Anna T. Kellya,
Carly S. Filgueiraa,
Desmond E. Schippera,
Naomi J. Halasab and
Kenton H. Whitmire*a
aDepartment of Chemistry, MS60, Rice University, 6100 Main Street, Houston, TX 77005, USA. E-mail: whitmir@rice.edu
bDepartment of Electrical and Computer Engineering, MS366, Department of Physics and Astronomy, MS61, Rice University, 6100 Main Street, Houston, TX 77005, USA
First published on 15th May 2017
Core–shell particles Fe2P@Au have been prepared beginning with Fe2P nanorods, nanocrosses and nanobundles prepared from the solvothermal decomposition of H2Fe3(CO)9(μ3-PtBu). Iron phosphide structures can be produced from a single-source organometallic precursor with morphological control by varying the surfactant conditions to yield fiber bundles and dumbbell-shaped bundles ranging from nanometers to microns. Derivatization of the surfaces with γ-aminobutyric acid was used to attach Au nanoparticle seeds to the surface of the Fe2P nanoparticles followed by completion of the Au shell by reduction with formaldehyde or aqueous HAuCl4/CO, with the latter giving somewhat better results. Shell thickness ranged from an incomplete, partially coated Au shell to a thickness of 65 ± 21 nm by varying the amount of gold decorated precursor particles. Increasing the thicknesses of the Au shells produced a redshift in the plasmonic resonance of the resulting structures as was observed previously for FeOx@Au.
When incorporating magnetic nanoparticles into systems intended for biological applications, careful consideration must be taken to ensure the biocompatibility of the system. Magnetic nanoparticles are often synthesized in organic media and capped with long chain organic surfactants. Therefore, surface functionalization of these particles must be performed to make them biocompatible, one example being the use of starch-coated superparamagnetic iron oxide nanoparticles for in vitro thermal ablation of cancer cells.11 A variety of successful approaches for the functionalization and incorporation of magnetic nanoparticles into biological systems have been reported.12–14
The combination of gold with magnetic nanoparticles in a core–shell structure presents an interesting bifunctional system. Gold is well-known for its biocompatibility and plasmonic properties, making it an optimal choice for the surface-coating of a variety of nanoparticles to produce a non-toxic, water soluble material that can be optically tracked within the body. The gold surface, being relatively chemically inert, resists oxidation and provides protection for the core particle. Additionally, owing to its high electron density, gold can be visualized easily by microscopy.
Gold has been used to coat diamond, metal, metal alloy and metal oxide nanoparticles for uses in plasmonic materials, catalysis and medical diagnostics and treatment.15–26 We have reported the use of faceted or tetracubic iron oxide nanoparticles as cores coated with a gold shell layer.27 In this work, it was shown that substitution of the core with a nonspherical morphology results in differences in the optical properties of these materials due to the reduction of symmetry introduced by variations in core geometry. When the spherical symmetry of the core was broken, new plasmon modes and larger shifts appeared in the spectrum, due to the mixing of plasmons of different multipolar symmetry. Other anisotropic core–Au shell morphologies have also been reported, including rice-shaped Fe2O3–Au28 and Au–FeOOH nanomaterials.29 Elongated structures are particularly interesting because they exhibit two plasmon resonances, transverse and longitudinal. The longitudinal plasmon is polarization dependent and its position is highly sensitive to the aspect ratio of the particles.30,31
We have been exploring the preparation of metal pnictide nanoparticles and thin films from single source precursors, which has proven a successful method for preparing phase-pure materials. Using H2Fe3(CO)9(μ3-PtBu) we have been able to prepare a variety of Fe2P nanostructures including split bundles, T-shapes, and crosses.32 These structures are prone to crystal splitting and a variety of morphologies can result, and they have magnetic moment values ranging from 2 to 3 μB at the saturation magnetization. We have also reported on the derivatization and coating of iron oxide nanoparticles with a gold shell along with their photonic properties.27 Coupling magnetic and plasmonic properties in one particle increases functionality and attaining a continuous Au layer enhances solubility and promotes biocompatibility. For example, analytical techniques that rely on plasmonic properties, such as surface plasmon resonance and surface enhanced Raman spectroscopy can be combined with magnetic techniques, such as separation, isolation, and purification. The anisotropic morphology of Fe2P structures is optically interesting because coupling between the plasmons will differ depending on the number and orthogonality of the particle arms. Two separate reducing agents were investigated for the reduction of gold onto the Fe2P particle surface, formaldehyde and carbon monoxide. Both of these approaches are presented, along with the corresponding experimentally observed solution extinction spectra for varying degrees of shell thickness.
In a typical procedure, 0.25 g of H2Fe3(CO)9(μ3-PtBu) was placed in a mixture of tri-n-octylamine and oleic acid in a suitable ratio (vide infra) totalling approximately 8 mL. The solution was heated slowly to >320 °C, upon which the solution turned black indicating the formation of a colloidal solution. The solution was cooled and the particles were precipitated by addition of ∼10 mL of ethanol. The supernatant was removed, and hexanes added to the flask. The resulting suspension was then transferred to a centrifuge tube; the resulting black solid was washed several times with hexanes to remove any residual surfactant. A solution of 0.10 g (1 mmol) of GABA dissolved in ∼1–3 mL of deionized water was prepared in a scintillation vial. The iron phosphide particles were suspended in hexane (∼5 mL) and added dropwise to this solution with vigorous stirring. The resulting solution was stirred overnight at room temperature. When the stirring was terminated, the less dense hexane layer was clear and the aqueous layer was dark gray, indicating that the surfactant exchange had been successful, producing water-dispersed iron phosphide particles. The particles could be isolated by centrifugation of the aqueous layer. A series of washes with water, involving the centrifugation of the sample followed by the removal of the supernatant and re-dispersion of the particles in water, were performed to remove any excess GABA present.
Decorated precursor nanoparticles were prepared by combining 40 mL of the colloidal gold solution with a concentrated solution of the GABA-functionalized iron phosphide nanoparticles in ethanol (∼1 mL) and 4 mL of 1 M NaCl in a 50 mL centrifuge tube. The tube was shaken, then sonicated briefly and placed in a refrigerator overnight. The solution was centrifuged, leaving a small pellet at the bottom or side of the tube. The optimum centrifuge conditions were found to be 3000 rcf for 20–30 minutes. The supernatant was removed, and the precipitated solid was washed three times with deionized H2O by centrifugation at 3000 rcf for 30 min per centrifugation cycle to remove any excess free unbound colloidal gold (bright red color). When redispersed, the resulting pellet generated an aqueous suspension of gold-decorated nanoparticles purple in color.
Varying amounts of a stock solution of the Au-decorated precursor nanoparticles (vide supra) suspended in 5 mL DI H2O were added to an aqueous potassium carbonate–gold(III) chloride hydrate (K2CO3/HAuCl4) solution. The plating solution was made using 400 mL Milli-Q H2O, 0.1 g K2CO3 (0.72 mmol), and 6 mL of an aqueous 1% HAuCl4 solution (∼0.02 mmol). These conditions were tested based on previous experiments with other core particles.39 The colloidal gold on the surface of the Fe2P nanostructures functioned as nucleation sites for the reduction of Au3+ to Au0 using either formaldehyde or carbon monoxide. In the case of formaldehyde, 20 mL of formaldehyde solution was added to the decorated precursor/plating solution (50, 75, 100, or 125 μL of decorated precursor solution combined with 3 mL of plating solution) and the vial was shaken in order to initialize the reaction and ensure that the reduction was homogeneous throughout the solution. After extinction spectra were acquired, the solutions were centrifuged and washed with Milli-Q H2O in order to stop the reaction and remove any residual formaldehyde. A similar procedure was followed employing CO reduction of the chloroauric acid. When CO was used as the reducing agent, 6 mL of the plating solution was combined with varying amounts of decorated precursor solution (25, 50, 75, 100, and 125 μL) in a vial and the solution was bubbled with CO for ∼1 minute. As the solution was bubbled, the color changed to varying shades of pale gray to pink, depending on the thickness of the gold shell formed. The products were characterized using UV-Vis spectroscopy and TEM. TEM grids were prepared by dispersing the product nanoparticles in hexane (∼5 mL) and drop casting onto the TEM (carbon-coated copper) grids. The solvent was evaporated and the sample analysed using JEOL 2000FX and JEOL 2010 microscopes.
Fig. 1 TEM image of the Fe2P nanorod after decoration with Au colloid (inset shows the entire nanorod). |
Once the Au-decorated precursor nanoparticles were obtained, electroless gold plating was accomplished using an aqueous solution of HAuCl4, which was reduced onto the nanoparticles using formaldehyde or carbon monoxide, forming a layer of gold around the Fe2P nanoparticles similar to the methods used for preparation of APTMS-based materials.40 The thickness of the gold shell is related to the amount of precursor solution added and the concentration of Au3+ in the solution. The general procedure for the formation of Au-coated Fe2P nanoparticles is depicted in Scheme 2.
Scheme 2 General procedure for the coating of Fe2P nanoparticles with gold to form Fe2P–Au nanostructures (not to scale). |
Formaldehyde has traditionally been used as the reducing agent in the synthesis of silica–Au nanoshells. However, Brinson et al. reported the use of carbon monoxide gas as the reducing agent to produce high quality, thin gold shell layers.40 The results of both the formaldehyde and carbon monoxide reductions will be presented.
Fig. 2 TEM images of the Fe2 particles (A–C) as synthesized, dispersed in hexane and (D–F) after being solubilized in water and decorated with Au nanoparticles. |
After decorating the precursor with gold colloid, the particles were combined in various amounts (50, 75, 100, 125, and 150 μL) with an aqueous gold plating solution (HAuCl4 and K2CO3). Formaldehyde (20 μL) was then introduced to initiate the reduction of gold. Depending on the concentration of precursor particles present, the shell thickness varied, as can be seen in Fig. 3. In the cases where less precursor was added, the gold shell was thicker and excess gold colloid was observed in the TEM images (as seen in Fig. 3A–C).
Fig. 3 TEM images of the Fe2P nanoparticles plated with a gold shell via formaldehyde reduction, using (A–C) 50 μL, (D–F) 75 μL, and (G–I) 125 μL of decorated precursor. |
As the amount of decorated precursor was increased and combined with a constant amount of plating solution, thinner gold shells were formed around the Fe2P structures. Extinction measurements were taken of the Au–Fe2P core–shell structures in order to determine their plasmonic properties as a function of shell thickness (Fig. 4). A redshift in the plasmon absorption peak was observed as the shell thickness increased. It is known that the plasmon resonant response of core–shell nanostructures will be dependent upon the core and shell dimensions, as well as the dielectric properties of the core, shell, and embedding medium.43 In silica-gold core–shell nanostructures, a blueshift is observed as the thickness of the gold shell is increased.33 Conversely, when iron oxide (Fe3O4 or FeO) cores with gold shells were studied, a redshift was observed upon increasing thickness of the gold shell.16,27 This change in the optical behavior from silica to iron oxide nanoshells has been explained in terms of plasmon hybridization.27,44,45 The redshift in the plasmon resonance as a function of increasing shell thickness is attributed to the high permittivity of the core iron oxide material (as compared to silica, which has a low permittivity).
As was the case with the formaldehyde system, different volumes of decorated precursor were combined with a constant volume of plating solution. These solutions were then bubbled with carbon monoxide for 60 seconds. A representative SEM image for the 50 μL decorated precursor system and TEM images for the 75, 100, and 125 μL decorated precursor systems can be found in the ESI (Fig. S1 and S2).† Extinction measurements were performed on the Fe2P–Au solutions (Fig. 6). A more thorough presentation of the dimensions of the particles along with aspect ratio and shell thickness information can be found in the Table S1.†
As was seen for the formaldehyde reduced Fe2P–Au particles, the extinction maximum increased as the shell thickness increased. The absorption for the sample made using 100 μL of decorated precursor redshifted back to higher wavelength, likely due to the fact that some of the Fe2P structures in this sample were not completely coated with a continuous gold layer (Fig. 7).
Fig. 7 TEM image of a partially coated Fe2P nanorod from the sample in which 100 μL of decorated precursor was used. |
Gold nanorods are known to exhibit two surface plasmon modes, longitudinal and transverse, the longitudinal mode occurring at higher wavelengths than the transverse mode. It is expected that the anisotropic Au–Fe2P structures should exhibit both transverse and longitudinal modes; the values reported here are believed to be of the higher energy transverse modes. Frequency of the longitudinal plasmon mode is known to depend sensitively on variations in aspect ratio31,40,46 and polarization31 and can occur into the near infrared (IR).47,48 Mirkin et al. studied the extinction spectra in D2O of gold rods of various lengths (96, 641, 735, and 1175 nm), all having diameters of ∼85 nm.47 For rods with lengths of 96 nm, the aspect ratio was close to 1, causing the transverse and longitudinal modes to overlap, resulting in one broad peak at ∼600 nm. As the aspect ratio was increased, the longitudinal mode shifted to higher wavelengths, with a maximum value of 1410 nm (for the 1175 nm long rods, aspect ratio ∼14). There have also been reports of the longitudinal band occurring in the mid IR region for Au, Ni, and Pd nanorods with aspect ratios greater than 25.49
Attempts to identify the longitudinal mode for the Au–Fe2P structures were unsuccessful due to experimental limitations. These measurements will provide more accurate information regarding how the shape of the particle influences the plasmon peaks, as the data presented here were collected as ensemble measurements in water, and there are a variety of shapes and orientations present, as seen in Fig. 8 and 9.
Fig. 8 TEM images of rods, T-shapes, and crosses of unfunctionalized Fe2P nanoparticles. All scale bars are 200 nm. |
Footnote |
† Electronic supplementary information (ESI) available: Additional SEM and TEM images, summary of solution extinction data for core–shell structures made by CO reduction. Elemental maps from SEM/EDAX spectra of the gold-coated particles. See DOI: 10.1039/c7ra01195d |
This journal is © The Royal Society of Chemistry 2017 |