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Fractional contributions of defect-originated photoluminescence from CuIn[S.sub.2]/ZnS coreshells for hybrid white LEDs.

1. Introduction

Light emitting devices (LEDs) are a key element in the photonic and optoelectronic devices including optical displays, room lighting, cell phones, motor vehicle head lights and indicators, and traffic lights. The spectral distribution and purity of optical materials lead to the realization of photonic and optoelectronic applications. The broad spectral distribution is required for white LEDs, and the spectral purity is required for photonic color indicator or displays. Semiconductor nanocrystals (SNCs) are of significant interest in developing LEDs [1-3] because of their wide optical tunability and good photostability. The quantum confinement in the SNCs with sizes near the bulk Bohr radius provides wide optical tunability with strong blue-shift of optical bandgap [4].

The SNCs have good photostability with less photobleaching compared to organic materials. The II-VI SNCs have a wide optical tunability, good photostability, and high color purity, but heavy metals and narrow spectral width are undesirable for white LED development [5]. The I-III-[VI.sub.2] SNCs have a broad emission spectral width, wide optical tunability, and good photostability in addition to no toxicity associated with the heavy metals including cadmium or lead chalcogenides. Therefore, the I-III-[VI.sub.2] SNCs are excellent optical materials for hybrid white LED development.

The emission of II-VI SNCs mainly comes from the exciton pair recombination in the conduction and valence bands and possibly the transitions from/to surface-trapped state just below the conduction band or above the valence band [6]. The emission of I-III-[VI.sub.2] SNCs comes from the optical transitions related surface-trapped state for core materials, interface-trapped state for coreshells, and shallow- and deep-trapped donor-acceptor (DA) states [7]. The interface-trapped state and shallow- and deep-trapped DA states are correlated to the emissions at the higher, intermediate, and lower energy spectral region, respectively [8, 9]. However, the numerous interface and interstitial and vacancy on/in the large numbers of coreshells lead to the broad optical spectrum and even overlap all emissions from the interface-trapped state and defect-related DA-trapped state [10-12].

In this paper, two selective I-III-[VI.sub.2] coreshells of CuIn[S.sub.2]/Zn[S.sub.665 nm] (aS/Zn[S.sub.665 nm]) and CuIn[S.sub.2]/Zn[S.sub.555 nm] (CIS/Zn[S.sub.555 nm]) with photoluminescence (PL) peaks ~555nm and ~665nm, respectively, are utilized for the hybrid white LED development. The temperature-dependent and time-resolved PL studies on the CIS/Zn[S.sub.665 nm] core shells reveal the contributions of interface-trapped state and defect-related DA-trapped state to the PL spectra, while the optical studies on the CIS/Zn[S.sub.555 nm] coreshells illustrate the modification of PL decays and spectral symmetry. Finally, the time-resolved and temperature-dependent PL studies of CIS/Zn[S.sub.665 nm] and CIS/Zn[S.sub.555 nm] describe the optical origins of better spectral covering and spectral coupling for developing hybrid white LEDs, where the SNCs are stacked on the blue LEDs for the excitation as well as the spectral coupling in the entire visible spectral region.

2. Experimental Details

The CIS/Zn[S.sub.665 nm] and CIS/Zn[S.sub.555 nm] coreshells were prepared by the literature procedure [13]. The absorption spectrum of CIS/ZnS SNCs was measured with a UV-VIS spectrophotometer (Cary 50 Bio, Varian Inc.) and a UV-VIS spectrometer (Agilent 8453). The photoluminescence excitation (PLE) spectra were collected using spectrofluorometer (Cary Eclipse, Varian Inc.) while the PL was monitored at 525 nm, 550 nm, and 600 nm using appropriate narrow band-pass filters for CIS/Zn[S.sub.555 nm] and at 650 nm, 575 nm, 640 nm, and 690 nm for CIS/Zn[S.sub.665 nm].

The PL lifetimes of CIS/ZnS were recorded using a FluoTime 200 fluorometer (PicoQuant, Inc.) with a diode laser excitation at ~470 nm, which has a pulse width less than ~70 ps and 100 KHz repetition rate. A long-wavelength pass (LWP) filter at 495 nm was used to exclude the laser excitation light. The selective PL wavelengths for measuring lifetimes were 525 nm, 550 nm, and 650 nm for CIS/Zn[S.sub.555 nm] and CIS/ZnS and 575 nm, 640 nm, and 690 nm for CIS/Zn[S.sub.665 nm] to study the fractional contribution of interface-trapped state and defect-related shallow- and deep-trapped DA states to the PL. The tail fitting with multiexponential decay equation and nonlinear least square function to the PL decay measurements was used to extract the PL lifetimes as Seo et al. described [14]. The multiexponential decay equation of emission intensity I(X, t) at the time (t) and wavelength (A) is [14]

[MATHEMATICAL EXPRESSION NOT REPRODUCIBLE IN ASCII], (1)

where [[tau].sub.i] is the characteristic lifetime of the ith decay component, [a.sub.i] is the subsequent decay amplitude, and [I.sub.0]([lambda]) is the fluorescence intensity at time t = 0. The intensity weighted average lifetime is given by [14]

[<[tau]>.sub.int] = [[SIGMA][a.sub.i][tau].sup.2.sub.i]/[SIGMA][a.sub.i][[tau].sub.i] = [summation over (i)] [f.sub.i][[tau].sub.i], (2)

where [f.sub.i] = [a.sub.i][[tau].sub.i]/[SIGMA][a.sub.i][[tau].sub.i] is the fractional contribution of each decay component to [I.sub.0] (A) and the denominator [SIGMA] [a.sub.i][[tau].sub.i] is over all amplitudes and decay times which is proportional to the total intensity.

The temperature-dependent PL of CIS/ZnS was detected using optical fibers (Ocean Optics, P600-VIS-NIR) and a spectrometer (Ocean Optics, USB4000) with a spectral resolution of ~1nm. A HeCd laser at 325 nm was used as an excitation source. The laser power was ~9mW with a beam chopper operating at a frequency of 300 Hz. The SNC materials were placed between two quartz microglasses on the cold finger in the helium closed-cycle cryostat (Janis, SHI4-1).

3. Result

Figure 1 shows absorption, PL, and PLE spectra of CIS/ZnS coreshells. The absorption spectra of coreshells have a strong blue-shift from the optical bandgap (~1.5 eV/~827nm) of bulk CIS due to quantum confinement [15]. The PLE spectra of CIS/Zn[S.sub.555 nm] displayed broad shoulders at ~470nm and ~480 nm for the monitoring PL wavelengths at ~525 nm, ~550 nm, and ~600 nm. It indicates the broad spectral contribution from the interface-trapped state and defect-related DA-trapped state to the PL of CIS/ZnS. However, the broad PLE shoulder disappeared or was reduced for CIS/Zn[S.sub.665 nm] which implies that the wide size distribution and various types of defect play a role in the further spectral broadening of PLE [16]. The absorption and PLE spectra of CIS/ZnS did not exhibit the multiple distinct peaks which could be observed from the II-VI SNCs with sizes near the bulk Bohr radius as a result of quantum confinement [17]. The optical transitions in II-VI SNCs are mainly related to the exciton pair recombination in the conduction and valence bands [18], and surface-trapped state, while those of I-III[VI.sub.2] are related to the surface/interface-trapped state and defect-related DAP recombination [15,19,20]. The PL spectra of CIS/Zn[S.sub.555 nm] and CIS/Zn[S.sub.665 nm] exhibit the peaks at ~555 nm and ~665 nm, which are attributed to the interface-trapped state and shallow- and deep-trapped DA states. The full width at half maximum (FWHM) of PL spectrum from CIS/Zn[S.sub.665 nm] at 300 K is ~115 nm and that of CIS/Zn[S.sub.555 nm] at 300 K is ~100 nm. The PL from CIS/Zn[S.sub.555 nm] has a better spectral coupling with the blue excitation for generating white light in the visible spectral region while CIS/Zn[S.sub.665 nm] has the undesired infrared emission which is similar to the previous reports [21]. The asymmetry of PL spectrum and the reduced spectral width of the CIS/Zn[S.sub.555 nm] compared to the PL properties of CIS/Zn[S.sub.665 nm] are due to the higher contributions from the interface-trapped state and shallow-trapped DA state in the lower wavelength spectral region and the less size-dependent confinement of deep-trapped state. Therefore, the time-resolved and temperature-dependent PL studies of CIS/Zn[S.sub.665 nm] and CIS/Zn[S.sub.555 nm] are required to explain the optical origins of spectral covering and coupling for developing hybrid white LEDs.

Figure 2 shows the PL decays (top), residual traces (middle), and decay components (bottom) from CIS/Zn[S.sub.665 nm] at shorter wavelength, 575 nm (a), center wavelength, 640 nm (b), and longer wavelength, 690 nm (c). The PL at 575 nm has three exponential decay times with fast ([[tau].sub.1]), intermediate ([[tau].sub.2]), and slow ([[tau].sub.3]) components of ~13.8ns, ~51.2ns, and ~180.1ns with the fractional amplitudes of 69.8%, 27.1%, 3.1%, respectively. The PL decays at 640 nm have fast ([[tau].sub.3]), intermediate ([[tau].sub.2]), and slow ([[tau].sub.3]) components of ~15.4ns, ~71.1ns, and ~236.8ns with the fractional amplitudes of 55.4%, 38.1%, and 6.5%, respectively. The PL decays at 690 nm have fast ([[tau].sub.3]), intermediate ([[tau].sub.2]), and slow ([[tau].sub.3]) components of ~37.6 ns, ~137.9 ns, and ~367.3 ns with the fractional amplitudes of 41.0%, 49.3%, and 9.7%, respectively. The averaged lifetimes of three exponential decays of CIS/Zn[S.sub.665 nm] are ~29.1ns, ~51.0ns, and ~119.0ns at the PL wavelengths 575 nm, 640 nm, and 690 nm, respectively. The fast lifetime ([[tau].sub.1] ) with larger fractional amplitude at the shorter wavelength as shown in Figure 2(a) is related to the interface defect state [15,19, 20]. The fractional amplitude of slow decay ([[tau].sub.3]) increases at longer wavelength as shown in the Figure 2(c) component. This suggests that the slow decay is related to the deep-trapped DA state [22]. Then, the intermediate ([[tau].sub.2]) decay component in the broad spectral region as shown in Figures 2(a), 2(b), and 2(c) is possibly assigned to the shallow-trapped DA state which is strongly overlapped with interface-tapped state and deep-trapped state. The fractional amplitude of fast ([[tau].sub.1] ) decay component is decreased at longer wavelength and that of intermediate ([[tau].sub.2]) and slow ([[tau].sub.3]) components is increased at longer wavelength. The fast (rx) and intermediate ([[tau].sub.2] ) decay components have large fractional amplitudes in the entire spectral region. It implies that interface-trapped state and shallow-trapped DA state provide the major contribution to the PL.

Figure 3 shows the PL decays (top), residual traces (middle), and decay components (bottom) from CIS/Zn[S.sub.555 nm] at shorter wavelength, 525 nm (a), center wavelength, 550 nm (b), and longer wavelength, 600 nm (c), to analyze the contributions of interface defect-related state and shallow and deep-trapped defect-related DA states. The PL at 525 nm has three exponential decay times with fast (rx), intermediate ([[tau].sub.2]), and slow ([[tau].sub.3]) components of ~17.3ns, ~116.3ns, and ~428.9ns with the fractional amplitudes of 48.8%, 40.3%, and 10.9%, respectively. The PL decays at 550 nm have fast ([[tau].sub.1]), intermediate ([[tau].sub.2]), and slow ([[tau].sub.3]) components of ~23.5 ns, ~160.8ns, and ~565.8ns with the fractional amplitudes of 49.8%, 43.4%, and 7.9%, respectively. The PL decays at 600 nm have fast (rx), intermediate ([[tau].sub.2]), and slow ([[tau].sub.3]) components of ~20.2 ns, ~184.0 ns, and ~575.4 ns with the fractional amplitudes of 42.2%, 45.6%, and 12.2%, respectively. The fractional amplitudes of fast (rj PL decay are slightly decreased, but those of intermediate ([[tau].sub.2]) PL decay are slightly increased. However, both fractional amplitudes of fast (r1) and intermediate ([[tau].sub.2]) decays have the major contributions to the PL and are widely distributed in the entire spectral region. It indicates that the interface-trapped state and shallow-trapped DA state are strongly overlapped. The average lifetimes of three exponential decays of CIS/Zn[S.sub.555 nm] are ~101.9ns, ~124.3ns, and ~ 162.3 ns at the PL wavelengths 525 nm, 550 nm, and 600 nm, respectively. The averaged PL lifetimes of CIS/Zn[S.sub.555 nm] are longer than those of CIS/Zn[S.sub.665 nm]. It implies that CIS/Zn[S.sub.555 nm] has less PL quenching through a nonradiative decay process.

The thermal quenching properties of PL from CIS/Zn[S.sub.555 nm] and CIS/Zn[S.sub.665 nm] make further confirmation on the implication of defect-related interface-trapped state and shallow- and deep-trapped DA states to PL distribution. The temperature-dependent PLs from CIS/Zn[S.sub.665 nm] (a) and CIS/Zn[S.sub.555 nm] (b) are shown in Figure 4. The insets of Figure 4 display the thermal quenching of PLs from CIS/Zn[S.sub.555 nm] and CIS/Zn[S.sub.665 nm] which indicate the fast PL quenching due to thermalization above ~50 K. The PL of CIS/Zn[S.sub.555 nm] has asymmetric spectral distribution, while the PL of CIS/Zn[S.sub.665 nm] has a symmetric spectral distribution. It implies that the deep-trapped DA state is less size-dependent on the confinement compared to the shallow-trapped DA state and defect-related interface state. It is well known that the surface/interface defects of nanomaterials increase as the relative surface area per volume is increased by decreasing the size [23]. The temperature-resolved spectroscopy shows that the PL from the interface-trapped state and shallow-trapped DA state has less thermal quenching and the PL at longer wavelength from the deep-trapped DA state has stronger thermal quenching. The PL peak of CIS/Zn[S.sub.665 nm] is shifted from ~670 nm to ~665 nm as the temperature is increased from 6K to 300 K. The PL irradiance reduction of CIS/Zn[S.sub.555 nm] at longer wavelength region is faster than that at shorter wavelength region as the temperature is increased. This implies the existence of stronger thermal ionization and phonon-assisted nonradiative decay at the deep-trapped DA state with the relatively stronger Coulomb interaction [24].

The FWHM (~115nm) of PL spectrum from CIS/Zn[S.sub.665 nm] is wider than that (~100 nm) of CIS/Zn[S.sub.555 nm] at 300 K. However, the PL from CIS/Zn[S.sub.555 nm] provides the better spectral coupling with the blue excitation for the hybrid white LEDs in the visible spectral region because CIS/Zn[S.sub.665 nm] has the undesired infrared emission as shown in Figure 5(a). Figure 5(b) shows the proposed schematic sketch of CIS/ZnS coreshells stacking on the InGaN blue LEDs emitting at ~470 nm. The hybrid white LED is based on the integration of broad PL spectra from CIS/ZnS and blue emission from InGaN diodes. Figures 5(c), 5(d), and 5(e) display the photo pictures of devices and emissions of InGaN (c), hybrid white LED with CIS/Zn[S.sub.555 nm] (d) and CIS/Zn[S.sub.665]nm (e), respectively.

4. Conclusion

CIS/Zn[S.sub.555 nm] and CIS/Zn[S.sub.665 nm] coreshells were utilized for developing the hybrid white LEDs where the nanoparticles were stacked on the blue LEDs. The time-resolved spectroscopy of CIS/Zn[S.sub.665 nm] revealed that the fast, intermediate, and slow decays were correlated to the interface-trapped state and shallow- and deep-trapped states, although the three exponential decays are distributed in the entire spectra. The asymmetry of PL spectrum and the reduced spectral width of the CIS/Zn[S.sub.555 nm] imply that the deep-trapped DA state is less size-dependent on the quantum confinement compared to the shallow-trapped DA state and defect-related interface state. The temperature-resolved spectroscopy revealed that the PL from deep-trapped DA state has a relatively large thermal quenching through the thermal ionization and the phonon-assisted nonradiative decay due to the stronger Coulomb interaction of deep-trapped DA pairs, while the PLs from interface defect state and shallow-trapped DA state have relatively less thermal quenching due to the weak Coulomb interaction at the near outer boundary of the nanocrystal. The spectral coupling between the PL from CIS/ZnS with a broad spectral width and the blue diode excitation leads to the realization of hybrid white LEDs.

http://dx.doi.org/10.1155/2014/979875

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

Acknowledgments

The work at HU was supported by the NSF HRD-1137747 and ARO W911NF-11-1-0177

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Quinton Rice, (1) Sangram Raut, (2,3) Rahul Chib, (2) Zygmunt Gryczynski, (2,3) Ignacy Gryczynski, (2) Wenjin Zhang, (4) Xinhua Zhong, (4) Mahmoud Abdel-Fattah, (1) Bagher Tabibi, (1) and Jaetae Seo (1)

(1) Department of Physics, Advanced Center for Laser Science and Spectroscopy, Hampton University, Hampton, VA 23668, USA

(2) Department of Cell Biology and Immunology, Center for Fluorescence Technologies and Nanomedicine, University of North Texas Health Science Center, Fort Worth, TX 76107, USA

(3) Department of Physics and Astronomy, Texas Christian University, Fort Worth, TX 76129, USA

(4) Department of Chemistry, Key Laboratory for Advanced Materials, East China University of Science and Technology, Shanghai 200237, China

Correspondence should be addressed to Jaetae Seo; jaetae.seo@hamptonu.edu

Received 27 July 2014; Revised 10 September 2014; Accepted 10 September 2014; Published 22 October 2014

Academic Editor: Ruibing Wang
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Title Annotation:Research Article
Author:Rice, Quinton; Raut, Sangram; Chib, Rahul; Gryczynski, Zygmunt; Gryczynski, Ignacy; Zhang, Wenjin; Z
Publication:Journal of Nanomaterials
Date:Jan 1, 2014
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