Infrared-light-induced carrier transfer is a key technology for ‘invisible’ optical devices for information communication systems and energy devices. However, clear and colourless photo-induced carrier transfer has not yet been demonstrated in the field of photochemistry, to the best of our knowledge. Here, we resolve this problem by employing short-wavelength-infrared (1400–4000 nm) localized surface plasmon resonance-induced electron injection from indium tin oxide nanocrystals to transparent metal oxides. The time-resolved infrared measurements visualize the dynamics of the carrier in this invisible system. Selective excitation of localized surface plasmon resonances causes hot electron injection with high efficiency (33%) and long-lived charge separation (~ 2–200 μs). We anticipate our study not only provides a breakthrough for plasmonic carrier transfer systems but may also stimulate the invention of state-of-the-art invisible optical devices.
‘Invisibility’ has emerged as an important feature of photo-responsive materials, with their increasing demand in energy devices1,2. The control of light-absorption-induced carrier transfer is the bedrock of this subject. For the fabrication of invisible materials, an effective strategy is selective absorption of the ultraviolet (UV) or infrared (IR) region of light. As UV light is unfavourable for light to energy-conversion systems, IR-light absorbers are the key to responding to this challenge. However, simultaneous pursuit of clear and colourless IR-induced carrier transfer has been an important goal of photochemistry research.
The development of an IR-responsive pigment remains a great challenge. In terms of artificial materials, IR-responsive narrow band-gap semiconductors (e.g. InSb, HgCdTe, etc.) are opaque and exhibit dark colours derived from inter- and intra-band transitions.
Plasmonic materials, which are artificial pigments, exhibit optical properties overwhelmingly superior to those of natural pigments in the IR region3,4,5,6,7,8. The localized surface plasmon resonance (LSPR) band derived from the collective oscillation of carriers in transparent conductive-oxide nanocrystals (NCs) makes it possible to achieve selective absorption of short-wavelength infrared (SWIR) (1400–4000 nm) light, which is an important wavelength band in sensors7,8,9.
Here we demonstrate SWIR-induced electron transfer from transparent indium tin oxide (ITO) NCs to metal oxides (SnO2 and TiO2). Time-resolved-IR spectroscopy of the ITO/SnO2 heterointerface reveals high electron-injection efficiency (33%) and long-lived charge separation (~2–200 μs). Furthermore, we demonstrate the potential expansion of applicable IR light beyond 4 μm by using the tunability of LSPR of ITO NCs. We anticipate our result could constitute a step forward, not only in the science of plasmonic-carrier transfer, but also for state-of-the-art invisible optical devices in general.
Fabrication and characterization of heterointerfaces
For carrier injection using LSPR in the SWIR-region, the fabrication of heterointerfaces with rational-band alignment is essential. As electron-acceptor phases to form heterointerfaces with ITO NCs, we selected two types of metal-oxide semiconductors, TiO2 (anatase or P25, a mixture of anatase and rutile) and SnO2, because these metal oxides can be “clear and colourless” and are commonly used as electron-transport layers and/or photocatalysts and possess suitable acceptor levels (i.e., position of the conduction band (CB)) for hot-electron injection from ITO NCs. Energy diagrams of the ITO NCs and metal oxides are shown in Fig. 1a. The energy difference (ΔE) between the Fermi level (EF) of the ITO and the CBs of SnO2 and TiO2 are 0.2 and 0.7 eV, respectively, which are accessible for hot electrons generated in ITO NCs10,11,12. The combination of ITO and SiO2 was also adopted as a monitoring reference for the LSPR-stimulated response of ITO NCs, because no electron transfer from the ITO NC to the insulating SiO2 phase is expected. The ITO NCs were synthesised according to previous reports13 and immobilised on metal oxides via thermal-annealing and a reductive-annealing process (see Methods). Figure 1b, c shows the UV–Vis–IR spectra of ITO NCs and three types of ITO/metal oxides. All samples have LSPR peaks in the IR region. TEM and XRD measurements revealed no changes in the size or crystalline structure of ITO NCs during the annealing process (Supplementary Figs. 1–5). The broadening of LSPR band of ITO NCs on SnO2 results from the plasmonic coupling of ITO NCs (see Supplementary Fig. 5).
Carrier dynamics at the heterointerfaces
To elucidate the LSPR-induced carrier dynamics of ITO/metal oxides, we performed femtosecond (fs)- and microsecond (μs)-laser flash photolysis to obtain time-resolved infrared-absorption (TR-IR). TR-IR spectroscopy allows us to directly observe the LSPR-induced carrier dynamics at the ITO/metal-oxide heterointerfaces. The observation of free-carrier absorption (FCA) by metal oxides is the direct evidence of electron injection from the ITO NCs into the CBs of metal oxides.
The kinetic profiles of ITO/metal-oxide interfaces on a picosecond (ps) scale were measured to investigate light-stimulated electron injection from ITO to the metal oxide (Fig. 2a and Supplementary Fig. 7). Upon excitation of ITO and ITO/SiO2, transient absorptions (ΔOD) appear within the time resolution of 285 ± 40 fs and decay with the time constant of 0.17 ± 0.08 ps and 0.37 ± 0.11 ps, respectively (Supplementary Tables 1 and 2). The sequence of events in plasmonic materials following pump excitation includes electron dephasing, electron–electron scattering, electron-phonon coupling and lattice-heat dissipation, all of which take place at different timescales14. The observed instantaneous appearance within time resolution and decay of transient-absorption signal upon the excitation of ITO and ITO/SiO2 are ascribed to electron dephasing and carrier scattering including electron–electron and electron-phonon scattering, respectively14.
On the other hand, the ITO/SnO2 and ITO/TiO2 heterointerfaces also showed the instantaneous appearance of signal within the time resolution, decaying dominantly with the time constant of 0.21 ± 0.1 ps and 0.14 ± 0.09 ps, respectively (Supplementary Tables 1 and 2). Subsequently, the signal becomes almost constant, which can be regarded as the component with lifetime much longer than time window of instrument (>3 ns). This instantaneous appearance within the time resolution and fast decay of signal is assignable to the above-mentioned LSPR-induced ultrafast events, and the long-lived component is assignable to FCA of SnO2 and TiO2, respectively15,16,17. To confirm FCA formation, we measured the IR spectra of the ITO/SnO2 interface at 10 ps after excitation by the 1700-nm laser (Fig. 2b). The observed broad-absorption band from the near-IR to mid-IR region agrees well with the FCA of SnO215. This result strongly indicates that the hot electrons generated in ITO NCs were injected into the conduction band of SnO2. As expected, no FCA was observed for SnO2 without ITO NCs and ITO NCs alone, and an ITO/SiO2 interface (Fig. 2a, Supplementary Fig. 7 and 8). For further confirmation of LSPR-induced carrier generation, we performed an excitation-spectrum measurement to probe the FCA. The excitation spectrum at 5000 nm and at 10 ps after the laser pulse reproduced the LSPR band of the ITO NCs, clearly proving LSPR-induced electron injection from ITO to SnO2 (Fig. 2c). The possibility of non-linear optical phenomena caused by the enhanced electromagnetic field around the ITO NCs18, was ruled out by the laser-power dependence of the FCA intensity at 5000 nm (see Supplementary Fig. 9). These facts clearly demonstrate that LSPR-induced electron injection proceeds from the ITO NCs to SnO2.
Notably, as shown in Fig. 2c, the FCA was observed even under excitation of NIR-to-SWIR lasers (1000–2500 nm). The quantum yield (Φ) of LSPR-induced charge injection at an ITO/SnO2 heterointerface was calculated by equation (1),
where ne (cm−3) is the free-carrier number per unit volume injected into SnO2 and Nphoton (cm−3) is the absorbed-photon number of the pump light per unit volume in ITO/SnO2. The electron-injection efficiency of the ITO/SnO2 interface by excitation with a 1700-nm laser pulse was determined to be 33% from equation (1) (see Methods for details)15. Furthermore, we demonstrated that the responsive IR light of the ITO/SnO2 system is extendable over 4000 nm. Since the peak position of LSPR of heavily-doped semiconductors is sensitive to the carrier density, the LSPR absorption of ITO can be easily tuned by changing the doping ratio of Sn13. As shown in Fig. 3, ITO NCs doped with 1% Sn, which exhibited LSPR absorption at around 2000–5000 nm, also showed LSPR-induced electron injection. This fact clearly indicates that IR light in the mid-wavelength infrared region (3000–8000 nm), which is the important region for the thermal sensors or free-space optical communications19, can be applicable to the present system.
The FCA of ITO/SnO2 monotonically decayed with a triple exponential function and the time constants are measured to be 2.0 ± 0.1, 33 ± 1 and 160 ± 1 μs (Fig. 2d and Supplementary Table 3). From the change of decay profiles depending on the size of SnO2, we concluded that multiple decay profiles of FCA reflect the multiple decay channels of FCA, including the charge recombination and carrier trapping (see Supplementary Figs.11 and 13 for detail). The decay of FCA represents the lifetime of charge separation, which is an important parameter in determining the light-energy-conversion efficiency or quantum yield of optical detector. The long-lived charge separation is favourable for efficient energy conversion. For plasmonic carrier injection systems, fast charge recombination is a major obstacle facing efficient light-energy conversion5,20. The long-lived charge separation in our ITO/SnO2 system, which reaches ~2–160 μs, indicates that combining plasmonic ITO with SnO2 is a promising technique for IR-light sensors and energy-conversion systems. The photocurrent measurement of the ITO NCs/SnO2/W photoelectrode further proves that IR-light-induced carrier injection from ITO to SnO2 provides practicable electromotive force, even under irradiation with IR light (Fig. 4). Although the IPCE measurement succeeded up to 1600 nm due to the limitations of the instrument (Fig. 4b), the photocurrent was also successfully extracted through the external circuit, even under SWIR light (1615–2280 and 2093–2547 nm in Fig. 4c, d, respectively) from the Xe lamp.
It was revealed that the LSPR-induced electron injection from ITO to the SnO2 or TiO2 phases takes place, but the real mechanism should be identified because there are several possible mechanisms for the formation of FCA in metal oxides by the sensitisation of plasmonic NCs, i.e., plasmon-induced hot-electron injection5, local-electromagnetic-field-induced in-situ electron and hole generation in a semiconductor21 and plasmon-induced resonant-energy transfer (PRET)22. PRET only occurs when the LSPR band of ITO NCs overlap with the absorption band of the semiconductor. However, the absorption of SnO2 does not overlap with the LSPR of ITO. On the other hand, the enhanced local electromagnetic fields of plasmonic materials can contribute the generation of electron-hole pairs in the semiconductor, even if the interlayer effectively blocks the injection of hot electrons generated by LSPR excitation21. To clarify whether this mechanism is responsible for our system, we measured the TR-IR of ITO/oleylamine(OAm)/SnO2, in which the ITO NCs are attached to the SnO2 through the insulating OAm with a molecular length of ~2 nm. As the result, the FCA was not observed for the ITO/OAm/SnO2, owing to the complete obstruction of electron injection from ITO NCs by insulating OAm layers (Supplementary Fig. 14). Consequently, we can conclude that LSPR-induced hot-electron injection is a key mechanism for the emergence of the FCA of SnO2. Additionally, the appearance of FCA within a short timescale (~1 ps) strongly suggests that hot-electron injection takes place in the tunnelling process through the Schottky barrier at the ITO/SnO2 heterointerfaces. Recently, the electron-injection mechanism from metal (Au or Al) to metal-oxide semiconductors upon LSPR excitation was investigated23,24. Both the LSPR-induced hot-electron injection and electron transfer via inter- or intraband transitions in metal were concluded to be responsible for electron injection. Note that the LSPR band of the ITO NCs was completely separated from the inter- of intraband-transition bands. This means that our ITO/SnO2 exhibited efficiency of 33% by only selective-excitation of LSPR (without inter or intraband). This fact is favourable for the application of the present LSPR-induced carrier transfer system to the invisible optical devices. In contrast to ITO/SnO2, the electron-injection efficiency to TiO2 (anatase) was poor (0.11%).
The hot-electron-injection efficiency of ITO/SnO2 is significantly high compared with that of ITO/TiO2, implying that the Schottky barrier at the heterointerface is a criterion for inducing such injection. It was reported that the ITO has both semiconducting and metallic natures and forms the Schottky barrier at the ITO/TiO2 interface25. The height and thickness of the Schottky barrier at the ITO/TiO2 heterointerface should be larger than that at the ITO/SnO2 heterointerface because the barrier is affected by the alignment of EF of materials forming these interfaces. Thus, in the case of the ITO/TiO2 system, the hot electrons generated in the ITO are unfavourable for tunnelling through or overcoming the Schottky barrier at the heterointerface. This barrier is an obstacle to electron injection and can suppress charge recombination as a positive effect. Such recombination suppression is thought to contribute to the long-lived charge separation of the ITO/SnO2 system. The present results provide us with fine tuning of the plasmonic material/semiconductor heterointerface to realise efficient charge separation, which to the best of our knowledge has not yet been established in plasmonic electron-injection systems.
In conclusion, we have demonstrated SWIR-LSPR-induced hot-electron injection from ITO NCs to SnO2 or TiO2 by means of the μs- and fs-TR-IR measurements. Considering the transparency of ITO and metal oxides, this is the first example of a clear and colourless system for IR-responsive carrier transfer, to the best of our knowledge. The selective-excitation of LSPR of ITO causes hot-electron injection with high efficiency (33%) and long-lived charge separation (~2–160 μs) thanks to fine control of the heterointerface. The reasonable electron injection efficiency and the much-longer-lived charge separation, compared with the typical Au/TiO2 and other Au/semiconductor systems, guarantee the value of our system for optical devices using IR-light. Furthermore, we demonstrated that IR light longer than SWIR region can be applicable to the present system owing to the ease controllability of LSPR band of heavily doped semiconductor NCs. We believe that our experimental results provide an important step for the LSPR-induced carrier transfer and a useful strategy for use in invisible optical devices.
Microsecond (μs) time-resolved IR-absorption measurements were conducted using custom-built spectrometers, as described in our previous papers26. ITO/metal oxide samples were photoexcited by using a 1400 nm laser pulses (energy: 2.7 mJ pulse−1, duration: 6 ns, repetition rate: 1 Hz) originating from a Nd: YAG laser (Continuum Surelite II) equipped with an optical parametric oscillator (OPO) system to generate the desired pump wavelength. The IR light emitted from the MoSi2 coil was used as the probe light in the mid-IR region (7000–1000 cm−1). The transmitted IR light from the ITO/metal oxide samples fixed on the CaF2 plate was then introduced into the grating spectrometer and the monochromated light from the spectrometer was detected by an MCT detector (Kolmar), and then the output electric signal was amplified using an AC-coupled amplifier (Standford Research System SR560, 1 MHz). The time resolution of the spectrometers was limited to ~1 μs by the bandwidth of the amplifier. The instrument response function (IRF) was evaluated by measuring the scattered laser pulses detected by the MCT. The FWHM value of IRF was estimated to be 0.485 μs as indicated in Supplementary Figure 12.
In the femtosecond-to-picosecond region, the ultrafast kinetic measurements were performed using on Ti:sapphire laser system (Spectra Physics, Solstice and TOPAS Prime, duration: 90 fs, repetition rate: 1 kHz) to generate the pump and probe wavelengths27. The ITO/metal oxide samples were photoexcited using 1700 nm (energy: 6 μJ pulse−1). The probe light was focused on the sample and the transmitted IR light during irradiation condition entered the spectrometer equipped with gratings. The monochromated light was then detected by MCT detector. The FWHM of IRF value was estimated to be 285 ± 40 fs (refer to Figure S6b). For the measurement of the kinetic profile shown in Supplementary Fig. 14, a femtosecond Ti:sapphire laser system (Spectra Physics; Hurricane and TOPAS; wavelength: 800 nm; pulse duration: 150 fs; repetition rate: 1 kHz) was used. The FWHM value of IRF of the system is 210 fs. The 1700-nm pulse from one OPA was used as a pump light. For the probe light, a 3440-nm pulse generated from the other OPA with a difference-frequency-generation crystal was used. The intensity of the probe light transmitted from the sample was detected using an MCT photodetector (KMPV11-1-J1, Kolmar technology).
Transmission electron microscopy
TEM observations (JEM-1011, JEOL) were carried out at an accelerating voltage of 100 kV. TEM samples were prepared by placing a drop of cluster solution onto a carbon-coated copper grid. HAADF-STEM and EDS elemental mapping were performed on Titan3 (FEI) (convergence semiangle: 17.9 mrad, a high-brightness Schottky emission gun (X-FEG) and double spherical aberration correctors, Oxford Instruments X-MaxN 100TLE EDS detector) electron microscopes with an operating voltage of 300 kV.
Steady-state UV–vis–NIR-absorption spectroscopy was conducted using a U-4100 spectrophotometer (HITACHI).
X-ray diffraction analysis
XRD patterns were taken by X’pert Pro MPD (PANalytical) with CuKα radiation (λ = 1.542 Å) at 45 kV and 40 mA.
Synthesis of ITO nanocrystals
ITO NCs doped with different ratio of Sn was synthesised as follows13. An n-octylether (10-mL) suspension of indium(III) acetate (1.2–x mmol), tin(II) 2-ethylhexanoate (x mmol), 2-ethylhexanoic acid (3.6 mmol) and oleylamine (10 mmol) was stirred at 80 °C under vacuum for 30 min. The solution was heated at 150 °C for 1 h under a N2 atmosphere and stirred for a further 2 h at 280 °C to afford the formation of ITO NCs. After cooling to room temperature, oleic acid (10.8 mmol) was injected into the solution and then stirred for 30 min under a N2 atmosphere. Repeated centrifugal purification by ethanol yielded pure ITO NCs protected by oleic acid. Finally, ITO NCs were re-dispersed in chloroform.
Loading of ITO nanocrystals onto metal oxides
ITO NCs were adsorbed onto nano-sized oxides through the dipole-induced dipole or dipole−charge interactions between the hydrophobic ITO NCs and hydrophilic oxides28. We used SiO2 (G-10, Fuji Sylisia), TiO2 (anatase or P-25, Aldrich) and SnO2 (Wako, 22–43 nm) as oxide supports. Oxide supports (100 mg) were added into the chloroform solution (50 mL) containing the desired quantity of ITO NCs (10-wt%-Sn doping vs oxides, wt of oxides were calculated as the sum of In and Sn), followed by stirring for 24 h. The solution was filtered and washed with hexane and chloroform. Based on the absorbance change of the filtrates before and after stirring with oxides for 24 h, we concluded that nearly all the ITO NCs were adsorbed onto oxide supports. After the adsorption, the sample was putted on the glass plate and calcined in air at 600 °C for 30 min to remove organic compounds, while the intensity of the LSPR peak was significantly reduced in all ITO/metal oxides upon the calcination due to the decrease in the free-electron density. This calcination removed the surface ligands of ITO NCs, thereby creating a heterointerface between ITO NCs and oxide supports. After calcination, the ITO/metal oxides are annealed under reductive atmosphere (4% H2/Ar) at 280 °C for 5 h to regenerate the LSPR. TEM and XRD measurements revealed no changes in size and crystalline structure of the ITO/oxide heterointerfaces upon heat treatments (Supplementary Fig. 1 and 2). For the measurement of absorption spectrum in IR region, we used CaF2 as substrate. All ITO/oxide show an LSPR peak in the NIR region, even after annealing under reductive atmosphere.
Preparation of the ITO-NC/SnO2/W photoelectrode
A dense SnO2 layer was prepared on tungsten substrates (Nilaco, 1.5 cm × 3 cm) by spin-coating 1-butanol containing 0.1-M SnCl2·2H2O (Aldrich) and annealing at 450 °C for 30 min. A mesoporous SnO2 layer was formed on the dense SnO2 layer using the SnO2-Sol squeeze method (obtained by mixing 10 mL of 1-butanol with 1.0 g of SnO2 NPs (diameter = 22–43 nm, Wako), 132.4 mg of ethylcellulose (90–110 mPa·s, TCI) and 1 mL of acetylacetone (Wako)), followed by annealing at 450 °C for 30 min. The thickness of the SnO2 film, which was measured by scanning electron microscopy (S-4800, HITACHI), was 5 μm. ITO NCs were deposited onto the surfaces of the SnO2 films by spin-coating an octane solution containing ITO NCs (50 mg mL−1). The resulting electrode was calcined in air at 600 °C for 30 min, followed by anneal under 4% H2/Ar at 280 °C for 5 h.
Estimation of the quantum yield of electron injection at an ITO/SnO2 heterointerface
The quantum yield (Φ) of LSPR-induced charge injection at an ITO/SnO2 heterointerface was calculated by equation (1),
where ne (cm−3) is the free-carrier number per unit volume injected into SnO2 and Nphoton (cm−3) is the absorbed-photon number of the pump light per unit volume in ITO/SnO2.
Nphoton was calculated by equation (2),
where A is the ratio of the beam intensity within the FWHM of a laser pulse (0.5) to the full intensity assuming that the laser pulse has a Gaussian intensity profile. The total energy of one pulse is 1 μJ and the single-photon energy was estimated as
where h, c and λ are the Planck constant (6.626 × 10−34 J·s), the speed of light (2.998 × 108 m/s) and the wavelength of the pump laser (1700 nm), respectively. From equation (3), the single-photon energy was calculated as 1.17 × 10−19 J. V is the volume of the pump-laser path in the sample pellet and is calculated to be 3.75 × 10−6 cm3 from the FWHM of the pump laser (349 μm) and the optical-path length (l = 39.2 μm). The OD of the sample is 1.35 at the excitation wavelength (1700 nm). Thus, Nphoton was calculated as 0.109 × 1019 cm−3. The absorption coefficient, α (cm−1), due to free-carrier injection into the SnO2 was calculated according to equation (4)
where ΔOD at 5000 nm is 0.00160. From equation (4), α was calculated to be 0.939 cm−1. Since the absorption cross section of the free carrier is expressed as σ = α/ne (cm2), ne is expressed by the following equation,
where σ′ is the apparent absorption cross section of SnO2 powder (2.59 × 10−18 cm2), which is calculated in the next section. From equation (5), ne was calculated to be 0.0363 × 1019 cm−3. Finally, the Φ value of electron injection was determined to be 33% from equation (1).
Estimation of the apparent absorption cross section of SnO2 powder
According to ref. 15, the absorption cross section (σ) of SnO2 is expressed as
where a┴ = −8.888, b┴ = 2.894, a// = −8.705 and b// = 2.863. When λ is 5000 nm, σ┴ and σ// are estimated as 65.59 × 10−18 cm2 and 76.763 × 10−18 cm2, respectively. As the direction of a-axis and b-axis is equal, the averaged σave value was calculated to be 69.312 × 10−18 cm2 using the equation σave = (σ// + 2σ┴)/3. Since the σave value is the value of a single SnO2 crystal, a correction that takes the number density of SnO2 powder into account is necessary to evaluate the apparent absorption cross section (σ′). As the density of single-crystal SnO2 and the bulk density of the sample powder are 6.95 g/cm3 and 0.26 g/cm3, respectively, σ′ was calculated by using the following equation:
From equation 6, σ′ was calculated as 2.593 × 10−18 cm2.
Estimation of the quantum yield of electron injection at an ITO/TiO2 (anatase) heterointerface
The quantum yield (Φ) of LSPR-induced charge injection at an ITO/TiO2 (anatase) heterointerface was estimated using the same procedure as in the case of the ITO/SnO2 interface discussed above.
In the present case, the total energy of one pulse is 6 μJ and the energy of a single photon was 1.17 × 10−19. The volume of the pump-laser path in the sample pellet (V) was calculated to be 5.55 × 10−6 cm3 based on the FWHM of the pump laser (349 μm) and the optical-path length (l = 58 μm). The OD of the sample is 1.49 at the excitation wavelength (1700 nm). Thus, Nphoton is calculated to be 4.48 × 1018 cm−3. The absorption coefficient, α (cm−1), due to the injection of free carriers into TiO2 (anatase) was estimated to be 0.635 cm−1 from the ΔOD at 5000 nm (=0.00160) and the optical-path length l (=58 μm). The apparent absorption cross section (σ′) of TiO2 (anatase) powder is 1.303 × 10−16 cm2, which is determined in next section. From the values of α and σ′, ne was calculated to be 4.87 × 1015 cm−3. Finally, the Φ of electron injection was estimated to be 0.11% at the ITO/TiO2 (anatase) heterointerface.
Estimation of the apparent absorption cross section of TiO2 (anatase) powder
According to refs. 16 and 29, the average σave value was calculated to be 6.549 × 10−16 cm2. As the σave value is that of a single crystal of TiO2 (anatase), correction taking the number density of TiO2 powder into account is necessary to evaluate the apparent absorption cross section (σ′). Since the density of single-crystal TiO2 (anatase) and the bulk density of the sample powder ranges from 3.90 g/cm3 to 0.776 g/cm3, respectively, σ′ was calculated as
From equation 8, the σ′ value of TiO2 (anatase) was calculated to be 1.303 × 10−16 cm2.
The data that support the findings of this study are available from the corresponding author upon reasonable request.
Lunt, R. R. & Bulovic, V. Transparent, near-infrared organic photovoltaic solar cells for window and energy-scavenging applications. Appl. Phys. Lett. 98, 113305 (2011).
Stanley, R. Plasmonics in the mid-infrared. Nat. Photon. 6, 409–411 (2012).
Lian, Z. et al. Near infrared light induced plasmonic hot hole transfer at a Nano-heterointerface. Nat. Commun. 9, 2314 (2018).
Sönnichsen, C. et al. Drastic reduction of plasmon damping in gold nanorods. Phys. Rev. Lett. 88, 077402 (2002).
Du, L., Furube, A., Hara, K., Katoh, R. & Tachiya, M. Ultrafast plasmon induced electron injection mechanism in gold–TiO2 nanoparticle system. J. Photochem. Photobiol. C. 15, 21–30 (2013).
Sachet, E. et al. Dysprosium-doped cadmium oxide as a gateway material for mid-infrared plasmonics. Nat. Mater. 14, 414–420 (2015).
Lounis, S. D., Runnerstrom, E. L., Bergerud, A., Nordlund, D. & Milliron, D. J. Influence of dopant distribution on the plasmonic properties of indium tin oxide nanocrystals. J. Am. Chem. Soc. 136, 7110–7116 (2014).
Johns, R. W. et al. Direct observation of narrow mid-infrared plasmon linewidths of single metal oxide nanocrystals. Nat. Commun. 7, 11583 (2016).
Luther, J. M., Jain, P. K., Ewers, T. & Alivisatos, A. P. Localized surface plasmon resonances arising from free carriers in doped quantum dots. Nat. Mater. 10, 361–366 (2011).
Park, Y., Choong, V., Gao, Y., Hsieh, B. R. & Tang, C. W. Work function of indium tin oxide transparent conductor measured by photoelectron spectroscopy. Appl. Phys. Lett. 68, 2699–2701 (1996).
Chung, I., Lee, B., He, J., Chang, R. P. H. & Kanatzidis, M. G. All-solid-state dye-sensitized solar cells with high efficiency. Nature 485, 486–489 (2012).
Grätzel, M. Photoelectrochemical cells. Nature 414, 338–344 (2001).
Kanehara, M., Koike, H., Yoshinaga, T. & Teranishi, T. Indium tin oxide nanoparticles with compositionally tunable surface plasmon resonance frequencies in the near-IR region. J. Am. Chem. Soc. 131, 17736–17737 (2009).
Guo, P., Schaller, R. D., Ketterson, J. B. & Chang, R. P. H. Ultrafast switching of tunable infrared plasmons in indium tin oxide nanorod arrays with large absolute amplitude. Nat. Photon. 10, 267–273 (2016).
Peelaers, H., Kioupakis, E. & Van de Walle, C. G. Fundamental limits on optical transparency of transparent conducting oxides: free-carrier absorption in SnO2. Appl. Phys. Lett. 100, 011914 (2012).
Matsuzaki, H. et al. Photocarrier dynamics in anatase TiO2 investigated by pump-probe absorption spectroscopy. J. Appl. Phys. 115, 053514 (2014).
Yamakata, A., Vequizo, J. J. M. & Matsunaga, H. Distinctive behavior of photogenerated electrons and holes in anatase and rutile TiO2 powders. J. Phys. Chem. C 119, 24538–24545 (2015).
Furube, A., Yoshinaga, T., Kanehara, M., Eguchi, M. & Teranishi, T. Electric-field enhancement inducing near-infrared two-photon absorption in an indium–tin oxide nanoparticle film. Angew. Chem. Int. Ed. 51, 2640–2642 (2012).
Haddadi, A., Adhikary, S., Dehzangi, A. & Razeghi, M. Mid-wavelength infrared heterojunction phototransistors based on type-II InAs/AlSb/GaSb superlattices. Appl. Phys. Lett. 109, 021107 (2016).
Wu, K., Chen, J., McBride, J. R. & Lian, T. Efficient hot-electron transfer by a plasmon-induced interfacial charge-transfer transition. Science 349, 632–635 (2015).
Brongersma, M. L., Halas, N. J. & Nordlander, P. Plasmon-induced hot carrier science and technology. Nat. Nanotech. 10, 25–34 (2015).
Cushing, S. K. et al. Photocatalytic activity enhanced by plasmonic resonant energy transfer from metal to semiconductor. J. Am. Chem. Soc. 134, 15033–15041 (2012).
Zheng, B. Y. et al. Distinguishing between plasmon-induced and photoexcited carriers in a device geometry. Nat. Commun. 6, 7797 (2015).
Clavero, C. Plasmon-induced hot-electron generation at nanoparticle/metal-oxide interfaces for photovoltaic and photocatalytic devices. Nat. Photon. 8, 95–103 (2014).
Pfeifer, V. et al. Energy band alignment between anatase and rutile TiO2. J. Phys. Chem. Lett. 4, 4182–4187 (2013).
Yamakata, A., Ishibashi, T. & Onishi, H. Water- and oxygen-induced decay kinetics of photogenerated electrons in TiO2 and Pt/TiO2: a time-resolved infrared- absorption study. J. Phys. Chem. B 105, 7258–7262 (2001).
Yamakata, A. et al. Behaviour and energy states of photogenerated charge carriers on Pt- or CoOx-loaded LaTiO2N photocatalysts: time-resolved visible to mid-infrared- absorption study. J. Phys. Chem. C 118, 23897–23906 (2014).
Zheng, N. F. & Stucky, G. D. A general synthetic strategy for oxide-supported metal nanoparticle catalysts. J. Am. Chem. Soc. 128, 14278–14280 (2014).
Hirose, Y. et. al. Large electron mass anisotropy in a -electron-based transparent conducting oxide: Nb-doped anatase epitaxial films. Phys. Rev. B 79, 165108 (2009).
We thank T. Nagai, and K. Kimoto for the observation of HAADF-STEM, HRTEM image and EDS mapping. This work was supported by JSPS KAKENHI grant number JP16H06520 (Coordination Asymmetry) (T.T.), JP17H05257 (Photosynergetics) (M.S.), JP17H05491 (Mixed Anion) (A.Y.), JP17K19031 (Grant-in-Aid for Challenging Exploratory Research) (M.S.), the Collaborative Research Project of the Institute of Chemical Research, Kyoto University and AIST Nano-characterisation Facility platform as a programme of “Nanotechnology Platform” of the Ministry of Education, Culture, Sports, Science and Technology (MEXT), Japan. We thank T. Yoshinaga for the support of synthesising samples and experiments. This work was supported by NIMS microstructural characterization platform as a program of “Nanotechnology Platform” of MEXT, Japan.
The authors declare no competing interests.
Journal peer review information: Nature Communications thanks the anonymous reviewers for their contributions to the peer review of this work. Peer Reviewer Reports are available.
Publisher’s note: Springer Nature remains neutral with regard to jurisdictional claims in published maps and institutional affiliations.
About this article
Cite this article
Sakamoto, M., Kawawaki, T., Kimura, M. et al. Clear and transparent nanocrystals for infrared-responsive carrier transfer. Nat Commun 10, 406 (2019). https://doi.org/10.1038/s41467-018-08226-2
Harvesting Sub-Bandgap IR Photons by Photothermionic Hot Electron Transfer in a Plasmonic p–n Junction
Nano Letters (2021)
Interfacial engineering of Bi2S3/Ti3C2Tx MXene based on work function for rapid photo-excited bacteria-killing
Nature Communications (2021)
The Journal of Physical Chemistry C (2021)
Abnormal Electron Emission in a Vertical Graphene/Hexagonal Boron Nitride van der Waals Heterostructure Driven by a Hot Hole-Induced Auger Process
ACS Applied Materials & Interfaces (2020)