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Photoconductivity Multiplication in Semiconducting Few-Layer MoTe2

We report efficient photoconductivity multiplication in few-layer 2H-MoTe2 as a direct consequence of an efficient steplike carrier multiplication with near unity quantum yield and high carrier mobility (∼45 cm2 V–1 s–1) in MoTe2. This photoconductivity multiplication is quantified using ultrafast, excitation-wavelength-dependent photoconductivity measurements employing contact-free terahertz spectroscopy. We discuss the possible origins of efficient carrier multiplication in MoTe2 to guide future theoretical investigations. The combination of photoconductivity multiplication and the advantageous bandgap renders MoTe2 as a promising candidate for efficient optoelectronic devices.


■ INTRODUCTION
Photoexcitation of semiconductors with photon energies (hυ) exceeding their bandgap (E g ) creates energetic electrons and holes. In most semiconductors, these so-called hot carriers can cool down to the band-edge via carrier-phonon scattering, on a subpicosecond time scale. Such ultrafast energy loss via hot carrier cooling accounts for over ∼30% efficiency reduction within the Shockley and Queisser framework. 1 Optical generation of multiple pairs of electrons and holes in semiconductors by an energetic photon (with hυ > 2E g ), a process known as carrier multiplication (CM) or multiexciton generation (MEG), 2 provides a novel solution to circumvent the energy losses in hot carriers relevant for high-efficiency photovoltaics. Substantial previous research has aimed at quantifying the CM efficiency and obtaining a fundamental understanding of the CM mechanism with a primary focus on semiconducting quantum dots (QDs). 3−11 The benefits from strong quantum confinement for CM in QDs come from the enhanced Coulomb interaction and relaxed momentum conservation condition. On the other hand, previous theoretical 12, 13 and experimental 14−17 studies have also shown that the reduced density of states imposed by confinement may constrain the energy conservation condition so that quantum confinement does not necessarily facilitate CM.
In this context, two-dimensional materials with atomic-level control of the thickness, combined with strong Coulomb effects 18,19 and still relatively high density of states, are potentially interesting platforms for efficient CM. Indeed, Aerts et al. reported a strong MEG effect in thin PbS nanosheets with much higher efficiency than that in zero-dimensional QDs, one-dimensional nanorods, and 3D bulk counterparts. 20 Furthermore, Kim and colleagues extended recently such studies into multilayered van der Waals (vdW) materials of MoTe 2 and WSe 2 . 21 They reported near-perfect MEG in vdW structures employing transient absorption (TA) spectroscopy, that is, a unity quantum yield with an onset energy of 2E g . However, the mechanism on which the CM/MEG takes place in vdW materials remains elusive. While the generation of multiexcitons following MEG was proposed, 21 direct spectroscopic evidence for these high-order excitonic states is missing. Finally, if indeed (multi)excitons are the primary photoproduct, they would have to be dissociated, for example, for photovoltaic applications. Therefore, establishing the nature of the multiple carrier generation process by CM/MEG in vdW structures is relevant for applications.

■ RESULTS AND DISCUSSION
Structural Characterization. Figure 1a shows the atomic configuration of the 2H phase of MoTe 2 . The sample is produced by chemical vapor deposition (from SixCarbon Technology, Shenzhen), and the layer thickness is about 5 nm (= ∼7 layers). The Raman spectrum in Figure 1b exhibits two prominent peaks at 173 and 235 cm −1 originating from the out-of-plane A 1g mode and in-plane E 2g mode in 2H-    25 To quantify its bandgap E g , we have conducted UV−vis absorption measurements. On the basis of the absorbance in Figure 1c, we quantify the bandgap of 2H-MoTe 2 to be 0.90 eV using a Tauc plots (see Figure S1). Other optical transitions, marked by A, B, A′, B′, C, and D, correspond to direct transitions at the K and Γ points of the Brillouin zone. 26 Note that the absorption of multilayered MoTe 2 on sapphire does not show the absorption quanta of ∼1.6% observed by Fang et al. for InAs thin films, presumably due to the indirect nature of transitions in MoTe 2 . 27 For monolayer MoTe 2 , strong exciton effects have been reported with binding energy up to 600 meV. 28−30 For the bulk phase, the exciton binding energy is small at ∼15 meV, substantially lower than the thermal excitation at room temperature (k B T). 31 Carrier Multiplication in 2H-MoTe 2 . To explore the CM effect, we employ optical-pump terahertz (THz)-probe (OPTP) spectroscopy to measure the ultrafast photoconductivity. As a purely optical technique, OPTP spectroscopy has been demonstrated to provide quantitative insight into the intrinsic electrical transport properties (including charge density, scattering time, and so forth) in a contact-free manner. 32−35 In a typical experiment, as shown in Figure 2a, a laser pulse with tunable photon energies above the bandgap is used to excite electrons from valence to conduction band. Subsequently, a single-cycle THz pulse with ∼1 ps duration is employed to probe the time-dependent photoconductivity (Δσ) dynamics by monitoring the photoinduced THz absorption (ΔE) at varied pump−probe delays. The photoconductivity is proportional to ΔE by Δσ = −ΔE = −(E pump − E 0 ), where E pump and E 0 represent the transmitted THz field with and without photoexcitation. Figure 2b shows the fluence-dependent THz photoconductivity following 1.55 eV excitation. This transient photoconductivity exhibits a subpicosecond rise, reflecting free carrier generation, and a fast decay within a few picoseconds. We attribute this fast decay to ultrafast carrier trapping at defects (see the extended discussion in SI) in line with previous studies. 21,36 While the passivation of these defects will be required for device applications, it does not affect the CM process in this study as CM occurs on a subpicosecond time scale. 21 In Figure 2c, we present the photoconductivities normalized to the absorbed photon density. We find that within the fluence ranges used in this study, the photoconductivities scale linearly with fluence. On the basis of these results, we can exclude the multiplication of charge carriers trivially by a two-photon excitation process.
To investigate the CM in MoTe 2 , we have further measured pump photon energy-dependent photoconductivities. The conductivity dynamics following the 3.1 eV excitation is shown in Figure S2a. In Figure 2d, we compare the fluencedependent peak value in photoconductivity of MoTe 2 under 3.1 and 1.55 eV excitations, corresponding to ∼3.4 (CM energetically possible) and 1.7 (CM impossible) times of the bandgap, respectively. For a given absorbed photon density, we find that the photoconductivity upon 3.1 eV excitation is nearly twice that of 1.55 eV excitation. While this photoconductivity multiplication provides a strong indication of possible CM effect in MoTe 2 , special care needs to be taken for data analysis. Particularly, the photoconductivity Δσ scales with the products of carrier density (N) and charge mobility (μ) as Δσ = N·e·μ with e as the elementary charge. To separate the contribution of the carrier density from the charge mobility, we have conducted THz time-domain spectroscopy (TDS, see SI) at the pump−probe delay close to the photoconductivity peak (at a pump−probe delay of 1.5 ps).
In Figure 2e, we compare the frequency-resolved photoconductivities for both 3.1 and 1.55 eV excitations obtained from TDS measurements. In both cases, the conductivities display a large real conductivity and essentially zero imaginary contribution. This result suggests that a substantial amount (if not all) of photogenerated carriers in our sample are present as free charges. Importantly, the free carrier response dominates the dynamics for all excitations so that we can rule out the free charge generation via "hot exciton dissociation", one of the most reported free charge generation mechanisms in excitonic materials. 37,38 To further shed light on the electrical transport properties and disentangle the contribution of carrier density from mobility in MoTe 2 at a given pump−probe delay time, we apply the standard Drude model (see SI). 32 We find that the model describes the data well, and we summarize the inferred parameters in Table 1. When comparing 3.1 and 1.55 eV excitations, the charge scattering times τ are found to be nearly identical; the only different parameter is the plasma frequency ω p , which is directly related to carrier density N. Microscopically, the charge carrier mobility μ in a material is given by μ = τ · * m e . The same τ for both 3.1 and 1.55 eV excitations implies that charge carrier mobility does not depend on the excitation photon energies at the time delay chosen for TDS (1.5 ps after photoexcitation). To make a quantitative correlation, we have plotted the carrier densities obtained from the fittings as the right Y-axis and compared them to the fluence-dependent photoconductivity data, as shown in Figure  2d. The overlap between rescaled carrier densities and photoconductivities offers direct, quantitative evidence for efficient CM taking place in our sample. Note that the conclusion is robust and does not depend on the model applied. Strong support for this argument comes from the normalized frequency-resolved conductivity, as shown in Figure S4 (see SI) based on the same data sets in Figure 2e, and we find no observable difference between the two. An extended analysis based on the Drude−Smith model leads to the same conclusion of CM (see Figure S5 and associated discussion in SI). This result also indicates that charge carriers reach a quasi-equilibrium condition (e.g., at the band-edge) at 1.5 ps after the excitation with both 1.5 (via cooling or phonon emission processes) and 3.1 eV (by CM) photons.
Finally, based on the τ inferred from the fittings, we calculate the dc electron mobility in our sample to be 45 ± 9 cm 2 V −1 s −1 . The value is much higher than that of the QD solids (with the reported value in most studies way below 1 cm 2 V −1 s −1 and the highest around 10 cm 2 V −1 s −1 ). 39,40 In addition, the estimated mobility is in the same range as the results (∼30−40 cm 2 V −1 s −1 ) from electrical transport measurements on  Figure 3a. Here, we take the photoconductivity maximum at a given absorbed photon density (or equivalently the slope in the fluence-dependent conductivity in Figure 3a) to quantify the CM efficiency, as these two values are linked in a linear fashion (see Figure 2d). In Figure 3b, we summarize the photoconductivity normalized to the absorbed photon density at varied photon energies. For the range of excitation energies between 1 and 2 times that of E g (no CM), we find that the carrier generation efficiency is independent of the pump photon energies, as expected. For further data analysis, we assume the carrier generation quantum yield for photon energy below twice the E g to be 100% (marked in the right Y-axis). With increasing the photon energy, we observe twice photoconductivity jumps at around 2.8 and 4.2 times of E g , which we attribute to CM effect following the previous discussion. Remarkably, we observe the enhancement of photoconductivity by CM by a steplike manner with nearly 100% CM quantum yields. 43 Finally, we investigate the recombination dynamics following CM. In QD systems, multiple pairs of electrons and holes generated by CM can effectively recombine in a few to tens of picoseconds via Auger recombination. 2,8,10,44 In contrast, as shown in Figure  S6, for all pump energies used in the study, we observe no changes in the decay dynamics. Apparently, the recombination process is dominated by the fast trapping by defects, which effectively competes with the Auger process. Note that this was previously also concluded by Kim et al. 21 Discussion. Now we discuss the mechanism by which CM in multilayer MoTe 2 takes place. The free carrier dominant dynamics observed in all pump photon energies implies that CM in our system occurs through a scattering mechanism known as impact ionization (II). 12,45−48 In the II process, a hot carrier with excess energy beyond the bandgap can effectively re-excite an additional electron across the bandgap on subpicosecond time scales, driven by carrier−carrier scattering processes. As a reverse Auger recombination process, this model has been previously applied to account for the CM effect in bulk silicon 45 and low-dimensional nanomaterials including QDs, 12,46,49 carbon nanotubes, 50 and 2D materials. 47 Within the II framework, the CM efficiency is directly governed by the kinetic competition between II itself and hot carrier cooling. To evaluate the observed CM efficiency and compare the impact ionization rate to the cooling rate, we conduct a further data analysis following a phenomenological model proposed by Beard and colleagues. 51 In the model, the detailed band structure of the material is neglected, and the CM efficiency is determined by the II and the carrier cooling via phonon emission.
Comparing the model (shown as dash-dotted lines in Figure  3b) to the data, we find the CM efficiency in 2H-MoTe 2 is nearly unity up to ∼94% (see details for the fitting in SI). The CM onset is found to be ∼2.8 E g . Given the high η CM , we can readily conclude that the II rate dominates over the cooling process in 2H-MoTe 2 . Here we estimate the energy loss rate via cooling by (hυ − E g )/τ cooling (with τ cooling ∼1.5 ps as the cooling time following 1.55 eV excitation) to be 0.43 eV/ps. We further assume a linear proportionality between the cooling time and the excess energy of hot carriers. Under such an assumption and applying the rate competition model by Beard, 51 the II rate is estimated to be nearly 1 order of magnitude higher than the cooling rate for the first CM step (e.g., 3.2 eV/ps for 3.1 eV excitation) to ensure a high CM efficiency in our system. The previously reported CM onset energy in MoTe 2 of ∼2 E g is lower than the 2.8 E g found here. 21 This difference may be due to variations in sample thickness and thus electronic structure but will require further study (see an extended discussion in SI).
While the phenomenological analysis captures the essence of CM, to fully unveil the efficient II and thus CM in 2H-MoTe 2 theoretical calculations (e.g., by tight-binding calculations) 3,12,46 explicitly on multilayer 2H-MoTe 2 are required. To guide future theoretical treatments in this system, we summarize some key observations from the experiments.
(1) CM onset. In our study, the first CM onset and the accompanying sharp rise of the photoconductivity in 2H-MoTe 2 is found to be in the range of 2.4−2.6 eV, corresponding to the optical transition at Γ point. To shed further insight on the CM at the Γ point, we discuss the band structure of MoTe 2 based on previous theoretical calculation Nano Letters pubs.acs.org/NanoLett Letter (see a simplified scheme in Figure 3c). 52 MoTe 2 in excess of three layers exhibits an indirect bandgap involving the K−Λ transition (with E g 0.90 eV). For the first CM step, while the absorption takes place at Γ point the CM involves the K−Λ transition. Note that the valence band maximum (VBM) at K and Γ points are similar in energy. This results in a favorable "asymmetric" absorption condition, so that most of the excess energy is transferred to hot electrons. In line with our discussion here, Siebbeles et al. have also shown that asymmetric transitions are involved in optical transitions and responsible for the onset of CM effects in PbS QDs and its bulk crystals. 3 Overall, the indirect bandgap nature and the relatively close position of VBM at the K and Γ points make energy conservation readily achieved. Note that this characteristic band structure shares similarities with a fictitious band structure proposed by Queisser and his colleagues for optimal CM. 45 Finally, to fully understand why CM occurs efficiently at Γ point insights into carrier cooling rate around Γ point are also essential and call for further studies.
(2) Weak electron−phonon coupling in MoTe 2 . As we discussed, a large rate ratio between II and hot carrier cooling processes k II /k cool is required for efficient CM. Hence, efficient II and slow cooling dynamics favor CM. For the latter process, the weak coupling between the photogenerated hot carriers to phonon modes is desirable. For MoTe 2 in both layered and bulk geometries, a few recent studies have reported an intrinsically weak carrier−phonon coupling. 53−55 For instance, Makino et al. reported remarkably long-lived optical phonon modes, particularly the A 1g mode (with ∼20 ps lifetime) in MoTe 2, even in the presence of a large number of photoexcited carriers. 55 This observation indicates very week coupling between photogenerated electrons and phonons; in conventional semiconductors (e.g., GaN, ZnO, and so forth), the electron−phonon coupling will lead to the coherent phonon dephasing on ultrafast, picosecond time scale. 56,57 The unusual optical phonon dynamics and weak electron−phonon coupling strength could favor the CM by lifting the time constraint for II.
Implication. To illustrate the relevance of CM effect in 2H-MoTe 2 for optoelectronics, we compare the CM effect in MoTe 2 to that in other extensively studied (e.g., PbS or PbSe systems) or technologically relevant materials (e.g., bulk Si or Si QDs), as shown in Figure 4a. While most of materials possess either only efficient CM (e.g., Si nanocrystals, 43 PbS nanosheets, 20 and PbSe superlattice solids 58 ) or high carrier mobility (e.g., bulk silicon 59 ), MoTe 2 uniquely combines both. This makes layered MoTe 2 a fascinating material platform for both fundamental study of CM effect and further device integration. In this context, we further estimate the maximum power conversion efficiency (PCE) for our sample using the detailed balance model as shown in Figure 4b. 60,61 In principle, the fast, sub-10 ps trapping process in MoTe 2 imposes a challenge for its application in optoelectronics. Effective passivation schemes for the defects have been previously developed for other TMDC materials and should be applicable for MoTe 2 . For the calculation, we assume that defects can be effectively passivated so that all photogenerated carriers can be efficiently collected. With a quantized band gap of 0.90 eV, the maximum PCE can be reached to 36.8%, increased from 29.5% without CM, with a substantial relative increase of ∼24.7%, illustrating the relevance of CM effect in MoTe 2 for optoelectronics.

■ CONCLUSIONS
In summary, we report that efficient photoconductivity or photocurrent multiplication occurs in few-layer 2H-MoTe 2 as a direct consequence of an efficient steplike carrier multiplication with near unity quantum yield and extremely high carrier mobility in MoTe 2 . We demonstrate that free carriers, rather than excitons, are involved in the CM process via impact ionization. The photocurrent multiplication, in conjunction with its ∼1 eV bandgap and easy device integration, thanks to the 2D geometry, makes MoTe 2 a promising candidate for hotcarrier related optoelectronics.
Estimating band gap energy E g using Tauc plots, the origin for the fast decay in carrier dynamics for few-layer MoTe 2 , photoconductivity dynamics of 2H-MoTe 2 with 3.1 eV photoexcitation energy, THz time-domain spectroscopy, fitting the frequency-resolved data by Drude Model, comparison of the normalized frequencyresolved THz conductivity for excitations of 1.55 and 3.1 eV, fitting the frequency-resolved data by Drude−Smith Model, the normalized, pump energy-dependent OPTP dynamics, discussion on CM onset energy difference between our studies and previous studies (PDF)