Hexagonal group 6 TMDs are appealing because of their electric bandgap8 and strong spin–orbit coupling (SOC; ref. 9), which is beneficial in diverse applications such as logic transistors2,8,10, charge density waves11, superconductors12, spintronics and valley-optoelectronics13. Recently, the distorted octahedral phase of TMDs has attracted increasing attention for its potential application in a novel type of device: topological field-effect transistors based on quantum spin Hall (QSH) insulators7. In contrast to the 2H phase, which possesses a large bandgap (≥1 eV) and is stable at room temperature, the 1T′ phase has been observed to be semimetallic, with a slight band overlap near the Fermi level7,14,15,16,17, and metastable1,18. So far, only inhomogeneous small-area 1T′-MoS2 has been reported6, as confirmed by transmission electron microscopy (TEM), which revealed the structural properties of the material; however, the electrical properties of 1T′-MoS2 have not been experimentally verified, and the limited size of the 1T′ region has hindered further device-scale investigations. Single crystals of 1T′-MoTe2 and 1T′-WTe2 have been synthesized on a large scale14,15,16,17, but a reversible structural phase transition, which is an intrinsic feature of the single crystals, and the role of strong SOC in few-layered 1T′-TMDs have not yet been reported.

Here, we report a synthesis of single-crystalline MoTe2 that shows a reversible structural phase transition between 2H- and 1T′-MoTe2 and the electronic phase transition between semimetallic (bulk) and semiconducting (few-layered) monoclinic single-crystalline MoTe2. Our 2H-MoTe2 exhibits electrical and optical properties similar to previously reported results, but produces a maximum field-effect mobility of 40 cm2 V−1 s−1. More importantly, the newly discovered 1T′-MoTe2 exhibits a maximum carrier mobility of 4,000 cm2 V−1 s−1 and a giant magnetoresistance (MR) of 16,000% in a magnetic field of 14 T at 1.8 K in the bulk form, and the few-layered 1T′-MoTe2 reveals a bandgap of up to 60 meV.

Single crystals of 2H- and 1T′-MoTe2 were synthesized using the flux method (see Methods). No regular octahedral 1T-MoTe2 phase was obtained using this method. The engineering of single-crystalline 2H- and 1T′-MoTe2 was achieved based on the alloy phase diagram presented in Fig. 1a. In contrast to the phase diagram in the ASM database phase diagram19 (Fig. 1a left), the stable 2H phase begins to transform into the 1T′ phase at temperatures greater than 500 °C (Fig. 1a right). Slow cooling of 1T′-MoTe2 leads to recovery of the 2H phase—that is, the structural phase transition between the two phases is reversible—with a new mixed phase appearing in a temperature range between 500 °C and 820 °C, depending on the excess Te content. The α and β phases previously recorded in the database are now found to be equivalent to the 2H and 1T′ phases, as shown in Fig. 1a. The atomic lattice structures of 2H- and 1T′-MoTe2 are described in Fig. 1b. The clear symmetry distinction between hexagonal and monoclinic unit cells is represented by the red parallelograms in the ball-and-stick lattices. A typical MoTe2 single crystal, with a length of 1 cm, obtained using our synthesis method is shown in Fig. 1c. Compared with previous synthesis methods, the key element of our method is the complete dissolution of Mo and Te powders in liquid NaCl during crystal formation, which prevents the Te deficiency that would otherwise arise as a result of the low sublimation temperature of Te (400 °C). This distinguishing feature of our method explains why previous studies have observed Te deficiencies in their single crystals and why no inverse structural phase transition from the 1T′ phase to the 2H phase has previously been observed16. The X-ray diffraction (XRD) patterns of the two types of MoTe2 single crystals, which are presented in Fig. 1d, are consistent with the lattice structures presented in Fig. 1b. Successive Rietveld refinements for 1T′-MoTe2 revealed that the 1T′ structure crystallizes in the P21/m space group with lattice constants of a = 6.33 Å, b = 3.48 Å and c = 13.82 Å (see Methods). The atomic arrangements of the 2H and 1T′ structures were determined using high-resolution TEM images and diffraction patterns, as shown in Fig. 1e, f, in which the unit cells are indicated by red dotted parallelograms and are clearly related to the unit cells presented in Fig. 1b.

Figure 1: Alloy phase diagram and atomic structures of MoTe2.
figure 1

a, Alloy phase diagram of MoTe2 in the ASM database (left) and the new phase diagram based on this work (right). b, Schematic diagrams of 2H- and 1T′-MoTe2 in ball-and-stick presentations. c, Image of typical single crystals of the 1T′ and 2H phases grown using the flux method. d, XRD patterns for 1T′-MoTe2 (blue) and 2H-MoTe2 (red) single crystals. e,f, TEM bright-field images of 2H-MoTe2 (e) and 1T′-MoTe2 (f) with the corresponding electron diffraction images in the insets. The yellow spheres represent Te atoms.

Figure 2 presents optical measurements of phase-controlled 2H- and 1T′-MoTe2. Two prominent peaks, Ag and Bg, in the 1T′-MoTe2 spectra (Fig. 2a) are newly assigned based on the first-principles calculations and group theory analysis of a monolayer lattice structure to the vibration modes described in the inset of Fig. 2a. Each peak shift is summarized in Fig. 2b. The position of the Ag peak exhibits redshift as the thickness of the 1T′-MoTe2 decreases and approaches 265 cm−1 for three layers of 1T′-MoTe2, consistent with the calculated peak position of 269 cm−1 for the monolayer. By contrast, there is no noticeable variation in the position of the Bg peak, which is consistent with the calculated value of 163 cm−1 for the monolayer (Supplementary Information). Notably, absorption spectroscopy of few-layered (1 10 layers) 1T′-MoTe2 revealed an absorption band edge near 60 meV (Fig. 2c), in contrast to previous reports14,16,17. To measure such a low-energy absorption edge, Fourier-transform infrared spectroscopy (FTIR) and pellets consisting of 1 10 layers of mechanically exfoliated 1T′-MoTe2 were used. In the case of the 2H phase, the positions of the two peaks corresponding to the A1g and E2g modes are distinct from those of the 1T′ phase. The peak-shift behaviour of 2H-MoTe2 is similar to previous reports20, including a Raman-inactive mode in the bulk, B2g1, near 291 cm−1. The bandgap of 2H-MoTe2 as measured from the optical absorption spectra is 0.9 eV, corresponding to the well-known semiconducting state21. Notably, the narrow bandgap of 60 meV observed in the 1T′-MoTe2 represents the first observation of a bandgap in monoclinic TMDs.

Figure 2: Optical measurements of 2H- and 1T′-MoTe2.
figure 2

a, Layer-dependent Raman signals for 1T′-MoTe2. The calculated Raman vibration modes are illustrated in the insets. b, Peak positions in 1T′-MoTe2 with various numbers of layers. c, Absorption spectroscopy results for 1T′-MoTe2. d, Layer-dependent Raman signals for 2H-MoTe2. The calculated Raman vibration modes are illustrated in the insets. e, Peak positions in 2H-MoTe2 with various numbers of layers. Error bars in b,e represent absolute minima and maxima of Raman signals. f, Absorption spectroscopy results for 2H-MoTe2.

The electrical properties of few-layered MoTe2 were investigated by means of temperature-dependent transport measurements, as shown in Fig. 3. The steady increase in conductance with increasing temperature observed in Fig. 3a, b clearly indicates that both the 1T′ and 2H polymorphs possess bandgaps, consistent with the previous photo-absorption spectroscopy results. The Arrhenius plots of the conductance of the few-layered 1T′ (red dots) and 2H (black dots) samples, presented in Fig. 3c, indicates energy barrier heights of 0.057 eV and 0.2 eV, respectively. The measured energy barrier of the 1T′ phase is close to the absorption edge observed in Fig. 2c, whereas the 2H phase exhibits a considerably lower value than the optical bandgap in Fig. 2f. This feature can be understood in the context of a metal–semiconductor junction and is explained by the relative differences in work function22 between the metal electrode (Cr/Au) and the two polymorphs of MoTe2. The metallic behaviour of bulk 1T′-MoTe2 (blue dots) reveals that the bandgap that is evident in a few-layered sample closes as the number of layers increases. The 2H-MoTe2 transport measurements presented in Fig. 3b reveal ambipolar behaviour and a field-effect mobility of 40 cm2 V−1 s−1 at room temperature; the latter is the highest mobility ever recorded in 2H-MoTe2 (refs 8, 10). Hall measurements of 1T′-MoTe2 yield a carrier density of 7.8 × 1020 cm−3 and a mobility of 4,000 cm2 V−1 s−1 at T = 1.8 K (Fig. 3d). The Seebeck coefficient in the 2H phase (230 μV K−1) is considerably larger than that in the 1T′ phase (30 μV K−1), which is consistent with the different bandgap properties of the two phases (Fig. 3d inset).

Figure 3: Transport in MoTe2.
figure 3

a, Temperature-dependent electric measurements of 10 nm thick 1T′-MoTe2. b, Electric gating characteristics of 10 nm thick 2H-MoTe2 at various temperatures. c, Arrhenius plot of the conductance, revealing different activation energies in few-layered 1T′-MoTe2 (left y axis) and in 2H-MoTe2 (right y axis). Bulk 1T′-MoTe2 (left y axis) exhibits metallic behaviour. d, Temperature-dependent mobility of 1T′-MoTe2 and Seebeck coefficients of both phases of MoTe2 (inset). e, Magnetoresistance at T = 1.8 K and the associated SdH oscillation (inset). f, SdH oscillation with beating and the fitting of temperature-dependent SdH amplitudes using the Lifshitz–Kosevich theory. Is.d. is the source–drain current, Vs.d. is the source–drain voltage, σ is the conductance, and Δρ and δR are the resistance changes.

The large MR of bulk single-crystalline 1T′-MoTe2 presented in Fig. 3e demonstrates that effective electron and hole compensation occurs and nullifies the Hall effect in 1T′-MoTe2, leading to a large MR of 16,000% through a mechanism similar to that recently reported for WTe2 (refs 15, 23). The small observed bandgap of tens of meV appears only in few-layered 1T′-MoTe2 (up to 10 layers) and progressively disappears in thicker bulk single crystals, which is also indicated by density functional calculations presented below. Moreover, a Shubnikov–de Haas (SdH) oscillation and its beating characteristic are observed in Fig. 3e, with an individual peak period of 280 T and a beating period of 26 T. The presence of beating implies that multiple bands participate in carrier transport: either electron and hole bands or spin bands formed through the Rashba effect may be the origin of the beating. The temperature dependence of the SdH oscillation amplitude can be fitted using the standard Lifshitz–Kosevich theory,

where ΔEN(B) = heB/2πm is the energy gap between the Nth and (N + 1)th Landau levels, T and B are temperature and magnetic field, TD is the Dingle temperature, m is the effective mass of the carriers, and h and kB are the Planck constant and the Boltzmann constant, respectively. The fitting results indicate that the effective mass of the carriers is 0.462me (where me = 9.1 × 10−31 kg is the mass of a free electron).

The absence of the 1T phase in MoTe2 is explained by the spontaneous structural distortion from 1T-MoTe2 to 1T′-MoTe2, which is driven by Fermi surface nesting, as described in Fig. 4a. The Fermi surface of 1T-MoTe2 exhibits electron (red) and hole (blue) pockets in the Brillouin zone. Although two nesting wavevectors, qK and qM, exist on the Fermi surface of 1T-MoTe2, qM is exclusively responsible for the Peierls distortion (Supplementary Information). The nesting of the Fermi surface can be lifted through spontaneous symmetry breaking to reach a lower energy, indicating that 1T-MoTe2 is unstable. Driven by the nesting vector qM and electron–phonon interactions, structural distortion such as depicted in Fig. 4b (side views of the 1T- and 1T′-MoTe2 lattice structures) should occur. It has been recently reported that this structural distortion causes an intrinsic band inversion in group 6 monoclinic TMDs (ref. 7). Theoretical calculations also indicate that further electron doping produces more effective Fermi surface nesting and thus greater instability of the 1T phase (see Fig. 4c and Supplementary Information). The stability of both 2H- and 1T′-MoTe2 is demonstrated through first-principles calculations in Fig. 4c; 2H-MoTe2 is the more stable structure at low temperature, but the energy difference between 2H- and 1T′-MoTe2 is approximately only 35 meV and does not vary significantly with external charge doping. This small energy difference is markedly different from that observed in other TMD materials and allows the selective synthesis of high-quality 1T′-MoTe2 and 2H-MoTe2 single crystals using the flux method.

Figure 4: The influence of the SOC and the Peierls distortion in MoTe2.
figure 4

a, Fermi surface of monolayer 1T-MoTe2. The nesting vector qM connects the electron pockets (solid red line), resulting in an instability in the material. b, The consequences of Fermi surface nesting, schematically illustrated using side views of 1T- and 1T′-MoTe2. c, Relative total energy per unit cell for three phases of MoTe2 with various levels of electron doping. d, Band structures of 1T′-MoTe2 with (blue line) and without (red line) spin–orbit coupling. A magnified view of the region marked by the square outline is presented separately. e, Calculated band structures of bulk 1T′-MoTe2.

Although Peierls distortion favours the formation of the 1T′ phase, this phenomenon does not necessarily involve bandgap opening. It is known that, in the 1T phase, the Mo d orbitals are split into the eg, a1g, and eg′ states by an octahedral crystal field with trigonal distortion. Because the Mo ions in the 1T′ phase deviate substantially from the octahedral positions, all d orbitals split, thereby significantly modifying the electronic structure (Supplementary Information). This result implies that simple Peierls distortion is insufficient to explain the bandgap opening, although it is the driving force for the structural transformation. The band structure of monolayer 1T′-MoTe2 is calculated using the hybrid functional (HSE06) for the exchange–correlation potential with experimentally obtained lattice constants (Fig. 4d). Without SOC, the two bands cross at a point along the Γ–X line, without any gap opening (red line). However, in the presence of SOC, the degeneracy at the crossing point is lifted, resulting in a small bandgap of approximately 28 meV, which is in qualitative agreement with the experimental observations. The narrow bandgap disappears and produces a semimetallic 66 meV band overlap in the bulk 1T′ phase (Fig. 4e), which is consistent with the bulk transport data. This allows a unique type of bandgap manipulation through modification of the number of MoTe2 layers. The SOC is also found to play a role in gap opening for other 1T′ TMDs (Supplementary Information). Such SOC-induced gap opening and the inverted band structure in few-layered 1T′-MoTe2 are hallmarks of the topological insulating phase7,24,25.



Well-ground Mo and Te powders were mixed in an appropriate ratio with sodium chloride (NaCl) in an alumina tube. This powder mixture was then sealed in a glass tube under vacuum at a pressure of 10−5 torr. After the temperature of the glass tube containing the mixed powder had been maintained at T = 1,100 °C in a furnace for 12 h, the glass tube was cooled to 900 °C at a rate of 0.5 °C h−1. Then, rapid cooling from 900 °C to room temperature was achieved by placing the glass tube in water (‘quenching’), resulting in 1T′-MoTe2, or continuous slow cooling from 900 °C to room temperature at a cooling rate of 0.5 °C h−1 was applied, yielding 2H-MoTe2.

Instrumental set-up for XRD, AFM-Raman and TEM measurements.

The crystal structures of the 2H- and 1T′-MoTe2 phases were investigated using an X-ray diffractometer (Rigaku, SmartLab) with Cu Kα radiation (λ = 1.54059 Å) in the Bragg–Brentano geometry. For few-layered MoTe2, a mechanical exfoliation technique was applied on a SiO2 substrate. The minimum thicknesses of the 1T′-MoTe2 were 3.6 nm (five layers) for the transport study and 2.3 nm (three layers) for the Raman study. For the device measurements presented in Fig. 3, a thickness of 10 nm was used for both the 2H and 1T′ phases. Topographic and phonon properties were studied using a combined system for atomic force microscopy (AFM) and confocal Raman spectroscopy (NT-MDT, NTEGRA). In both the 2H and 1T′ samples, quantitative analysis using energy-dispersive X-ray spectroscopy (EDS) revealed an atomic ratio of Mo:Te = 1:2. To study the atomic structures of the materials, transmission electron microscopy (TEM) images were analysed. Fourier-transform infrared (FTIR) spectroscopy and polycrystalline 1T′-MoTe2 were used for the small-bandgap measurements. Temperature-dependent conductance measurements were performed to investigate the Schottky barrier in 1T′-MoTe2.


Density functional theory (DFT) calculations were performed using the generalized gradient approximation (GGA; ref. 26) for the exchange–correlation potential and the projector augmented wave potentials27, as implemented in the VASP code28. The wave functions were expanded in plane waves up to an energy cutoff of 400 eV. We employed a supercell geometry with a vacuum region of larger than 10 Å to prohibit interactions between adjacent supercells. We used Γ-centred k points generated by 20 × 20 and 20 × 10 Monkhorst–Pack meshes for 1T-MoTe2 and 1T′-MoTe2, respectively. The experimentally measured lattice parameters (a = 3.48 and b = 6.33 Å) were used for 1T′-MoTe2, whereas the GGA-optimized lattice parameters (a = b = 3.49 Å) were used for 1T-MoTe2. All atomic positions were fully optimized until the residual forces were less than 0.02 eV Å−1. For calculation of the band structure of 1T′-MoTe2, the hybrid functional (HSE06) was used as the exchange–correlation potential29 to improve the bandgap, whichis typically underestimated by the GGA. In our hybrid functional calculations, the screening parameter was fixed to ω = 0.207 Å−1.

Rietveld refinement of XRD for MoTe2.

Rietveld refinements for the two different phases were performed using the General Structure Analysis System (GSAS) software. Structural factors were extracted after successive refinements using different structural models at the condition of convergence with the best pattern match. Their lattice constants were determined through Rietveld analysis of X-ray diffraction30. The representative refinement results are summarized in Supplementary Table 1. In Supplementary Fig. 2, there are considerable differences between the calculated and measured peaks of the (00l) reflections because micro-single-crystalline and/or polycrystalline MoTe2 particles were mixed into the investigated powder samples, which resulted in an increase in the Rwp and Rp values in the refinements.

Absorption spectroscopy.

For optical absorption measurements of the small bandgaps (0.06 eV), expected from the electrical measurements, the tricky part is that we must use the FTIR (Fourier-transformed infrared spectroscopy) technique, which requires lateral sample dimensions of 0.5 cm and sample thicknesses of 2 mm for low-noise measurements. We note that conventional absorption spectroscopy or photoluminescence systems cannot detect or analyse such long wavelength light (20 μm, which corresponds to 0.06 eV). As we cannot produce uniformly thick (<10 nm) 1T′-MoTe2 with a lateral size of 0.5 cm, we used pellets consisting of exfoliated layers of 1T′-MoTe2. Single crystals of 1T′-MoTe2 were pulverized and mechanically exfoliated. The TEM images in Fig. 1e, f were taken with the sample dispersed after the mechanical exfoliation, indicating that we successfully obtained very thin layers (1 10 layers) by this method. For absorption measurement, we further pressed the exfoliated MoTe2 layers to make a pellet to enhance absorption. As bulk single crystals do not exhibit the band edge, the absorption edge observed from absorption (in Fig. 2c.) came from thin layers. The minimum energy of FTIR absorption is 50 meV, indicating that we can observe the absorption edge only if the bandgap is larger than 50 meV. We also confirmed that 20-layer 1T′-MoTe2 exhibits metallic behaviour by combining AFM and device measurements.