## Abstract

The downscaling of silicon-based structures and proto-devices has now reached the single-atom scale, representing an important milestone for the development of a silicon-based quantum computer. One especially notable platform for atomic-scale device fabrication is the so-called Si:P *δ*-layer, consisting of an ultra-dense and sharp layer of dopants within a semiconductor host. Whilst several alternatives exist, it is on the Si:P platform that many quantum proto-devices have been successfully demonstrated. Motivated by this, both calculations and experiments have been dedicated to understanding the electronic structure of the Si:P *δ*-layer platform. In this work, we use high-resolution angle-resolved photoemission spectroscopy to reveal the structure of the electronic states which exist because of the high dopant density of the Si:P *δ*-layer. In contrast to published theoretical work, we resolve three distinct bands, the most occupied of which shows a large anisotropy and significant deviation from simple parabolic behaviour. We investigate the possible origins of this fine structure, and conclude that it is primarily a consequence of the dielectric constant being large (ca. double that of bulk Si). Incorporating this factor into tight-binding calculations leads to a major revision of band structure; specifically, the existence of a third band, the separation of the bands, and the departure from purely parabolic behaviour. This new understanding of the band structure has important implications for quantum proto-devices which are built on the Si:P *δ*-layer platform.

## Introduction

Si:P *δ*-doping offers potential for the realisation of true atomic-scale components for quantum computer applications^{1,2,3,4,5,6,7,8}, whilst retaining compatibility with the simple processing, stability, and technological relevance of silicon. Understanding, manipulating, and controlling the properties of Si:P *δ*-layers, has therefore been the centre of an intense research effort, however, a real understanding of the electronic structure has remained elusive. Density functional theory (DFT) calculations and angle-resolved photoemission spectroscopy (ARPES) recently shed new light on these systems, giving the first glimpse of their electronic structure^{9,10,11,12,13,14,15,16,17,18}: the metallic nature of Si:P *δ*-layers was believed to originate from two nearly-parabolic states, called 1*Γ* and 2*Γ*, dispersing across the Fermi level (*E*_{F}) as a consequence of the strong electronic confinement created by the P dopants in the semiconducting Si bulk (see Fig. 1a, b). The energy separation of these states, which is called valley-splitting^{14}, together with their many-body interactions^{15} is responsible for transport properties in this material system and ultimately the function of Si:P *δ*-layer-based quantum electronic devices.

In this work, we show that important details of the electronic band structure were previously reported incorrectly. We reveal the presence of additional anisotropic electronic states crossing *E*_{F}, resolved only for specific directions in the BZ (see Fig. 1f, g). Whilst in the diagonal direction (**k**_{xy}) only two electronic states can be seen, along the axial directions (*k*_{x} and *k*_{y}), a clear three-band structure is resolved which has not been predicted. The original 1*Γ* appears to actually consist of two sub-bands, indicated by the red and yellow parabolae in Fig. 1g. The presence of three states across *E*_{F} cannot be reconciled with published DFT^{9,11,12} and tight-binding (TB) calculations^{10}. This discrepancy is also seen in our TB calculations (Fig. 1d and see Supplementary Information), where only two bands, instead of three, are responsible for the metallic properties of the system. This opens an interesting question about the origin of the sub-band structure resolved by ARPES, as all the states which contribute to this sub-band structure are expected to contribute to the transport properties of Si:P *δ*-layers.

We examine some ingredients which have previously been ignored, such as spin–orbit coupling (SOC), the role of the dielectric constant, *ϵ*, and an asymmetric doping profile, to explain the origin of this sub-band structure. [Note: Although reports of SOC in Si:P *δ*-layers are generally absent, studies of SOC in Si:P derived structures do exist^{19}.] We show that *ϵ* is expected to be dramatically increased in the vicinity of the high-density dopant layer, thereby causing a large increase in the efficiency of the screening. This causes the confinement to be stronger than previously expected, and hence for additional states originally predicted to be well above *E*_{F} (as in Fig. 1d) to become occupied.

## Discussion and results

Before further discussing the origin of the fine structure of Si:P *δ*-layers, we first present a qualitative discussion of the electronic structure and the parameters to which it is sensitive. First of all, the available calculations have predicted two nearly parabolic bands with a valley splitting of ≈30 meV^{9,10,11,12}. It is worth noting that this value is somewhat controversial, and depends on a number of parameters within the model, such as the order/disorder of the dopants^{11}. Our measurements reveal the presence of three bands, of which the most occupied bands have a valley splitting which is too small to resolve experimentally (i.e., <35 meV). In other words, the observed valley splitting is either small or zero. Furthermore, in the axial *k*_{x} and *k*_{y} directions, the dispersion of the most occupied band deviates significantly from parabolic behaviour, whereas in the diagonal direction (labelled **k**_{xy}) the dispersion of these bands is very close to parabolic, and they appear to either be degenerate or to have a very small separation. The state with its minimum closest to the Fermi level (i.e., the blue parabola in Fig. 1f, g) is separated from the other bands by ≈220 meV, which is very large compared to our TB calculated valley splitting. In other words, it is unclear which of the three bands (if any) correspond to the calculated 1*Γ* and 2*Γ*. It is especially unclear whether the additional band is split off from 1*Γ*, or whether it actually corresponds to the calculated 2*Γ* (thereby implying that the least occupied band has another origin). In any case, it is clear that the calculated band structure deviates significantly from the experimentally observed band structure.

In principle, symmetry breaking in one form or another could give rise to additional bands. More specifically, the in-plane dopant order/disorder is not well known in practice, but is thought to influence the electronic structure^{18}. In any case, whilst the band structure is influenced by the symmetry and ordering of the dopants, this is not able to account for the observed behaviour (see Supplementary Information).

This notion that dopant ordering is not a significant factor is also supported empirically: We have prepared three different *δ*-layer samples, in which the dopant ordering is dissimilar, however the electronic structure remains very similar. The spectra in Fig. 2a correspond to a ‘standard’ single-dose Si:P *δ*-layer with <1/4 of a monolayer (ML) of P dopants in an almost atomically sharp plane. Figure 2b corresponds to a similarly sharp ‘double dose’ with dopant density >1/4 ML and increased disorder^{20}. Figure 2c corresponds to a ‘thick’ (1.5 nm) region with a similar (i.e., ≈25%) doping concentration (see Supplementary Information).

The measured band structure is very similar for all three preparations: The electronic structures of Fig. 2 map onto each other very well, needing only a small shift of the bands, to account for the different degrees of doping. Perhaps the most significant difference is that the least occupied band is shifted above the Fermi level when the doping density is lowest. The similarity of the band structure for these three different growth methods indicates that dopant ordering alone cannot be responsible for the mysterious third band.

Symmetry breaking (specifically, the breaking of in-plane inversion symmetry by the dopants in the *δ*-layer) together with SOC will lift degeneracy and thus give rise to bands which are non-degenerate with respect to their spin^{21,22}. This could lead to 1*Γ* having two branches, with no splitting at **k**_{∥} = 0, anisotropic splitting at larger **k**_{∥}, and a band structure which qualitatively matches the ARPES measurements. However, the expected energy splitting due to SOC is about 120× smaller than the observed energy separation of the two most occupied bands (refs. ^{23,24} and see Supplementary Information). We therefore discount SOC as a possible origin of the observed band structure.

Another possible factor which modifies the electronic structure is strain. By replacing a Si atom with a P dopant, some degree of strain will be introduced. On the other hand, Si (*Z* = 14) and P (*Z* = 15) are similar in size, and hence the strain is small: For Si:P *δ*-layers, the strain has been estimated to be between 0.1 and 0.9%^{9,12} (whereas the change in Si–P bond length for an isolated P dopant in an Si host is reported to be 1.7%^{25}). This small degree of strain is insufficient to describe the existence of an extra band in the measured band structure (see Supplementary Information).

On the other hand, the modification of the dielectric constant *ϵ* in the vicinity of the *δ*-layer is surprisingly important and can significantly influence the electronic structure. The reason that *δ*-layer causes 2D electronic states to exist at all is because of the confinement caused by the layer of dopant atoms (see for example, Fig. 1b). The number of occupied states, and the energy separation of the states is directly related to the strength of the confining potential. The sharpness of this confinement potential strongly depends on the effectiveness of the screening within the vicinity of the *δ*-layer, and this in turn depends on the carrier density. Therefore, in order to describe the potential well, the screening (i.e., dielectric constant) needs to be well described. Since a larger dielectric constant is associated with more efficient screening. This means that the quantum well is less confined than previously thought (for example, ref. ^{10}) and as a result, the splitting between some of the bands is reduced, and more bands become occupied.

For the moderate doping densities found in semiconducting Si wafers, *ϵ* is typically considered to be independent of dopant concentration, but for the extreme doping around the *δ*-layer, this view is no longer valid^{28}: As the dopant density is increased, a subsequent increase in the susceptibility of the material, and thus in *ϵ* can be expected^{26,27,29}. Following ref. ^{28}, it is possible to estimate *ϵ* as a function of dopant density (*N*_{D}, in units of cm^{−3}), for P dopants in Si:

For the case of Si:P *δ*-layers, the 2D doping concentration is known to be close to 1/4 ML. Whilst there is some uncertainty involved in converting the 2D concentration to a 3D concentration, this problem has been addressed previously (see, for example refs. ^{20,30,31}). Previous works suggest that in the vicinity of the *δ*-layer *N*_{D} is 2 × 10^{20} cm^{−3} ^{20,31}, and our own previous work^{30} suggests that whilst the peak concentration is ≈6 × 10^{20} cm^{−3}. However, we agree that the average concentration within 2–4 nm of the layer is ≈2 × 10^{20} cm^{−3}. Using Eq. (1), we can therefore estimate that for *N*_{D} = 2 × 10^{20} cm^{−3}, *ϵ* ≈ 38, however at the peak of *N*_{D} ≈ 6 × 10^{20} cm^{−3} it is conceivable that near to the dopant plane, *ϵ* could be as high as 70. In any case, it is clear that the dielectric constant may be several times higher than the value for weakly doped bulk Si.

We also point out that the role of the dielectric constant in the Slater–Koster TB theory is not the same as in ab-initio DFT. In DFT, typically the core and the valence electrons are considered, and the electronic density is computed by populating all these electronic states up to the Fermi level through self-consistent iteration of the Kohn–Sham equations. Hence, a dielectric constant of vacuum can be used, and the effective dielectric constant can be extracted from the method. In contrast, in the semi-empirical Slater–Koster TB method used here, the atomic basis functions responsible for valence bonding only are optimised to reproduce the bulk band-structure of the material without performing any self-consistent iterations of the charge density in the process. Hence, the Slater–Koster TB method in its original form cannot reproduce the dielectric constant of the material, and hence it is necessary to explicitly input a realistic value for *ϵ* in the Poisson equation. This is a standard technique in atomistic device simulations where the Poisson and Schrodinger/Green’s functions are solved self-consistently^{32,33,34}.

The qualitative understanding is readily confirmed by TB calculations (see Fig. 3) in which *ϵ* has been increased only in the vicinity of the *δ*-layer (see Supplementary Information). Whilst it is not correct to use *ϵ* as a freely adjustable ‘fitting parameter’, it is interesting to see what happens if a range of values for *ϵ* are tested. Interestingly, by increasing *ϵ* the 1*Γ* − 2*Γ* valley-splitting stays roughly constant. However, an additional parabolic band minimum (identified from the calculations as 3*Γ*) is pulled down towards the Fermi level. For *ϵ* > 16, 3*Γ* starts to become occupied, and TB calculation looks more similar to the measured band structure. As *ϵ* continues to increase, additional parabolic band minima may also be pulled below the Fermi level, and for *ϵ* > 40, a fourth state also becomes partially occupied. [Note: In fact, this observation makes it possible to disentangle the role of strain: Even if we consider the small strain in the lattice to be important, then we expect a small change in the 1*Γ* − 2*Γ* valley splitting. However, because 3*Γ* arises from the higher excited orbital states of the 1*Γ* valley state, we expect the 1*Γ* − 3*Γ* valley splitting to be essentially unaffected by strain: i.e., the opposite behaviour to the TB calculation which includes enhancing *ϵ*.]

It is clear that adjusting *ϵ* has a dramatic influence on the TB calculated band structure. Therefore, the next question to ask is ‘What is the most justifiable value to use?’ From the above simple argument of the estimated dopant density, we anticipate *ϵ* to be exceptionally large; i.e., in the range 38–70 (3–5 times higher than the bulk value). On the other hand, we can also use our measured ARPES data to make a self-consistent estimate, which we find to be somewhat lower. We therefore take the following approach: We perform the TB calculations for a range of values of *ϵ* (i.e., Fig. 3). As discussed previously, the increased values of *ϵ* correspond to a priori estimates of the carrier density. Since the resulting TB calculations give us full access to the electronic structure including the Fermi surface, we can use this output to estimate the filling, and hence to check that *N*_{D} is consistent with the a priori assumed values. In other words, the self-consistency of the TB calculation is not implicit in the method, but by comparing the output estimate of *N*_{D} with the input value of *N*_{D} used to estimate *ϵ*, we can ensure that the carrier density, and therefore the dielectric constant and screening are indeed self-consistent. Finally, we can also ensure that these parameters match with *N*_{D} extracted from the experiment.

The energy of the 1*Γ*, 2*Γ*, and 3*Γ* minima are plotted in Fig. 3a. By comparison with our experimental data, we find best agreement for *ϵ* ≈ 20: i.e., depending on the preparation, we generally observe the minimum of the most occupied state (1*Γ*) to be at *E*_{B} ≈ 220 meV, and the minimum of the least occupied state (now assigned as 3*Γ*) to be at *E*_{B} ≈ 40 meV. We also find good agreement with the TB electronic dispersions of Fig. 3b–d; The TB calculation indicates that the two most occupied bands (now assigned as 1*Γ* and 2*Γ*) are parabolic, with a small energy separation (30 meV) at **k**_{∥} = 0 and in the diagonal **k**_{xy} direction, but have an increasing non-parabolic behaviour with increasing *k* in the axial *x* and *y* directions.

A value of *ϵ* of 20 is consistent with *N*_{D} ≈ 6 × 10^{19} cm^{−3} ^{28}. Assuming that the dopant layer has a thickness of ≈0.5 nm^{15}, this corresponds to a 2D carrier density of 1.2 × 10^{13}. From the corresponding TB calculation with *ϵ* = 20 the 2D carrier density is extracted to be 7.6 × 10^{13} (and a similar extraction from the ARPES data gives 6 × 10^{13}). In other words, the carrier density based on estimates of the size of the Fermi contours yields a value which is consistent with the assumption on which *ϵ* is based, but indicates that the carrier density is underestimated by assuming *ϵ* = 20 (i.e., this is a conservative estimate for *ϵ*). This could also be a consequence of one of the assumptions used: for example estimates of the thickness of the 2D layer vary and the conversion from 2D to 3D carrier density requires this to be known. In any case, the carrier density resulting from TB calculations for *ϵ* ≥ 20 is realistic.

Based on ARPES measurements and TB calculations, we conclude that the enhancement of *ϵ* due to the high dopant density is the origin of the additional electronic structure, however, some discrepancies with previous work remain. In previous studies on similar samples^{14}, the 1*Γ* − 2*Γ* valley-splitting was reported to be ≈130 meV, whereas in this work, we conclude that the 1*Γ* − 2*Γ* splitting is <30 meV. Due to the lower sample quality and data quality in the earlier work, this was unresolvable and mistaken for a single band, and therefore the previously reported splitting of 130 meV presumably corresponded instead to the 1*Γ* (or 2*Γ*) to 3*Γ* splitting. On the other hand, this splitting is still small compared to the TB calculations and ARPES measurements here in which the 2*Γ* − 3*Γ* splitting is ≈200 meV. Whilst it is not possible to give a definitive explanation for this, we propose that it is most likely also a consequence of poorer sample quality; it is known that 1/4 ML dopant activation is only achievable when the Si surface is pristine, and that imperfections act to reduce this number. We therefore consider that the previously reported 130 meV valley splitting presumably corresponds to the (1*Γ* or 2*Γ*) to 3*Γ* splitting of a sample with a lower doping concentration than used in the current work.

Finally, we reiterate that a revision of the electronic structure of Si:P is necessary in which three nearly parabolic bands, 1*Γ*, 2*Γ*, and 3*Γ* all cross *E*_{F}, contrary to only two bands as previously thought. Jointly, all three of these bands must be responsible for the transport properties of the system^{30,35} and carrier density. Importantly, the valley-splitting, i.e., separation between 1*Γ* and 2*Γ* seems to be relatively robust against variations in the sample preparation and can be estimated to be ≤35 meV. This is an important result which also shows how the properties of a device built upon a Si:P *δ*-layer platform are not dramatically affected by changes in the growth, but instead are reliable due to the robustness of the valley-splitting. Indeed, since the valley-splitting in devices built from the Si:P *δ*-layer platform affects the lifetime of carriers^{36}, its correct value and interpretation is important for quantum device performance. Similarly, the presence of a third band crossing *E*_{F} will have significant consequences for Si:P *δ*-layer-based quantum devices, and hence it is important that this is taken into consideration when developing device structures.

## Methods

The ARPES measurements are carried out at the beamline I4 of the synchrotron facility ‘MAX-Lab’ (Lund, Sweden)^{37}. The energy and momentum resolutions are better than 35 meV and 0.02 Å^{−1}, respectively. The sample growth is monitored by low-energy-electron diffraction and X-ray photoemission spectroscopy. The temperature of the sample during data acquisitions is 100 K. The growth of the samples is carried out in situ; similarly to the growth method in refs. ^{13,14,15,16,17}. For specific details on the growth see the Supplementary Information. The Si:P *δ*-doped layer’s band structure is modelled by an empirical *s**p*^{3}*d*^{5}*s*^{*} TB model coupled with the Poisson equation^{10} (see Supplementary Information for details about the dielectric constant).

## Data availability

The datasets generated and analysed during the current study are available from the corresponding author on reasonable request.

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## Acknowledgements

J.W.W. acknowledges useful discussions with Prof. Jacob Linder and Dr. Simon Cooil. This work was partly supported by the Research Council of Norway through its Centres of Excellence funding scheme, Project Number 262633, ‘QuSpin’, and through the Fripro program, Project Numbers 250985 ‘FunTopoMat’, 262339 ‘NEAT’, and by the Villum Fonden through the Centre of Excellence for Dirac Materials (Grant No. 11744). J.A.M. acknowledges funding support from the Danish Council for Independent Research, Natural Sciences under the Sapere Aude program (Grant No. DFF-6108-00409) and the Aarhus University Research Foundation. P.D.C.K. acknowledges financial support from The Royal Society.

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F.M., X.-G.Z., C.M.P., T.B., J.A.M., and J.W.W. contributed to the data acquisition. F.M., J.A.M., and J.W.W. analysed the data. C.-Y.C. and R.R. carried out the calculations. F.M., T.B., P.D.C.K., P.H., J.A.M., and J.W.W. contributed to the interpretation of the data and calculations. All authors were involved in the drafting and final approval of the manuscript.

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Mazzola, F., Chen, CY., Rahman, R. *et al.* The sub-band structure of atomically sharp dopant profiles in silicon.
*npj Quantum Mater.* **5, **34 (2020). https://doi.org/10.1038/s41535-020-0237-1

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