Today lighting and energy savings is an important part of life and traditional methods of lighting are inefficient, while the light emitting devices (LEDs) can be used in technologies applications for saving energy .LEDs produce light using a fundamentally different principle than those used by incandescent, neon, fluorescent, or high-intensity discharge (HID) lamps. Traditional light sources produce light by heating a filament to incandescence and this is inefficient but LEDs emit light from a small semiconducting chip when a current is applied. So controlling equipment and techniques is one of the most cost-effective and significant opportunities for reduce energy waste and improve output light quality. Researches have also provided new structures to improve the efficiency of LED devices. Conjugated polymers offer many advantages as materials for use in light-emitting diodes . Because of the advantages of quantum dots and their application in optoelectronic devices such as LEDs, researches fabricated quantum dot light emitting diode with improvement efficiency; which was replaced with traditional light sources. Quantum dot light emitting diodes use in energy-efficient, high-color-quality thin-film display and solid-state lighting applications .
In 1907, H. J. Round found the effect of electroluminescence, so the notion of light emitting diode was introduced . III-V materials were discovered in the 1950s, and by using of these materials the first p-n junctions GaAs LED, with epitaxial growth was made [5, 6]. In 1962 GaAsP LED with visible red light was realized by Holonyak . In 1992, the first blue LED based on GaN with efficiency of 1 % was introduced by Akasaki et al , also green LEDs could be made using GaInN with improvement efficiencies up to 10% . The possibility of color displays with blue, red, and green LEDs was successfully realized . Different LEDs can have different characteristics, so they have different application in related technologies. According to the importance of LEDs in new technologies, in recent years there are so motivations by doing a lot of researches to improve the quality of LEDs, so recently they introduced quantum dot based light emitting diodes (QD-LEDs) [3, 11]. According to improvement of QD-LEDs the efficiency of this kind of LEDs has increased from 0.01% to 18%, in 1994 . Nano crystals also known as quantum dots (QDs), are nano-sized semiconductor particles, by the synthetic method, the QDs can be classified into epitaxial and colloidal QDs. Colloidal QDs are chemically synthesized and consist of small inorganic semiconductor core (1–10 nm in diameter) and a wider-band gap inorganic semiconductor shell, and a coating of organic passivation ligands . Original QDs contain a core; however, the optical properties of QDs can be improved by coating higher band gap materials or passivation of the surface of the core . Colloidal QDs exhibit some advantages such as larger excitonic interaction between the electrons and holes, stronger carrier confinement, high quantum yield, narrow emission spectrum. Therefor colloidal QDs have the potential to change the way that electronic devices, including solar cells and LEDs, are manufactured [13, 14]. QDs exhibit quantum confinement effect, because of their radius which is smaller than the characteristic Bohr exciton radius, so the carriers in all three directions confined and the density of states will change. According to quantum confinement effect, the optical properties such as absorption and emission can be changed . Band gap is tunable by controlling the size of the QDs during the synthesis process and cheap solution processability of them makes colloidal quantum-dot a promising candidate for optoelectronic devices [3, 15]. The color emitted from QDs and the wavelength of emission, depends on the size of the QDs. According to changing in the size of QDs, the emission wavelength can be changed, so the color of light emission can be changed, also QDs have the high photo-luminescence efficiency; therefore these advantages make colloidal QDs candidates for making quantum-dot light emitting diodes [3, 12]. Figure 1 shows the size changing of QDs and band gap of them.
QD-LEDs are multilayer structures, consist of hole transport layer (HTL), electron transport layer (ETL) and QD layer as an emissive layer. In this type of LEDs, Indium tin oxide (ITO) (as an anode) and Al (as a cathode) are used as usual electrodes [3, 16]. At first QD-LEDs presented in the form of hybrid organic/inorganic light emitting diodes by Colvin et al . For the hybrid diodes, the QDs were fabricated from inorganic semiconductors and the transport layers from organic semiconductors. This kind of LEDs was later improved by Coe-Sullivan et al . However organic transport layers have stability problems and these layers are sensitive to air, because of these problems the efficiency of hybrid organic/inorganic LEDs decreases [3, 16]. Therefore, inorganic semiconductor transport layers were developed and used in QD-LEDs. Using of inorganic charge transport layers lead to device stability in air . Nevertheless the advantages of QD-LEDs and using them in optoelectronic devices like thin film displays, which cause the improvement in color saturation in this kind of displays, there are some problems limit the applicability of QD LEDs which can be listed as follows:
Efficient non-radiative Forster resonant energy transfer (FRET) of excitons within the inhomogeneous size distribution of QDs to non-luminescent sites, where they have non-radiative recombine, cause self-quenching phenomenon.
Quenching in photoluminescence (PL) of QDs by the surrounding conductive metal oxides because of carrier imbalance (due to a large hole or electron injection barrier between the p or n type metal oxides and the QDs) [3, 17].
Using of inorganic charge-transport materials is desirable because they can facilitate charge carrier injection and transport to the QD layer and also improve the charge confinement in the QD luminescent layer. As a result it is expected that HTL and ETL make the LEDs less susceptible to the problems . Nowadays NiO and ZnO are common materials to use as charge transport layers, which NiO is a p-type material as a HTL and ZnO is a n-type material as an ETL [16, 18]. Engineering the defect energy levels in the structure of p and n type metal oxides can improve their charge transport properties. These defects levels can be engineered using synthesis methods and also by doping of different atoms in the structure of materials. These defect levels act as a radiative recombination center, therefore photon production probability will be increased . The other way to increasing intensity of emitted light of LEDs is Forster resonance energy transfer (FRET). In this way inorganic materials act as core and organic molecules as capping materials. FRET is an energy transfer between these organic and inorganic materials, which one of them is as electron donor and the other one is as electron acceptor .
2. Physics and theory of LEDs and QD-LEDs
LEDs are pn-junction diodes which have many applications in displays and lighting. These LEDs made from III-V semiconductors. Figure 2 shows pn-junction and energy level of it, which indicate pn-junction under zero bias and forward bias. The junction between p-type and n-type is non-conductive, because of moving of electrons by diffusion from the n-type region into the p-type region and combine with the acceptors. So this causes to formation of depletion zone or space charge region. According to Figure2, EV and EC indicate valence band and conduction band of energy level diagram respectively, which shows under forward bias, the potential barrier between p-type and n-type reduces. Also EF and WD indicate Fermi level and depletion width respectively. By current injection and applying a voltage in the forward direction of the device, electrons and holes are pushed to the junction, so the electron-hole pairs appear and recombine together, this result in the formation of light. The electroluminescence phenomenon causes the generation of light in LEDs. The wavelength of generated light depends on used materials as a p-type and n-type [21, 22].
In semiconductors electrons and holes recombine together radiative or non-radiative, which radiative recombination creates light (photon) and non-radiative recombination creates phonon. Figure 3 illustrates radiative and non-radiative recombination [21, 22].
Because of the presence of electron and hole in recombination process, this process is called bimolecular recombination. The recombination rate, R is given by:
where B is bimolecular recombination coefficient and R is proportional to the density of electron-hole pairs. In light emitting diodes non-radiative recombination is unwanted, because this process creates phonon, so the phonons causes to increase heat and heating of the material has harmful effects on emitted light and lifetime of device [21, 22]. QD-LEDs are another structure of LEDs that have multilayers and QD layer is an active layer. This LEDs consist of hole transport layer (HTL), electron transport layer (ETL) and QD layer as an emissive layer. In this type of LEDs, Indium tin oxide (ITO) (as an anode) and Al (as a cathode) use as usual electrodes. The HTL is contacted by ITO and ETL is contacted by Al, which acts as an injector . In this device by applying forward bias and current injection, the holes and electrons are injected from anode and cathode respectively, and they are travel through of HTL and ETL to the QD layer, then they recombine together in QD layer [3, 16]. Figure 4 indicates QD-LEDs structure, energy level diagram, and physical performance of QD-LEDs. Forster resonant energy transfer (FRET) is excitation mechanism of QDs in close proximity to small organic molecules and inorganic layers. In FRET mechanism, in the charge transport layers formed electron-hole pairs transfer energy non-radiative to the QD layer by dipole-dipole coupling. Direct charge injection is the efficient method of injection carriers .
For explain the performance of QD-LEDs, these devices consist of five parts which listed as follow :
Carrier injection from the electrodes
By assuming of position (0 and w), and ohmic contacts at anode and cathode, the carrier concentrations inside the transport layers are equal to the equilibrium carrier concentrations that are given in Eq. 2.
At the electrodes, there is no space charge, so we have the following condition (Eq. 3).
where n and p are electron and hole concentrations respectively, ni is intrinsic carrier concentration, and Nd is the donor concentration and Na is the acceptor concentration. At the electrodes, the electrostatic potential is given by the following equations (Eqs. 4 and 5).
According to Anderson’s rule, the last term in equation, accounts for the discontinuities in the conduction band and valence band.
Transport in the ETL and HTL
The equations used to describe the transport in the HTL and ETL are similar to the bulk drift and diffusion equations, which is given as follows (Eqs. 6-10).
G indicates generation parameter which is assumed to be negligible and U is recombination rate and given by Shockley-Read-Hall (SRH) recombination, which will be described in (e) section.
Carrier injection from transport layers into the QD layers
Assuming that the QD layer adjacent to the HTL, the nearest QDs are considered to be traps for holes. In equilibrium and using detailed balance, the rate of emission is equal to the rate of captured holes by these QDs, so, we have (Eq. 11):
p(0) and p() are hole density in the QD layer and HTL, which adjacent together, respectively. NT is the density of trap states in the QD layer (each QD can only accommodate one hole). e and c are emission rate coefficient and the capture rate coefficient for the trap states, respectively. Also subscript (0) is used for equilibrium condition. The ratio of emission and capture coefficients is given by Eq. 12 as follows.
The difference of capture and emission can be describes the rate of change of carrier concentration under non-equilibrium conditions, thus, we have (Eq. 13):
The capture and emission coefficients can be taken to be the same as for equilibrium, if device is close to equilibrium. Also if the carrier concentration is non-degenerate, the following equation manage rate of carrier change (Eq. 14) as:
where is capture/emission time constant and equals to , also depends on the used material. At the interface of ETL and QD layer, which are adjacent together, equations for electrons are entirely similar to holes.
Transport among the quantum dot layers
The QDs can be assumed semiconductor particles with a surrounded insulating layer. The transport from one QD to another occurs by direct tunneling process. In this case the QDs act as potential wells and the insulating layer acts as tunnel barriers. Using a one-dimensional WKB approximation, the tunneling probability from QD layer 12, is given by Eq. 15:
where κ is the inverse characteristic length for tunneling and dins is the thickness of the insulating layer around the QDs. The electron is “oscillating” in the well with “frequency” . is the thermal velocity of electron, d is the diameter of the QD, and it has probability of T12 to making a transition to the neighboring QD layer. The total density of electrons per second tunneling from 1 2 assuming an unoccupied layer 2 are:
where is the number of electrons in layer 1. Because of the same size of the particles and temperature in layer 1 and 2, so the total number of electrons per second tunneling from 2 1, assuming an unoccupied layer 1, is given by Eq. 17 as:
Therefore the flow of electrons from layer 1 to layer 2 is given by Eq. 18 as:
If are equilibrium concentrations of electrons in layers 1 and 2 respectively, and , so the net exchange is given by Eq. 19 as:
The equations of transporting of holes in QDs are similar to electrons equations.
Recombination in the QDs
In QD-LEDs like LEDs there are two types of recombination, radiative and non-radiative. If the recombination of electrons and holes are radiative, photons are emitted, and the wavelength of photon is independent to the charge transport layers and only depends on the QDs. According to doping of QDs, the radiative recombination can be either monomolecular or bimolecular. Monomolecular recombination occurs in doped quantum dots and the rate of recombination depends on minority carrier density. If the quantum dots are undoped, the recombination rate depends on both of the carriers, so this kind of recombination is bimolecular. Bimolecular recombination is given by Eq. 20 as:
where Ur is recombination rate, is recombination rate coefficient, n and p are electron and hole concentrations respectively, is intrinsic carrier concentration. Also non-radiative recombination is given by Shockley-Read-Hall (SRH) recombination, as follow (Eq. 21).
where Unr is non-radiative recombination rate, n and p are electron and hole concentrations respectively, ni is intrinsic carrier concentration, also are electron and hole recombination lifetimes.
This section provides materials synthesis and fabrication methods of QD-LED devices that are realized by our research group. All of the fabricated devices consist of p-type and n-type materials as HTL and ETL, respectively. Synthesis of these materials will be explained in this section.
3.1. Synthesis of materials
3.1.1. P-type materials
22.214.171.124. Processing of NiO
NiO synthesized by electrochemical and sol-gel methods which is used in the structure of QD-LED, also ZnO:Cu is another material which is used as a HTL.
NiO film is fabricated using two electrode system at a deposition temperature of 50 °C. An indium tin oxide ITO/glass and a Pt wire were used as the cathode and anode, respectively. The electrolyte was an aqueous solution containing 5mmol nickel nitrate and 5mmol hexamethylenetetramine (HMT). The voltage during deposition was-2.2 V and the deposition time was 30 min .
The NiO sol–gel precursor was prepared by dissolving 0.01mol nickel nitrate in 20ml acetic acid and in a separate beaker 3ml tri-ethyleneamine dissolved in 30ml methanol and was added under stirring to the improve sol stability. The prepared gel were then placed immediately into a tube furnace and annealed under air at 600 °C for 2 hours, after that the gel changed to powder form. 0.01 g of obtained NiO dispersed in 2 ml methanol and the dispersed solution were deposited on the ITO substrate at 100°C.
126.96.36.199. Processing of ZnO:Cu
ZnO:Cu synthesized by sol-gel method by the following manner. For preparing of this material, 3.1g of zinc acetate and 0.18g of CuSO4,were dissolved in 40ml distilled water, then 1.5g of citric acid and 1.5g of polyethylene glycol was added under stirring to the improve sol stability. The prepared gel were then placed immediately into a tube furnace and annealed under air at 600 °C for 15 hours, after that the gel changed to powder form.
3.1.2. N-type materials
The ZnO sol–gel precursor was prepared by dissolving 3.27g zinc acetate in 40ml distilled water, then 1.5g of citric acid and 1.5g of polyethylene glycol was added under stirring to the improve sol stability. The prepared gel were then placed immediately into a tube furnace and annealed under air at 500 °C for 15 hours, after that the gel changed to powder form.
ZnO:Ga was synthesized by solvothermal method using the following manner. In a typical experiment to synthesis Zn0.95Ga0.05O nanoparticles, NaOH (1mmol), tri-octylphosphineoxide (TOPO, 5mmol), Zn(CH3CO2)2(H2O)2 (0.95 mmol), Ga(NO3)3H2O (0.05mmol), were mixed in 75ml 2-propanol and the mixture was transferred into autoclave. The autoclave was sealed and maintained at 180°Cfor 24 hour, then allowed to cool to room temperature naturally. The obtained powder material is centrifuged by distilled water, ethanol and 2-propanole for several times.
ZnO:Nd was synthesized by sol-gel method using the following manner. For preparing of Zn0.95Nd0.05O, 3.1g of zinc acetate and 0.26g of NdCl3(6H2O), were dissolved in 40ml distilled water, then 1.5g of citric acid and 1.5g of polyethylene glycol was added under stirring to the improve sol stability. The prepared gel were then placed immediately into a tube furnace and annealed under air at 600 °C for 15 hours, after that the gel changed to powder form.
3.1.3. Quantum dots
We utilized CdSe\ZnS core\shell structures as quantum dots in the fabricated QD-LED. For synthesis of CdSe QDs, Cd (NO3)2(3.24 mmol) and Oleic acid (5ml) were mixed together under vacuum conditions at 100°C. Then Se (1.62mmol) dispersed in the 2-propanol (5ml) and 7mmol NaBH4 added in it and the obtained colorless solution were injected to the mixture of Cd(NO3)2 and oleic acid and heated at 100°C for 30min. The obtained material was centrifuged with n-hexane, ethanol and acetone for several times. The obtained CdSe capped with oleic acid was dried at 70°C.Then 0.63g of CdSe and 0.37g of Zinc acetate solved in 10 ml n-hexane and 10ml 2-propanol at 100°C under vacuum conditions. 0.02g NaOH and 0.05g thioacetamide solved in 15ml 2-propanol and was added to the solution and the reaction was done for 30 min at 120°C. The obtained material was centrifuged with n-hexane, ethanol, acetone and distilled water for several times.
CdS is another quantum dot, which has been used in the fabrication of QD-LED. For synthesis of CdS QDs, CdO (1mmol) and TOPO (0.3g) and chloroform (30ml) were mixed together under vacuum conditions at 100°C. Then S (2mmol) dispersed in 2ml of Tri-tert-butylphosphine and this solution was injected to the mixture of CdO (1mmol) and TOPO (0.3g) and chloroform (30ml) at 100°C for 30min. The obtained material was centrifuged with n-hexane, ethanol and acetone for several times.
Surface of the synthesized CdS QDs for applying in QD-LEDs should be improved. For this purpose we got help from FRET mechanism and capping molecules for using as surface modification, selected based on enhancement of illumination of CdS using FRET mechanism. So we carried out surface modification of QDs by organic molecules, which listed as follow:
One of the materials for modification of QD surface is Thioacetamide (TAA). For preparing of CdS with TAA ligands, CdS (0.01g) capped with TOPO (synthesized QD) and TAA (0.01) and 2-propanol (5ml) were mixed together under stirring for 24 hours, after that the obtained material was centrifuged with 2-propanol, n-hexane, ethanol and distilled water for several times.
Ammonium hexafluorophosphate (F6H4NP) is another material which used as surface modification of QD. For preparing of CdS with this molecule, CdS (0.01g) and F6H4NP (0.01g) and 2-propanol (5ml) were mixed together under stirring for 24 hours, after that the obtained material was centrifuged with 2-propanol, n-hexane, ethanol and distilled water for several times.
Mercaptoacetic acid (MAA) is used as surface modification of CdS too. For preparing of CdS with Mercaptoacetic acid, NaOH (1mmol) and Mercaptoacetic acid (0.01 g) and 2-propanol (5ml) were mixed together. Then the obtained solution was added on 0.01 g of the CdS and 5ml 2-propanol and the mixture stirred at room temperature for 24 hours; then the obtained material was centrifuged with 2-propanol, n-hexane, ethanol and distilled water for several times.
3.2. Device fabrication
This section provides seven kinds of QD-LEDs by using p-type, n-type and quantum dots materials which the synthesis of them were explained above. For fabrication of first, second and third QD-LEDs, ITO coated glasses with a sheet resistance of 20ohm/sq was purchased from Aldrich. Also For fabrication of fourth, fifth, sixth and seventh, flexible ITO which was coated on PET was utilized. For fabrication of all of the devices, traditional physical method and solution processed method were utilized.
For fabrication of first QD-LED, NiO synthesized by sol-gel method as HTL layer was used. In this case CdSe/ZnS QD layer used as emissive layer and ZnO:Ga as ETL. All of applied materials dispersed in 2-propanole and coated by spin coating method.
For fabrication of second QD-LED, electrochemically synthesized NiO was deposited on ITO and CdSe/ZnS QD layer and ZnO:Ga as ETL layer were deposited on it by spin coating method respectively.
For fabrication of third QD-LED, ZnO:Cu as HTL layer was deposited on ITO and CdSe/ZnS QD layer was fabricated by spin coating method and ZnO:Nd as ETL layer was deposited on it by spin coating method respectively.
For fabrication of fourth, fifth, sixth and seventh QD-LED, sol-gel NiO as HTL, QD layer, ZnO:Nd ETL were all deposited by spin coating method. The QD layer in fourth QD-LED is CdS capped with TAA molecule and in fifth QD-LED the QD layer consist of CdS capped with F6H4NP molecule, also the QD layer in sixth QD-LED is CdS capped with MAA, in seventh QD-LED the QD layer consists of CdS-TOPO.
In all seven devices, the Al cathode was deposited by the electron beam evaporation technique.
3.2.1. Spectroscopic studies and structural characterization
In this chapter all the measurements and characterizes carried out by the following devices:
Photoluminescence (PL) measurements were carried out by a Perkin-Elmer LS45 luminescence spectrophotometer. UV-Vis absorption spectra were recorded using a PG instrument T70 UV/V is spectrophotometer. Surface morphology and distribution of the particles were studied via a TESCAN model MIR3 scanning electron microscope (SEM), and by a Dual-scope C26 scanning probe and microscope DME atomic force microscope (AFM) operating in tapping mode. The crystal structure of nanoparticles were characterized by X-ray diffraction (XRD) on a Siemens D500 using Cu-kα radiation (λ=1.541 A°). X-Ray photoelectron spectroscopy (XPS) was carried out by Surface Science Instruments (SSX-101 M-Probe ESCA).
4.1. Increasing efficiency
Because of the importance of light quality and lifetime of QD-LEDs, nowadays increasing efficiency of QD-LEDs is very considerable; therefore our group (OIC) by introducing new structures of QD-LEDs and using solution process method for fabrication of QD-LEDs has several works for improving of efficiency of this type of LEDs. In this way, crystal engineering and effects of FRET in QD-LED were investigated, which both of them improve quality of QD-LEDs .
4.1.1. Crystal engineering
This section is based on trap level engineering in inorganic materials to achieve improved QD based LEDs. For this purpose, we investigate three types of QD-LEDs which in two types of them NiO applied as transparent, conductive hole transport layer (HTL) and CdSe/ZnS QDs as luminescent layer and ZnO:Ga as electron transport layer (ETL). The arrangement of the layers that form the QD-LED is illustrated in Figure 5. As Figure 5a shows, there is an energy barrier for hole injection from ITO to the p-NiO layer and from p-NiO layer to the QD layer. Such a barrier is not present for electron injection and transportation. This causes a carrier density imbalance in QDs that prevents efficient recombination of electron-hole pairs. This phenomenon causes self-quenching in QD-LEDs. One way to solve this problem is synthesis of NiO nanoparticles with a wider band gap to decreasing energy barrier between p-NiO and QDs. To improve hole injection from ITO to the p-NiO layer, trap levels in the band gap of NiO are created that results in a much lower barrier for hole injection. As mentioned previously, engineering these trap energy levels is possible with considering different methods for nano structure synthesis. For this purpose, we investigate two types of NiO synthesized via sol–gel and electrochemical methods.
The purity and crystallinity of the NiO nanoparticles synthesized by sol-gel and electrochemical methods were examined using powder X-ray diffraction (XRD). XRD pattern of nanoparticles synthesized by sol-gel method is shown in Figure 6 which is similar to the pattern for material synthesized by electrochemical method. This figure shows narrow diffraction peaks which indicate high crystallinity of the synthesized materials and the peaks appeared at 2θ=37.39°, 43.38°, 62.94° are related to (111), (200), (220) crystal planes of the synthesized NiO which crystallizes in cubic system. Metal-Oxides like NiO usually contain a large number of defects and these defects convert the NiO to conductive material. In equilibrium defect chemistry, NiO usually has an oxygen excess accommodated by nickel vacancies [25, 26]. To preserve the overall electrical neutrality in the crystal, some Ni2+ ions must be converted to Ni3+ ions, which are responsible for conduction in NiO. Lattice defects are not well-defined in NiO films synthesized by different methods. On the other hand, the vacancy model is little discussed with regard to NiO films prepared by different methods. Due to its uncertain mechanism most papers use nickel vacancy and/or interstitial oxygen to explain the electrical properties of the NiO films .
The PL spectra of the synthesized materials are studied for characterization of trap levels, formed in the structures. Figure 7 shows strong narrow bands appeared in UV and visible ranges for both spectra. A strong UV emission at 350 nm for electrochemically synthesized NiO and 335nm for NiO synthesized by sol-gel method are generally originated from the direct recombination of the free excitons through an exciton-exciton collision process which is called near band edge emission. It is believed that the visible emission is due to the crystalline defects in the NiO structures and is related to intrinsic defects and Ni2+ vacancies play a key role for it.
As figures show, intensity of the emission bands appeared in visible range for the material synthesized by sol-gel method is higher than electrochemical method that indicates density of trap levels in the material synthesized by so-gel method is high. Absorption spectra for synthesized materials show broad bands in the range of 190-350 nm for the material synthesized by electrochemical method which is narrower in the material synthesized by sol-gel method. This result indicates high uniformity of the particles synthesized by sol-gel method. On the other hand appearing the band at 335 nm for the material synthesized by sol-gel method shows a blue shift rather than electrochemically synthesized material which this peak appears at 350 nm. This result shows creation of wide band gap material with sol-gel method.
Figure 9 shows the scanning electron microscope (SEM) images of the synthesized NiO using sol-gel and electrochemical methods which indicates uniform and smaller size of particles for NiO synthesized by sol-gel method. AFM images (Figure 10) confirm smooth surface and uniform size of NiO synthesized by sol-gel method.
Intrinsic defects are created during crystallization process of ZnO and by this way n-type ZnO can obtain [27-30]. In previously reported devices ZnO with intrinsic n-type defects has been used. We tried to fabricate such devices with extrinsic defects that are created by Ga or Nd doping in the structure of ZnO. The reason for choosing these atoms as dopant atoms will describe in DFT calculation section. Since ZnO is crystalizes as n-type semiconductor, the number of p-type ZnO is limited and synthesis of this type of ZnO is not usual. Here we describe the devices based on Cu doped ZnO as the HTL beside devices based on p-type NiO which is applied as HTL layer in these structures.
Figure 5a shows, electron injection between Al (as electrode)-ZnO and ZnO-QD depends on electronic structure of ZnO. Although there is a small energy barrier in this case, increasing electronic levels in conduction band of ZnO can improve electron transport between layers. As calculations show, with doping of Ga3+ in the structure of ZnO electronic levels are created in the band structure of ZnO which these new levels appears inside the conduction band (Figure 11).
However, from view point of crystal structure, Ga3+ is expected to cause only a small lattice distortion because of their similar tetrahedral radii. The X-ray diffraction (XRD) patterns of ZnO: Ga nanoparticles are shown in Figure 12 which peak positions correspond to crystalline ZnO with the hexagonal wurtzite structure. The morphology of the ZnO: Ga analyzed by SEM and AFM images (Figure 13). These images confirm the small size of ZnO:Ga nanoparticles which are about 50nm.The surface composition of films was determined using XPS technique. The XPS spectra of the ZnO: Ga films (Figure 14) show that the binding energy (BE) of each constituent element was positioned at 1117.72 eV (Ga 2p3/2), 1022.23 eV (Zn 2p3/2) and 530.9 eV (O1s) as calibrated to 285.43 eV (C1s). The Ga-doped ZnO sample prepared using the 5 wt. % Ga (NO3)3 reveals 4.75% Ga on the surface of the films. The broadening of oxygen spectrum (Figure 13) is believed to be composed of two components located around 531 eV and 532 eV respectively. The low BE component is ascribed to covalently bonded oxygen in ZnO structure (lattice oxygen) while the high BE is attributed to the adsorbed oxygen. The higher binding energy at 532 eV is usually attributed to chemisorbed or dissociated oxygen or OH species on the surface of the ZnO thin film, such as adsorbed H2O or adsorbed O2.
PL study of this thin ZnO film indicates high degree of surface and structural trap levels characterized by visible-region fluorescence (Figure 15).
Nd doped ZnO has been synthesized previously by Zheng and coworkers . DFT calculations show, doping of Nd in the structure of ZnO increases electronic levels in conduction band of ZnO (Figure 16) and these levels are more than levels in Ga doped ZnO structure which is expected that this structure will improve the efficiency of LED more than previous structure.
Figure 17 shows the X-ray diffraction (XRD) patterns of ZnO: Nd nanoparticles. Peak positions correspond to crystalline ZnO with the hexagonal wurtzite structure. For Zn0.95Nd0.05O, diffraction peaks become broader and weaker compared to undoped ZnO which shows decreasing of crystallinity of the structure by increasing in doping concentration. The morphology of the ZnO: Nd analyzed by AFM images (Figure 18). The grain sizes of the nanoparticles were 50-70nm.
For making improvement in HTL layer, a structure based on Cu doped ZnO (instead of p-type NiO) is fabricated. Doping of Cu2+ has effect on photoluminescence (PL) and structure of ZnO . Calculation results indicate that with doping of Cu2+ in the structure of ZnO electronic levels are created in the band structure of ZnO which these new levels appears inside the valence band. Since electronic configuration in Cu2+ is d9, so, there is a level in created levels that is half full and can act as hole transfer. Figure 19 indicates the band structure of ZnO: Cu.
To get the information about the morphology and size of the ZnO:Cu nanoparticles, AFM studies had been carried out. It is observed from the AFM images, shape of the nanoparticles are spherical type. Figure 20 shows AFM image of ZnO: Cu. Nanoparticles size are about 10-40nm.
Figure 21 shows photoluminescence spectra of ZnO: Cu and ZnO: Nd which confirm the defects created in the structure of doped materials (visible region emission). According to Figure 21 in both of the doped (Cu and Nd) ZnO there is a peak in the UV region which shows band edge of ZnO.
The colloidal QDs employed in our synthesized structures contain a core/ shell; CdSe/ZnS. Figure 22 shows PL spectra of CdSe/ZnS nanoparticles that demonstrate high emission peak at 600 nm. The absence of other peaks in the spectrum and relatively narrow emission band at 600 nm show uniformity of particles and good passivation of the surface of CdSe using ZnS shell. The SEM image of synthesized CdSe/ZnS core/shell material is illustrated in Figure 23 in which the diameter of particles is about 30nm.
The PL spectra of QD-LEDs are shown in Figure 24 and indicate that electron–hole recombination is occurring predominantly in the QD layer, as required for optimal device operation. I-V behavior of the devices is illustrated in Figure 25 which confirms PL and EL emission results. Turn-on voltage for the devices based on NiO nano-materials is about 1V which is higher than the device based on ZnO: Cu. This turn-on voltage demonstrates that an ETL such as ZnO: Ga and ZnO: Nd and NiO HTL or ZnO: Cu facilitate effective electron and hole injection into the QD conduction and valence bands. According to Figure 25a and 25b measurements of the EL emission intensity yield a peak brightness of 500 cdm-2 and 340 cdm-2 at an applied operating bias of 5 V for fabricated LEDs based on materials synthesized by sol-gel and electrochemical methods respectively, which is considerable compared with other recently reported QD-LEDs. This brightness is 700cdm-2 for the device based on ZnO: Nd (as ETL layer) and ZnO: Cu (as HTL layer) which the result confirms by I-V curve. As we can see in Figure 25 the current for it is higher than others. Also the current for the device based on NiO synthesized by sol-gel method is higher than NiO synthesized by electrochemical method. This shows that by engineering in the structure of QDLEDs their performance can be improved.
4.1.2. Effects of FRET in QD-LEDs
188.8.131.52. Effects of organic molecules as shell around QDs
The emitted light and efficiency of QD-LEDs can be increased by Forster resonance energy transfer (FRET); in this way organic materials act as capping molecules for inorganic QDs. FRET is an energy transfer between two molecules, which one of them is a donor and the other is an acceptor. In the FRET process, first a donor material absorbs the energy and then transfer absorbed energy to a nearby acceptor and this process occurs through long-range dipole-dipole interactions [20, 34]. So, FRET mechanism leads to enhancement in the emission of fabricated QD-LEDs when QDs use as acceptor. Also in FRET process there are some important factors for transfer energy between acceptor and donor, such as the distance between the donor and acceptor molecules and the extent of spectral overlap . Figure 26 shows FRET mechanism.
In the devices with luminescent species like inorganic semiconductors and organics molecules which in close proximity to the QDs, FRET is a mechanism that is unique to these devices. So, at first in the luminescent species, an exciton formed, and then the excitons energy is transferred to a QD non-radiative by dipole–dipole coupling . QDs exhibit tune able emission by controlling their size and structure, therefor the spectral tune ability of QDs with quantum confinement effect allows to control FRET energy flow . In our research group we utilized different capping organic molecules synthesized for surface passivation of synthesized QDs and these materials used as an active layer in the fabrication of QD-LEDs. The PL spectra of these materials indicate enhancement of emitted light via FRET mechanism. Figure 27 shows PL spectra of CdS QD and modified CdS QDs.
Figure 27 shows Intensity of emitted light for the CdS passivated by Ammonium hexaflurophosphate is higher than TAA and the PL intensity of CdS passivated by TAA is higher than CdS passivated by MAA. In this structure organic molecules are as donors and QDs are as acceptors. In FRET process the suitable distance for transmission of energy is about 1 to 10 nm, so for generating of an energy gradient structure and occurring of FRET mechanism the donor organic molecules should be close to the acceptors (QDs). The trapped exciton can be transferred to the nearby QD and a fraction of the migrated excitons from trapped states can contribute to the acceptor luminescence by radiative recombination. So, this leads to enhancement in the emission. Figure 28 illustrates I-V behavior of the devices, fabricated by capped QDs; turn on voltage of three devices is about 1V, however, for the device based on CdS: TAA the turn on voltage is 1.5 volt, which is more than the other devices. This is while; the PL result of QD capped by TAA is higher than others.
The PL and EL results of fabricated QD-LEDs based on FRET mechanism indicate high intensity of emitted light. It is necessary to be mentioned that in the structure of FRET based QDLEDs, ZnO:Nd acts as ETL and NiO synthesized by sol-gel method is used as HTL layers.
5. Conclusions and perspectives
In this section design and fabrication of QD-LEDs and solution of their problems including self-quenching and carrier injection have been described. All of described devices are fabricated by solution-processed methods. The base is finding the materials with suitable defect levels for achieving improved QD based LEDs. For this purpose, we investigated three types of QD-LEDs, which in both of them NiO applied as the transparent, conductive hole transport layer (HTL), and in the other one ZnO:Cu is the HTL. However, in one device, the synthesis route of NiO was sol-gel, whereas in the other, the electrochemical synthesis route is used. Characterization of NiO synthesized by sol-gel and electrochemical methods showed that different trap levels are created in the crystalline structures of NiO. Also DFT calculations indicate doping of Gallium and Neodymium atoms in the structure of ZnO increases electronic levels in the conduction band of ZnO. These calculations confirm experimental results. The obtained structure facilitates electron injections, and doping of Copper atoms in ZnO causes this material acts as a p-type, so facilitates hole injections, when that used as HTL. Fabrication of FRET based QD-LEDs could introduce suitable organic capping molecules for fabrication of high performance LEDs. In this way Ammonium hexafluorophosphate as capping molecule acts the best performance from view point of PL and EL results. Increasing in drive voltage and created heating in the light emitting diodes cause that the intensity of output light decrease and this is inefficient. In this work by introducing novel structures and improvement in the optical properties of materials used in devices, drive voltage and so, creating of heating in the fabricated devices is decreased so the light efficiency increases.
Light emitting devices; LEDs
high-intensity discharge; HID
Quantum dots; QDs
Hole transport layer; HTL
Electron transport layer; ETL
Indium tin oxide; ITO
Forster resonant energy transfer; FRET
Scanning electron microscope; SEM
Atomic force microscope; AFM
X-ray diffraction; XRD
X-Ray photoelectron spectroscopy; XPS
Binding energy; BE
Polyethylene terephthalate; PET
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