Article | Open | Published:

Pressure-induced iso-structural phase transition and metallization in WSe2

Scientific Reports volume 7, Article number: 46694 (2017) | Download Citation


We present in situ high-pressure synchrotron X-ray diffraction (XRD) and Raman spectroscopy study, and electrical transport measurement of single crystal WSe2 in diamond anvil cells with pressures up to 54.0–62.8 GPa. The XRD and Raman results show that the phase undergoes a pressure-induced iso-structural transition via layer sliding, beginning at 28.5 GPa and not being completed up to around 60 GPa. The Raman data also reveals a dominant role of the in-plane strain over the out-of plane compression in helping achieve the transition. Consistently, the electrical transport experiments down to 1.8 K reveals a pressure-induced metallization for WSe2 through a broad pressure range of 28.2–61.7 GPa, where a mixed semiconducting and metallic feature is observed due to the coexisting low- and high-pressure structures.


Band structure engineering in transition metal dichalcogenides MX2 (M = Mo, W; X = S, Se) has attracted considerable interest due to not only the resulted exotic physics but also their potential technological relevances1,2,3,4,5,6,7,8,9,10,11,12,13,14. The MX2 structure consists of X-M-X sandwiched monolayers linked by weak van der Waals (vdW) interlayer forces, as shown in Fig. 1(a). When mechanically exfoliated, the indirect gap of bulk MX2 increases and transforms to a direct gap in the monolayer limit1, making them appealing for applications in electronics, optoelectronics as well as valleytronics2,3,4,5,6. In addition, doping7, temperature8 and strain1,9,10 can also be used to manipulate the size and nature of the gap and to drive a semiconducting to metal transition. Moreover, by intercalation or an electrostatic carrier injection using a field effect transistor, the carrier mobility can be modulated and even superconductivity can be induced11,12,13,14.

Figure 1
Figure 1

(a) The atomic arrangement of WSe2 in perspective and side views. W is represented by pink balls and Se by blue balls. a and c are cell parameters. θ is Se-W-Se bond angle and dWSe is W-Se bond length. (b) The XRD pattern of WSe2 at ambient conditions. Inset: a piece of WSe2 single crystal. (c) Representative synchrotron X-ray diffraction patterns of WSe2 during the compression and decompression (by d) runs (λ = 0.4246 Å). The observed and Rietveld refined profiles at 1.8 GPa is shown. The open circles and red lines are the experimental and calculated data. The positions of the Bragg reflections are marked by vertical sticks. The refined value is RP = 1.05% with weighted profile RWP = 1.40%.

Pressure is known as a powerful tool to tune lattice and the band gap, and its related studies on semiconducting MX2, indeed, have given rise to many novel physical phenomena. For example, MoS2 was reported to undergo a pressure-induced semiconductor to metal transition at high pressure15,16. Under further compression up to megabar, even a superconductivity is observed17. The pressure-induced metallization in MoS2 was related to a 2Hc to 2Ha iso-structural transition via layer sliding15,16,18. Very recently, the tunable electronic band gap of MoS2 was found to correlate intrinsically to a common structural characteristic, which was proposed to be readily extendible to other semiconducting MX219.

The pressure-induced metallization may not be always accompanied by a structural transition. In MoSe2, a pressure-induced metallization is observed, without any sign of structural change. The absence of structural transition in MoSe2 is empirically related to the relatively delocalized 4p orbitals of Se2− than the 3p orbitals of S2−, which results in stronger interlayer interactions to prevent the sliding process and thus the structural transition20.

To date, the high-pressure properties of WSe2 have not been well understood due to the lack of sufficient experimental data. Liu et al. found a slope change of electrical resistivity at ~38.1 GPa for WSe2, but the data was taken only in a temperature range of 290–420 K21. Based on theoretical calculations, this resistivity anomaly is related to a semiconductor to semimetal transition21. An early XRD study showed that the pristine 2Hc structure of WSe2 was stable up to 35.8 GPa22. Later, a Raman investigation confirmed no structural anomaly up to 20 GPa23. Recently, a first-principles study revealed an anomaly at 40 GPa consistently in the bulk modulus, Young’s modulus and Poisson’s ratio of WSe2, which may imply a possible structural transition21,24. More experimental efforts are therefore necessary to gain comprehensive knowledge of the high-pressure behavior of WSe2.

In the present study, we employ combined in situ synchrotron XRD and Raman spectroscopy, and electrical transport measurements to study the structural and electronic properties of single crystal WSe2. Both the XRD and the Raman data document an iso-structural transition. The resistivity measurements down to 1.8 K indicate that a pressure-induced metallization occurs in a broad pressure range, due to the coexistence of the low-pressure and high-pressure structural phases.

Results and Discussion

High-quality plate-like single crystals (inset of Fig. 1(b)) with typical dimensions of 2 mm × 1 mm × 0.2 mm were grown by chemical vapor transport method25,26. The crystal structure was characterized by single crystalline XRD (Fig. 1(b)), which shows a (00l) preferable orientation (defined as c axis). At ambient conditions, WSe2 crystallizes in a hexagonal lattice with space group of P63/mmc27, referred to as 2Hc-WSe2. To enrich the knowledge of the high-pressure structural symmetry than a previous study to 35.8 GPa22, we carried out in situ synchrotron XRD measurements by extending the pressure up to 62.8 GPa at room temperature. Selected experimental patterns are displayed in Fig. 1(c). At 1.8 GPa, the XRD profile is well reproduced by the 2Hc structure (see the bottom of Fig. 1(c)). Upon compression, there seems no evident anomaly throughout the whole pressure range studied except for a consistent broadening of all peaks above 19.1 GPa, which is in good agreement with a previous report to 35.8 GPa22. Assuming that the pristine 2Hc structure of WSe2 exists up to 62.8 GPa, we calculated the normalized cell parameters a/a0 and c/c0 as well as the volume V as a function of pressure. The results are displayed in Fig. 2. For comparison, previous theoretical and experimental structural data22,24 are also included. It is observed that, below 20 GPa (marked as PC1), all data agrees nicely with each other. Above PC1, however, a deviation starts to appear. The deviation above PC1 between the present and previous data may be related to a structural transition since all of these XRD data was fitted only based on a 2Hc structural model, without considering the possibility of a structural transition induced by pressure. In addition, here the broadening of all XRD peaks above 19.1 GPa may be a manifestation of this pressure-induced structural anomaly. We fitted the pressure-volume data below PC1 using the third-order Birch-Murnaghan equation of state28 (as shown by a gray zone in Fig. 2(c)). The bulk modulus is estimated to be B0 = 72(5) GPa and its first pressure derivative  = 4.6(5).

Figure 2
Figure 2

The normalized cell parameters a/a0 (a), c/c0 (b), and the volume V (c) as a function of pressure. The experimental data points from Selvi et al.22 and the theoretical results of Feng et al.24 are plotted for comparison. The gray zone represents the fitted data with the third-order Birch-Murnaghan equation of states.

To further check whether there is a possible structural transition, we plotted the axis ratio (c/a), the Se-W-Se bond angle (θ) and the W-Se bond length (dWSe) as a function of pressure (as illustrated in Fig. 1(a)). From Fig. 3(a), c/a shows a nonlinear decrease during the initial compression, indicating that the cell parameter c is much more compressible than a. This can be related to the weaker vdW interlayer forces relative to the stronger intralayer covalent chemical bonding29. Above PC1, the change rate of c/a varies drastically, following a roughly linear decrease with pressure, which suggests that the cell parameters a and c have nearly-isotropic contractions. Further compression to about 40 GPa (marked as PC2), the change rate of c/a shows a small uprise and then decreases almost linearly up to the highest pressure. At 62.8 GPa, a and c are reduced by 7.5% (Fig. 2(a)) and 13.4% (Fig. 2(b)), respectively, which clearly evidences an anisotropic compression. Meanwhile, both the θ and dWSe also display two anomalies with increasing pressure, namely, changes of slope at PC1 and PC2 (Fig. 3(b) and (c)). In addition to the above mentioned broadening of peaks (Fig. 1(c)) and deviation behavior (Fig. 2(c)), the consistent discontinuities in c/a, θ and dWSe at PC1 and PC2 should imply structural changes. It is noted that similar discontinuities in c/a or volume were also observed in high pressure MoS2, which was related to an iso-structural transition from 2Hc to 2Ha15. The iso-structural transition involves only a lateral sliding of adjacent layers and the change is subtle, probably making it not easy to decipher the structural changes directly from the raw XRD data.

Figure 3
Figure 3

Pressure dependence of (a) axial ratio c/a, (b) θ, and (c) dWSe of WSe2. The error bars, given by GSAS, are smaller than the size of the markers. The lines are for eye guide.

Raman spectroscopy is a sensitive and effective technique in detecting small changes in the structural transition. We carried out a detailed Raman study with pressures up to 57.2 GPa. Selected Raman spectra during compression and decompression are displayed in Fig. 4. Under ambient conditions, two main and several small Raman peaks are observed in the frequency range of 200–450 cm−1. The peaks at 248.4 and 257.3 cm−1 can be assigned to the and A1g vibrational modes respectively, and other small peaks (2 M modes) are related to the second order and combinational Raman modes, consistent with previous literature results23,30,31. As the pressure is increasing, while the peak intensity of A1g shows only a small variation, the peak intensity of the mode increases significantly. Going up from 28.5 GPa, the peak intensity of reduces rapidly and the mode begins to split into two peaks. Subsequently, a splitting of A1g mode starts to appear at 35.8 GPa. The splitting of the and A1g Raman modes for WSe2 under pressure is also reproduced in another run (see supplementary materials for details). Both the change of peak intensity and splitting of peaks give strong evidences of a pressure-induced iso-structural transition like in MoS216. Further increasing the pressure up to the highest pressure of 57.2 GPa, the splittings of and A1g can still be clearly observed, indicating an incompleteness of the structural phase transition and coexistence of the low- and high-pressure structural phases up to this pressure. In addition, we noted that the intensity of both Raman peaks from the high-pressure phase (red triangles, Fig. 4(a)) becomes dominant over those from the low-pressure phase (blue solid dots, Fig. 4(a)) above around 40 GPa, in excellent agreement with the critical pressure PC2 observed in our above XRD results (Fig. 3). When the pressure is released, the Raman spectra first show a splitting in the intermediate pressure (Fig. 4(b)) and then came back (0.2 GPa) to the starting positions at 0.3 GPa (Fig. 4(c)), manifesting the reversible structural transition.

Figure 4
Figure 4

Room temperature Raman spectra of WSe2 at selected pressures up to 57.2 GPa in the compression (a) and decompression (denoted by d) (b) runs. The numbers represent pressures in unit of GPa. The blue solid dots and red triangles indicate the appearance of splitting of the and A1g modes owing to pressure-induced phase transitions. (c) Comparison of Raman spectra at 0.3 and 0.2 GPa during compression and decompression, respectively.

The pressure dependence of the frequencies of the and A1g modes are shown in Fig. 5. Upon compression, both modes show almost linear behaviors in the 2Hc phase, in roughly accordance with previous results to 20 GPa23. The slope of the and A1g mode is 0.72 cm−1 GPa−1 and 1.52 cm−1 GPa−1, respectively. As is known, the symmetry of WSe2 lattice can be described by the space group, and the irreducible representation of phonon modes at the center of the Brillouin zone is Γ = A1g + 2 A2u + B1u + 2B2g + E1g + 2E1u + E2u + 2E2g, where the A and B modes are out-of-plane lattice vibrations, while the E modes are in-plane32. The mode is from the vibrations involved in both W and Se atoms in the basal plane, with the opposite directions from each other. The A1g mode refers only to the vibrations of the Se atoms along the c-axis (see the inset of Fig. 5). Consequently, the smaller slope of the mode than the A1g mode can be understood in terms of the anisotropic compressibility as the c-axis decreases much faster than the a-axis (see Fig. 3(a)). For the 2Ha phase, both modes increase linearly again but the slope of the mode changes to 0.89 cm−1 GPa−1.

Figure 5: Peak frequencies of and A1g modes as a function of pressure of WSe2, respectively.
Figure 5

The solid lines are for eye guide. The peak intensity of modes is indicated by a colour scale extending from 787 (dark blue) to 64711 (bright red). The insets show the schematics of vibrational Raman modes with the black dotted line representing weak vdW bonds between the adjacent layers.

Upon approaching to the structural transition, the peak intensity of the A1g mode increases slightly as can be seen from Figs 4 and 5 (color scale). Meanwhile, the intensity of increases violently and then decreases rapidly at PC1 above which the iso-structural transition occurs. Outside the transition region, the peak intensity of both modes varies gradually with pressure. In addition, the slope of A1g variation remains constant before and after the structural transition but the slope of variation becomes larger from the 2Hc (0.72 cm−1 GPa−1) to 2Ha (0.89 cm−1 GPa−1). These observations imply that, while the out-of-plane compression is involved in the iso-structural transition due to anisotropic compressibility, the in-plane compression (strain) plays a dominant role in triggering the transition via layer sliding. This conclusion may explain the relatively low transition pressure (PC1 ~ 28.5 GPa) here compared with the previous theoretical calculations by only taking free mutual sliding of layers into consideration (~40 GPa)21,24.

We also performed in situ high-pressure resistivity (ρ) measurements for WSe2 in a diamond anvil cell up to 61.7 GPa. Standard four-point probe method was used. In order to get a more comprehensive understanding on the electrical properties than a previous investigation (290–420 K)21, we extended the temperature range down to 1.8 K. The results are displayed in Fig. 6(a). Roughly, two regimes can be identified upon compression: firstly, below 19.1 GPa, a typical semiconductor behavior (dρ/dT < 0) is observed; secondly, from 28.2 GPa to the highest pressure of 61.7 GPa investigated in this experiment, the resistivity first shows a plateau between 100 K and 200 K and then a metallic-like behavior (dρ/dT > 0), which becomes increasingly dominant. Figure 6(b)–(d) display the representative ρ-T curves for each phase. Our results clearly reveal a pressure-induced metallization for WSe2. In addition, the resistivity in the intermediate phase can be considered as a superposition of the low-pressure semiconducting and high-pressure metallic behaviors. These characteristics can be related to a coexistence of the low-pressure 2Hc and high-pressure 2Ha structures, in good agreement with the above XRD and Raman data.

Figure 6
Figure 6

(a) The pressure dependence of resistivity curves of WSe2 as a function of temperature, with the maximum pressure up to 61.7 GPa. (b,c,d) The resistivity curves of WSe2 as a function of temperature at representative pressures: 19.1, 28.2 and 61.7 GPa, respectively.


In summary, we have investigated the structural and electrical properties on single crystal WSe2. In spite of the lack of evident changes in the XRD patterns, the pressure dependent c/a, θ and dWSe consistently reveal two anomalies at PC1 ~ 20 GPa and PC2 ~ 40 GPa. The Raman active and A1g modes split into two peaks, beginning at 28.5 GPa and 35.8 GPa, respectively, and lasting to the highest pressure of 57.2 GPa. These results strongly evidence that there exists an iso-structural transition for high-pressure WSe2. The distinctly different trend of peak intensity between and A1g with pressure suggests that the in-plane strain plays a dominant role in triggering the transition over the out-of-plane compression. Consistently, the resistivity measurements show a pressure-induced metallization, through a broad pressure range of 28.2–61.7 GPa, where the resistivity feature can be treated as a superposition of the low-pressure semiconducting and high-pressure metallic behaviors.


WSe2 single crystals were grown via chemical vapour transport technique. High purity powders of tungsten (99%, Alfa Aesar) and selenium (99.99%, Alfa Aesar) with chemical stoichiometry were ground and sealed in an evacuated quartz ampoule (<10−4-torr vacuums). First, the components were made to react at 600 °C for 3 days. The loose sample was then re-ground and sealed in an evacuated quartz ampoule to get polycrystalline WSe2 samples. Second, an ampoule containing some polycrystalline WSe2 was placed in a two-zone furnace. The hot zone was maintained at 1060 °C and the cold zone was maintained at 1000 °C for 14 days. All weighing and mixing was carried out in a glove box. The crystal structure was characterized by room temperature XRD with Cu X-ray radiation (Kα = 1.5418 Å).

In situ high pressure synchrotron radiation XRD experiments were performed at 16-BM-D, HPCAT33 of Advanced Photon Source of Argonne National Laboratory using a Mao-Bell symmetric diamond anvil cell (DAC) with a culet of 300 μm diameter. The as-grown single crystals were ground into fine powder for XRD experiments. A focused monochromatic X-ray beam (4.3 μm (v) × 3.6 μm (h) in FWHM) with a wavelength of 0.4246 Å was used for the X-ray diffraction experiment. The T301 stainless-steel gasket was pre-indented from a thickness of 300 μm to ~35 μm, and a center hole at 140 μm in diameter was drilled to serve as the sample chamber. A pre-pressed powder sheet with a typical size of 30 μm × 30 μm × 5 μm was loaded into the chamber together with a ruby ball34 and Daphne 7373 oil as pressure marker and pressure transmitting medium, respectively. The XRD patterns were collected with a Mar345 image plate detector. Refinements of the measured XRD patterns were performed by the GSAS software35.

Raman scattering experiments were carried out at the Center for High Pressure Science and Technology Advanced Research (HPSTAR) in Shanghai. The Raman spectrum measurement was performed using a commercial Renishaw Raman spectroscopy system with a 532 nm laser excitation line. The Raman system was first calibrated by using single crystal silicon with the characteristic peak at 520 cm−1 and the uncertainty is within 0.5 cm−1. The focused laser beam was about ~5 μm. The laser power was 50% and the collection time was 100 s. Mao-Bell type DAC was used to generate the pressure. The measurements were conducted on a freshly cleaved single crystal (dimensions of 30 μm × 25 μm × 10 μm). Daphne 7373 oil was used as the pressure medium. The diamond culet was 300 μm in diameter. A rhenium gasket was pre-indented to a thickness of 29 μm, and a center hole at 124 μm in diameter was drilled. The pressure was determined by the ruby fluorescence scale below 20 GPa34 and the diamond Raman scale above 20 GPa36.

The pressure-dependent electrical transport experiments were performed by employing the standard four-probe method in a nonmagnetic Be-Cu cell. The diamond anvils is 300 μm culets. A T301 stainless-steel gasket covered with a mixture of epoxy and fine cubic boron nitride (c-BN) powder was used for high-pressure transport measurements. Pt-foil (5 μm) was used as the electrical lead. Standard four-probe method was applied in the ab plane of single crystals with typical dimensions of 90 × 40 × 10 μm3. NaCl powder was used as the pressure transmitting medium. Pressure was calibrated with the ruby fluorescence shift at room temperature34.

Additional Information

How to cite this article: Wang, X. et al. Pressure-induced iso-structural phase transition and metallization in WSe2. Sci. Rep. 7, 46694; doi: 10.1038/srep46694 (2017).

Publisher's note: Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.


  1. 1.

    , , , & Thickness and strain effects on electronic structures of transition metal dichalcogenides: 2H-MX2 semiconductors (M = Mo, W; X = S, Se, Te). Phys. Rev. B 85, 033305 (2012).

  2. 2.

    , , , & Electronics and optoelectronics of two-dimensional transition metal dichalcogenides. Nat. Nanotechnol. 7, 699–712 (2012).

  3. 3.

    , , , & Two-dimensional transition metal dichalcogenides as atomically thin semiconductors: opportunities and challenges. Chem. Soc. Rev. 44, 8859 (2015).

  4. 4.

    et al. Monolayer MoS2 heterojunction solar cells. ACS Nano 8, 8317–8322 (2014).

  5. 5.

    et al. Magnetic control of valley pseudospin in monolayer Wse2. Nat. Phys. 11, 148 (2015).

  6. 6.

    , , , & Valley polarization in MoS2 monolayers by optical pumping. Nat. Nanotechnol. 7, 490 (2012).

  7. 7.

    et al. Superconducting dome in a gate-tuned band insulator. Science 338, 1193–1196 (2012).

  8. 8.

    et al. Thermally driven crossover from indirect toward direct bandgap in 2D semiconductors: MoSe2 versus MoS2. Nano Lett. 12, 5576–5580 (2012).

  9. 9.

    & Tuning the electronic properties of semiconducting transition metal dichalcogenides by applying mechanical strains. ACS Nano 6, 5449–5456 (2012).

  10. 10.

    , , , & Strain-induced semiconductor to metal transition in the two-dimensional honeycomb structure of MoS2. Nano Res. 5, 43–48 (2011).

  11. 11.

    , & Strain-enhanced superconductivity of MoX2 (X = S or Se) bilayers with Na intercalation. Phys. Rev. B 93, 155430 (2016).

  12. 12.

    et al. High-mobility holes in dual-gated WSe2 field-effect transistors. ACS Nano 9, 10402–10410 (2015).

  13. 13.

    , , & Electric-field-induced superconductivity at 9.4 K in a layered transition metal disulphide MoS2. Appl. Phys. Lett. 101, 042603 (2012).

  14. 14.

    , , & Electrostatically induced superconductivity at the surface of WS2. Nano Lett. 15, 1197–1202 (2015).

  15. 15.

    et al. Pressure-induced semiconducting to metallic transition in multilayered molybdenum disulphide. Nat. Commun. 5, 3731 (2014).

  16. 16.

    et al. Pressure-induced metallization of molybdenum disulfide. Phys. Rev. Lett. 113, 036802 (2014).

  17. 17.

    et al. Ultrahigh pressure superconductivity in molybdenum disulfide. (2015).

  18. 18.

    , & Structure change, layer sliding, and metallization in high-pressure MoS2. Phys. Rev. B 87, 144105 (2013).

  19. 19.

    , & Structural characteristic correlated to the electronic band gap in MoS2. Phys. Rev. B 94, 020101 (2016).

  20. 20.

    et al. Pressure induced metallization with absence of structural transition in layered molybdenum diselenide. Nat. Commun. 6, 7312 (2015).

  21. 21.

    et al. Pressure induced semiconductor-semimetal transition in Wse2. J. Phys. Chem. C 114, 14251–14254 (2010).

  22. 22.

    , , & High-pressure x-ray diffraction study of tungsten diselenide. J. Phys. Chem. Solids 69, 2311–2314 (2008).

  23. 23.

    , , , & Raman spectroscopic investigations on transition-metal dichalcogenides MX2 (M = Mo, W; X = S, Se) at high pressures and low temperature. J. Raman Spectrosc. 45, 971–979 (2014).

  24. 24.

    , , & Effect of pressure on elastic, mechanical and electronic properties of WSe2: A first-principles study. Mater. Res. Bull. 50, 503–508 (2014).

  25. 25.

    et al. Pressure-driven dome-shaped superconductivity and electronic structural evolution in tungsten ditelluride. Nat. Commun. 6, 7805 (2015).

  26. 26.

    et al. Pressure-induced superconductivity in a three-dimensional topological material ZrTe5. PNAS 113, 2904–2909 (2016).

  27. 27.

    , & Crystal structures of tungsten disulfide and diselenide. Solid State Chem. 70, 207–209 (1987).

  28. 28.

    Finite elastic strain of cubic crystals. Phys. Rev. 71, 809–824 (1947).

  29. 29.

    , & Phase transitions between polytypes and intralayer superstructures in transition metal dichalcogenides. Phys. Rev. B 69, 134111 (2004).

  30. 30.

    et al. Mechanical exfoliation and characterization of single- and few-layer nanosheets of WSe2, TaS2, and TaSe2. Small 9, 1974–81 (2013).

  31. 31.

    et al. Optical signature of symmetry variations and spin-valley coupling in atomically thin tungsten dichalcogenides. Sci. Rep. 3, 1608 (2013).

  32. 32.

    & Long wavelength optic phonons in WSe2. Can. J. Phys. 55, 379–382 (1977).

  33. 33.

    et al. New developments in micro-X-ray diffraction and X-ray absorption spectroscopy for high-pressure research at 16-BM-D at the advanced photon source. Rev. Sci. Instrum. 86, 072205 (2015).

  34. 34.

    , & Calibration of the ruby pressure gauge to 800 kbar under quasi-hydrostatic conditions. J. Geophys. Res. 91, 4673–4676 (1986).

  35. 35.

    & Gsas-general structure analysis system. Los Alamos National Laboratory Report LAUR. 86–748 (2000).

  36. 36.

    & High-pressure raman spectroscopy of diamond anvils to 250 GPa: Method for pressure determination in the multimegabar pressure range. J. Appl. Phys. 96, 3748–3751 (2004).

Download references


This work is supported by the Ministry of Science and Technology of China (National Basic Research Program, Grant No. 2016YFA0401804) and the National Natural Science Foundation of China (Grant Nos 11574323, U1632275). X. C. thanks for the support from the Natural Science Foundation of Anhui Province (1708085QA19). The X-ray work was performed at HPCAT (Sector 16), Advanced Photon Source (APS), Argonne National Laboratory. HPCAT operations are supported by DOE-NNSA under Award No. DE-NA0001974 and DOE-BES under Award No. DE-FG02-99ER45775, with partial instrumentation funding by NSF. The Advanced Photon Source is a US Department of Energy (DOE) Office of Science User Facility operated for the DOE Office of Science by Argonne National Laboratory under Contract No. DE-AC02-06CH11357.

Author information


  1. Anhui Key Laboratory of Condensed Matter Physics at Extreme Conditions, High Magnetic Field Laboratory, CAS and University of Science and Technology of China, Hefei 230031, China

    • Xuefei Wang
    • , Xuliang Chen
    • , Yonghui Zhou
    • , Chao An
    • , Ying Zhou
    • , Ranran Zhang
    • , Chuanchuan Gu
    •  & Zhaorong Yang
  2. High Pressure Collaborative Access Team, Geophysical Laboratory, Carnegie Institution of Washington, Argonne, Illinois 60439, USA

    • Changyong Park
  3. Center for High Pressure Science and Technology Advanced Research (HPSTAR), Shanghai 201203, China

    • Wenge Yang
  4. High Pressure Synergetic Consortium (HPSynC), Geophysical Laboratory, Carnegie Institution of Washington, Argonne, Illinois 60439, USA

    • Wenge Yang
  5. Key Laboratory of Materials Physics, Institute of Solid State Physics, Chinese Academy of Sciences, Hefei 230031, China

    • Zhaorong Yang
  6. Collaborative Innovation Center of Advanced Microstructures, Nanjing University, Nanjing 210093, China

    • Zhaorong Yang


  1. Search for Xuefei Wang in:

  2. Search for Xuliang Chen in:

  3. Search for Yonghui Zhou in:

  4. Search for Changyong Park in:

  5. Search for Chao An in:

  6. Search for Ying Zhou in:

  7. Search for Ranran Zhang in:

  8. Search for Chuanchuan Gu in:

  9. Search for Wenge Yang in:

  10. Search for Zhaorong Yang in:


Z.R.Y. conceived and supervised the project. X.F.W. synthesized the WSe2 single crystals and performed the room temperature single crystal X-ray diffraction experiment. X.L.C. and C.P. performed the high-pressure synchrotron X-ray diffraction experiments. X.F.W. performed the electrical transport and Raman experiments with the help of Y.H.Z., C.A., Y.Z., R.R.Z., C.C.G., and W.G.Y. X.F.W., X.L.C. and Z.R.Y. analysed the data and wrote the manuscript. C.P. helped proofread the manuscript. All authors reviewed and commented on the manuscript.

Competing interests

The authors declare no competing financial interests.

Corresponding authors

Correspondence to Xuliang Chen or Zhaorong Yang.

Supplementary information

Word documents

  1. 1.

    Supplementary Materials

About this article

Publication history






By submitting a comment you agree to abide by our Terms and Community Guidelines. If you find something abusive or that does not comply with our terms or guidelines please flag it as inappropriate.