Jennifer A. Hollingsworth and Victor I. Klimov
CONTENTS
1.1 Introduction
1.2 Colloidal Nanosynthesis
1.2.1 Tuning Particle Size and Maintaining Size Monodispersity
1.2.2 CdSe NQDs: The âModelâ System
1.2.3 Optimizing Photoluminescence
1.2.4 Aqueous-Based Synthetic Routes and the Inverse-Micelle Approach
1.3 Inorganic Surface Modification
1.3.1 (Core)Shell NQDs
1.3.2 Giant-Shell NQDs
1.3.3 Quantum-Dot/Quantum-Well Structures
1.3.4 Type-II and Quasi-Type-II (Core)Shell NQDs
1.4 Shape Control
1.4.1 Kinetically Driven Growth of Anisotropic NQD Shapes: CdSe as the Model System
1.4.2 Shape Control Beyond CdSe
1.4.3 Focus on Heterostructured Rod and Tetrapod Morphologies
1.4.4 SolutionâLiquidâSolid Nanowire Synthesis
1.5 Phase Transitions and Phase Control
1.5.1 NQDs under Pressure
1.5.2 NQD Growth Conditions Yield Access to Nonthermodynamic Phases
1.6 Nanocrystal Doping
1.7 Nanocrystal Assembly and Encapsulation
Acknowledgment
References
1.1 Introduction
An important parameter of a semiconductor material is the width of the energy gap that separates the conduction from the valence energy bands (Figure 1.1a, left). In semiconductors of macroscopic sizes, the width of this gap is a fixed parameter, which is determined by the materialâs identity. However, the situation changes in the case of nanoscale semiconductor particles with sizes less than ~10 nm (Figure 1.1a, right). This size range corresponds to the regime of quantum confinement for which electronic excitations âfeelâ the presence of the particle boundaries and respond to changes in the particle size by adjusting their energy spectra. This phenomenon is known as the quantum size effect, whereas nanoscale particles that exhibit it are often referred to as quantum dots (QDs).
As the QD size decreases, the energy gap increases, leading, in particular, to a blue shift of the emission wavelength. In the first approximation, this effect can be described using a simple âquantum boxâ model. For a spherical QD with radius R, this model predicts that the size-dependent contribution to the energy gap is simply proportional to 1/R2 (Figure 1.1b). In addition to increasing energy gap, quantum confinement leads to a collapse of the continuous energy bands of the bulk material into discrete, âatomicâ energy levels. These well-separated QD states can be labeled using atomic-like notations (1S, 1P, 1D, etc.), as illustrated in Figure 1.1a. The discrete structure of energy states leads to the discrete absorption spectrum of QDs (schematically shown by vertical bars in Figure 1.1c), which is in contrast to the continuous absorption spectrum of a bulk semiconductor (Figure 1.1c).
Semiconductor QDs bridge the gap between cluster molecules and bulk materials. The boundaries between molecular, QD, and bulk regimes are not well defined and are strongly material dependent. However, a range from ~100 to ~10,000 atoms per particle can been considered as a crude estimate of sizes for which the nanocrystal regime occurs. The lower limit of this range is determined by the stability of the bulk crystalline structure with respect to isomerization into molecular structures. The upper limit corresponds to sizes for which the energy level spacing is approaching the thermal energy kT, meaning that carriers become mobile inside the QD.
Semiconductor QDs have been prepared by a variety of âphysicalâ and âchemicalâ methods. Some examples of physical processes, characterized by high energy input, include molecular-beam-epitaxy (MBE) and metalorganic-chemical-vapor-deposition (MOCVD) approaches to QDs,1,2,3 and vapor-liquid-solid (VLS) approaches to quantum wires.4,5 High-temperature methods have also been applied to chemical routes, including particle growth in glasses.6,7 Here, however, the emphasis is on âsoftâ (low-energy-input) colloidal chemical synthesis of crystalline semiconductor nanoparticles that will be referred to as nanocrystal quantum dots (NQDs). NQDs comprise an inorganic core overcoated with a layer of organic ligand molecules. The organic capping provides electronic and chemical passivation of surface dangling bonds, prevents uncontrolled growth and agglomeration of the nanoparticles, and allows NQDs to be chemically manipulated like large molecules with solubility and reactivity determined by the identity of the surface ligand. In contrast to substrate-bound epitaxial QDs, NQDs are âfreestanding.â This discussion concentrates on the most successful synthesis methods, where success is determined by high crystallinity, adequate surface passivation, solubility in nonpolar or polar solvents, and good size monodispersity. Size monodispersity permits the study and, ultimately, the use of materials-size-effects to define novel materials properties. Monodispersity in terms of colloidal nanoparticles (1â15 nm size range) requires a sample standard deviation of Ï â€ 5%, which corresponds to ± one lattice constant.8 Although colloidal monodispersity in this strict sense is increasingly common, preparations are also included in this chapter that achieve approximately Ï â€ 20%, in particular where other attributes, such as novel compositions or shape control, are relevant. In addition, âsoftâ approaches to NQD chemical and structural modification as well as to NQD assembly into artificial solids or artificial molecules are discussed.
1.2 Colloidal Nanosynthesis
The most successful NQD preparations in terms of quality and monodispersity entail pyrolysis of metal-organic precursors in hot coordinating solvents (120°Câ360°C). Generally understood in terms of La Mer and Dinegarâs studies of colloidal particle nucleation and growth,8,9 these preparative routes involve a temporally discrete nucleation event followed by relatively rapid growth from solution-phase monomers and finally slower growth by Ostwald ripening (referred to as recrystallization or aging) (Figure 1.2). Nucleation is achieved by quick injection of precursor into the hot coordinating solvents, resulting in thermal decomposition of the precursor reagents and supersaturation of the formed âmonomersâ that is partially relieved by particle generation. Growth then proceeds by addition of monomer from solution to the NQD nuclei. Monomer concentrations are below the critical concentration for nucleation, and, thus, these species only add to existing particles, rather than form new nuclei.10 Once monomer concentrations are sufficiently depleted, growth can proceed by Ostwald ripening. Here, sacrificial dissolution of smaller (higher-surface-energy) particles results in growth of larger particles and, thereby, fewer particles in the system.8 Recently, a more precise understanding of the molecular-level mechanism of âprecursor evolutionâ has been described for II-VI11 and IV-VI12 NQDs. Further, it has also been proposed that the traditional La Mer model is not valid for hot-injection synthesis schemes because nucleation, ripening, and growth may occur almost concurrently. Moreover, the presence of strongly coordinating ligands may also alter nucleation and growth processes, further complicating the simple interpretation of reaction events.13 Finally, a modification of the Ostwald ripening process has also been described wherein the particle concentration decreases substantially during the growth process. This process has been called âself-focusing.â14,15
Alternatively, supersaturation and nucleation can be triggered by a slow ramping of the reaction temperature. Precursors are mixed at low temperature and slowly brought to the temperature at which precursor reaction and decomposition occur sufficiently quickly to result in supersaturation.16 Supersaturation is again relieved by a ânucleation burst,â after which temperature is controlled to avoid additional nucleation events, allowing monomer addition to exi...