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Text: After the transfer , the quality of the MoS 2 flakes was verified by Raman spectroscopy . The two Raman maps in To examine the atomic composition as well as the chemical bonding environment of our samples , HR - XPS measurements at room temperature were carried out for pristine and hydrogen doped MoS 2 . The spectra were collected in a surface sensitive condition at a photon energy at h = 340 eV ( the photoelectrons were detected at 0 ° from the sample surface normal ⃗ and at 46 ° from the polarization vector ⃗ ) . The C-1s spectrum corresponding to the underlayer p doped graphene is shown in Figure S1 . The experimental data points are displayed as dots . The solid line is the envelope of fitted components . The pristine underlayer C1s spectra consist of two components located at the binding energies of 282.5 and 284.3 eV. These components correspond to bulk SiC and bilayer graphene , respectively . 27 The shape and the position of the C 1s peak , arising from the graphene and the SiC underlayer , have not changed after the exposition to three hydrogen doses , with respect to the pristine one . This confirms that the hydrogen did not interact with the graphene / SiC underlayer . The evolution of the Mo 3d and S 2p peaks from the pristine MoS 2 through the three different hydrogen doses are shown in Figure    2 ) for the second hydrogen dose . We notice that the spectra in In order to probe the effects of atomic hydrogen on the electronic properties of hydrogen doped MoS 2 ( 8  10 4 L ) , we performed micro - Raman spectroscopy on two flakes with the same orientation angle with respect to the graphene underlying substrate . This choice is made so that we can assume that the flakes are subjected to the same orientation - induced strain . 36,44,45 In Figure 4(c ) , the Raman spectra of MoS 2 before and after the hydrogenation are shown . The two vibrational modes are separated by about 19 cm -1 which corresponds to a single layered MoS 2 as was reported for MoS 2 monolayer . 46,47 After the treatment , we clearly observe that a downshift of the E 1 2 g peak has occurred together with a splitting of this peak . This is likely due to a strain induced by the hydrogen intercalation ( which is probably responsible for the appearance of the 1T - phase ) ; 48   Photoluminescence ( PL ) spectra of pristine and hydrogenated MoS 2 are provided in Figure S3 . We notice that the PL intensity decreases after hydrogenation ; this PL quenching can be explained by the suppression of defects from MoS 2 at room temperature as was observed for pristine and irradiated MoS 2 . 14 This confirms again that the used process is noninvasive and that it is possible to hydrogenate MoS 2 even with better quality .<|eot_id|><|start_header_id|>assistant<|end_header_id|>

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