Abstract:Optical phonon modes, confined in CdS x Se 1−x nanocrystal (NC) quantum dots (≈2 nm in radius) grown in a glass matrix by the melting-nucleation method, were studied by resonant Raman scattering (RRS) spectroscopy and theoretical modeling. The formation of nanocrystalline quantum dots (QDs) is evidenced by the observation of absorption peaks and theoretically expected resonance bands in the RRS excitation spectra. This system, a ternary alloy, offers the possibility to investigate the interplay between the eff… Show more
“…[7][8][9][10][11][12][13] Raman spectroscopy has often been employed to study semiconductor nanostructures, 14 including colloidal nanocrystals (NCs). [15][16][17][18] In addition to fundamental knowledge about the elementary excitations, 19,20 the phonon spectra provide information on chemical composition, [21][22][23][24] strain, 24 and coupling to the environment. [25][26][27] Raman spectroscopy was applied to study interdiffusion at core/shell interfaces of spherical CdSe/CdS and CdSe/ZnS NCs and nanorods.…”
Recently developed two-dimensional colloidal semiconductor nanocrystals, or nanoplatelets (NPLs), extend the palette of solution-processable free-standing 2D nanomaterials of high performance. Growing CdSe and CdS parts subsequently in either side-by-side or stacked manner results in core-crown or core/shell structures, respectively. Both kinds of heterogeneous NPLs find efficient applications and represent interesting materials to study the electronic and lattice excitations and interaction between them under strong one-directional confinement. Here, we investigated by Raman and infrared spectroscopy the phonon spectra and electron-phonon coupling in CdSe/CdS core/shell and core-crown NPLs. A number of distinct spectral features of the two NPL morphologies are observed, which are further modified by tuning the laser excitation energy E between in- and off-resonant conditions. The general difference is the larger number of phonon modes in core/shell NPLs and their spectral shifts with increasing shell thickness, as well as with E. This behaviour is explained by strong mutual influence of the core and shell and formation of combined phonon modes. In the core-crown structure, the CdSe and CdS modes preserve more independent behaviour with only interface modes forming the phonon overtones with phonons of the core.
“…[7][8][9][10][11][12][13] Raman spectroscopy has often been employed to study semiconductor nanostructures, 14 including colloidal nanocrystals (NCs). [15][16][17][18] In addition to fundamental knowledge about the elementary excitations, 19,20 the phonon spectra provide information on chemical composition, [21][22][23][24] strain, 24 and coupling to the environment. [25][26][27] Raman spectroscopy was applied to study interdiffusion at core/shell interfaces of spherical CdSe/CdS and CdSe/ZnS NCs and nanorods.…”
Recently developed two-dimensional colloidal semiconductor nanocrystals, or nanoplatelets (NPLs), extend the palette of solution-processable free-standing 2D nanomaterials of high performance. Growing CdSe and CdS parts subsequently in either side-by-side or stacked manner results in core-crown or core/shell structures, respectively. Both kinds of heterogeneous NPLs find efficient applications and represent interesting materials to study the electronic and lattice excitations and interaction between them under strong one-directional confinement. Here, we investigated by Raman and infrared spectroscopy the phonon spectra and electron-phonon coupling in CdSe/CdS core/shell and core-crown NPLs. A number of distinct spectral features of the two NPL morphologies are observed, which are further modified by tuning the laser excitation energy E between in- and off-resonant conditions. The general difference is the larger number of phonon modes in core/shell NPLs and their spectral shifts with increasing shell thickness, as well as with E. This behaviour is explained by strong mutual influence of the core and shell and formation of combined phonon modes. In the core-crown structure, the CdSe and CdS modes preserve more independent behaviour with only interface modes forming the phonon overtones with phonons of the core.
“…This resonance Raman scattering creates an important avenue to studies of band/excitonic excitations in diverse nanomaterials. [34][35][36][37] It also offers unique insight into multiphonon process due to the relaxation of selection rules and a huge amplification of Raman intensity under the resonance condition. Fortunately, the direct gaps of all the above MX 2 bulk crystals and few-layer flakes ($1.5 eV-2.5 eV) 38 overlap the photon energies of visible light, which enables our studies of resonance Raman scattering in these materials by using visible laser excitations.…”
We have performed a comparative study of resonance Raman scattering in transition-metal dichalcogenides 2H-MX 2 semiconductors (M ¼ Mo, W; X ¼ S, Se) and single-layer MoS 2. Raman spectra were collected using excitation wavelengths 633 nm (1.96 eV), 594 nm (2.09 eV), 532 nm (2.33 eV), 514 nm (2.41 eV), and 488 nm (2.54 eV). In bulk-MoS 2 and WS 2 , the resonant energies appear to coincide with their exciton excitations. The resonance can be fine tuned by varying sample temperatures, which confirms its excitonic origin in both MoS 2 and WS 2. Temperature dependence of Raman intensities is analyzed in the context of resonance Raman theory, which agrees well with the existing absorption data. While in WSe 2 , the resonance has been observed in a wider range of excitations from 633 to 514 nm, which cannot be explained with its excitonic energies of 1.6 and 2.0 eV. It is considered that additional excitonic bands induced by band splitting are involved in the inter-band transitions and substantially extend the resonance energy range. The Raman resonance energy range remains unchanged in single-layer MoS 2 compared with that in the bulk sample. However, most phonon modes in single-layer MoS 2 are significantly broadened or strongly suppressed under resonance conditions. This change could be related to the modification of acoustic modes by the substrate. V
“…1a) was a consequence of the sp-d exchange interactions between electrons confined in dot states and those located in the partially filled Mn 2+ states. This explanation is reasonable since replacing Cd 2+ with Mn 2+ ions should increase the energy gap of Cd1-xMnxS QDs [18]. In addition, it is interesting to note the weak sp-d exchange interaction in the Cd1-xMnxS bulklike NCs because their OA band remains in an almost fixed position (~2.58 eV).…”
Section: Carrier Dynamicsmentioning
confidence: 80%
“…Figure 1a shows that the undoped CdS QDs (x = 0.000) exhibit confinement energy ( conf E ) as indicated by the OA band peak at ~3.10 eV. From this value and using a confinement model based on effective mass approximation [12,[15][16][17][18], the mean QD radius R was estimated by the expression: Econf = Eg + (ħ 2 π 2 ⁄ 2 R 2 ) -1.8(e 2 ⁄ εR), where Eg is the bulk material energy gap, is the reduced effective mass, e is the elementary charge, and ε is the dielectric constant. From this, a mean radius of about R~2.0 nm was estimated for the CdS QDs, thus confirming strong size quantum confinement [16].…”
Section: Carrier Dynamicsmentioning
confidence: 98%
“…The dot size increase for increasing annealing time is a well known phenomenon governing the growth kinetic of nanoparticles in glass matrices [18,27,28]. However, a recent study of thermal treatments on undoped CdSe QDs [12] embedded in this same glass matrix (SNAB) showed a much smaller redshift (~0.03 eV) when annealed for 6 h. Since CdSe and CdS structures display great similarities, as well as Cd1-xMnxS with dilute Mn-concentration, it is reasonable to assume that they have the same growth kinetic in the same glass matrix.…”
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