## Abstract

Over seventy years ago, Niels Bohr described how the charge state of an atomic ion moving through a solid changes dynamically as a result of electron capture and loss processes, eventually resulting in an equilibrium charge state. Although obvious, this process has so far eluded direct experimental observation. By peeling a solid, such as graphite, layer by layer, and studying the transmission of highly charged ions through single-, bi- and trilayer graphene, we can now observe dynamical changes in ion charge states with monolayer precision. In addition we present a first-principles approach based on the virtual photon model for interparticle energy transfer to corroborate our findings. Our model that uses a Gaussian shaped dynamic polarisability rather than a spatial delta function is a major step in providing a self-consistent description for interparticle de-excitation processes at the limit of small separations.

## Introduction

The simple idea of observing a charged particle while interacting with matter has captivated scientists for decades. At the beginning of the 20th century, Ernest Rutherford was the first to experimentally realise the scattering of *α* and *β* particles by matter^{1} and thereby paved the way for a new field of research: ion–solid interaction. The findings of these early experiments laid the foundation of today’s atomic physics in solids and studying the interaction of ions with matter has been a hot topic ever since. Not only have a number of different industrial applications developed^{2,3}, but also essential methods for medical treatment of certain types of tumours^{4,5}. Besides that, knowledge of ion-solid interaction is fundamental for many analysis techniques^{6,7} and materials studies, e.g. in plasma–wall interaction^{8,9} and astrophysical science^{10,11}.

While factors like kinematics, energy deposition, material response, and the emission of secondary particles have already been studied extensively^{12,13,14,15,16,17,18,19}, the charge state of the ion has been mostly disregarded. For ions with moderate energies, Niels Bohr considered counteracting electron capture and loss processes upon entering a sample and deduced a relation for an equilibrium charge state *q*_{eq} the projectile accommodates^{20}. The value *q*_{eq} ~ *v*/*v*_{0} × *Z*^{1/3} (and \({q}_{{{{{\rm{eq}}}}}} \sim Z\left(1-{{{{{{{{\rm{e}}}}}}}}}^{-\frac{v}{{v}_{0}}{Z}^{-2/3}}\right)\) for higher *v*, respectively) is velocity dependent and refers to the Bohr velocity *v*_{0} = 2.19 × 10^{6} m s^{−1}, i.e. for slow projectiles *v* < *v*_{0} ions are neutralised when travelling through a solid and for *v* > *v*_{0} they are stripped. Measured equilibrium charge state distributions for ions transmitted through foils in various energy ranges may be found in literature^{21,22,23} and for high ion velocities, the code ETACHA provides a good description^{24}. However, the issue of how and how fast this equilibrium charge state is reached is not yet completely resolved. This is due to the lack of possibilities of measuring ion charge states within a solid. In addition, the effect of the ion passing the surface on the way out of material was discussed as a possible source for obscuring the measured charge state with respect to the actual value in the material^{25}.

While material damage and intentional modification are driven by the ion’s energy deposition, this energy deposition per monolayer (or per unit path length) is determined by the ion’s charge state. In fact, the electronic energy loss scales as *q*^{n}, *n* ≈ 2^{20,26} and the nuclear energy transfer is also affected^{27,28}. Previous attempts to observe charge states in a solid relied on transmission through thin foils or performing backscattering spectroscopy^{29,30}. A conclusive answer could not be given using either method because the experiment selected certain trajectories including close collisions (backscattering) or surface effects, and contamination could not be neglected^{25,31,32,33}. Another approach was the detection of emitted X-rays from a Be target with high resolution^{34,35}. This approach fails for slow ions which are stopped in a fraction of the radiative lifetime.

Two-dimensional (2D) materials offer the unique opportunity to disassemble a solid, e.g. graphite, layer by layer in order to solve this 100-year-old puzzle (Fig. 1). We perform transmission experiments of slow (*v* < *v*_{0}) highly charged ions (HCIs) with single-layer graphene^{36} (SLG), bilayer graphene (BLG) and trilayer graphene (TLG) and study the neutralisation behaviour taking two different approaches: variation of the projectiles’ velocity for constant graphene layer numbers as well as variation of the number of graphene layers for constant velocities. In general, ions have not yet reached their equilibrium charge state after transmission through a single layer of graphene^{37}. We derive charge state dependent characteristic velocities *v*_{n} necessary for neutralisation in one layer of graphene, i.e. incident charge decay by a factor of 1/*e*. In either experimental approach, we find the resulting *v*_{n} to be in excellent agreement with one another. This already indicates that surface effects have only a minor influence at the velocities probed.

While theory has already been well-advanced in describing models for charge transfer from solids to approaching (highly charged) ions for several decades^{38}, the subsequent processes leading to full neutralisation and de-excitation have not been understood in their entirety. In recent experiments with HCIs and two-dimensional (2D) materials^{37,39,40}, new insights in participating de-excitation mechanisms have been found, whereupon interatomic Coulombic decay (ICD)^{41,42,43,44,45,46,47,48,49,50} was proposed to be the dominant mechanism in HCI neutralisation and de-excitation^{51}. The present study is accompanied by first-principles calculations applying the virtual photon model for ICD^{41} on the neutralisation mechanisms of HCIs. In our present study HCIs serve as an experimental toolkit, because transmitted ions are not fully neutralised but still keep a small charge enabling easy experimental access. Our conclusions, however, do not depend on the fact that the ions are highly charged and are therefore largely universal.

## Results

### Ion velocity variation for a constant number of material layers

We find a clear difference between the exit charge states of HCIs transmitted through one, two or three layers of graphene (Supplementary Note 1). In Fig. 2a, the mean number of captured electrons *n*_{e} for Xe^{30+} and various incident projectile velocities *v* is presented. We observe that *n*_{e} is strongly dependent on the velocity of the impinging projectile.

As suggested by Bohr and Lindhard^{52} and applied by Brandt^{53}, Hattass^{54} and Gruber^{37} our experimental data can be fitted by the simple exponential expression

The number of captured electrons *n*_{e} is calculated as the difference of incident *q*_{in} and mean exit projectile charge state \({\overline{q}}_{{{{{\rm{out}}}}}}\). Exponential decay is assumed for the interaction time, with *τ*_{n} being the neutralisation time constant. The interaction time *t* can further be expressed as

where the interaction length *d* is given as the product of the number of graphene layers *n*_{L} and the interaction distance around each material layer *d*_{n}, which we assume to be the same for each graphene layer. In Eq. (2) we have assumed that *d*_{n} is smaller than the interlayer spacing of the material. A justification will follow in the discussion of the paper (Section “Discussion”). For a constant number of graphene layers, i.e., *d* = *c**o**n**s**t*. the exponent in Eq. (1) simplifies to \(-\frac{1}{v}/\frac{1}{{v}_{n,v}}\). In the case of SLG, the remaining fitting parameter *v*_{n,v} then describes a charge state dependent characteristic velocity necessary for neutralisation (charge decay to *q*_{in}/*e*) within one material layer. The second index *v* is used to indicate that the experimentally determined neutralisation velocity *v*_{n,v} stems from a variation of projectile velocity *v*.

To see whether *n*_{e} for ion transmission through BLG and TLG scales linearly with the increasing material thickness and thus the time spent interacting with the material, we re-scaled the *x*-axis for BLG and TLG in Fig. 2b by *v*/2 and *v*/3, respectively, in order to take into account the number of material layers. This combines measurements with all three samples to show a universal behaviour. Such behaviour is also found for other charge states, e.g. data for Xe^{q+}, *q* = {20, 40}, have been added in Fig. 2b.

### Variation of the number of material layers for constant ion velocities

As a second approach directly resulting from Eq. (2) we can also alter the number of graphene layers *n*_{L} for constant ion velocity *v* in order to vary the interaction time of projectile and material. The SLG, BLG and TLG structures of commercially acquired samples were confirmed using scanning transmission electron microscopy (STEM). Atomic resolution images of appropriate SLG, BLG and TLG samples from Graphenea are shown in Fig. 3 together with their fast Fourier transforms as insets.

The dependence of the number of captured electrons *n*_{e} on the number of penetrated material layers *n*_{L} is shown for various incident projectile energies and charge states in Supplementary Note 2. According to Eqs. (1) and (2) we find a characteristic neutralisation length \({n}_{{L}_{n}}\), i.e. the number of material layers necessary for neutralisation. \({n}_{{L}_{n}}\) is naturally dependent on the ion velocity *v* and thus is presented as a function of the projectile velocity *v* in Fig. 4 for various incident charge states.

We find that the number of layers \({n}_{{L}_{n}}\) necessary for neutralisation increases linearly with the projectile velocity *v*. As the slope of the linear relation in Fig. 4 is of dimension time per distance it represents an inverse velocity \(1/{v}_{n,{n}_{L}}\). Thus, for each charge state, we again find a characteristic neutralisation velocity \({v}_{n,{n}_{L}}\) necessary for neutralisation within one graphene layer. Here, the second part of the index signifies that this neutralisation velocity \({v}_{n,{n}_{L}}\) was derived from studying the interaction of HCIs with samples of different numbers of material layers *n*_{L} at constant velocities *v*.

## Discussion

### Neutralisation dynamics of HCIs

Figure 5 shows neutralisation velocities found in the velocity (*v*_{n,v}) and layer (\({v}_{n,{n}_{L}}\)) analysis. In either way, we found neutralisation velocities that are charge state-dependent and decrease linearly with increasing incident ion charge state. Our resulting data correspond well within the given uncertainties and thus we conclude that *v*_{n,v} = \({v}_{n,{n}_{L}}\) = *v*_{n}. The maximum ion velocity *v*_{n} for which the ion neutralises during transmission of a single layer of graphene can then be described using Eq. (3) depending only on its charge state *q*. Coloured areas in Fig. 5 above and below this linear relation, respectively, indicate charge state/velocity combinations that will lead on average to neutral (blue) or still charged (orange) particles after transmission through SLG.

In terms of interaction time, this means that for a higher incident charge state a longer interaction time is needed for neutralisation, i.e. the ion needs to be travelling more slowly through a single layer of graphene, or at a given velocity the material needs to be thicker.

More generally we find that velocity and thickness variation can be directly linked via the simple relation in Eq. (2), namely the interaction time. Hence, the charge exchange depends only on the time the ion spends in close proximity to the material layer: we find the same number of captured electrons *n*_{e} for an ion with velocity *v* interacting with a single layer of graphene and an ion with 2*v* transmitting through BLG (Fig. 6). The interaction time scales linearly with the number of material layers (see Fig. 2 and Eq. (2)). The stopping and charge exchange of atomic particles penetrating through a material is usually described using corresponding cross-sections leaving only a velocity dependence^{20}.

Recently, we used the critical distance for resonant charge transfer stemming from the classical over the barrier (COB) model^{38} as effective interaction length *d*_{n} ~ 9 Å and an upper estimate for the interaction time of HCIs with a single layer of graphene given the incident projectile velocity *v*^{37}. This distance of 9 Å is significantly larger than the interlayer spacing of multiple graphene layers and a graphite sample (~3.34 Å ^{55}). The linear scaling of the interaction time with a number of graphene layers indicates, however, that the interaction length determining the neutralisation process *d*_{n} needs to be even smaller than the graphene interlayer spacing. If this were not the case, a non-linear behaviour would be expected. This justifies the assumption made in Eq. (2), where we replaced the total interaction length with *d*_{n} times the number of material layers.

When ions reach a distance to a surface smaller than or equal to the critical distance of the COB model^{38} the formation of a hollow atom characterised by empty inner and occupied outer (high *n* Rydberg) states is initiated (Fig. 1)^{38,56,57}. Following our conclusion above we suggest that the interaction time of HCIs and materials is thus not primarily determined by the hollow atom formation but rather by the de-excitation of the same. We recently identified interatomic Coulombic decay (ICD) as a dominant process in the de-excitation of hollow atoms^{40,51}. In general, ICD is described by a rate Γ exhibiting a strong dependence on interatomic distances *R*, i.e. Γ ~ 1/*R*^{6} at large interatomic separations^{44,58}. For small *R* an even stronger dependence is expected^{59}. Thus, the de-excitation of a hollow atom happens primarily in a limited area around the graphene layer with diminishing interatomic separation *R* of the hollow atom and material atoms.

### Ab-initio model description of HCI de-excitation

In order to model the local de-excitation dynamics dominating the final charge state after passing one material layer in a truly atomistic picture, we developed an approach to treat ICD at small interatomic separations (see “Methods” section). Our theoretical considerations are based on the virtual photon model of ICD^{41}. The resulting ICD rate Γ for five different incidents Xe charge states is given in Fig. 7a in dependence of the interatomic separation *R*. For the figure legend we used *n* = *q*_{in}, which is a good approximation for the principal quantum number *n* into which resonant charge transfer occurs initially^{37,38,60}. One can observe that Γ is indeed enhanced substantially at *R* smaller than the interlayer spacing of graphene layers/graphite.

One particularly noteworthy outcome of this model is the plateau value at a limit of small separations. Since Γ is in general unknown at *R* < 2 Å and diverging in theoretical models ~1/*R*^{6} ^{41}, its value was recently extrapolated as an ad hoc assumption based on various data found in the literature to small interatomic distances also leading to a plateau value, which is independent of the incident charge state^{28}. By contrast, in the virtual photon model applied here plateau values for each incident charge state come out naturally and match in the order of magnitude with the rate Γ found in ref. ^{28}. The ICD rate plateau value Γ(*R* → 0) decreases with decreasing incident charge state and amounts to insignificant values for low charge states compared to well-known Auger rates, e.g. for *q* = 1 → Γ(*R* → 0) ~ 10^{2} s^{−1} (10^{−13} eV) (Fig. 7b)^{61}. This implies that ICD becomes substantial only in the de-excitation and neutralisation of HCIs whereas for lowly charged ions as important in ion-induced Auger electron spectroscopy^{62} and low energy ion scattering (LEIS), which uses protons or He, common intraatomic Auger processes with rates of 10^{14}–10^{15} s^{−1} (0.1–1 eV) dominate. The vanishing rate of ICD for lower charged ions is well in agreement with the observation of intraatomic Auger de-excitation for low-charged ions (i.e. the absence of ICD) in methods like LEIS^{32}.

For an estimate on the effective ICD range (Fig. 6), we used the separation *R* at which Γ(*R*) has decreased to a fraction of 1/*e* of its plateau value. This effective interaction distance for ICD was (numerically) found to be *d*_{n} ≈ 1.69 Å independent of the incident charge state.

The value of the reciprocal of the ICD rate Γ(*R*) corresponds to the lifetime of the de-excitation process at a given interatomic separation *R*. Assuming that the ion needs to spend at least this ICD lifetime within a region of ±*d*_{n} around a carbon atom (marked as dashed pink line in the zoom-out in Fig. 6) we can identify a maximum ion velocity for neutralisation within one material layer. For incident ion charge states 28–32 with the corresponding Γ(*R*) shown in Fig. 7, we thereby find neutralisation velocities *v*_{n} in the range of 0.8–2.1 nm fs^{−1} which agrees well with our experimentally found neutralisation velocities presented in Fig. 5. Note, that this consideration is only a rough estimation for central collisions and is not fully comparable to our experiment.

### Implementation of the ab initio model in experiment simulations

In the experiment, we observe ions scattered within a detector angle of ±0.5^{∘} measured from the forwarding scattering direction. Thus, there is only a limited range of impact parameters that we access in our ion beam spectrometer. Wilhelm and Grande recently presented a code based on a time-dependent potential (TDPot) to directly simulate the measured interaction of HCIs and atomically thin materials^{28}. In TDPot we define a simulation cell based on the discussed sample explicitly taking into account material geometry, i.e. possible impact parameters. The ICD rate from our presented model, however, includes only weak dependences on material properties in terms of atom radii, the photon absorption cross-section of carbon, and the Xe energy level splitting. In fact, experimentally found ICD rates from various materials also do not differ strongly^{28}. Recent publications have successfully applied this model to carbon nanomembranes and molybdenum disulfide, respectively, using extrapolated ICD rates from experimental data^{40,63}. A short description of the code and underlying model can be found in Supplementary Note 3; for further information, the reader is referred to the original publication^{28}.

When introducing the ICD rate Γ (see Eq. (19) and Fig. 7) in the code TDPot we simulated the mean number of captured electrons *n*_{e} for *q* = {28, 30, 32} and derive neutralisation velocities *v*_{n} as shown for experimental data in Fig. 2. The model allows the determination of the charge exchange for individual trajectories (not only central collisions) with Γ(*R*) and the material structure as the only necessary input. For each charge state, we again set *n* = *q*_{in}, as an approximation for the principal quantum number *n* into which resonant charge transfer occurs initially^{37,38,60}. Simulated data points can be found in Supplementary Note 4. We again find an agreement in order of magnitude of resulting *v*_{n} compared to experimental results. For example, with incident ion charge states 28–32 we find *v*_{n} between 0.6 and 1.7 nm fs^{−1}. These values are smaller than our simple estimation based on the ICD lifetime, which is reasonable since small impact parameters with high ICD rates (and large scattering angles) are not accessible in our experiment^{28}. However, using Γ(*R*) from Eq. (19), we currently cannot reproduce the exact values found in the experiment. This might follow from the fact that dynamical screening (reducing the effective incoming charge) is not included in our quasi-static first-principles calculation in the dipole approximation. Please note, that TDPot specialises in the description of neutralisation dynamics of slow HCIs and reaches its limits when it comes to smaller incident charge states (where common Auger processes dominate, see Fig. 7b) and higher velocities (when electron loss cannot be neglected anymore). For further discussion and simulations covering these limits, the reader is referred to Supplementary Note 5.

### Neutralisation time constants

By taking 2 × *d*_{n} = 3.38 Å (from our simple estimate above) as a constant trajectory-independent estimate for the interaction distance of each material layer and going back to Eq. (2) we can also find a new estimation of the characteristic neutralisation times of HCIs. As an example, for Xe^{20+} to Xe^{40+} we find neutralisation time constants ranging from *τ*_{n} ≈ 0.8 fs (*q*_{in} = 20) to *τ*_{n} ≈ 2 fs (*q*_{in} = 40). These values indicate that the neutralisation process is ~40% faster than discussed by Gruber et al.^{37} which even strengthens the conclusion of the same work that graphene responds to a strong and localised electric field (introduced for example by an HCI) in an ultra-fast way. Being aware of the time scales of interaction processes of charged particles and material can thus help to approach material properties under extreme conditions as shown in the case of local current densities in graphene in ref. ^{37}. Aside from material properties, material compositions are often studied using charged particles^{64}. In ion-beam spectroscopy techniques like Rutherford backscattering spectrometry and low or medium energy ion scattering, material composition and depth profiling are obtained via consideration of collision kinematics and ion stopping. Since the electronic energy loss depends on *q* it is highly beneficial to understand charge exchange processes inside a material to enhance depth profiling resolution. In addition to material studies, ion neutralisation in graphene is also part of a recently presented new setup of a ^{229}Th nuclear clock^{65}.

While we observed the neutralisation time dependence using the particular model system of highly charged Xe on graphene, our theoretical predictions are independent of the particular choice of the ion-target combination and therefore universal, whereas they are dominant for slow HCIs and become less significant for lower charge states and/or higher velocities. Our combined experimental and theoretical effort finally bridges the gap between atomic physics of isolated atoms and molecules in the gas phase and understanding interparticle energy transfer in a solid and during a heavy particle scattering event.

## Methods

### Ion beam spectroscopy

The ion beam spectrometer at TU Wien is equipped with a Dresden EBIS-A electron beam ion source^{66} producing Xe^{1+} to Xe^{44+} ions with kinetic energies of 1–400 keV. A Wien filter is used to select specific charge states for irradiation^{67}. Our experiments are performed in transmission geometry: projectiles are transmitted through thin materials and detected afterwards angle-resolved on a position-sensitive RoentDek delay line microchannel plate (MCP) detector^{68}. Determination of exit charge states can be done by analysing the deflection of particles after transmission of the sample in a pair of deflection plates. In combination with the MCP signal, an electron detector close to the target position^{69} allows us to measure the time of flight (TOF) of projectiles, recorded in coincidence with exit charge states in a list mode. For more details on the spectrometer please see^{70}.

Samples of SLG, BLG and TLG studied in this work were commercially acquired from Graphenea^{71}. Freestanding sample areas are found on holes with 2 μm diameter on a 10–20 nm thick Quantifoil support both placed on Au TEM grids. The materials are grown by chemical vapour deposition and transferred (multiple times) onto the TEM grid applying a polymer-based transfer technique. We heat samples in situ using a Lasertack laser diode (6 W, 445 nm)^{72} and Ohmic heating (400 °C) to remove residuals from production and transfer processes as well as contaminants adventitiously adsorbed while sample handling in ambient conditions according to the procedure described in^{73,74}. Filtering exit charge states for their TOFs discriminates signals from both the Quantifoil support and still contaminated areas. To prevent re-adsorption of contaminants during measurements at a base pressure of 5 × 10^{−9} mbar, we keep samples at 180 °C.

### Electron microscopy

STEM was done in a Nion UltraSTEM 100 at 60 kV. Images were taken via a high-angle annular dark-field detector.

### Theoretical model

The theory underpinning the experiment is based on the virtual photon model of ICD^{41}, which was later generalised to arbitrary environments in^{58}. The main result was the following expression for the ICD rate Γ

where *γ*_{D} is the spontaneous decay rate of the donor transition with frequency *ω*_{D}, *σ*_{A}(*E*) is the photoionisation cross-section of the acceptor at energy *E*_{D} = *ℏ**ω*_{D}, and \({\mathsf{G}}({{{{{{{\bf{r}}}}}}}},{{{{{{{\bf{r}}}}}}}}^{\prime} ,\omega )\) is the dyadic Green’s tensor describing the propagation of electromagnetic excitations of frequency *ω* from point \({{{{{{{\bf{r}}}}}}}}^{\prime}\) to **r**.

In its original^{41} and generalised^{58} forms, the virtual photon model applies only when donor and acceptor are sufficiently far apart that there is no appreciable wave function overlap, but this is not the situation found in the experiment described here. In principle, one should use a full ab initio electronic structure calculation, but for highly charged ions in asymmetric environments, this is computationally infeasible. In order to remedy this, we adopt a technique from the theory of the van der Waals forces (recently applied to Auger decay^{75}), whereby the dynamic polarisability *α*(*ω*) of donor and acceptor are taken to be ‘smeared out’ over a finite region (see, e.g.^{76}), instead of being taken as a spatial delta function as is implicitly done in the virtual photon model. In particular, we take

where *a* is a characteristic length, roughly corresponding to the spatial extent of the atomic wave function. As discussed in detail in ref. ^{77}, this leads to a modified Green’s tensor which, upon substitution into Eq. (4) leads to

with

where *R* is the interatomic separation, and the parameters *a*_{D} and *a*_{A} describe the spatial extents of the Xe donor and C acceptor, respectively. At large separations *R* (or, equivalently, small radii *a*_{D} and *a*_{A}), equations (6) and (7) together reproduce the well-known point-like rate

At small separations, the rate becomes

in contrast to the point-like rate, which diverges at small separations.

We now need to choose some reasonable parameters for the various radii, the energy level splitting of the Xe donor, and the cross-section of the C acceptor. The Xe donor is in a high Rydberg state of principal quantum number *n*, so we take *a*_{D} = *a*_{0}*n*^{2}/*Z* ≈ 9 Å and energy level splittings of

where *m* and *k* are the principal quantum numbers of the two states at hand, and *E*_{Ryd} is the Rydberg energy. For the carbon acceptor, we use the van der Waals radius of 1.7Å, and the tabulated photoionisation cross-sections found in refs. ^{78,79,80}.

The process of decay from a multiply-occupied high Rydberg state can be complex, consisting of a cascade decay through different paths. In order to take this into account, we use the following rate equation for the population *P*_{k} of level *k*

where *γ*_{k→m} is the decay rate connecting level *k* to level *m*. The expected (virtual) photon population *F*_{k} for a particular frequency *k* after a given cascade can then be found from

The decay rates we use are those for hydrogen-like atoms, scaled by the appropriate factor *Z*^{4} for nuclear charge *Z*. We, therefore, use the following as a weighting factor in the expression for the ICD rate

where \({\gamma }_{k\to m}^{{{{{{{{\rm{H}}}}}}}}}\) are the hydrogen-like decay rates^{81}, so that the decay rate from a particular level *n* is

To a good approximation, the values of the weighting *g*(*k*, *m*) calculated from the from level *n* turn out to be equal at the 0.1% level to the those that would be found by taking the transition *n* → *n* − 1, so that we may simplify by taking

where *C*(*n*) is a fitted function of *n* found from the numerical solution of the rate equations

The relevant hydrogen-like rates are well-approximated by

with *A* = 4.86 × 10^{−6} eV. As shown in Supplementary Note 6, the photoionisation cross-section of carbon is well-approximated (in the relevant range of energies) by

where *σ*_{0} = 0.115 Å^{2}. Combining Eqs. (14), (15) and (18), we get

Using the various parameters discussed in this section, at the limit of small separations *R* this can be simplified to

As shown in Fig. 7, this agrees with the full position-dependence found by evaluating Eq. (19).

## Data availability

All data needed to evaluate the conclusions in the paper are present in the paper and/or the Supplementary Materials. Additional data that support the findings of this study are available from the corresponding authors upon reasonable request.

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## Acknowledgements

The authors acknowledge funding from the Austrian Science Fund (FWF): Y 1174-N36, I 4914-N. A.N., B.C.B and R.A.W. acknowledge funding from TU Wien’s competitive Innovative Projects programme. J.S. appreciates funding from the Doctoral College TU-D.

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A.N., J.S., R.A.W. and F.A. designed the research, A.N, S.C., J.S. and B.W. performed ion beam spectroscopy measurements, T.G., D.E. and B.C.B. conducted electron microscopy analysis of used materials. P.L.G. and R.A.W. developed the simulation code used which was applied by A.N. J.P.M. provided radiative absorption cross-sections for comparison. R.B. developed the first-principles model presented. A.N. and R.B. wrote the paper. All authors commented.

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Niggas, A., Creutzburg, S., Schwestka, J. *et al.* Peeling graphite layer by layer reveals the charge exchange dynamics of ions inside a solid.
*Commun Phys* **4, **180 (2021). https://doi.org/10.1038/s42005-021-00686-1

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