largest radial distance to a smaller distance r0. By comparing the coefficient of determination and the fitted value of λ as a function of r0, we could identify the minimum value of r0 that gave a coefficient of determination value >0.9, which was the smallest value of r0 that had a near constant λ fitting parameter.
Scanning tunnelling spectroscopy
Variable gap dI/dV spectra of individual Si adatoms were obtained directly with a lock-in amplifier in the region from 0 to −2.5 V from an initial stabilizing voltage of +1 V at 100 pA. The tunnelling gap was reduced by 25 pm V−1 to amplify the signal at low bias within the band-gap region. A typical spectrum contained 200 data points each acquired over 150 ms with a lock-in modulation of 20 mV at 521 Hz. The STS curves presented here are the average of 38 such measurements.
Inflation model: 2D surface state
For each molecular adsorption site we find site-specific nonlocal manipulation and STS properties, reflecting site-specific coupling to the specific charge-transport surface state. We therefore determine site-specific energy onsets and the bandwidths. We model the 2D surface state, which mediates the coherent expansion as a cosine tight-binding like electronic state with dispersion relation E=E0+ΔE/2[cos(ka)−1], where E0 is the bandedge, ΔE is the bandwidth and a is the Si(111)-7 × 7 unit cell length of 2.68 nm. The energy onset E0 of the state is given by the thresholds found for the various transport regions identified in the diffusion length-scale λ, see for example Fig. 2b, giving for UM injections and UM molecular manipulations for the S3 state an onset of −1.15±0.1 V and for the S4 state −1.55±0.1 V; for UC molecules, −1.15 and −1.55 eV; for FM molecules, −1.15 and −1.35 eV; and for FC molecules −1.15, −1.65 eV and a third transport region starting at −2.15 eV. The S3 onsets match with that reported by photoemission for the S3 state and the fact that a section of the ARUPS measured results lie within the projected bulk band-gap is strong evidence for a surface state of the Si(111)-7 × 7 unit cell29,30. The S3 state has been found to have downward dispersion29,31 and be coupled to px and py orbitals confirming the downwards dispersion.
To determine a state-specific bandwidth ΔE we use the width of the peaks found on our site-specific STS measurements averaged across all the sites giving a mean peak full width at half maximum (FWHM) of 0.49 eV for S3 and 0.76 eV for S4. In ref. 29 a ∼0.35 eV dispersion between the point and half way to the point is reported, giving a full bandwidth of ∼0.7 eV. Hence, our measured STS FWHM of 0.49 eV corresponds to a bandwidth of 0.7 eV for S3 and a bandwidth of 1.1 eV for S4. We introduce a Lorentz broadening with a half width at half maximum σ=ħ/ with the inflation lifetime. The resulting energy and momentum spectral density n(E, k||) is given by
and shown in Fig. 3a for the S3 state.
Charge carriers tunnel across the STM junction with a probability that depends on their energy and lateral momentum k||. The standard transmission coefficient for tunnelling32 is
where we take the barrier height Eb to be the mean height of the barrier of the tunnel junction and assume a vacuum level Ev at 4.6 eV for both sides giving Eb=Ev+Ei/2, where Ei is the injection energy.
The solutions to the 2D cylindrical Schrödinger equation are the Bessel functions. We construct a time-dependent wavepacket from a weighted sum over k-space,
where A is an overall constant of normalization, is the normalization constant for each k|| state and is the relative amplitude of the particular k|| reflecting the probability of tunnelling into it:
where EF is the Fermi level in the sample and Ei the injection energy (STM bias voltage).
We use the Bessel functions in equation (4) to describe the surface band eigen-functions, since detailed knowledge of the actual wave functions is not available. Strictly speaking, the Bessel functions are only applicable to states exhibiting free-electron like dispersion, which is only the case towards the edges of the surface bands here. To assess the likely impact of this we have also considered inflation of the initial wavepacket within the opposing limit, solving on a hexagonal lattice the time-dependent Schrödinger equation iħ∂/∂t=H assuming the tight-binding Hamiltonian,
corresponding to one orbital |i〉 per Si(111)-7 × 7 unit cell, nearest-neighbour hopping, and with , γ appropriate to the known dispersion of the surface band. Supplementary Fig. 10 shows the radial evolution predicted in the two cases, and we see both yield comparable expansion properties, with the state density advancing at similar rates, and being relatively uniformly distributed behind the front. This demonstrates the inflation is relatively insensitive to the precise nature of the assumed surface band wave functions.
Radial diffusion and decay
Numerical calculation use an evenly spaced grid of radii up to 300 nm in Δr=1 nm steps and 400 time-steps Δt to a time 2. We use a reduced time t′=t/, Δt′=Δt/ and a reduced distance =ri/λ and Δr′=Δr/λ to write the standard iterative scheme including an exponential decay term to compute the radial probability distribution P(, ) of the diffusing charge
The shape of the time-integrated radial probability density, used below to fit to the experimental data, is independent of the choice of the lifetime . The lifetime does affect the overall computed probability per hole of inducing manipulation β. In this work we focus on the shape and range of the nonlocal effect not the absolute probability per hole. Nevertheless, to give consistent and realistic values we use =200 fs in line with the results found for nonlocal electron manipulation9.
Fit to experimental data
Experimentally we measure the number of molecules that leave their original location N(r) due to an injection of ni holes and the original number of molecules N0(r) within an annulus at radius r. Hence,
See Lock et al.9 for full derivation. Thus, the only fitting parameters in the two-step inflation-diffusion model are (i) the inflation lifetime and (ii) β, the probability per hole of inducing manipulation. We justify the use of a single inflation time for all voltages within a transport region, since the energy relaxation time for hot holes in bulk silicon is near constant for holes with at least 0.1 eV of excess energy above the band edge23, and for electrons in the U1 band of the Si(111)-7 × 7 surface with 0.1–0.3 eV of excess energy22.
All data supporting this study are openly available from the University of Bath data archive at http://doi.org/10.15125/BATH-00230.
How to cite this article: Rusimova, K. R. et al. Initiating and imaging the coherent surface dynamics of charge carriers in real space. Nat. Commun. 7:12839 doi: 10.1038/ncomms12839 (2016).
Sloan, P. A. & Palmer, R. E. Two-electron dissociation of single molecules by atomic manipulation at room temperature. Nature 434, 367–371 (2005).
Minato, T. et al. Tunneling desorption of single hydrogen on the surface of titanium dioxide. ACS Nano 9, 6837–6842 (2015).
Morgenstern, K., Lorente, N. & Rieder, K.-H. Controlled manipulation of single atoms and small molecules using the scanning tunnelling microscope. Phys. Status Solidi B 250, 1671–1751 (2013).
Maksymovych, P., Dougherty, D. B., Zhu, X.-Y. & Yates, J. T. Nonlocal dissociative chemistry of adsorbed molecules induced by localized electron injection into metal surfaces. Phys. Rev. Lett. 99, 016101 (2007).
Gawronski, H., Carrasco, J., Michaelides, A. & Morgenstern, K. Manipulation and control of hydrogen bond dynamics in absorbed ice nanoclusters. Phys. Rev. Lett. 101, 136102 (2008).
Hahn, J. R., Jang, S. H., Kim, K. W. & Son, S. B. Hot carrier-selective chemical reactions on Ag(110). J. Chem. Phys. 139, 074707 (2013).
Ladenthin, J. N. et al. Hot carrier-induced tautomerization within a single porphycene molecule on Cu(111). ACS Nano 9, 7287–7295 (2015).
Schendel, V. et al. Remotely controlled isomer selective molecular switching. Nano Lett. 16, 93–97 (2016).
Lock, D., Rusimova, K. R., Pan, T., Palmer, R. E. & Sloan, P. A. Atomically resolved real-space imaging of hot electron dynamics. Nat. Commun. 6, 8365 (2015).
Crommie, M., Lutz, C. & Eigler, D. Confinement of electrons to quantum corrals on a metal-surface. Science 262, 218–220 (1993).
Nilius, N., Wallis, T. & Ho, W. Development of one-dimensional band structure in artificial gold chains. Science 297, 1853–1856 (2002).
Naydenov, B., Rungger, I., Mantega, M., Sanvito, S. & Boland, J. J. Single-atom based coherent quantum interference device structure. Nano Lett. 15, 2881–2886 (2015).
Schofield, S. R. et al. Quantum engineering at the silicon surface using dangling bonds. Nat. Commun. 4, 1649 (2013).
Wang, Y. et al. Observing atomic collapse resonances in artificial nuclei on graphene. Science 340, 734–737 (2013).
Tomimoto, H. et al. Study of adsorption structure of benzene and toluene on Si(111)7 × 7 surfaces. Surf. Sci. 566, 664–670 (2004).
Sakulsermsuk, S., Sloan, P. A., Theis, W. & Palmer, R. E. Calibrating thermal and scanning tunnelling microscope induced desorption and diffusion for the chemisorbed chlorobenzene/Si(111)7 × 7 system. J. Phys. Condens. Matter 22, 084002 (2010).
Palmer, R. & Rous, P. Resonances in electron-scattering by molecules on surfaces. Rev. Mod. Phys. 64, 383–440 (1992).
Nakamura, Y., Mera, Y. & Maeda, K. Desorption of chlorine atoms on Si(111)-(7 × 7) surfaces induced by hole injection from scanning tunneling microscope tips. Surf. Sci. 601, 2189–2193 (2007).
Sloan, P. A., Sakulsermsuk, S. & Palmer, R. E. Nonlocal desorption of chlorobenzene molecules from the Si (111)-(7 × 7) surface by charge injection from the tip of a scanning tunneling microscope: remote control of atomic manipulation. Phys. Rev. Lett. 105, 048301 (2010).
Hamers, R., Tromp, R. & Demuth, J. Surface electronic-structure of Si(111)-(7 × 7) resolved in real space. Phys. Rev. Lett. 56, 1972–1975 (1986).
Teichmann, K. et al. Controlled charge switching on a single donor with a scanning tunneling microscope. Phys. Rev. Lett. 101, 076103 (2008).
Mauerer, M., Shumay, I. L., Berthold, W. & Hofer, U. Ultrafast carrier dynamics in Si(111)7 × 7 dangling bonds probed by time-resolved second-harmonic generation and two-photon photoemission. Phys. Rev. B 73, 245305 (2006).
Bernardi, M., Vigil-Fowler, D., Lischner, J., Neaton, J. B. & Louie, S. G. Ab initio study of hot carriers in the first picosecond after sunlight absorption in silicon. Phys. Rev. Lett. 112, 257402 (2014).
Liebhaber, M. et al. Surface phonons of the si(111)-(7 × 7) reconstruction observed by raman spectroscopy. Phys. Rev. B 89, 045313 (2014).
Nouchi, R., Masunari, K., Ohta, T., Kubozono, Y. & Iwasa, Y. Ring of c60 polymers formed by electron or hole injection from a scanning tunneling microscope tip. Phys. Rev. Lett. 97, 196101 (2006).
Chen, L., Li, H. & Wee, A. T. S. Nonlocal chemical reactivity at organic-metal interfaces. ACS Nano 3, 3684–3690 (2009).
Myslivecek, J. et al. Structure of the adatom electron band of the Si(111)-7 × 7 surface. Phys. Rev. B 73, 161302 (2006).
Lock, D., Sakulsermsuk, S., Palmer, R. E. & Sloan, P. A. Mapping the site-specific potential energy landscape for chemisorbed and physisorbed aromatic molecules on the Si(111)-7 × 7 surface by time-lapse STM. J. Phys. Condens. Matter 27, 054003 (2015).
Martensson, P., Ni, W.-X., Hansson, G. V., Nicholls, J. M. & Reihl, B. Surface electronic structure of Si(111)7 × 7-Ge and Si(111)5 × 5-Ge studied with photoemission and inverse photoemission. Phys. Rev. B 36, 5974–5981 (1987).
Uhrberg, R. I. G., Hansson, G. V., Nicholls, J. M., Persson, P. E. S. & Flodstrom, S. A. Photoemission study of the surface and bulk electronic structures of Si(111)-7 × 7 and Si(111) × :Al. Phys. Rev. B 31, 3805–3810 (1985).
Northrup, J. E. Origin of surface states on Si(111)(7 × 7). Phys. Rev. Lett. 57, 154–154 (1986).
Wiesendanger, R. Scanning Probe Microscopy and Spectroscopy: Methods and Applications Cambridge University Press (1994).
P.A.S. gratefully acknowledges support from the EPSRC Grant EP/K00137X/1. K.R.R. was supported by a University of Bath studentship and D.L. by an EPSRC DTA studentship. R.E.P. is grateful to EPSRC for the award of a Fellowship.
The authors declare no competing financial interests.
About this article
Cite this article
Rusimova, K., Bannister, N., Harrison, P. et al. Initiating and imaging the coherent surface dynamics of charge carriers in real space. Nat Commun 7, 12839 (2016). https://doi.org/10.1038/ncomms12839
This article is cited by
Combining scanning tunneling microscope (STM) imaging and local manipulation to probe the high dose oxidation structure of the Si(111)-7×7 surface
Nano Research (2020)
Electronic transport in planar atomic-scale structures measured by two-probe scanning tunneling spectroscopy
Nature Communications (2019)