Lin
Zhu
,
Lingling
Xu
,
Jing
Wang
,
Shenyang
Yang
,
Cai-Feng
Wang
,
Li
Chen
and
Su
Chen
*
State Key Laboratory of Materials-Oriented Chemical Engineering, College of Chemistry and Chemical Engineering, Nanjing University of Technology, No. 5 Xinmofan Road, Nanjing, 210009, P. R. China. E-mail: chensu@njut.edu.cn; Tel: +86-25-83172258
First published on 26th July 2012
We report an available route for the synthesis of poly(methacrylic acid) (PMAA) macromonomers/N-acetyl-L-cysteine (NAC)-co-capped CdTe quantum dots (QDs) toward multicolor fluorescent patterns and warm white LED devices. The properties of the as-prepared CdTe QDs herein were thoroughly investigated by Fourier transform infrared spectra (FT-IR), ultraviolet-visible (UV-vis), photoluminescence (PL), X-ray diffraction (XRD) and transmission electron microscopy (TEM) measurements. We have found that the PMAA/NAC-capped CdTe QDs exhibited stable and strong photoluminescence (PL) with a narrow size distribution and a high quantum yield (QY) of ∼45%. Moreover, the as-prepared CdTe QDs demonstrated a quick growth rate and favorable fluorescent stability without any aggregation and phase separation when they were blended with a polymer matrix. Subsequently, by virtue of their excellent polymer-compatibility, we extended the water-soluble PMAA/NAC-capped CdTe QDs as “fluorescent ink” for multicolor fluorescent patterns by silk screen printing, which may find application in the anti-counterfeit field. In addition, we explored the robust CdTe QDs as “red phosphor” to fabricate a white LED device, the resulted LED emitted a higher rendering color index (CRI) warm white light compared to the conventional phosphor-only LEDs. It is believed that the route reported here could offer an available pathway to achieve robust QDs for diverse applications.
Herein, we describe the synthesis of water-soluble CdTe QDs co-stabilized by N-acetyl-L-cysteine (NAC) and poly(methacrylic acid) (PMAA) macromonomers toward multicolor fluorescent patterns and warm white LED devices (Scheme 1). First, PMAA macromonomers were fabricated as polymeric ligands via catalytic chain transfer polymerization (CCTP) technique according to our previous work.27–29 CCTP is a powerful synthetic route to produce a relatively low-molecular weight polymer chain. Subsequently, water-soluble CdTe QDs were prepared using NAC and the as-prepared PMAA macromonomers as stabilizing agents under microwave irradiation. Not only do the resulted CdTe QDs retain the performance originated from the short-straight NAC ligand, such as highly efficient fluorescence, good photostability and quantum yield (QY) of ∼45%, but they also exhibit favourable polymer-compatibility and size-tunable optical properties with a quick growth rate. Finally, taking advantage of the as-prepared QDs with good polymer-compatibility, we extended the robust CdTe QDs as “fluorescent ink” to print elegant photoluminescent patterns and as color convert materials to fabricate warm white LEDs. It is believed that the route reported here could offer an available pathway to achieve robust QDs for diverse applications.
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Scheme 1 Illustration of the route for the synthesis of PMAA/NAC-capped CdTe QDs and their applications on white LED and photoluminescent patterns. |
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Fig. 1 FT-IR spectra of (1) the PMAA macromonomer via CCTP, (2) PMAA/NAC-capped CdTe QDs, and (3) NAC-capped CdTe QDs. |
We then investigated the effect of NAC/PMAA molar ratios on the luminescence QYs of CdTe QDs, as shown in Fig. 2a. Several runs were performed at different NAC/PMAA molar ratios, ranging from 0 to 4/1 (mol/mol). We found increasing the NAC molar concentration resulted in the increase of luminescence QY, which gradually levelled off when the NAC/PMAA molar ratios reached 1/1, so we fixed the NAC/PMAA ratio at 1/1. An indication for comparing the refluxing time of the CdTe QDs capped by both PMAA and NAC with that by only NAC comes from the PL peak position vs. time curves, as displayed in Fig. 2b. After refluxing for 90 min, the characteristic emission peak position of PMAA/NAC-capped CdTe QDs is 635 nm (curve 1), however, in the case of NAC-capped CdTe QDs, it takes more than 180 min to reach 635 nm of PL emission (curve 2). The different growth rates in both cases confirmed the effect of the PMAA macromonomers on the growth of QDs, which can be explained by the PMAA macromonomers having a higher molecular weight and stronger steric hindrance compared to the short-straight NAC, increases the size of the CdTe QDs.32,33 From this point of view, our strategy can accelerate the growth rate of QDs, which may provide a reference method to fabricate high-quality near infrared red (NIR) QDs.
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Fig. 2 (a) Effect of different molar ratios between NAC and PMAA on QYs of CdTe QDs prepared at the pH = 10, and [Cd2+]/[HTe−]/[stabilizer] = 2/1/4 (mol/mol/mol). (b) Peak position of PL emission as a function of reaction time with (1) PMAA/NAC-capped CdTe QDs and (2) NAC-capped CdTe QDs obtained strictly under the same conditions. (c) Normalized UV-vis absorption spectra of PMAA/NAC-capped CdTe QDs during their growth in refluxing synthesis, and (d) the corresponding PL spectra. Inset of (c): the digital images under an ultraviolet lamp of five typical as-prepared CdTe QDs. |
The UV-vis absorption spectra and PL spectra of five typical as-prepared CdTe QDs as a function of reaction time can be observed in Fig. 2c and 2d. On prolonging the microwave heating time, the growth of the CdTe QDs was clearly indicated by the red-shift of both absorption and emission spectra, and their bright fluorescence of color appears to vary from green to red, exhibiting “quantum size effects”. Their corresponding digital images under an ultraviolet lamp are also displayed in the inset of Fig. 2c. According to the method reported by Peng's group,34 the estimated mean particle sizes with the progress of growth were 3.1 nm, 3.4 nm, 3.7 nm, 4.1 nm, 5.0 nm, respectively. Simultaneously, the sharp emission with full width at half-maximum (fwhm) of ca. 50 nm suggests the narrow size distribution of the as-prepared CdTe QDs and few electronic defect sites. Compared with the fluorescence emission of rhodamine 6G, the calculated QY of the CdTe QDs was ∼45%. The PMAA macromonomers via CCTP do not influence the “quantum size effects” of the CdTe QDs due to their low molecular weight compared with conventional polymers.
The as-prepared CdTe QDs were further characterized by TEM and XRD (Fig. 3). In the TEM image (Fig. 3a), the QDs appear as spherical particles without any aggregation. The HRTEM image of an individual nanocrystal is shown in Fig. 3b, from which the atomic lattice fringes of the CdTe nanocrystal are clearly visible. The selected area electron diffraction (SAED) pattern in Fig. 3c appears as broad diffuse rings due to the small particle size and good dispersity in solution. The powder XRD profile of the QDs shows broad peaks typical for nanocrystals, which are assigned to the (111), (220) and (311) planes of the cubic zinc blended structure of the bulk CdTe crystal. The addition of PMAA macromonomers as stabilizing agent does not change the structure of the CdTe QDs.
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Fig. 3 (a) TEM image, (b) HRTEM image, (c) SAED pattern and (d) XRD pattern of PMAA/NAC-capped CdTe QDs with the PL emission at 635 nm. |
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Fig. 4 (a) A typical time-resolved fluorescence decay curve of PMAA/NAC-capped CdTe QDs (λex = 405 nm) measured at the PL peak of 605 nm. (b) PL spectra of CdTe QDs stabilized together by PMAA and NAC with (1) fresh sample; (2) 6 months. |
It is worth noting that a key factor in the applications of QDs is their stability, so we assessed the stability of the resulted CdTe QDs. Time-resolved photoluminescence measurements were performed using time-correlated single-photon counting methodology. The decay curve at the maximum of the exciton peak is depicted in Fig. 4a. Decay traces for the sample was well fitted with biexponential function based on nonlinear least-square, using the following expression (eqn 2).35
Y(t) = α1exp(−t/τ1) + α2exp(−t/τ2) | (2) |
Where α1, α2 are fractional contributions of time-resolved decay lifetimes τ1, τ2 and average lifetime could be concluded from eqn 3:
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For PMAA/NAC-capped CdTe QDs, is 67.36 ns, which is ∼2 times longer than conventional thiol-capped CdTe QDs.36 A distribution in decay times is expected as a result of a variation in the non-radiative decay rates.37 The longer fluorescence-decay time expresses that the polymer ligand in this system could prevent the aggregation of QDs, decrease the defects of QDs and further avoid non-radiative recombination. We also investigated their long-term stability with respect to the photoluminescence properties. The PL spectra of the as-prepared CdTe QDs under ambient conditions, which were stored in air and room light with different times of (1) a fresh sample and (2) 6 month old sample, are displayed in Fig. 4b. We can observe a slight red-shift of the PL peak about 3 nm after 6 months, along with about 5% decrease of the apparent fluorescence intensity, which demonstrates the resulted CdTe QDs are stable under ambient conditions. The good fluorescent stability of the QDs might be correlated with the polymer ligands on their surface, which heal defects of the QDs.
In addition, we compared the photostability of the QD/polymer nanocomposites derived from CdTe QDs capped by PMAA/NAC dual ligands and NAC as the solo ligand, respectively. As seen in Fig. 5a, the initial PL intensity of both QDs/polymer nanocomposites is almost the same (curve 1 and 2). Whereas, the PL intensity of NAC-capped CdTe/PVP composites declined by ∼45% after being stored under ambient conditions for one week (curve 4), while the PL intensity of PMAA/NAC-capped CdTe/PVP composites only showed a slight decrease (<8%, curve 3), manifesting the good polymer-compatibility of the dual ligand-capped QDs. Coupled with their favourable fluorescence, the as-prepared QDs might be utilized as “fluorescent ink” for versatile photoluminescent patterns on polymer film. We used silk screen printing, an easily-handled method, for fluorescent patterns in our case. The “inks” with different fluorescence obtained from CdTe QDs with the PL emission peaks centring at 540 nm, 560 nm and 625 nm, respectively, were screened through woven meshes onto a PVP substrate by extruding the scraper blade. As seen in Fig. 5b and 5c, the flower patterns are invisible on the PVP film under daylight (Fig. 5b), but exhibit bright fluorescent multi-colors under the UV lamp (Fig. 5c), which may offer a further development for optoelectric devices and in the anti-counterfeit field.
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Fig. 5 (a) PL spectra of QD/PVP nanocomposites derived from (1) PMAA/NAC-capped CdTe QDs, (2) NAC-capped CdTe QDs and their corresponding PL spectra stored after one week, respectively (3,4). Photographs of the patterned films from QD/PVP nanocomposites via screen printing under (b) daylight and (c) UV light. |
The semiconductor QDs turn out to be promising candidates for the fabrication of white LEDs.38–42 Typically, the addition of conventional QDs always results in a decrease in PL intensity due to the phase separation of QDs in the polymer, which limits their applications.43 Taking advantage of the favorable polymer-compatibility of the resulted QDs, we directly employed the as-prepared solid red QDs to construct LED devices. The white LED was fabricated from the color convert materials using a mixture of yellow phosphors, red CdTe QDs and silicone, with their diagram illustrated in Fig. 6b. The as-prepared LED lamp could produce bright white light for illuminating an image in the dark, as shown in Fig. 6a. From this point of view, we believed the emitted blue light was transformed into white light as it passed through the color convert materials. The color of the emission can be better quantified with the CIE (Commission Internationale d'Éclairage) 1931 chromaticity coordinates, which serves to specify how the human eye perceives light with a given spectrum. As seen in Fig. 5c, the coordinates of the LEDs are located at (0.3485, 0.3634) belonging to the white gamut. The luminescence spectrum of the device takes on two emissions (Fig. 5d), one from the LED chip centered at 460 nm and the other from the corresponding visible component in the range of 480∼770 nm emanated from the QD-phosphor nanocomposite. This reveals the pronounced contribution of red QDs for high-color rendering index (CRI) lighting owing to their extraordinarily broad emission.44,45
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Fig. 6 (a) The photograph of the as-prepared LED device in the dark. (b) Schematic view of the fabrication of the white LED device with QD-phosphor nanocomposites. (c) Placement of the emission spectrum of the white LED on the CIE 1931 chromaticity chart. (d) Emission spectrum of the corresponding white LED lamp. |
We also measured the performance of white LEDs before and after blending with red QDs, as summarized in Table 1. We found the CRI increased from 76.1 to 84.0 and the correlated color temperature changed to warm white, which can be attributed to the red QDs compensating for the deficient emission of the phosphor in the red region. Therefore, the LED fabricated with the QD-phosphor nanocomposite represents a more warm color than the phosphor-only used LEDs. However, the luminous efficacy of the white LEDs fabricated with QDs hardly improved compared to the phosphor-only used LED, which can be explained by the addition of red CdTe QDs influencing the luminous flux of the LED, leading to slight decrease of the luminous efficacy.
CRI | Color Temp. | CIE (x, y) | Luminous Efficacy | |
---|---|---|---|---|
With QDs | 84.0 | 4913 K | 0.3485, 0.3634 | 56.4 lm W−1 |
Without QDs | 76.1 | 6125 K | 0.3190, 0.3499 | 68.1 lm W−1 |
Footnote |
† Electronic supplementary information (ESI) available: GPC profile of the PMAA macromonomer via CCTP. See DOI: 10.1039/c2ra20950k |
This journal is © The Royal Society of Chemistry 2012 |