# Indium Phosphide-Based  Semiconductor Nanocrystals and Their Applications

Authors: Paul Mushonga; Martin O. Onani; Abram M. Madiehe; Mervin Meyer
Journal: Journal of Nanomaterials
 (2012)

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## Abstract

Semiconductor nanocrystals or quantum dots (QDs) are nanometer-sized fluorescent materials with optical properties that can be fine-tuned by varying the core size or growing a shell around the core. They have recently found wide use in the biological field which has further enhanced their importance. This review focuses on the synthesis of indium phosphide (InP) colloidal semiconductor nanocrystals. The two synthetic techniques, namely, the hot-injection and heating-up methods are discussed. Different types of the InP-based QDs involving their use as core, core/shell, alloyed, and doped systems are reviewed. The use of inorganic shells for surface passivation is also highlighted. The paper is concluded by some highlights of the applications of these systems in biological studies.


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## Body

## 1. Introduction

Spherical semiconductor nanocrystals, which may be referred to simply as quantum dots (QDs), are nanometer-sized clusters that are generally composed of a few hundreds to several thousands of atoms from Groups II-VI, III-V, and IV-IV [1–5]. The physical dimensions of QDs are on the scale of the excitonic Bohr radius, a property that leads to a phenomenon called the quantum confinement effect (QCE), whose origins are explained by Andersen et al. using II-VI nanocrystallites [6]. The QCE leads to tunable optical and electronic properties that are not observed in either the bulk solids or the molecular level.The QDs have unique and distinctive optical properties in comparison to organic dyes and fluorescent protein molecules. These properties [7] include (i) broad absorption spectra that increase towards the ultra violet (UV) region from the first absorption band edge; (ii) very large molar extinction coefficients in the order of 0.5–5 × 106 M-1cm−1, about 10–50 times larger than those of organic fluorophores, making them brighter probes suitable for studies involving in vivo investigations, where light intensities are severely attenuated by absorption and scattering; (iii) longer excited state lifetimes and hence large effective Stokes shifts enabling the separation of QD fluorescence from the background fluorescence; (iv) large surface area-to-volume ratio which allows them to be conjugated to various molecules; (v) high photostability, a versatile property that facilitates visualization of biological material for a longer period; and (vi) narrow and symmetrical emission spectra that allow various colors to be distinguished without any spectral overlap.


## 2. Quantum Dots of Group III-V

For more than two decades, research into semiconductor nanocrystals has been focused on the fabrication of versatile groups II-VI QDs owing to their potential application in lasers [8], light-emitting diodes [9], and more importantly biological studies [10–12]. However, due to the presence of highly toxic cadmium in the design, their biological application has been limited. In order to alleviate this toxicity problem, a process of overcoating the cadmium-based core with a less toxic shell such as ZnS was developed. In this regard, the shell would prevent leakage of the toxic ions. Unfortunately this did not make the II-VI QDs completely innocuous as exposure to UV light or oxidation as a result of inflammatory responses induces the release of cadmium via surface oxidation [13]. The focus in the last two decades was therefore shifted towards the fabrication of III-V QDs in general, and InP in particular. The principal attraction to these semiconductors lies in the robustness of the covalent bond found in groups III-V semiconductor matrix compared to the ionic bond in the groups II-VI semiconductors. The presence of the covalent bond serves two functions, which are the enhancement of the optical stability of the QD systems as well as the reduction of the toxicity as a result of the nonerosion of the constituent species when used in biological milieu [14, 15]. The other reason for the interest in the III-V systems lies in the fact that the excitonic Bohr radius is larger in III-V than in the II-VI systems (Table 1). Consequently, groups III-V QDs exhibit stronger size quantization effects in comparison with the groups II-VI systems [16].Table 1
Band gap (Eg) and excitonic Bohr radius (rB) in some semiconductors.
CompoundBand gap (eV)rB (nm)ReferenceInP1.3515[17]InAs0.35434[18]InSb0.1765.6[19]CdS2.435.8[20]CdSe2.875.3[21]CdTe1.57.3[22]ZnSe2.674.5[23]In order for these QD to display their superior properties well, they ought to be monodispersed. The surfactant organic molecules are usually employed for this purpose because they bind to the QD core during the synthesis effectively preventing their aggregation [24]. The surfactant layer also has the ability to control the size and shape of the growing QDs. The layer provides imperfect passivation of the nanocrystal surface dangling bonds due to the lability of the organic ligands [25]. The resultant defects, also referred to as surface traps, act as sites for nonradiative decay of the QD excited state [26]. Some of the excited state electrons can first decay to the surface states lying in the mid band gap and then recombine nonradiatively with the holes in the valence band, reducing the photoluminescent quantum yield. Several techniques have been employed to enhance the photoluminescence quantum yield. The effective strategies involve epitaxially growing an inorganic shell of a large band gap material around each particle, or just chemically modifying the particle surface. Sometimes overcoating the nanocrystal core with an inorganic shell of a higher band gap semiconductor effectively passivates surface-related defects resulting in an improved fluorescence quantum yield as well as enhanced photostability [27]. Kim et al. [28] reported that the emission efficiency of the InP/ZnSe core/shell was 6.8 times higher than that of the bare InP QDs, demonstrating that surface traps are effectively depressed after epitaxially depositing the larger band gap semiconductor ZnSe onto the InP nanocrystal core. The inorganic shell type and shell thickness are critical in the tailoring of the optical and electronic properties of the QDs [25]. Chemically modifying the surface of the InP QD core entails etching them with dilute ethanolic or butanolic solutions of HF [29] or NH4F [30]. This etching process effectively removes phosphorus dangling bonds [31] culminating in an increase in near band edge emission by a large factor of 10 [29].


## 3. General Synthetic Techniques

The general synthesis of high-quality QDs is of utmost importance as all their properties are dependent on particle quality which is controlled by size distribution and crystal defects. There are generally two techniques, namely, the hot-injection and heating-up techniques which have evolved in the last two decades. These techniques have been established for the synthesis of the majority of the reported QDs [32].


### 3.1. Hot-Injection Technique

This technique involves the rapid injection of a room temperature solution of precursors into an extremely hot reaction medium in the presence of carefully chosen surfactant molecules. The rapid injection of the precursor solution induces the sudden supersaturation of the solution resulting in a short burst of nucleation. The injected solution reduces the reaction temperature and dilutes the concentration of reactants. With the reaction temperature dropping in response to addition of the cold precursor solution, coupled with the low concentration of the remaining precursor molecules, further nucleation is prevented. The eventual growth of the nanocrystals follows at a lower temperature than that of the nucleation process. This sequential separation of the nucleation and growth processes generally leads to a precise control of the size and shape of the semiconductor nanocrystals. This latter process forms the strength of this technique. A pioneering example of this technique was reported by Murray et al. [33]. They injected cadmium and selenium precursors into a hot (300°C) solution of tri-n-octylphosphine oxide (TOPO). The growth temperature used was 230–260°C. Here the surfactant acts in fourfold. Firstly, it is as a coordinating solvent that controls the growth process while at the same time stabilizing the nanocrystal core. Secondly, the surfactant binds to the surface of the nanocrystals providing a barrier to the addition of more material to the surface of the nanocrystals slowing down the growth kinetics [24]. Thirdly, it serves to prevent the aggregation of particles and finally passivates the surface of the nanocrystals.


### 3.2. Heating-up Technique

This is a batch process where all the precursors are mixed at room temperature followed by a rapid heating of the system to the appropriate growth temperature for the nanocrystals. There is no operation under this method that induces high supersaturation as in the hot-injection method. Under this technique, the supersaturation level and the temperature of the solution increase together, and the nucleation rate is sensitive to both [34]. The procedure allows for scaling up as well as improving reproducibility [35].


## 3.1. Hot-Injection Technique

This technique involves the rapid injection of a room temperature solution of precursors into an extremely hot reaction medium in the presence of carefully chosen surfactant molecules. The rapid injection of the precursor solution induces the sudden supersaturation of the solution resulting in a short burst of nucleation. The injected solution reduces the reaction temperature and dilutes the concentration of reactants. With the reaction temperature dropping in response to addition of the cold precursor solution, coupled with the low concentration of the remaining precursor molecules, further nucleation is prevented. The eventual growth of the nanocrystals follows at a lower temperature than that of the nucleation process. This sequential separation of the nucleation and growth processes generally leads to a precise control of the size and shape of the semiconductor nanocrystals. This latter process forms the strength of this technique. A pioneering example of this technique was reported by Murray et al. [33]. They injected cadmium and selenium precursors into a hot (300°C) solution of tri-n-octylphosphine oxide (TOPO). The growth temperature used was 230–260°C. Here the surfactant acts in fourfold. Firstly, it is as a coordinating solvent that controls the growth process while at the same time stabilizing the nanocrystal core. Secondly, the surfactant binds to the surface of the nanocrystals providing a barrier to the addition of more material to the surface of the nanocrystals slowing down the growth kinetics [24]. Thirdly, it serves to prevent the aggregation of particles and finally passivates the surface of the nanocrystals.


## 3.2. Heating-up Technique

This is a batch process where all the precursors are mixed at room temperature followed by a rapid heating of the system to the appropriate growth temperature for the nanocrystals. There is no operation under this method that induces high supersaturation as in the hot-injection method. Under this technique, the supersaturation level and the temperature of the solution increase together, and the nucleation rate is sensitive to both [34]. The procedure allows for scaling up as well as improving reproducibility [35].


## 4. Synthesis and Optical Properties of InP-Based QDs

### 4.1. Building Core and Core/Shell InP QDs

The central part of a nanocrystal constitutes the core, and the immediate surrounding comprises the shell. In 1994, well-crystallized InP QDs with a zinc blende structure were for the first time synthesized [36]. A chloroindium oxalate complex (prepared from the reaction of indium trichloride and sodium oxalate) and tris(trimethylsilyl)phosphine [(TMS)3P] were used as sources of indium and phosphorus, respectively. A mixture of TOPO and trioctylphosphine (TOP) was used as a stabilizer and the reaction was carried out at 270°C over three days. The nanocrystals were characterized by X-ray diffraction (XRD) and high-resolution transmission electron microscopy (HRTEM) (Figure 1). X-ray diffraction data on the InP nanocrystal powders showed the 〈111〉, 〈220〉, and 〈311〉 peaks of crystalline zinc blende InP at 2θ values of 26.2±0.2°, 46.3±0.2°, and 51.7±0.2°, respectively. HRTEM images showed that the particles were ellipsoidal rather than spherical in shape.An X-ray diffraction pattern for dried InP QD exhibiting broadened prominent peaks for InP (a) and an HRTEM micrograph showing lattice fringes (b) (reprinted with permission from [36], Copyright 1994, American Chemical Society).
(a)(b)An optimization exercise for the properties of the obtained nanocrystals was done by changing the ratios of the In : P.  A marked narrowing of the QD size distribution was obtained when indium was added in excess whereas the photoluminescence (PL) spectrum had two bands—one close to the band edge and the other above 800 nm (Figure2) [37]. In the case of excess addition of phosphorus, only band edge emission was observed and the absorption spectrum did not show any resolved excitonic structure indicating a broad size distribution.Room temperature absorption and PL spectra of InP QDs synthesized with different ratios of In and P: (a) In : P = 1.6; (b) In : P = 0.62 (reprinted with permission from [37], Copyright 2009, Elsevier).
(a)(b)Further optimization was achieved by the etching process [31]. The etching of the QDs by using HF produced a photoluminescence emission spectrum consisting of a single narrow peak near the absorption band edge with quantum yield (QY) of about 30% after the treatment. The InP QD cores with a lattice-matched ZnCdSe2 shell and photoluminescence QYs of 5–10% have also been synthesized [38]. However, it is worth noting that preetching the InP cores before shell growth results in poor core-shell structures as the HF blocks the surface of the QDs.Kim et al. synthesized InP/CdSe core/shell type structure showing an increase in QY at the beginning of the overcoating process due to the small difference between the InP and CdSe conduction bands of 0.19 eV which gives a type-I configuration but changes to type-II which is associated with loss of QY yield with increased shell thickening [39]. In such a synthesis, increase in the thickness of the shell should be avoided because it may result in a red shift, broadening of the full width at half maximum (FWHM), and a decrease in QYs. In 2009, InP/ZnS QDs with a diameter of 15–20 nm were reported [15]. Here, myristic acid was used as a stabilizer and octadecene as the noncoordinating solvent. PL studies showed that the QDs exhibited a band edge emission at around 650 nm with QY of 25–30%. These InP/ZnS QDs were further functionalized using mercaptosuccinic acid rendering them highly dispersible in aqueous media. The mercaptosuccinic acid-capped QDs were stable for more than one week while dispersed in a common physiological buffer such as the phosphate buffer saline (PBS). Highly luminescent InP/ZnS nanocrystals were also synthesized following a single-step heating-up procedure [35]. Here, indium myristate, (TMS)3P, zinc stearate, and dodecanethiol were used for the fabrication of the nanocrystals which gave high fluorescence quantum yields (50–70%). These high PL QYs are attributed to the nanocrystals possessing a radial composition gradient that relieves the strain due to the lattice mismatch between InP and ZnS. A similar preparation was reported by another group but using stepwise process [40]. Again, palmitic acid was used as a stabilizer and octadecene as the noncoordinating solvent. The reaction between zinc acetate and palmitic acid gave that acetic acid causes the etching of the surface of the InP core leading to the easy formation of the shell. A blue shift in the emission and an improvement in quantum yield (38%) were realized. The use of the poisonous PH3 gas, generated from the reaction of a metal phosphide (calcium phosphide) with HCl as a phosphorus source in InP QD synthesis, was also reported by Li et al. [41]. Again, octadecene and myristic acid were used as noncoordinating solvent and ligand, respectively. Unlike the single injection of (TMS)3P, here the PH3 gas is continuously and slowly generated and added to the reaction system ensuring that the growth of the InP nanocrystals takes place in the size-focusing regime. The use of higher overall precursor concentrations resulted in the formation of a large number of nuclei and hence a smaller average size of the QDs. The PL spectra of the as-prepared InP nanocrystals showed two additional bands around 730 and 820 nm. These bands were attributed to trap-state-related emissions, which are suppressed upon overcoating with ZnS obtained from the monomolecular zinc ethylxanthate precursor. The PL QY of up to 22% was achieved [41]. In a different experiment, the as-synthesized bare InP nanocrystals, prepared using PH3 gas, did not exhibit detectable photoluminescence owing to the presence of surface states [42]. However, when overcoated with a ZnS shell, a very strong PL intensity was observed, which was attributed to the passivation of these surface states by the inorganic shell. The emission profiles of the InP core varied as a function of size in the range of 600–700 nm while the 470 nm band is attributed to defect-related emissions from the shell (Figure 3).Figure 3
Steady-state photoluminescence spectra of two different sized InP/ZnS QD samples under the 370 nm excitation (reprinted with permission from [42], Copyright 2009, IOP Publishing).The molar ratios of indium to phosphorus of 2 : 1 give the best quality InP nanocrystals when the noncoordinating octadecene is used as a solvent [43, 44]. When the ratios of the metal to ligand are above or below this ratio, the reaction gives nanocrystals with no distinguishable UV-Vis spectral features, implying that the size distribution is broad. The use of the ZnS coating layer gives the red-shift in both the absorption and PL spectra of about 2-3 nm (Figure 4) as well as an improvement in the PL QY from <1 to ~20% [44].(a) Temporal evolution of the UV-Vis spectra of InP nanocrystals in ODE. (b) UV-Vis spectra of InP nanocrystals before (black dashed) and after (red solid) passivation with ZnS and PL spectra of InP (green solid) and InP/ZnS nanocrystals (blue solid) (reprinted with permission from [44], Copyright 2008, American Chemical Society).
(a)(b)Myristic and palmitic acids, which are fatty acids of intermediate chain length, serve as the best ligands for controlled nucleation growth rates that yield relatively monodisperse nanocrystals when the ratio of the fatty acid to indium is 3 : 1 [43].  Uniquely, a “green” approach where by high-quality InP nanocrystals are synthesized without the addition of a coordinating solvent or ligands, using indium carboxylates as precursors for indium, was reported [45]. The carboxylate ions act as the in situ coordination ligands. The usage of weakly coordinating fatty acid esters in the preparation of high-quality InP QDs is known [46]. In these reactions, trimethylindium is used. It readily dissolves in the ester at room temperature and generates a soluble indium-ester complex with a higher activity than the indium carboxylate. The reported reaction pathway for this reaction is given in Scheme 1.Scheme 1
Proposed reaction scheme through an indium-ester intermediate (reprinted with permission from [46], Copyright 2006, American Chemical Society).The FWHM of the produced InP QD PL spectra is about 60 nm. When protic reagents such as amines are used, they hydrolyze (TMS)3P thereby accelerating the reaction with the indium precursors, but reducing the FWHM to around 48 nm. The role of the fatty acids and the protic reagents is mainly to increase the polarity of the reaction media affording better solubility as well as homogeneity of the precursors culminating in rapid but controlled reactions [47]. Polyethylene glycol (PEG) has been used as a weakly coordinating solvent for the one-pot synthesis of InP/ZnS QDs [47]. PEG offers the major advantages that it is nontoxic, inexpensive, and recyclable. The InP/ZnS QDs prepared in the PEG medium have quantum efficiencies as high as 30% with emissions ranging from 500 to 655 nm with FWHM of approximately 46 nm. Extremely small InP QDs have also been synthesized in a reaction where the protic reagents are used and heating carried out at 100–220°C for a day [48]. Protière and Reiss also reported the activation effects of amines when they prepared In2O3-coated InP QDs having an emission profile of 583 nm and FWHM of 50–60 nm [49]. The shell growth was done in situ without an addition of any precursor but was induced by oleylamine which was added at the start of the reaction. In 2010, Bawendi’s group published a mechanism for the formation of InP QDs (Scheme 2) [50], demonstrating that amines inhibited precursor decomposition, contrary to the aforementioned reports that they are activating agents in the synthesis.Scheme 2
Proposed mechanism for amine inhibited InP synthesis (reprinted with permission from  [50], Copyright 2010, Wiley-VCH Verlag GmbH and Co. KGaA).According to the scheme, amine inhibition resulted from solvation effects associated with steps that lead to the formation of complexes1and 2. Both the amine and (TMS)3P compete for the same indium metal centre and hence an increase in the concentration of the amine decreases the formation of complex 1 as the sterically hindered phosphine precursor is less likely to approach the metal centre. During the nucleation step, molecular phosphorus precursors are completely used up. As a result, subsequent growth in nanocrystal sizes is exclusively due to ripening from nonmolecular InP species giving rise to broad size distributions.Li and coworkers [51] reported a low-temperature solvothermal synthesis of InP nanocrystals that gave a broad size distribution due to a lack of separation of the nucleation and growth steps. UV irradiation of the nanocrystals in the presents of Zn2+ ions and thioglycolic acid yielded a thick ZnS shell and improved their PL efficiencies (30–68%). When the HF etching of the InP cores preceded the ZnS coating step, a blue shift in the absorption spectra was observed and this was ascribed to a slight QD size reduction during the etching process, while the observed improvement in the photoluminescence was due to a partial surface oxidation of the InP QD surfaces [17].Another green chemistry approach recently documented involves the usage of an aqueous synthetic route to InP QDs. The system uses an indium oxide, In2O3, and white phosphorus P4 for the synthesis of the InP core [52]. The formation of the InP nanocrystals (Scheme 3) was confirmed by both the X-ray photoelectron spectroscopy and energy-dispersive X-ray (EDX) analyses that gave In : P ratios of 1 : 1.02 and 1 : 1.01, respectively.Scheme 3
Growth pathway to InP QDs adapted from the GaP scheme [52].However, this synthetic route produces larger-sized nanocrystals with poor size distribution.Yet another approach by Green and O’Brien involves the pyrolysis of a single source precursor In(PBu2t)3 in 4-ethylpyridine at 167°C to give large InP QDs [53]. The nanocrystals obtained were about 7 nm in diameter with the PL spectrum exhibiting a broad near band edge luminescence peak at 534 nm. No QY data was reported here. A coreduction colloidal method for the synthesis of relatively high-quality InP nanocrystals using indium acetate, PCl3, and a superhydride LiBH(C2H5)3 and stearic acid is equally known [54]. In this heating-up type synthesis in the presence of noncoordinating octadecene, the simultaneous reduction of the indium and phosphorus precursors was carried out at low temperature followed by the elevation of the temperature to around 250–270°C for growth of the InP nanocrystals. The PL spectra containing both a high-energy band edge and a low-energy surface trap-related emission were obtained. Posttreatment of the cores with the etchant HF resulted in the fluorescence intensity increasing by a factor of 80 and the PL efficiency improved from about 0.25% to about 20%.


### 4.2. Alloying and Doping of the InP QDs

Most of the prepared QDs are binary in nature. The binary quantum dots have the size of the nanocrystals, and hence the emission profile controlled by a systematic adjustment of the reaction parameters, namely, temperature, time, and concentration of both the precursors and surfactant molecules. The emission profiles of alloyed III-V nanocrystals can be fine-tuned using composition as well, allowing them to emit in the near-infrared region. One such system, InAsxP1-x/InP/ZnSe, with a PL QY of about 3.5%, has been reported [55]. Another alloyed QD system, InGaP, was synthesized using a microwave-enhanced method [56]. QYs of about 15% were obtained prior to etching and improved to 68% upon etching due to the passivation of surface states. Few literature reports on the doping of InP QDs are due to the low solubility of the dopants in the III-V semiconductor matrix [57, 58]. Manganese-doped InP QDs were obtained by using the high-temperature dehalodesilylation and injection methods in a coordinating solvent. The PL studies showed only small differences between the doped and pure samples. In another report, InP : Mn QDs gave a PL spectrum with a maximum peak at 570 nm and an FWHM of 110 nm. However, it was not feasible to estimate the contribution of the dopant to the overall PL property of this system [59]. Copper-doped InP/ZnSe (Cu : InP/ZnSe) QDs have also been reported, exhibiting emission profiles that could be tuned from 630 to 1100 nm, thus covering the critical near-infrared (NIR) window for biomedical applications [60]. In these copper-doped QDs, the band edge emission from InP is eliminated (Figure 5), and pure dopant emission, with PL QYs of up to 40%, is attained.Figure 5
PL spectra of Cu : InP d-dots (5% of Cu : P precursor ratio) with different thicknesses of ZnSe shells (a) and PL spectra of Cu : InP/ZnSe QDs formed with different Cu : P precursor ratios (b) (reprinted with permission from [60], Copyright 2009, American Chemical Society).


## 4.1. Building Core and Core/Shell InP QDs

The central part of a nanocrystal constitutes the core, and the immediate surrounding comprises the shell. In 1994, well-crystallized InP QDs with a zinc blende structure were for the first time synthesized [36]. A chloroindium oxalate complex (prepared from the reaction of indium trichloride and sodium oxalate) and tris(trimethylsilyl)phosphine [(TMS)3P] were used as sources of indium and phosphorus, respectively. A mixture of TOPO and trioctylphosphine (TOP) was used as a stabilizer and the reaction was carried out at 270°C over three days. The nanocrystals were characterized by X-ray diffraction (XRD) and high-resolution transmission electron microscopy (HRTEM) (Figure 1). X-ray diffraction data on the InP nanocrystal powders showed the 〈111〉, 〈220〉, and 〈311〉 peaks of crystalline zinc blende InP at 2θ values of 26.2±0.2°, 46.3±0.2°, and 51.7±0.2°, respectively. HRTEM images showed that the particles were ellipsoidal rather than spherical in shape.An X-ray diffraction pattern for dried InP QD exhibiting broadened prominent peaks for InP (a) and an HRTEM micrograph showing lattice fringes (b) (reprinted with permission from [36], Copyright 1994, American Chemical Society).
(a)(b)An optimization exercise for the properties of the obtained nanocrystals was done by changing the ratios of the In : P.  A marked narrowing of the QD size distribution was obtained when indium was added in excess whereas the photoluminescence (PL) spectrum had two bands—one close to the band edge and the other above 800 nm (Figure2) [37]. In the case of excess addition of phosphorus, only band edge emission was observed and the absorption spectrum did not show any resolved excitonic structure indicating a broad size distribution.Room temperature absorption and PL spectra of InP QDs synthesized with different ratios of In and P: (a) In : P = 1.6; (b) In : P = 0.62 (reprinted with permission from [37], Copyright 2009, Elsevier).
(a)(b)Further optimization was achieved by the etching process [31]. The etching of the QDs by using HF produced a photoluminescence emission spectrum consisting of a single narrow peak near the absorption band edge with quantum yield (QY) of about 30% after the treatment. The InP QD cores with a lattice-matched ZnCdSe2 shell and photoluminescence QYs of 5–10% have also been synthesized [38]. However, it is worth noting that preetching the InP cores before shell growth results in poor core-shell structures as the HF blocks the surface of the QDs.Kim et al. synthesized InP/CdSe core/shell type structure showing an increase in QY at the beginning of the overcoating process due to the small difference between the InP and CdSe conduction bands of 0.19 eV which gives a type-I configuration but changes to type-II which is associated with loss of QY yield with increased shell thickening [39]. In such a synthesis, increase in the thickness of the shell should be avoided because it may result in a red shift, broadening of the full width at half maximum (FWHM), and a decrease in QYs. In 2009, InP/ZnS QDs with a diameter of 15–20 nm were reported [15]. Here, myristic acid was used as a stabilizer and octadecene as the noncoordinating solvent. PL studies showed that the QDs exhibited a band edge emission at around 650 nm with QY of 25–30%. These InP/ZnS QDs were further functionalized using mercaptosuccinic acid rendering them highly dispersible in aqueous media. The mercaptosuccinic acid-capped QDs were stable for more than one week while dispersed in a common physiological buffer such as the phosphate buffer saline (PBS). Highly luminescent InP/ZnS nanocrystals were also synthesized following a single-step heating-up procedure [35]. Here, indium myristate, (TMS)3P, zinc stearate, and dodecanethiol were used for the fabrication of the nanocrystals which gave high fluorescence quantum yields (50–70%). These high PL QYs are attributed to the nanocrystals possessing a radial composition gradient that relieves the strain due to the lattice mismatch between InP and ZnS. A similar preparation was reported by another group but using stepwise process [40]. Again, palmitic acid was used as a stabilizer and octadecene as the noncoordinating solvent. The reaction between zinc acetate and palmitic acid gave that acetic acid causes the etching of the surface of the InP core leading to the easy formation of the shell. A blue shift in the emission and an improvement in quantum yield (38%) were realized. The use of the poisonous PH3 gas, generated from the reaction of a metal phosphide (calcium phosphide) with HCl as a phosphorus source in InP QD synthesis, was also reported by Li et al. [41]. Again, octadecene and myristic acid were used as noncoordinating solvent and ligand, respectively. Unlike the single injection of (TMS)3P, here the PH3 gas is continuously and slowly generated and added to the reaction system ensuring that the growth of the InP nanocrystals takes place in the size-focusing regime. The use of higher overall precursor concentrations resulted in the formation of a large number of nuclei and hence a smaller average size of the QDs. The PL spectra of the as-prepared InP nanocrystals showed two additional bands around 730 and 820 nm. These bands were attributed to trap-state-related emissions, which are suppressed upon overcoating with ZnS obtained from the monomolecular zinc ethylxanthate precursor. The PL QY of up to 22% was achieved [41]. In a different experiment, the as-synthesized bare InP nanocrystals, prepared using PH3 gas, did not exhibit detectable photoluminescence owing to the presence of surface states [42]. However, when overcoated with a ZnS shell, a very strong PL intensity was observed, which was attributed to the passivation of these surface states by the inorganic shell. The emission profiles of the InP core varied as a function of size in the range of 600–700 nm while the 470 nm band is attributed to defect-related emissions from the shell (Figure 3).Figure 3
Steady-state photoluminescence spectra of two different sized InP/ZnS QD samples under the 370 nm excitation (reprinted with permission from [42], Copyright 2009, IOP Publishing).The molar ratios of indium to phosphorus of 2 : 1 give the best quality InP nanocrystals when the noncoordinating octadecene is used as a solvent [43, 44]. When the ratios of the metal to ligand are above or below this ratio, the reaction gives nanocrystals with no distinguishable UV-Vis spectral features, implying that the size distribution is broad. The use of the ZnS coating layer gives the red-shift in both the absorption and PL spectra of about 2-3 nm (Figure 4) as well as an improvement in the PL QY from <1 to ~20% [44].(a) Temporal evolution of the UV-Vis spectra of InP nanocrystals in ODE. (b) UV-Vis spectra of InP nanocrystals before (black dashed) and after (red solid) passivation with ZnS and PL spectra of InP (green solid) and InP/ZnS nanocrystals (blue solid) (reprinted with permission from [44], Copyright 2008, American Chemical Society).
(a)(b)Myristic and palmitic acids, which are fatty acids of intermediate chain length, serve as the best ligands for controlled nucleation growth rates that yield relatively monodisperse nanocrystals when the ratio of the fatty acid to indium is 3 : 1 [43].  Uniquely, a “green” approach where by high-quality InP nanocrystals are synthesized without the addition of a coordinating solvent or ligands, using indium carboxylates as precursors for indium, was reported [45]. The carboxylate ions act as the in situ coordination ligands. The usage of weakly coordinating fatty acid esters in the preparation of high-quality InP QDs is known [46]. In these reactions, trimethylindium is used. It readily dissolves in the ester at room temperature and generates a soluble indium-ester complex with a higher activity than the indium carboxylate. The reported reaction pathway for this reaction is given in Scheme 1.Scheme 1
Proposed reaction scheme through an indium-ester intermediate (reprinted with permission from [46], Copyright 2006, American Chemical Society).The FWHM of the produced InP QD PL spectra is about 60 nm. When protic reagents such as amines are used, they hydrolyze (TMS)3P thereby accelerating the reaction with the indium precursors, but reducing the FWHM to around 48 nm. The role of the fatty acids and the protic reagents is mainly to increase the polarity of the reaction media affording better solubility as well as homogeneity of the precursors culminating in rapid but controlled reactions [47]. Polyethylene glycol (PEG) has been used as a weakly coordinating solvent for the one-pot synthesis of InP/ZnS QDs [47]. PEG offers the major advantages that it is nontoxic, inexpensive, and recyclable. The InP/ZnS QDs prepared in the PEG medium have quantum efficiencies as high as 30% with emissions ranging from 500 to 655 nm with FWHM of approximately 46 nm. Extremely small InP QDs have also been synthesized in a reaction where the protic reagents are used and heating carried out at 100–220°C for a day [48]. Protière and Reiss also reported the activation effects of amines when they prepared In2O3-coated InP QDs having an emission profile of 583 nm and FWHM of 50–60 nm [49]. The shell growth was done in situ without an addition of any precursor but was induced by oleylamine which was added at the start of the reaction. In 2010, Bawendi’s group published a mechanism for the formation of InP QDs (Scheme 2) [50], demonstrating that amines inhibited precursor decomposition, contrary to the aforementioned reports that they are activating agents in the synthesis.Scheme 2
Proposed mechanism for amine inhibited InP synthesis (reprinted with permission from  [50], Copyright 2010, Wiley-VCH Verlag GmbH and Co. KGaA).According to the scheme, amine inhibition resulted from solvation effects associated with steps that lead to the formation of complexes1and 2. Both the amine and (TMS)3P compete for the same indium metal centre and hence an increase in the concentration of the amine decreases the formation of complex 1 as the sterically hindered phosphine precursor is less likely to approach the metal centre. During the nucleation step, molecular phosphorus precursors are completely used up. As a result, subsequent growth in nanocrystal sizes is exclusively due to ripening from nonmolecular InP species giving rise to broad size distributions.Li and coworkers [51] reported a low-temperature solvothermal synthesis of InP nanocrystals that gave a broad size distribution due to a lack of separation of the nucleation and growth steps. UV irradiation of the nanocrystals in the presents of Zn2+ ions and thioglycolic acid yielded a thick ZnS shell and improved their PL efficiencies (30–68%). When the HF etching of the InP cores preceded the ZnS coating step, a blue shift in the absorption spectra was observed and this was ascribed to a slight QD size reduction during the etching process, while the observed improvement in the photoluminescence was due to a partial surface oxidation of the InP QD surfaces [17].Another green chemistry approach recently documented involves the usage of an aqueous synthetic route to InP QDs. The system uses an indium oxide, In2O3, and white phosphorus P4 for the synthesis of the InP core [52]. The formation of the InP nanocrystals (Scheme 3) was confirmed by both the X-ray photoelectron spectroscopy and energy-dispersive X-ray (EDX) analyses that gave In : P ratios of 1 : 1.02 and 1 : 1.01, respectively.Scheme 3
Growth pathway to InP QDs adapted from the GaP scheme [52].However, this synthetic route produces larger-sized nanocrystals with poor size distribution.Yet another approach by Green and O’Brien involves the pyrolysis of a single source precursor In(PBu2t)3 in 4-ethylpyridine at 167°C to give large InP QDs [53]. The nanocrystals obtained were about 7 nm in diameter with the PL spectrum exhibiting a broad near band edge luminescence peak at 534 nm. No QY data was reported here. A coreduction colloidal method for the synthesis of relatively high-quality InP nanocrystals using indium acetate, PCl3, and a superhydride LiBH(C2H5)3 and stearic acid is equally known [54]. In this heating-up type synthesis in the presence of noncoordinating octadecene, the simultaneous reduction of the indium and phosphorus precursors was carried out at low temperature followed by the elevation of the temperature to around 250–270°C for growth of the InP nanocrystals. The PL spectra containing both a high-energy band edge and a low-energy surface trap-related emission were obtained. Posttreatment of the cores with the etchant HF resulted in the fluorescence intensity increasing by a factor of 80 and the PL efficiency improved from about 0.25% to about 20%.


## 4.2. Alloying and Doping of the InP QDs

Most of the prepared QDs are binary in nature. The binary quantum dots have the size of the nanocrystals, and hence the emission profile controlled by a systematic adjustment of the reaction parameters, namely, temperature, time, and concentration of both the precursors and surfactant molecules. The emission profiles of alloyed III-V nanocrystals can be fine-tuned using composition as well, allowing them to emit in the near-infrared region. One such system, InAsxP1-x/InP/ZnSe, with a PL QY of about 3.5%, has been reported [55]. Another alloyed QD system, InGaP, was synthesized using a microwave-enhanced method [56]. QYs of about 15% were obtained prior to etching and improved to 68% upon etching due to the passivation of surface states. Few literature reports on the doping of InP QDs are due to the low solubility of the dopants in the III-V semiconductor matrix [57, 58]. Manganese-doped InP QDs were obtained by using the high-temperature dehalodesilylation and injection methods in a coordinating solvent. The PL studies showed only small differences between the doped and pure samples. In another report, InP : Mn QDs gave a PL spectrum with a maximum peak at 570 nm and an FWHM of 110 nm. However, it was not feasible to estimate the contribution of the dopant to the overall PL property of this system [59]. Copper-doped InP/ZnSe (Cu : InP/ZnSe) QDs have also been reported, exhibiting emission profiles that could be tuned from 630 to 1100 nm, thus covering the critical near-infrared (NIR) window for biomedical applications [60]. In these copper-doped QDs, the band edge emission from InP is eliminated (Figure 5), and pure dopant emission, with PL QYs of up to 40%, is attained.Figure 5
PL spectra of Cu : InP d-dots (5% of Cu : P precursor ratio) with different thicknesses of ZnSe shells (a) and PL spectra of Cu : InP/ZnSe QDs formed with different Cu : P precursor ratios (b) (reprinted with permission from [60], Copyright 2009, American Chemical Society).


## 5. InP QDs Applied in Biomedical Research

The most recent major application of QDs lies in the area of biomedicine. One critical requirement for the use of luminescent QDs in biotechnology and medicine requires that the nanocrystals be compatible with the aqueous media [11]. To address this issue, various strategies have been developed such as introducing bifunctional hydrophilic capping ligands which include ligand exchange reactions. When solubilization of the QDs is attained, the QDs can then be further functionalized by conjugation to a number of biological molecules that include targeting peptides or antibodies. There are three modes of conjugating biomolecules to QDs which are commonly employed (a) covalent attachment, (b) direct attachment of biomolecules to the surface of the QDs, and (c) noncovalent electrostatic interaction. The discussion of these methods can be found in the review by Sapsford et al. [61].There are reports in the literature on the application of indium-based quantum dots in biological systems. The use of folic acid in the biofunctionalization of mercaptoacetic acid-capped InP/ZnS for use in the folate-receptor-mediated delivery was reported [14]. The folate-receptors are overexpressed in human cancerous cells which include the malignancies of the kidney, ovary, or prostate. The uptake of the QD-FA conjugates in the KB cells was confirmed by their rapid uptake which was immediately followed by the formation of multivesicular bodies (MVBs). Competition experiments in which the KB cells were first saturated with excess folic acid and then subsequently incubated with the QD conjugates confirmed the receptor-mediated delivery of the QDs (Figure 6).Figure 6
Confocal images showing fluorescence (intensity coded red-white channels) of QD-FA in MVBs of KB cells and a localized PL emission spectrum (reprinted with permission from [14], Copyright 2005, American Chemical Society).Mercaptosuccinic acid-capped InP/ZnS QDs have also been used in the imaging of human pancreatic cancer cells (MiaPaCa or Panc-1) [15]. These QDs were first bioconjugated to pancreatic cancer targeting monoclonal antibodies anticlaudin 4 and antiprostate stem cell antigen (anti-PSCA) whose corresponding antigens are well known to be overexpressed in primary and metastatic pancreatic cancer. Cellular uptake of the QD bioconjugates was observed from the optical signal of the MiaPaCa cells as shown in Figure 7.Confocal microscopic images of (a) MiaPaCa cells treated with anticlaudin 4-conjugated InP/ZnS QDs, (b) MiaPaCa cells treated with unconjugated InP/ZnS QDs, (c) MiaPaCa cells treated with anti-PSCA-conjugated InP/ZnS QDs, (d) XPA3 cells treated with anticlaudin 4-conjugated InP/ZnS QDs, and (e) KB cells treated with anticlaudin 4-conjugated InP/ZnS QDs. Red and blue represent emissions from InP/ZnS QDs and Hoechst 33342, respectively (reprinted with permission from [15], Copyright 2009, American Chemical Society).
(a)(b)(c)(d)(e)There were no signs of morphological damage to the cells, showing the low cytotoxicity of the indium-based QDs which could make the usage of indium-based QDs highly favourable for biological applications.


## 6. Conclusions

A lot of progress has been registered in the preparation of high-quality InP QDs. These systems have been best prepared by using coordinating and noncoordinating solvents. Other reports of fully applying “green chemistry” have also been documented. The PL QY properties of these systems can be largely improved by employing the core/shell strategy. The FWHM values ranging from 50 to 100 nm are still broad in comparison with the long known cadmium-containing QD systems. This clearly demonstrates that the QDs lack one major quality of being monodispersed in comparison to the II-VI systems. Research on improving their optical properties is ongoing. Furthermore, the development of alloyed QDs based on InP which allow for fine-tuning the emission profiles without altering particle size ushers in new possibilities in designing near-infrared emitting probes forin vivo molecular imaging.The near-infrared emitting probes have the main advantage of being able to overcome problems of autofluorescence from biological materials. The latest demonstration of the use of biofunctionalized InP/ZnS QDs raised interest in the development of future nanoprobes for biomedical applications.  The nanoprobes would be a more welcomed replacement of the highly toxic cadmium-based QD systems that have dominated current bioimaging studies.



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*Source: 869284-2012-02-14.xml*