In the presence of spin–orbit coupling (SOC), the spin s and the orbital angular momentum l of the electron lose their time invariance; it is the total angular momentum of the electron j = s + l that preserves it. This fundamental property of electrons is the playground of a number of fascinating phenomena, such as the Dirac edge states in topological insulators (TIs)1, the quantum spin Hall effect2, and the formation of Majorana fermions3,4,5. In case of three-dimensional TIs, SOC forces the surface electrons to form helical spin structures, wrapping an odd number of massless Dirac cones, with the simplest and most-studied systems being the Bi2Se3 and Bi2Te3 tetradymides. Angle resolved photoemission spectroscopy (ARPES) experiments in combination with theoretical studies have shown that these systems acquire a single Dirac Cone and large band gap6,7, thus providing an ideal platform for studying SQPs. However, despite the simplicity of their topological edge states, important quasiparticle excitations of Dirac electrons, such as the Majorana zero mode3,4,5, the excitonic superfluid condensate8, or the propagation of chiral spin waves on topological surfaces9 remain to a great extent experimentally unexplored. It is furthermore noticed that the detection of Majorana excitations requires the simultaneous probing of the response from both the bulk and edge states, which is difficult to achieve with current experimental techniques10.

Since many SQPs depend on the way that the spin of the Dirac electrons couples with their orbital motion and how this interaction propagates through the crystal, an experimental probe sensitive to both the spin and orbital motion of the Dirac electrons with atomic scale resolution is crucial in the efforts to further understand the physics of topological materials. NMR appears to fulfill these requirements as the nuclear magnetic shielding, and consequently the NMR frequency shift, depends on the spin and orbital magnetic susceptibility at the position of each resonating nucleus. Specifically, the total NMR Knight shift can be expressed as δtot=δFC + δdip + δorb, where the first two terms are the Fermi-contact and spin-dipolar terms originating from the electron spin polarization at the Fermi level, and the third is the orbital term generated by the orbital currents of the Dirac electrons11,12. According to recent theoretical calculations on TI’s the orbital term δorb from the Dirac electrons dominates over δFC and δdip, and induces large negative shifts, and very short spin-lattice relaxation times T112. However, until now experimental 125Te NMR studies on Bi2Te3 nanoparticles13 and microcrystalline (bulk) powders14 have given contradicting results.

In this article, combining advanced broadband solid-state NMR methods with Cs-corrected scanning transmission electron microscopy (STEM) and DFT calculations on pristine Bi2Te3 nanoplatelets, we succeeded for the first time to resolve the NMR signal assigned to the Dirac electron states, and monitored through the NMR parameters the way that the spin and orbital magnetic susceptibilities induced by the Dirac electrons vary across the nanoplatelets.


Crystal and band structure analysis of the Bi2Te3 nanoplatelets

Bi2Te3 nanoplatelets were synthesized in the liquid phase using a solvothermal method, as described in the “Methods” section. Figure 1a and Supplementary Figs. 13 illustrate the excellent quality of the nanoplatelets, which exhibit perfect hexagonal shapes with sharp edges, average diameter of 600 nm, and mean thickness of 10 nm. The structural characteristics were examined at atomic scale by means of high angle annular dark/bright field HAADF/ABF imaging, as presented in Fig. 2a and Supplementary Fig. 3. Since the intensity of the HAADF images is proportional to the atomic number Z2, atomic columns in the HAADF/ABF image could be identified, and were labeled according to the Bi, Te(1), and Te(2) atomic sites by brown, blue, and magenta dots, respectively15. The Bi and Te atoms are organized in well-defined quintuple atomic layers comprising of five covalently bonded atomic sheets of alternating Bi and Te atoms, i.e. Te(1)–Bi–Te(2)–Bi–Te(1), that are bound to each other by van der Waals interactions, as seen in the intensity profiles in Fig. 2b and Supplementary Fig. 3.

Fig. 1: Band structure analysis and Dirac states of stoichiometric Bi2Te3 nanoplatelets.
figure 1

a High-resolution TEM and HAADF image of Bi2Te3 nanoplatelets (top view and cross-section). b Band structure of a 9-quintuplets-thick (10 nm) Bi2Te3 slab. c The projected k-resolved DOS of the Te(1) |5p〉 and Bi |6p〉 orbital states at the outer (edge) quintuplets, and the Te(1) |5p〉 orbital states at the central quintuplet. Dirac states are observed only at the edge quintuplets (more details in Supplementary Fig. 6).

Fig. 2: Atomic scale TEM analysis and 1D 125Te NMR.
figure 2

a Cross-sectional HAADF-ABF images of a Bi2Te3 nanoplatelet. Brown, blue, and magenta dots indicate the Bi, Te(1) and Te(2) columns in the quintuplets. b The intensity profile from the cross section (yellow line) in the HAADF image. c 125Te static frequency sweep NMR (yellow circles) and the isotropic projection of the 2D 125Te aMAT NMR at 14 kHz MAS (solid line) of bulk Bi2Te3. d 125Te static frequency sweep NMR (gray circles) and the isotropic projection of the 2D 125Te aMAT at 30 kHz MAS of a Bi2Te3 nanoplatelets sample.

In order to examine the way in which the Dirac states propagate through the nanoplatelets and how this feature is encoded into the NMR Knight shift, DFT calculations were carried out on a Bi2Te3 slab comprising 9 quintuplets, corresponding to the mean thickness of the Bi2Te3 nanoplatelets. Details on the DFT calculations are given in the Supplementary Information (SI). Figure 1b shows the relevant band structure, in agreement with previous calculations6. In particular, the band structure shows an energy band gap of ≈160 meV and a single surface Dirac cone enclosing the k = Γ symmetry point. The Fermi energy was calculated at EF = 6.5942 eV, i.e. at slightly higher energy than the maximum of the valence band. Figure 1c, and Supplementary Figs. 46 show that the Dirac states are defined mainly by the Te(1) |5p〉 and Bi |6p〉 states of the terminating quintuplets. Furthermore, the density of the Dirac states is observed to be substantially reduced in the central region of the nanoplatelets. It is therefore expected that the NMR signals from the surface of the nanoplatelets will be shifted with respect to the signals from the bulk (interior), because the Dirac electrons are predicted to induce large negative orbital Knight shifts12. Despite this expectation, until now efforts to detect the Dirac states through 125Te NMR have not been successful, either with static or with magic-angle-spinning (MAS) one-dimensional (1D) NMR methods. The main reason is the large Knight shift anisotropy, which gives rise to broad unresolved NMR signals that are difficult to excite.

The shortcomings of 1D NMR for acquiring well-resolved spectra is clearly seen in Fig. 2c, d, which compare the static frequency-sweep 125Te NMR spectra of two samples (c) microcrystalline (bulk) Bi2Te3 where Dirac electron states are almost absent and (d) Bi2Te3 nanoplatelets where Dirac electron states dominate in the electron band structure. Both spectra exhibit different overall profiles, but with similar features; each is characterized by a central peak at a shift of 250 ppm (microcrystals) and 480 ppm (nanoplatelets), respectively, with a tail at higher shift, and a shoulder at negative shift. In case of the microcrystalline material these features have been explained as originating from the presence of two overlapping signals shifted relative to each other14: one strong narrow resonance at 250 ppm from Te(1), and a broader asymmetric resonance at a shift of −400 ppm from Te(2). Implementation of advanced 1D solid-state MAS NMR methods, such as the double adiabatic echo (DAE) experiment did not improve the resolution, as seen in the Supplementary Fig. 8c.

Resolving the bulk and Dirac edge states with aMAT NMR

In order to resolve these individual 125Te NMR signals, and to identify those from the topological edge states, the 2D adiabatic magic-angle turning (aMAT) NMR experiment was implemented (Fig. 3a), which in the indirect dimension provides the isotropic NMR shifts free from spectral broadening due to any kind of anisotropy16,17. Details on the implemented NMR techniques are provided in the "Methods” section. The effectiveness of the method is in evidence in Fig. 2c, d, which overlay the isotropic 125Te NMR projections of the 2D aMAT of both the microcrystalline and nanoplatelet samples onto the 1D frequency-sweep spectra. In the case of the microcrystalline sample a single broad resonance is observed at 250 ppm, which comprises the two overlapping Te(1) and Te(2) NMR signals. No isotropic signal component is observed at negative shifts, as is also clearly shown in Supplementary Fig. 7. In case of the nanoplatelets the isotropic “bulk” NMR signal resolves into two distinct components at shifts of 765 and 93 ppm with a ratio of integrals of 2:1, corresponding to Te(1) and Te(2) respectively; The difference in the isotropic NMR shift between the microcrystalline and nanoplatelets samples reflects differences in the electron/hole doping of the two samples18, and in general in the distribution of the conduction electrons across the nanoplatelets. Most importantly, a third distinct signal component is observed in the aMAT NMR signal of the nanoplatelets at a markedly different shift of −452 ppm, which is assigned to the topological edge states. This signal appears reproducibly in different nanoplatelet samples, including those exhibiting some oxidation of the surface, as observed in Supplementary Fig. 8, which is an important finding for many applications. Furthermore, the possibility that this signal is produced by trivial edge effects, such as (i) sudden changes in the surface composition or structure (e.g. stacking faults) and (ii) gradual structural variations can be ruled out. In the first case, with the aid of TEM and high-resolution cross-sectional HAADF imaging (Supplementary Figs. 2 and 3), we see clean surfaces with no evidence of defects, thus confirming that the nanoplatelets are pristine. In the second case, we would expect substantial inhomogeneous broadening of bulk NMR signals, rather than the additional resonance at −452 ppm.

Fig. 3: 125Te aMAT NMR and \(T_2^\prime\) dephasing analysis of the Dirac edge states.
figure 3

a 2D 125Te aMAT NMR spectrum of Bi2Te3 nanoplatelets. Blue and magenta color contours indicate signals from the bulk interior of the nanoplatelets, while the orange color contours show signals from the surface Te sites, shielded by the orbital motion of the Dirac electrons. b The expanded isotropic projections of 125Te MAT NMR spectrum acquired at four different evolution times. c The 125Te NMR \(T_2^\prime\) distribution as a function of the resonance frequency of microcrystalline (bulk) Bi2Te3. The orange color cross section shows the \(T_2^\prime\) distribution at frequency 250 ppm. d The 125Te NMR \(T_2^\prime\) distribution with respect to the resonance frequency of the Bi2Te3 nanoplatelets.

We note that, because of the long adiabatic pulses (33.33 μs)17, aMAT signals with very short spin–spin relaxation times T2 may be partially wiped out. The way that nuclear spin coherences dephase across the spectrum is shown in Fig. 3c, d, which display the \(T_2^\prime\) distribution vs. shift for both the microcrystalline and nanoplatelet samples, acquired by 1D inverse-Laplace-transform Carr–Purcell–Meiboom–Gill (CPMG) spin-echo pulse trains.

In addition to the inherent T2 relaxation, \(T_2^\prime\) dephasing includes coherent signal decay due to the extended nuclear dipolar coupling network across the particles19. Experimental details on the CPMG inversion are presented in the SI. In the case of the microcrystalline sample the two signals corresponding to Te(1) and Te(2) are resolved, with Te(2) showing a highly anisotropic frequency distribution. In case of the nanoplatelets, the third strong signal component at −452 ppm, exhibits significantly shorter \(T_2^\prime\) times, indicating enhanced relaxation, which is attributed to the Dirac electrons.

To test whether such short \(T_2^\prime\) influences the signal intensity in the aMAT spectrum, the isotropic shift projections of standard MAT experiments were obtained at different shift evolution times as shown in Fig. 3b16,17,20. The large signal intensity at −452 ppm at short evolution times indicates that a large proportion of the atomic layers in the nanoplatelets have a surface-like electronic structure, and its rapid dephasing at longer evolution times relative to the other signals from the nanoplatelet interior confirms the difference in dephasing times shown in Fig. 3d.

On comparing the \(T_2^\prime\) distribution maps for the microcrystalline and nanoplatelet samples in Fig. 3c, d, we note two striking features: firstly, the \(T_2^\prime\) coherence lifetimes of the signals due to bulk Te have the same value of ~1 ms; and secondly the \(T_2^\prime\) of the signal at −452 ppm for the nanoplatelet sample is an order of magnitude shorter, at ~0.1 ms. Whilst the interpretation of these \(T_2^\prime\) data is complicated by the fact that \(T_2^\prime\) encapsulates the effects of both spin–spin relaxation, and coherent dephasing effects, these observations are consistent with enhanced relaxation of the surface Te due to the Dirac electrons according the following mechanisms. The enhanced \(T_2^\prime\) relaxation may be assigned to slow orbital magnetic field fluctuations21, produced by the surface orbital currents of the Dirac electrons, or otherwise to the Ruderman–Kittel–Kasuya–Yosida (RKKY) interaction between the nuclear spins, also mediated by the Dirac electrons22.

The variation of the spin-lattice relaxation times T1 with the Knight shift is somewhat different, as shown in Supplementary Fig. 11. Here, we see that the measured T1s are uniformly an order of magnitude shorter for the nanoplatelets compared to the microcrystalline sample (200 vs. 20 ms), but see no variation between the bulk Te compared to the surface Te signals, within experimental error, as we do for \(T_2^\prime\). This is an interesting observation, which indicates that in these quasi-2D topological systems the nuclear spin relaxation mechanisms are more intricate than considered12. Nevertheless, the observation of a shorter T1 for the nanoplatelets is evidence that the Dirac electrons prevail on the spin-lattice relaxation mechanism, the effect of which extends into the bulk. This uniformity for T1 across the whole nanoplatelet may be explained by the quasi-2D topology of the Bi2Te3 nanoplatelets12, which confines orbital currents in parallel to the external surfaces. In Fermi liquids with similar orbital current topology, Lee and Nagaosa23 have shown that T1 is independent of the position of the resonating nuclei, which resembles our observation.

DFT calculations

To strengthen our interpretation of the 125Te aMAT spectra, and in particular to confirm the assignment of the resonance at −452 ppm, DFT calculations of the NMR shifts were carried out, using the full-potential linearized augmented plane-wave method, as implemented in the Wien2k DFT software package. Figure 4a, c show the calculated orbital, Fermi-contact (spin), and spin-dipolar terms of the Knight shift in the presence of SOC, of bulk Bi2Te3 and a 5-quintuplets slab (with thickness d5 nm), representing the microcrystalline Bi2Te3 and the nanoplatelets, respectively. The latter was selected because it allows tractable DFT calculations with satisfactory k-grid, while Dirac electron states remain gapless24. The total isotropic Knight shift is, as previously discussed, equal to δtot = δFC + δdip + δorb. Conventionally, the orbital term is referenced according to δorb = σref − σorb25, with the reference shielding set to σref = 2370 ppm, from Supplementary Fig. 9, whilst the Fermi-contact and the spin dipolar terms, δFC and δdip, are set as minus the relevant calculated shielding, i.e., −σFC, respectively −σdip. In case of the microcrystalline material δtot was found to be +720 ppm for Te(1) and −660 ppm for Te(2), as shown in Fig. 4a, c. These values are shifted in comparison to the experimental ones, mainly due to the strong temperature dependence of the NMR frequency14, as shown in the inset of Fig. 4a. (Data in the inset of Fig. 4a are not isotropic NMR Knight shifts, but merely the frequency position of Te(1) and Te(2) NMR peaks, acquired from 1D 125Te NMR spectra.) However, we note that this variation with temperature is similar for the shifts of both Te(1) and Te(2) and, in particular, that the ordering of the two peaks does not change. It is stressed that in the presence of SOC, calculations of NMR shifts require substantial computational efforts, and are dependent on intrinsic errors of the GGA-DFT level of theory, number of k-points, and smearing of the electron occupancy around the Fermi level11. Nevertheless, the calculated NMR shifts, and the predicted ordering of the peaks in the spectrum, are sufficient to facilitate the interpretation of the experimental NMR signals.

Fig. 4: DFT analysis of the 125Te NMR Knight shifts in Bi2Te3 nanoplatelets.
figure 4

a Calculated 125Te orbital (green), Fermi contact (red), and dipolar terms (light yellow) of the Knight shift of bulk Bi2Te3 (SOC is set on). The inset shows the temperature dependence of the Knight shift according to experimental data in ref. 14. b The Te(1) and Te(2) DOS at the Fermi level N(EF), across a 9-quintuplet (9 nm) Bi2Te3 slab. The gray-shaded area marks a central region in the slab with “bulk-like” character, i.e. significant drop of the DOS. c Calculated 125Te Knight shift of a 5-quintuplet Bi2Te3 slab (SOC is set on). d Simulation of the 125Te NMR signal of a 9-quintuplet slab, by combining calculated bulk and edge state Knight shifts. The bulk/edge intensity ratio was set according to the number of Te sites in in the central (gray-shaded) and edge areas in panel b. Calculated NMR lines were convoluted with a Gaussian function. e The experimental isotropic 125Te NMR spectrum of the Bi2Te3 nanoplatelets. The NMR signal from the edge states at −452 ppm was corrected to account for differential \(T_2^\prime\) signal dephasing.

In the case of the 5-quintuplet-thick slab the isotropic total Knight shift of Te(1) and Te(2) coalesce to a single resonance, acquiring strong negative shift, δtot −2670 ppm. This is explainable by the fact that in very thin nanoplatelets (d ≤ 5 nm), Dirac electrons spread almost uniformly across the slab (Supplementary Fig. 5), inducing a strong negative Knight shift δorb via their orbital currents. By increasing the slab thickness the system splits into an interior “bulk” region that occupies the center of the slab, which is sandwiched between two “topological” surface regions. This is shown in Fig. 4b, which displays the Te(1) and Te(2) N(EF) across a 9-quintuplets slab. At the center of the nanoplatelet the DOS drops significantly (gray shaded area) and a band gap begins to open, as shown in Fig. 1c and Supplementary Fig. 6. Combining the theoretical bulk and surface Knight shifts at the appropriate signal intensity ratio, as explained in the caption of Fig. 4, the simulated ground state 125Te NMR spectrum of a 9-quintuplet-thick slab was depicted (Fig. 4d), and compared with the experimental isotropic 125Te NMR spectrum of the nanoplatelets (Fig. 4e). In the latter case, the shown signal intensities have been corrected by considering the \(T_2^\prime\) dependence of the signal on the interpulse time intervals of the aMAT experiment. In analogy to the microcrystalline system, the calculated NMR Knight shifts are more negatively shifted in comparison to the experimental ones, due to the strong, temperature dependent, negative shift; however the similar NMR patterns of the experimental and calculated spectra are unambiguous evidence that the NMR signal at −452 ppm originates from the Dirac electron states.


Bearing in mind the strong negative NMR frequency shift by decreasing temperature12,14, a nice correlation between the theoretical and experimental spectra is witnessed. This is strong evidence that the isotropic 125Te NMR signal component at −452 ppm belongs to the surface NMR signal shielded by the Dirac electrons. In this perspective, the intensity ratio of the surface-to-bulk NMR signals provides the mean volume of the nanoplatelets that is occupied by the Dirac electrons, whereas T1 (Supplementary Fig. 11) and \(T_2^\prime\) relaxation measurements on the pertinent peaks highlight the interaction of the Dirac electrons with the bulk interior. While ultrathin Bi2Te3 nanoplatelets are shown to be quantum topological species, where the NMR signals are dominated by the Dirac electrons, it is expected that by increasing the thickness of the nanoplatelets the NMR signals of the bulk interior will prevail, while at intermediate thicknesses, the interaction of the Dirac electrons with the bulk interior can be monitored both through the change in the T1 and \(T_2^\prime\) times of the distinct NMR peaks, and the measured Knight shifts. The presented experimental approach enables the simultaneous probing of the bulk and edge states, which is important in the study of SQPs.



Bi2Te3 nanoplatelets were synthesized following a solvothermal approach. Specifically, 1 mmol BiCl3 and 1.5 mmol Na2TeO3 were dispersed in 15 mmol of an alkaline solution (NaOH), and 1.16 M polyvinylpyrrolidone (PVP, Mw = 40,000 g/mol Da) were dissolved in 40 mL of ethylene glycol. The mixture was magnetically stirred until it turned highly translucent, then it was transferred and sealed into a Teflon-lined stainless-steel autoclave (capacity of 80 mL). The sealed autoclave was put into an oven at 180 °C for 36 h and cooled to room temperature. The resulting products were collected by repeated centrifugations, and subsequently washed with distilled water and ethanol, two times each, and finally vacuum dried overnight at 90 °C for further characterization.


The 125Te MAS experiments of the Bi2Te3 microcrystalline material were performed with a 4 mm HXY triple-resonance probe, at 14 kHz MAS on a Bruker 400 Avance-III spectrometer operating at a 125Te Larmor frequency of 126.23 MHz. Spectral acquisition was done with a double adiabatic spin-echo sequence (DAE) with a 2.5 μs 90° excitation pulse length, corresponding to an RF field of 100 kHz, followed by a pair of rotor-synchronized short high-power adiabatic pulses (SHAPs)17 of 71.43 μs length and a 5 MHz frequency sweep. For the separation of the isotropic shift and chemical shift anisotropy, which is of significant magnitude in heavy spin-1/2 nuclei26 and strong electron correlated systems, the adiabatic magic-angle-turning (aMAT) pulse sequence was employed16, which consists of a π/2 excitation pulse followed by six refocusing SHAP π-pulses. The same SHAPs as in the DAE were used. Separation of isotropic Knight Shifts was achieved in the isotropic dimension, whereas the MAS dimension corresponds to the conventional MAS spectrum. The diagonal ridges in the sidebands appear because of the inhomogeneous broadening of the sidebands, as they extend along the isotropic shift for each respective Te site. The 125Te MAS spectra of the Bi2Te3 nanoplatelets were acquired on the same spectrometer with a 2.5 mm HX probe, at 30 kHz MAS. For the acquisition of the DAE and the aMAT spectra, rotor synchronized SHAPs sweeping through 5 MHz in 33.33 μs were employed with RF field amplitude of 160 kHz. For the aMAT spectra, the same SHAPs were used with an evolution time of 66.66 μs, excluding the length of the SHAPs, which is equivalent to two rotor periods. Chemical shifts were referenced to TeO227.

The frequency-sweep 125Te NMR spectra were acquired on a home-built NMR spectrometer under static conditions, operating at Larmor frequency of 126.23 MHz. For the spin-lattice relaxation time T1 and the coherence lifetime \(T_2^\prime\) experiments a π/2-t-π/2 saturation recovery pulse sequence and a CPMG pulse sequence π/2-τ-{π-2τ-π-…-π-2τ-π}300 with a train of 300 π pulses were implemented, respectively. The T1 and \(T_2^\prime\) distribution analysis was performed by applying a non-negative Tikhonov Regularization Algorithm. Details on the relaxation analysis are provided in the SI.

Electron microscopy (SEM/STEM)

Scanning electron microscopy (SEM) images were recorded on a Hitachi S4800 microscope while the size distribution of the Bi2Te3 nanoplatelets were obtained by measuring 100 randomly selected Bi2Te3 platelets in the SEM image. STEM images and their energy-dispersive X-ray (EDX) elemental mappings were measured using a JEOL JEM-2100F. High-resolution TEM and STEM images were acquired using a Jeol ARM200 with probe Cs-corrector, operated at 200 kV. Cross-sectional TEM samples were prepared by FIB in KBSI (Quanta 3D FEG, FEI). Atomic-coordinates analysis from HAADF images was performed via intensity refinement method. The atomic coordinates analysis was performed with the following steps: (i) HAADF image normalization, (ii) Laplacian of Gaussian filtering, (iii) image erosion, (iv) atom position detection using circular pattern matching, (v) pattern matching errors correction, (vi) center position of atoms correction, (vii) computation of the average pixel intensity around the center of atoms, and finally (viii) two kind of markers based on intensity values has been depicted on the HAADF image, so that the coordinates of Bi and Te are clearly identified from each other.


The XRD spectra were recorded with an analytical PANalytical X’Pert PRO powder diffractometer. The sample was mounted on a zero-background holder and scanned by using Cu-Kα radiation (λ = 1.5418 Å) with the following experimental conditions: applied voltage of 40 kV, intensity of 30 mA, angular range (2θ) 5–80° and 0.03 steps/s. Rietveld refinement of obtained powder XRD pattern was carried out using the FULLPROF program software. Refined parameters include: overall scale factor, background (BGP), lattice parameters, atomic positions and orientation.

DFT calculations

DFT calculations were carried out with the QUANTUM ESPRESSO package28 on a Bi2Te3 slab comprised of 9 quintuplets, acquiring the mean thickness of the Bi2Te3 nanoplatelets. The slab surface was set according to the top-view HAADF image in Fig. 1a, along the (001) plane. Calculations were performed on the basis of the Perdew–Burke–Ernzerhof (PBE) type generalized gradient approximation. For the Brillouin zone integrations we used a 11 × 11 × 1 Monkhorst–Pack k-point mesh, and the kinetic energy cutoff was fixed to 800 eV. The lattice constants were acquired by the Rietveld refinement of the XRDs (a = b = 4.395 Å, c = 29.830 Å). Spin–orbit effects were treated self-consistently using fully relativistic projector augmented wave (PAW) pseudopotentials29.

NMR Knight Shift calculations were performed by using the full-potential linearized augmented plane-wave method, as implemented in the Wien2k DFT software package30. The spin–orbit interaction was considered in a second variational method. Calculations were performed with and without SOC on two different atomic configurations; bulk Bi2Te3, and a five quintuplets Bi2Te3 slab (25 atoms) with thickness 5 nm. The k-mesh convergence was checked up to 100,000 points for the bulk materials and up to 5000 points for the slab. Other computational parameters like atomic sphere radii, as well as potentials and wave functions inside the atomic spheres are kept as set by Wien2k defaults. The plane wave basis set size was determined by seting RKmax = 8, and for presented results we have used the PBE generalized gradient approximation31. The orbital part of the Knight shift δorb was calculated by using the x_nmr script of the Wien2k software package, by activating switches to include SOC, the Dirac states metallicity, and Fermi–Dirac smearing between 2 and 8 mRy. The Fermi contact and dipolar terms were calculated in the presence of SOC, using a spin-polarized set-up in an external magnetic field of 100 T, as explained in refs. 11,30.