Graphene has attracted large interest in photonic applications owing to its promising optical properties, especially its ability to absorb light over a broad wavelength range, which has lead to several studies on pure monolayer graphene-based photodetectors. However, the maximum responsivity of these photodetectors is below 10 mA W−1, which significantly limits their potential for applications. Here we report high photoresponsivity (with high photoconductive gain) of 8.61 A W−1 in pure monolayer graphene photodetectors, about three orders of magnitude higher than those reported in the literature, by introducing electron trapping centres and by creating a bandgap in graphene through band structure engineering. In addition, broadband photoresponse with high photoresponsivity from the visible to the mid-infrared is experimentally demonstrated. To the best of our knowledge, this work demonstrates the broadest photoresponse with high photoresponsivity from pure monolayer graphene photodetectors, proving the potential of graphene as a promising material for efficient optoelectronic devices.
Graphene, a two dimensional allotrope of carbon atoms on a honeycomb lattice with unique band structure, has recently attracted significant interest in photonic applications for realizing, for example, transparent electrodes1, optical modulator2, polarizer3, surface plasmonic devices4,5 and photodetectors6,7,8,9. One of the most impressive advantages is its ability to absorb ~2.3% of incident light over a broad wavelength range despite its one-atom layer thickness10. This advantage makes the realization of broadband photodetectors possible, far exceeding the bandwidth of the current photodetectors. In addition, graphene also shows high mobility, which is promising for applications in ultrafast detection. Based on these properties, several works have been reported on the realization of graphene-based photodetectors in a field-effect transistor (FET) structure6,7,8,9. However, the highest photoresponsivity (photo-generated current per incident optical power) is <10 mAW−1. Although some strategies such as using surface plasmons11,12 or microcavity13 have been adopted to enhance the performance of the graphene photodetector, the photoresponsivity is still as low as several tens of mAW−1 and the fabrication processes are complex. In conventional FET-based graphene photodetectors, the low photoresponsivity is mainly attributed to the low optical absorption in monolayer graphene and the short recombination lifetime (on the scale of a picosecond) of the photo-generated carriers, leading to a low internal quantum efficiency of ~6–16% (6). Thus, to achieve high photoresponsivity, one should increase either the absorption efficiency of graphene11,12,13 or the lifetime of the photo-excited carriers, while still maintaining the high mobility by modifying the properties of graphene. In addition, although pure monolayer graphene photodetectors have been predicted as having ultra-wideband operation in theory10, all of the reported results based on pure monolayer graphene photodetectors are realized in the visible or the near-infrared ranges6,7,8,9,11,12,13,14,15 and not demonstrated in the longer wavelength range.
Band structure engineering of graphene has been widely investigated. A bandgap can be created in graphene for electronic applications, for example, by patterning graphene nanoribbon or nanomesh structures through electron-beam lithography16, nanowire shadow mask etching17, block copolymer lithography18 and/or unzipping of carbon nanotubes19,20. On the other hand, various defect states can also be created in graphene by defect engineering21 for manipulating electrical22,23, chemical23,24 and magnetic25,26 properties. Here we introduce defect midgap states band (MGB)27, as well as a bandgap in graphene through a Titanium (Ti) sacrificial layer fabrication method for achieving high photoresponse. Through this scheme, we have demonstrated a high photoresponsivity of 8.61 AW−1, which are about three orders of magnitude higher than those in previous reports from pure monolayer graphene photodetectors. The methodology presented here can provide a new avenue for the development of graphene-based broadband high performance photodetectors and other optoelectronic devices.
In addition to a high photoresponsivity, we have demonstrated the broadest photoresponse from the visible (532 nm) up to the mid-infrared (~10 μm) in a single pure graphene photodetector. We noted that graphene hybrid photodetector with an ultrahigh photoconductive gain has been recently demonstrated where semiconductor quantum dots were adopted as light absorbers and graphene was used as an ultrafast transport medium28. While, as the photoresponse of these devices are dependent on the properties of the quantum dots, the broadband advantage of the graphene is lost, for example, the hybrid graphene photodetector does not work in the important mid-infrared regime. Compared with the traditional mid-infrared photodetectors such as HgCdTe (HCT) and quantum well infrared photodetector, the proposed graphene photodetector possesses the advantages of a lower cost and a lower operation power, and it is compatible with the complementary metal-oxide-semiconductor technologies, while still maintaining a high photoresponse.
Concept of the proposed graphene photodetector
To increase the photoresponsivity of pure graphene photodetectors, apart from the prevailing methods of increasing the absorption efficiency of graphene11,12,13, one could also increase the lifetime of the photo-generated electrons. However, owing to the fast interband and intraband recombination rate of a few picoseconds of the photo-generated electrons29 (Fig. 1a), even though a carrier multiexcitation generation (MEG) process has been theoretically predicted30 in a perfect graphene with a multiplication factor of approximately four by the impact ionization process (also called the inverse Auger recombination (AR)), up to now no multiplication effect has been experimentally observed in pure graphene sheet (we noticed that the MEG effect in graphene was observed experimentally and reported almost simultaneously31 at the time of this publication, confirming the high efficiency of carrier-carrier scattering in graphene.).
The detailed physical picture on how a high photoconductive gain is achieved in this work is depicted as follows: we first process the graphene sheet into a graphene quantum dot-like (GQD)-arrays structure; then defect MGB electron trapping centres are formed on the boundary and surface of the GQDs and a bandgap is created due to the quantum confinement. The corresponding energy band diagram is shown in Fig. 1b. The sequence of the carrier MEG and trapping in the MGB is depicted in Fig. 1c–e. As shown in Fig. 1c, the impact ionization (II) process exists in the GQDs: one photo-excited electron relaxes to a lower-energy state within the conduction band, exciting a valence band electron into the conduction band. Meanwhile, electrons of the conduction band will be involved in the AR process (Fig. 1d): an electron is scattered from the conduction band into the valence band, while simultaneously the released energy is transferred to another electron, which is excited to a higher-energy state in the conduction band. Despite the competing processes between II and AR, II can be more efficient than the AR process in quantum-confined systems32 because of the asymmetry between the II and AR33. Therefore, carrier multiplication (the MEG effect) occurs, which generates more secondary electrons in the conduction band, see Fig. 1c, thus enhancing the electron generation efficiency. As a bandgap is formed, the electron–phonon scattering rate from the conduction band to valence band decreases34 so that more photo-generated, as well as the secondary-generated electrons can be trapped in the MGB (Fig. 1e). It is noted that holes can also contribute to the carrier MEG process assisted by an external electrical field, as illustrated in the latter part of the paper. When the photo-generated and the secondary-generated electrons are trapped in the MGB, the related holes can be recirculated many times through hopping within the lifetime of the MGB trapped electrons (Fig. 1f); thus a photoconductive gain is achieved. Owing to the relatively long electron trapping time in the MGB together with the high efficiency of the carrier MEG effect in graphene, we expect a high photoresponse can be achieved in GQD array photodetectors.
Device fabrication and characterization
We fabricated pure graphene photodetectors in a FET structure through a Ti etching fabrication method, which is shown schematically in Fig. 2a–d and discussed in more details in Methods. Three devices were fabricated and compared: Sample A is based on a pristine graphene structure (without the Ti layer fabrication); Sample B is a GQD arrays structure fabricated with a ~2-nm thick Ti layer; and Sample C is a GQD arrays structure fabricated with a ~20-nm thick Ti layer. Raman spectra measurements were used to characterize the density of defects of these samples35 (see Methods). As shown in Fig. 3a, a higher number of defects were observed in Sample C than in Sample B due to the higher Raman ID/IG ratio36,37 (ID and IG are the D-band and G-band Raman intensities, respectively). For Sample C, the average crystallite size of the GQDs La is estimated to be ~7.5 nm from38 La(nm)=(2.4 × 10−10)λ(nm)4(ID/IG)−1, where λ=532 nm is the wavelength of the Raman signal. Similarly, Sample B has an average GQD size of ~20.5 nm. The electrical characteristics of the Samples A and C are shown in Fig. 3b, respectively. For Sample A, the transfer curve shows an ambipolar transfer property with the Dirac point at ~60 V, while it is at ~80 V for Sample C.
Carrier transport in the processed graphene device
To investigate the carrier transport properties of the processed graphene device, i.e. the GQD arrays device (refer to Sample C in the latter part of the paper, if not specified), we measured the electrical properties of the device at different temperatures (Fig. 4a–c). The observations indicate the carrier transport in the graphene FET photodetector is influenced by the Coulomb blockade of charges39 (see Methods). Figure. 4b shows the current (I) versus temperature (T) characteristics in the temperature range 8–290 K, that is, the temperature dependence of the conductivity. The best fit of the temperature-dependent data is obtained with the T−1/3 curve fitting (inset, Fig. 4b), but not with the T−1 or T−1/2 fitting (see Supplementary Fig. S1 and Supplementary Note 1). These results show that variable range hopping (VRH), frequently observed in disordered systems including carbon-related materials40, is the main carrier transport mechanism (see Methods), which involves consecutive hopping process between two localized states. It is thus confirmed that the processed device is formed by GQD arrays with polydispersed GQDs.
To further study the Coulomb blockade effect in the processed graphene device, the temperature-dependent transfer curves are also measured (Fig. 4c). Obvious oscillations appear in the transfer curves at low temperatures and these oscillation peaks are gradually broadened with the temperature and disappear when the temperature is higher than 150 K. These observations are clear evidence of the Coulomb blockade effect41,42. To calculate the charge energy of the GQDs, we measured differential conductance (dI/dV) as functions of VG and VD, as shown in Fig. 4d. By calculating the height of the diamond-shape regions16,39, we obtain an energy gap of about 75 meV, consistent with the estimated value of ~88 meV calculated from , where νF ≈ 106 ms−1 is the Fermi velocity in graphene, and W is the average size of the GQDs (~7.5 nm).
Broadband photoresponse measurement
We measured the photoresponse characteristics of the processed graphene device at 20-mV source-drain bias and zero gate voltage, with illuminations on the whole device at various wavelengths, and at low temperatures (see Fig. 5). Light sources at the visible (532 nm), the near-infrared (1.47 μm) and the mid-infrared (9.9 μm, 10.1 μm and 10.31 μm) were used in the photoresponse measurements. For comparison, the photoresponse of the pristine graphene device was also measured (see Supplementary Fig. S2 and Supplementary Note 2) and no obvious response was observed at a low optical input power density ~633 mWcm−2, which agrees with the previous results (only a low responsivity of about 10 mAW−1 was reported under a high optical pumping of 108 mW cm−2). The photoresponse of the processed graphene device is shown in Fig. 5a–f, respectively, for the visible, the near-infrared and the mid-infrared illuminations. The processed graphene device shows high photoresponse in the whole tested wavelength range (high photoresponsivity of 1.25 AW−1, 0.2 AW−1 and 0.4 AW−1 in the visible, near-infrared and mid-infrared ranges, respectively). These values are about two-three orders higher than those reported in the literature based on pure monolayer graphene photodetectors. More importantly, to the best of our knowledge, this is the broadest range reported for a single graphene-based photodetector device.
The proposed graphene photodetector also possesses high sensitivity capable of nW-level optical power detection, demonstrated in Fig. 5b. The power dependence of the photodetector is also shown at different wavelength illuminations (Fig. 5b). The photoresponse can be expressed by a power law Ipc ∝ Pγ, where Ipc is the photocurrent and P is the power of the illumination. For the visible, near-infrared and mid-infrared illuminations, γ is 1.07, 0.83 and 0.95, respectively. The non-unity exponentials are the result of complex processes of electron-hole generation, trapping and recombination43, implying complex MGB electron trapping and carrier transport in the processed graphene photodetector.
Dependence on temperature and voltage and GQDs size
The bias dependence of the photoresponse of Sample C is shown in Fig. 6a. As the bias increases from zero to 0.1 V, the photoresponsivity increases up to 8.61 A W−1 correspondingly. The temperature-dependent characteristics of Sample C are shown in Fig. 6b. The results show a strong dependence of the temperature on the photoresponse of the detector. The decrease of the photoresponse with the temperature could be understood as: with the increase of temperature a faster recombination of captured electrons in the MGB states occurs, thus the photoresponse is reduced.
The gate-bias dependence of photoresponse of Sample C is shown in Fig. 7a. As the gate-bias decreases from +20 V to −20 V, the photocurrent increases and the device becomes a more p-type material seen from the transport characteristics in Fig. 3c. This is in contrary to the normal understanding that the electron-hole pair generation by direct photoexcitation would be decreased as the quasi-Fermi level moves below the valence band edge (fewer valence band states are filled with electrons). The observed gate-bias dependence of the photocurrent, we believe, is attributed to the effective electron-hole pair generations by the hole impact ionization assisted by the external electrical field, which was also observed in the carbon nanotube system44. As shown in Fig. 7b, the rest mass energy of one photo-excited hole in a higher-energy level is combined with the kinetic energy to create a lower-energy hole plus several electron-hole pairs, expressed as:
where Kh is the kinetic energy of holes induced by the external electric field, hk and hj indicate the higher-energy and lower-energy level holes, respectively, (e+h) refer to electron-hole pairs, and n is an integer. As the gate-bias decreases (the quasi-Fermi level decreases), more holes are involved in the impact ionization process inducing more electron-hole pairs. Thus, there is a competing effect between the hole impact ionization and the direct photoexcitation for electron-hole pair generation. The former is more efficient than the latter when the material is converted to be more p-type.
Figure 7c shows the photoconductive gain spectra of the Samples B and C with different average GQD sizes. For both devices, the photoconductive gain increases with the photon energy, arising from the increase of the carrier MEG efficiency. As the photo-excited electron occupies a higher-energy level in the conduction band under a shorter wavelength illumination (532 nm), it undergoes more exciton excitations through the impact ionization process when scattered into the lower-energy levels in the conduction band. This leads to an increase of the conduction-band electrons thus the captured electrons in the MGB as well, resulting in a higher photoconductive gain. In addition, Fig. 7c shows that the Sample B with a larger average GQD size (~20.5 nm) has a smaller photocurrent gain than the Sample C with a smaller average GQD size (~7.5 nm). As the size of the GQDs increases, the defect density decreases as evidenced in the Raman measurement results (Fig. 3a), resulting in a fewer number of photo-excited electrons captured by the MGB states.
Theoretically, we can quite accurately calculate the photoconductive gain as a function of bias by the microscopic density matrix method30, but the microscopic analysis requires intensive derivations and accurate prediction of certain parameters, which are beyond the scope of this paper. Here we provide a simple macroscopic estimation on the photoconductive gain based on the population dynamic analysis. In our calculation, the source-drain bias and gate voltage are set as 20 mV and 0 mV, respectively. Here we assume the electron populations in the conduction band and the MGB are n1 and n2, respectively. The recombination rate of electrons is R~1 ps (45), the measured current is I, the capture rate of the MGB is α, the lifetime of the trapped electrons is τ1, the transition time is τt, and the photogeneration rate is β. We assume the number of electrons per absorbed photon due to both electron and hole impact ionizations is χ. As the electron multiplication factor in perfect graphene sheet is estimated to be around four30, we reasonably assume that this factor in our device is not high neither. The hole impact ionization is not expected to be strong, as a zero gate voltage is applied resulting in a low hole density and a low drain-source voltage is applied. In this case, we assume the factor χ induced by both electron and hole impact ionizations is a small value <10. Under illumination, the variation of the number of the electrons in the conduction band originates from photogeneration, carrier multiplication (carrier impact ionization), recombination and relaxation to the MGB. The variation of the electrons on the MGB states results from excitation to the conduction band, relaxation from the conduction band, and recombination with holes in the valance band. Thus, we have
From equations (2)–(4), the capture rate can be expressed as
and the quantum efficiency η of the photo-excited and secondary-generated electrons captured by MGB is expressed as
From equations (5) and (6), we obtain α is about 106 and η is about 10−6 by applying appropriate values, where τ1 is about 30 s obtained from Supplementary Fig. S3 and Supplementary Note 3 and τt is about 250 ns achieved from Supplementary Fig. S4. We can then calculate the photoconductive gain of the fabricated graphene photodetector by using43 , which leads to a photoconductive gain of about 120.
We could also calculate the photoconductive gain by G=Nelectrons/Nphotons where Nelectrons and Nphotons are the number of generated electrons that measured in the FET and the number of incident photons, respectively. We take the measured photocurrent of 6.961 nA and the visible irradiation of 5.57 nW on Sample C for calculation. A photoconductive gain of ~127 is obtained at a 20-mV source-drain bias and a zero gate voltage, in good agreement with that obtained from the above population dynamic analysis.
We attribute the high and broadband photoresponse of our devices to the electron trapping in the defect MGB enhanced by the carrier impact ionization. We now discuss additional sets of reasons that address potential explanations of these findings. One is based on the ‘built-in-field’ scenario6,7,14,46. In this scenario, the slope of the I–V curve should keep a constant with and without illuminations, and the device should have a certain output photocurrent even when no bias is applied owing to the presence of the ‘built-in-field’ which separates the generated electron-hole pairs. In addition, the photoresponsivity should be at the level of several mAW−1. These are in contrast to our observations. Another possible reason proposed in the literature is relied on the photo-thermoelectric effect8,9,47. This effect only occurs in asymmetric situations, either with asymmetric materials such as graphene p–n junctions or with asymmetric illuminations. In our case, the channel material is built by just a single layer graphene sheet (no junction exists) and the illumination is uniform. Therefore, none of the above explanations proposed in the literature can explain the observed high photoresponsivity.
Our device covers a broad wavelength range, including the mid-infrared. The mid-infrared detector has wide applications ranging from medicine48, remote sensing49, environment monitoring50, to telecommunications51. The traditional mid-infrared HgCdTe and quantum well infrared photodetector photodetectors require complicated fabrication and growth of single-crystalline alloys using expensive molecular beam epitaxy or metalorganic chemical vapour deposition, thus the fabrication process is complex and has a high cost. The proposed graphene photodetector has a much lower cost and a lower operation voltage, and is compatible with the complementary metal-oxide-semiconductor technology.
Despite the reported high photoresponsivity of our graphene photodetector over a broadband range, it needs to be mentioned that one drawback of the current device is that the operation speed is not high, which is mainly limited by the relatively long trapped electron lifetime in the defect states, caused by the present chemical fabrication/etching method introducing extremely complex deep surface and edge defects. The lifetime of the trapped electrons in the MGB is influenced by many factors, for example, defect types, trap-state density and defect trap depths. It has been demonstrated that by varying the types and the densities of defects one can significantly reduce the electron trap lifetime in various material systems52,53,54,55 from tens of seconds down to a few milliseconds or even shorter. Thus we reasonably believe that the trapped electron lifetime in graphene can also be decreased by engineering the defect types and defect densities, for example, by achieving mechanically fabricated quantum dot edge defects with electron-beam lithography16 or well-defined extended defects22 using nickel supporting layer, or atomic-level nanoribbons with edge defects by a surface-assisted coupling method32. Certainly, by decreasing the lifetime of the trapped electrons, the photoresponsivity of the photodetector is sacrificed. This, however, can be compensated by increasing the low carrier mobility (caused by the VRH effect and the high defect scattering) in our highly disordered GQD array devices. This can be achieved by using more accurate fabrication techniques, for example, electron-beam lithography, helium ion lithography56, scanning tunnelling microscope lithography57 and focused ions beam58 to reduce the disorders and defect density, and by exploring other nanostructures such as nanoribbons and nanomeshs (without relying on the VRH effect), which are now under investigations. Therefore, we could conduct further band structure engineering of graphene to improve the operation speed as well as the temperature performance while still maintaining a high photoresponsivity of the proposed photodetector.
In summary, we have demonstrated a new type of broadband pure monolayer graphene-based photodetector through band structure engineering. The demonstrated pure graphene photodetector shows a high photoresponsivity, which are about two–three orders of magnitude higher than those in the former reports. Compared with other band structure engineering approaches, the proposed fabrication method is simpler and a larger scale of device can be easily fabricated. Further device performance improvement can also be achieved through defect engineering and nanostructure engineering. The proposed scheme opens up exciting opportunities for band structure engineering of graphene for future graphene-based optoelectronic applications.
We fabricated pure graphene photodetectors in a FET structure (inset, Fig. 3a) for characterizations. First, a monolayer graphene was fabricated by using the micromechanical exfoliation technique on a 285-nm SiO2/Si substrate where the Si substrate is highly doped. Two electrode terminals (Ti/Au: 20 nm/80 nm), that is, the source and the drain terminals, were then formed by standard photolithography and lift-off techniques on top of the graphene. To clean the photoresist, Ar/H2 annealing was applied at 400 degree for 2 h. Then, the gate terminal was fabricated on the bottom of the Si substrate. After that, a thin Ti sacrificial layer with different thicknesses was deposited by e-beam evaporation. Finally, the GQD array structures were formed by removing the Ti sacrificial layer using hydrofluoride, hydrodioxide (H2O2) and deionized water with a volume ratio of 1:1:200 (the etching rate was around 20 nm min−1). The thicker the deposited Ti layer, the smaller the average size of the GQDs after etching. Thus the Ti sacrificial layer with various thicknesses can be deposited to control the average size of the GQDs.
Raman spectra measurements were used to characterize the density of defects of the fabricated devices (Fig. 3a). The Raman spectra were excited at 532 nm with an incident power <1 mW (laser spot diameter of 500 nm). For the pristine graphene sample (Sample A), the G-band and the 2D band are at 1,578 cm−1 and 2,666 cm−1, respectively. For the processed graphene samples B and C, three defect-related Raman peaks are excited, namely D, D′ and D+D′ located around 1,338 cm−1, 1,620 cm−1 and 2,934 cm−1, respectively. The D and D′ peaks originate from double-resonance processes at the K point in the presence of defects, involving, respectively, intervalley (D) and intravally (D′) phonons37. A higher number of defects were observed in Sample C than in Sample B due to the higher Raman ID/IG ratio. As shown in Fig. 3b, after defects are introduced, the on-state electric conductance decreases to 0.14G0.
Carrier transport in the device
We measured the electrical properties of the devices at different temperatures (Fig. 4a–c). It is observed that the I–V characteristics of the processed graphene is linear at 294 K for VD changes from −1 V to 1 V, while it become remarkably nonlinear and highly symmetric, and the conductance reduces at low biases, at 12 K. These phenomena indicate the Coulomb blockade effect exists as carriers transport in the processed graphene sample. It is noted that the Schottky barrier formed between the contact and the graphene layer could also generate a decreased conductance at a lower bias, but this effect is excluded because it would also introduce a nonlinear effect at room temperature and an asymmetric behaviour at low temperatures41, which are not observed in our measurements. This means the observed phenomena comes from the graphene FET channel.
The photoresponsivity measurement was performed in a digital deep level transient spectroscopy (BIORAD) system with a compressor (CTI-CRYOGENICS, 8200). Three light sources (visible: 532 nm semiconductor laser; near-infrared: 1470 nm fibre laser; mid-infrared: tunable quantum cascade laser from 9.75 to 10.48 μm) were used to illuminate the whole device. The electrical characteristics were collected by a semiconductor device analyser (Agilent, B1500A).
How to cite this article: Zhang, Y. et al. Broadband high photoresponse from pure monolayer graphene photodetector. Nat. Commun. 4:1811 doi: 10.1038/ncomms2830 (2013).
Bae, S. et al. Roll-to-roll production of 30-inch graphene films for transparent electrodes. Nat. Nano. 5, 574–578 (2010).
Liu, M. et al. A graphene-based broadband optical modulator. Nature 474, 64–67 (2011).
Bao, Q. et al. Broadband graphene polarizer. Nat. Photon. 5, 411–415 (2011).
Fei, Z. et al. Gate-tuning of graphene plasmons revealed by infrared nano-imaging. Nature 487, 82–85 (2012).
Chen, J. et al. Optical nano-imaging of gate-tunable graphene plasmons. Nature 487, 77–81 (2012).
Xia, F., Mueller, T., Lin, Y.-m., Valdes-Garcia, A. & Avouris, P. Ultrafast graphene photodetector. Nat. Nano. 4, 839–843 (2009).
Mueller, T., Xia, F. & Avouris, P. Graphene photodetectors for high-speed optical communications. Nat. Photon. 4, 297–301 (2010).
Gabor, N. M. et al. Hot carrier–assisted intrinsic photoresponse in graphene. Science 334, 648–652 (2011).
Lemme, M. C. et al. Gate-activated photoresponse in a graphene p–n junction. Nano. Lett. 11, 4134–4137 (2011).
Nair, R. R. et al. Fine structure constant defines visual transparency of graphene. Science 320, 1308 (2008).
Echtermeyer, T. J. et al. Strong plasmonic enhancement of photovoltage in graphene. Nat. Commun. 2, 458 (2011).
Liu, Y. et al. Plasmon resonance enhanced multicolour photodetection by graphene. Nat. Commun. 2, 579 (2011).
Furchi, M. et al. Microcavity-integrated graphene photodetector. Nano. Lett. 12, 2773–2777 (2012).
Xia, F. et al. Photocurrent imaging and efficient photon detection in a graphene transistor. Nano. Lett. 9, 1039–1044 (2009).
Shi, S. F., Xu, X., Ralph, D. C. & McEuen, P. L. Plasmon resonance in individual nanogap electrodes studied using graphene nanoconstrictions as photodetectors. Nano. Lett. 11, 1814–1818 (2011).
Han, M. Y., Özyilmaz, B., Zhang, Y. & Kim, P. Energy band-gap engineering of graphene nanoribbons. Phys. Rev. Lett. 98, 206805 (2007).
Bai, J., Duan, X. & Huang, Y. Rational fabrication of graphene nanoribbons using a nanowire etch mask. Nano. Lett. 9, 2083–2087 (2009).
Bai, J., Zhong, X., Jiang, S., Huang, Y. & Duan, X. Graphene nanomesh. Nat. Nano 5, 190–194 (2010).
Kosynkin, D. V. et al. Longitudinal unzipping of carbon nanotubes to form graphene nanoribbons. Nature 458, 872–876 (2009).
Jiao, L., Zhang, L., Wang, X., Diankov, G. & Dai, H. Narrow graphene nanoribbons from carbon nanotubes. Nature 458, 877–880 (2009).
Terrones, H., Lv, R., Terrones, M. & Dresselhaus, M. S. The role of defects and doping in 2D graphene sheets and 1D nanoribbons. Rep. Prog. Phys. 75, 062501 (2012).
Lahiri, J., Lin, Y., Bozkurt, P., Oleynik, I. I. & Batzil, M. An extended defect in graphene as a metallic wire. Nat. Nano. 5, 326–329 (2010).
Cai, J. et al. Atomically precise bottom-up fabrication of graphene nanoribbons. Nature 466, 470–473 (2010).
Boukhvalov, D. W. & Katsnelson, M. I. Chemical functionalization of graphene with defects. Nano. Lett. 8, 4373–4379 (2008).
Yazyev, O. Magnetism in disordered graphene and irradiated graphite. Phys. Rev. Lett. 101, 037203 (2008).
Palacios, J. J., Fernandez-Rossier, J. & Brey, L. Vacancy-induced magnetism in graphene and graphene ribbons. Phys. Rev. B 77, 195428 (2008).
Chen, J.-H., Cullen, W. G., Jang, C., Fuhrer, M. S. & Williams, E. D. Defect scattering in graphene. Phys. Rev. Lett. 102, 236805 (2009).
Konstantatos, G. et al. Hybrid graphene-quantum dot phototransistors with ultrahigh gain. Nat. Nano. 7, 363–368 (2012).
Breusing, M., Ropers, C. & Elsaesser, T. Ultrafast carrier dynamics in graphite. Phys. Rev. Lett. 102, 086809 (2009).
Winzer, T., Knorr, A. & Malic, E. Carrier multiplication in graphene. Nano. Lett. 10, 4839–4843 (2010).
Tielrooij, K. J. et al. Photoexcitation cascade and multiple hot-carrier generation in graphene. Nat. Phys. 9, 248–252 (2013).
Sukhovatkin, V., Hinds, S., Brzozowski, L. & Sargent, E. H. Colloidal quantum-dot photodetectors exploiting multiexciton generation. Science 324, 1542–1544 (2009).
Schaller, R. D. & Klimov, V. I. High efficiency carrier multiplication in PbSe nanocrystals implications for solar energy conversion. Phys. Rev. Lett. 92, 186601 (2004).
Ellingson, R. J. et al. Highly efficient multiple exciton generation in colloidal PbSe and PbS quantum dots. Nano. Lett 5, 865–871 (2005).
Jiao, L. Y., Zhang, L., Wang, X. R., Diankov, G. & Dai, H. J. Narrow graphene nanoribbons from carbon nanotubes. Nature 458, 877–880 (2009).
Ni, Z., Wang, Y., Yu, T. & Shen, Z. Raman spectroscopy and imaging of graphene. Nano. Res. 1, 273–291 (2008).
Martins Ferreira, E. H. et al. Evolution of the Raman spectra from single-, few-, and many-layer graphene with increasing disorder. Phys. Rev. B 82, 125429 (2010).
Ni, Z. H. et al. On resonant scatterers as a factor limiting carrier mobility in graphene. Nano. Lett. 10, 3868–3872 (2010).
Sols, F., Guinea, F. & Neto, A. H. C. Coulomb blockade in graphene nanoribbons. Phys. Rev. Lett. 99, 166803 (2007).
Gómez-Navarro, C. et al. Electronic transport properties of individual chemically reduced graphene oxide sheets. Nano. Lett. 7, 3499–3503 (2007).
Joung, D., Zhai, L. & Khondaker, S. I. Coulomb blockade and hopping conduction in graphene quantum dots array. Phys.Rev. B 83, 115323 (2011).
Romero, H. E. & Drndic, M. Coulomb blockade and hopping conduction in PbSe quantum dots. Phys. Rev. Lett. 95, 156801 (2005).
Rose, A. Concepts In Photoconductivity and Allied Problems Krieger (1978).
Gabor, N. M., Zhong, Z., Bosnick, K., Park, J. & McEuen, P. L. Extremely efficient multiple electron-hole pair generation in carbon nanotube photodiodes. Science 325, 1367–1371 (2009).
George, P. A. et al. Ultrafast optical-pump terahertz-probe spectroscopy of the carrier relaxation and recombination dynamics in epitaxial graphene. Nano. Lett. 8, 4248–4251 (2008).
Lee, E. J. H., Balasubramanian, K., Weitz, R. T., Burghard, M. & Kern, K. Contact and edge effects in graphene devices. Nat. Nano. 3, 486–490 (2008).
Xu, X., Gabor, N. M., Alden, J. S., van der Zande, A. M. & McEuen, P. L. Photo-thermoelectric effect at a graphene interface junction. Nano. Lett. 10, 562–566 (2009).
Jackson, M., Sowa, M. G. & Mantsch, H. H. Infrared spectroscopy: a new frontier in medicine. Biophys. Chem. 68, 109–125 (1997).
Datskos, P. G. et al. Remote infrared radiation detection using piezoresistive microcantilevers. Appl. Phys. Lett. 69, 2986–2988 (1996).
Werle, P. et al. Near- and mid-infrared laser-optical sensors for gas analysis. Opt. Lasers Eng. 37, 101–114 (2002).
Karstad, K. et al. Detection of mid-IR radiation by sum frequency generation for free space optical communication. Opt. Lasers Eng. 43, 537–544 (2005).
Soci, C. et al. ZnO nanowire UV photodetectors with high internal gain. Nano. Lett. 7, 1003–1009 (2007).
Yadav, H. K. & Gupta, V. A comparative study of ultraviolet photoconductivity relaxation in zinc oxide (ZnO) thin films deposited by different techniques. J. Appl. Phys. 111, 102809 (2012).
Afsal, M., Wang, C.-Y., Chu, L.-W., Ouyang, H. & Chen, L.-J. Highly sensitive metal–insulator–semiconductor UV photodetectors based on ZnO/SiO2 core–shell nanowires. J. Mater. Chem. 22, 8420 (2012).
Guo, F. W. et al. A nanocomposite ultraviolet photodetector based on interfacial trap-controlled charge injection. Nat. Nano. 7, 789 (2012).
Bell, D. C., Lemme, M. C., Stern, L. A., Rwilliams, J. & Marcus, C. M. Precision cutting and patterning of graphene with helium ions. Nanotechnology 20, 455301 (2009).
Dayen, J. F. et al. Side-gated transport in focused-ion-beam-fabricated multilayered graphene nanoribbons. Small 4, 716–720 (2008).
Krasheninnikov, A. V. & Banhart, F. Engineering of nanostructured carbon materials with electron or ion beams. Nat. Mater. 6, 723–733 (2007).
Y.Z.Z would like to thank Dr Hong Li for discussions. This work is supported by the grant (M58040017) from Nanyang Technological University (NTU), and partially by the Ministry of Education, Singapore (MOE2011-T2-2-147 and MOE2011-T3-1-005).
The authors declare no competing financial interests.
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Zhang, B., Liu, T., Meng, B. et al. Broadband high photoresponse from pure monolayer graphene photodetector. Nat Commun 4, 1811 (2013). https://doi.org/10.1038/ncomms2830
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