New MRI contrast agents based on silicon nanotubes loaded with superparamagnetic iron oxide nanoparticles.

This article describes the preparation and fundamental properties of a new possible material as a magnetic resonance imaging contrast agent based on the incorporation of preformed iron oxide (Fe3O4) nanocrystals into hollow silicon nanotubes (Si NTs). Specifically, superparamagnetic Fe3O4 nanoparticles of two different average sizes (5 nm and 8 nm) were loaded into Si NTs of two different shell thicknesses (40 nm and 70 nm). To achieve proper aqueous solubility, the NTs were functionalized with an outer polyethylene glycol-diacid (600) moiety via an aminopropyl linkage. Relaxometry parameters r1 and r2 were measured, with the corresponding r2/r1 ratios in phosphate buffered saline confirming the expected negative contrast agent behaviour for these materials. For a given nanocrystal size, the observed r2 values are found to be inversely proportional to NT wall thickness, thereby demonstrating the role of nanostructured silicon template on associated relaxometry properties.

Introduction

Superparamagnetic iron oxide nanoparticles (Fe3O4 NPs) are the focus of extensive attention in areas such as catalysis [1], as well as biomedical applications such as cell labelling [2], biosensing [3], drug delivery [4], hyperthermia [5] and magnetic resonance imaging (MRI) [6]. In addition to their size-selective synthesis and useful fundamental magnetic properties, Fe3O4 NPs have a very low toxicity and are biocompatible [7,8].

There is fundamental interest in the packaging of multiple magnetic nanocrystals in a well-defined host material, along with the accompanying impact on physical properties [9-13]. One appealing option involves high surface area elemental silicon (Si) for this purpose, in the form of porous Si NPs [14,15] or silicon nanotubes (Si NTs) of a well-defined size and uniform structures. The NT length, along with the outer and inner diameter of the Si NTs, is in principle broadly tunable, with a wall thickness-dependent aqueous dissolution behaviour [16].

The characteristic quality of an MRI contrast agent is typically measured by the parameters of relaxivity r1 or r2, which describe the ability of a given contrast agent to shorten the T1 or T2 relaxation time of water [17]. The most popular class of contrast agents in current use involves Gd-complex based T1 MRI contrast agents, with extensive development of nanoparticulate T1 contrast agents containing Gd3+ or Mn2+ ions intensively pursued in recent years [18]. However, toxicity problems still persist in these NP-based T1 contrast agents, thereby motivating additional studies towards the establishment of new alternatives. Of possible choices, Fe3O4 offers a superior biocompatibility relative to the above gadolinium-based materials [19]. Fe3O4 MRI contrast agents are considered a negative contrast agent (or r2 weighted), with the possible enhancement often determined by several factors such as: (i) NP size; (ii) composition; (iii) surface coating; and (iv) synergistic magnetic effects arising from the presence of multiple superparamagnetic Fe3O4 NP centres in a relatively small volume [20].

For MRI applications, Fe3O4 NPs have been functionalized with different surface moieties to increase solubility [21]. The local concentration of Fe3O4 in solution has also been increased by the assembly of other structures such as Fe3O4 nanorods and clusters of individual Fe3O4 NPs [22,23]. However, these clusters often lack uniformity and a well-defined three-dimensional structure. There is one report of Fe3O4 NPs formed in carbon NTs [24]. Since the Fe3O4 NPs are formed in situ inside the NTs, the Fe3O4 nanostructures do not have a uniform particle size distribution [25]. To our knowledge, there are no reports of Si NTs loaded with Fe3O4 NPs for MRI applications.

In this article, we describe loading processes for incorporating Fe3O4 NPs into SiNTs, routes to surface modification of such loaded NTs for proper solubility, and the relaxivity properties of these Fe3O4 NP-loaded Si NTs. We selected Si NTs of well-defined thickness (40 nm and 70 nm) that will not degrade during the timescale of the relaxivity measurements. To examine the role of Fe3O4 nanocrystal size on loading and associated properties, we use NPs of both 5 nm and 8 nm diameter for this purpose. These experiments complement our earlier experiments involving investigations of the fundamental magnetic properties (blocking temperature, temperature-dependent coercivity) of new materials potentially useful as an MRI contrast agent based on Fe3O4 NPs loaded into silicon nanostructures [26].

Material and methods

Iron oxide nanoparticles

The Fe3O4 NPs used here were fabricated using a well-known route involving high temperature decomposition of a suitable molecular iron precursor. Further details regarding the fabrication process of these NPs can be found in previous publications [27].

Silicon nanotubes

Si NTs were fabricated by a sacrificial template method reported previously by our research group [16]. In general terms, it involves the initial formation of ZnO nanowire array (NWA) templates on a substrate (such as silicon wafers or F-doped tin oxide (FTO) glass), followed by Si deposition (540°C for 40 nm shell thickness Si NTs, 580°C for 70 nm shell thickness) and subsequent template removal by an NH3/HCl etch under a helium atmosphere at 400°C. ZnO NWA templates were prepared on a given substrate (FTO or Si) that were previously seeded with ZnO nanocrystals (according to a previously described procedure) by placing in a mixture (1 : 1 v : v) of 0.03 M Zn(NO3)2 and 0.03 M hexamethylenetetramine at 92°C for 9 h. Polyethylenimine (100 µl, branched, low molecular weight, Aldrich) was added into 100 ml of ZnO growth solution. A given ZnO NWA sample was inserted into a quartz tube reactor and Si deposition on the ZnO NWA was achieved through the use of diluted silane (20 sccm, 0.5% in He) mixed with He carrier gas (200 sccm) that was passed through a furnace. These Si-coated ZnO NW samples were then placed in another quartz reactor and heated to 450°C; NH4Cl was loaded in an alumina boat located upstream and heated to 350°C. The gaseous etchant was transported via He gas downstream (170 sccm) to the furnace for 1 h for removal of the ZnO NWA template.

Loading of Fe3O4 NPs into silicon nanotubes

The process for loading Fe3O4 NPs into these NTs is illustrated in figure 1. This is readily achieved by initial physical removal of the Si NT film from the underlying substrate (such as FTO glass) and placing it face down on top of an Nd magnet with a piece of filter paper in between. Fe3O4 NPs (oleic acid terminated, hexane solution) at a concentration of 7 mg ml−1 are added dropwise, followed by rinsing the infiltrated sample with acetone several times and allowed to air dry.

Figure 1.

Loading process of Fe3O4 NPs into silicon nanotubes (Si NTs). Si NT arrays are physically detached from their substrate; the film is then inverted and exposed to a solution of Fe3O4 NPs with a bar magnet underneath.

Ferrozine assay

A Ferrozine assay was used to determine the concentration of iron [28]. This assay consists of taking a 400 µl solution containing a known mass of Si NTs loaded with Fe3O4 NPs. This solution is then mixed with 400 µl of 12 M HCl and allowed to sit for 1 h, this solution is mixed with 400 µl of 12 M NaOH to neutralize the solution, followed by addition of 96 µl of 2.8 M HONH2 in 4 M HCl, followed by a waiting period of 1 h. Ammonium acetate (40 µl 10 M) is then added, followed by 240 µl of 300 mM of ferrozine dissolved in 0.1 M of ammonium acetate. These solutions are allowed to sit overnight and the absorbance of a given solution at 562 nm is recorded.

APTES and PEG-diacid (600) functionalization

Si NTs were immersed in 1% (3-aminopropyl)triethoxysilane (APTES) solution for 4 h in acetone, followed by rinsing with deionized (DI) water. Poly(ethylene glycol) diacid 600 (PEG-diacid 600) functionalization is achieved using APTES-functionalized Si NTs. This procedure involves the preparation of a solution of PEG-diacid (600) (3.3 mmol), 1-ethyl-3-(3-dimethylaminopropyl) carbodiimide (1 mmol) and N-hydroxysuccinimide (1 mmol) in 2 ml of DI water. This mixture is stirred for 15 min. Then APTES-Si NTs was added (0.8 mg) and stirred for 3 h. The product was dialysed against DI water by changing the DI water several times. The samples were stored in solution at room temperature for further use.

Results and discussion

Structural and morphological characterization

Transmission electron microscopy (TEM) analysis (JEOL JEM-2100) confirms that the Fe3O4 NPs used in these experiments are uniformly spherical (figure 2) and have narrow size distributions of 5.10 ± 0.98 nm and 8.15 ± 1.76 nm (for associated histograms see the electronic supplementary material, figure S1). High-resolution TEM analysis confirms that each particle consists of well-oriented single domains with the measured distance between two adjacent lattice fringes of a value of 0.258 nm (electronic supplementary material, figure S2), close to the reported value of 0.253 nm (corresponding to the lattice spacing associated with the (311) planes of Fe3O4), thereby supporting the presence of the magnetite structure.

Figure 2.

TEM images of Fe3O4 NPs of (a) 5 nm average diameter and (b) 8 nm average diameter.

Si NTs offer a uniform wall structure and relatively large interior loading capacity, with a separation distance of magnetic NPs between tube interiors that is effectively two times the wall thickness of a given type of Si NT. TEM also confirms the successful loading of Fe3O4 NPS into the Si NTs. Figure 3a shows empty Si NTs with a wall thickness of 40 nm; figure 3b,c shows these Si NTs loaded with Fe3O4 NPs of 5 nm and 8 nm, respectively. In figure 3d, empty Si NTs with a wall thickness of 70 nm are presented, with figure 3e,f presenting these Si NTs loaded with 5 nm and 8 nm Fe3O4 NPs, respectively. We observe a uniform filling of Fe3O4 NPs inside a given Si NT. No Fe3O4 NPs are observed outside these Si NTs, meaning that the washing process was successful, with no significant amount of Fe3O4NPs removed from inside the Si NTs.

Figure 3.

(a–c) TEM imaging of 40 nm Si NTs: (a) empty Si NTs; (b) Si NTs loaded with 5 nm Fe3O4; (c) Si NTs loaded with 8 nm Fe3O4. (d–f) TEM of 70 nm Si NTs: (d) empty Si NTs; (e) Si NTs loaded with 5 nm Fe3O4; (f) Si NTs loaded with 8 nm Fe3O4.

It should also be pointed out that under high magnification conditions, lattice planes of Fe3O4 NPs can be imaged inside the NTs, confirming the presence of the magnetite structures at this location. The lattice spacing of the plane of the magnetite phase can be readily confirmed (figure 4a). Interestingly, in selected NTs a closest packed arrangement of Fe3O4 NPs can also be observed (figure 5).

Figure 4.

(a) Fe3O4 NPs (8 nm average diameter) loaded into 40 nm wall thick Si NTs; (b) high-resolution TEM imaging of this sample, showing {111} spacings associated with the magnetite phase.

Figure 5.

Si NT loaded with Fe3O4 NPs, illustrating the closest packing of the nanocrystals inside the tube.

Magnetic characterization

To evaluate the potential use of this new material as an MRI contrast agent, we measured the T1 and T2 values of a given sample using a relaxometer (Bruker Minispec mq60) at 1.41 T. T1 and T2 values were recorded in phosphate buffered saline (PBS) at 37°C. A linear dependence is observed between the inverse proton relaxation times and the iron concentration according to the following equation: where 1/T,obs (i = 1, 2) is the inverse relaxation time measured experimentally in the presence of the magnetic nanomaterial, 1/T,0 is the inverse relaxation time of pure water in the absence of the contrast agent, [Fe] is the iron concentration in the contrast agent and r is the longitudinal (i = 1) or transverse (i = 2) relaxivity (i.e. proton relaxation rate enhancement per mM Fe cation concentration) [29]. Representative plots are shown in figure 6 for 1/T2 versus iron concentration for all Fe3O4 NPs housed within Si NTs. Similar plots were undertaken for 1/T1 (see the electronic supplementary material, figure S3). From linear fits of the plots, r1 and r2 can be calculated from the slopes. These r1 and r2 values are shown in table 1, as well as the corresponding r2/r1 values. As expected, r2/r1 > 2 is consistent with the classification of all Fe3O4—containing structures as a negative contrast agent. This is also true from the observation that r1 values are observed here in the range of 0.05–0.35 mM−1 s−1.

Figure 6.

1/T2 versus [Fe] of Si NTs loaded with: (a) 8 nm Fe3O4 NPs and (b) 5 nm Fe3O4 NPs.

Table 1.

r1, r2 and r2/r1 values associated with Fe3O4 NPs loaded into different Si NTs.

5 nm Fe3O4 in:	r1 (mM−1 s−1)	r2 (mM−1 s−1)	r2/r1	8 nm Fe3O4 in:	r1 (mM−1 s−1)	r2 (mM−1 s−1)	r2/r1
40 nm wall Si NTs	0.15	20.59	138.16	40 nm wall Si NTs	0.62	21.05	35.04
70 nm wall Si NTs	0.37	11.31	30.32	70 nm wall Si NTs	0.31	3.96	12.93

Some trends emerge from a simple analysis of the measured r2 values. For all Fe3O4 NPs loaded into Si NTs possessing 40 nm wall thickness, r2 is apparently insensitive to particle size, with a value of approximately 21 mM−1 s−1. Also, for a given Fe3O4 NP size, we observe the fact that r2 drops a minimum of 50% with increasing wall thickness (from 40 to 70 nm).

To interpret the above trends, it is useful to examine the following size-dependent expression for T2 [30]: where γ, gyromagnetic ratio; V*, volume fraction; a radius of Fe3O4 core; D diffusivity of water molecules; L, thickness of an impermeable surface coating.

By looking at the above results, it appears that for samples in PBS, the changes in T2 values are dictated by thickness of surface coating. T2 relaxivity decreases as the Si NTs wall thickness increases, as presumably thicker Si NTs are less permeable to aqueous diffusion.

It is also informative to compare these r1 and r2 values with representative data from the existing literature. For example, Zhou obtained an r1 value for 5 nm Fe3O4-coated with dimercaptosuccinic acid (DMSA) of 6.21 mM−1 s−1, an r2 of 39.53 mM−1 s−1 and r2/r1 of 6.58 (at 1.5 T) [31]. Huang et al. reported that 5 nm Fe3O4 coated with sodium tartrate shows an r1 of 4.3 mM−1 s−1, an r2 of 23 mM−1 s−1 and r2/r1 of 5.3 [32]. Mamor and co-workers report that 8 nm Fe3O4 NPs coated with citric acid possesses an r1 of 28.8 mM−1 s−1, an r2 of 54.4 mM−1 s−1 and r2/r1 of 1.89 [33]. It is important to consider that in our system, Fe3O4 NPs are not widely dispersed in the medium. Rather, all Fe3O4 NPs are concentrated in a one-dimensional construct inside a given Si NT, but these Si NTs are well dispersed in the medium as a result of PEG (diacid) surface functionalization. Based on the data presented here, the very low values obtained for r1 (in general, less than 1 mM−1 s−1) suggests that protons in a given medium do not have facile access to the surface of the encapsulated Fe3O4 NPs.

For this reason, it is perhaps more appropriate to compare our system with relaxometry data from Fe3O4 clusters comprised aggregates of similar sizes of Fe3O4 NPs previously reported [34]. Resovist®, commercially available Fe3O4 NPs clusters coated with carboxydextran, have an overall diameter of 60 nm with an individual particle size of 4.6 nm; this cluster has an r1 of 10.9 mM−1 s−1, an r2 of 190 mM−1 s−1 and r2/r1 of 17.4 [35]. Qin et al. reported data for a cluster size of 71 nm with an individual particle size of 10.1 nm; this cluster is coated with Pluronic F127. These workers obtained an r1 of 0.31 mM−1 s−1, an r2 of 71 mM−1 s−1 and r2/r1 of 229 [36]. Tilborg and co-workers reported a cluster size of 62.4 nm coated with PEG2000 and an individual particle size of 9 nm. An r1 of 0.62 mM−1 s−1, r2 of 402.48 mM−1 s−1 and r2/r1 of 647 was obtained for this system [37]. However, the extremely high value of the latter system is probably influenced by the fact that the experiments were made at 9 T versus the 1.5 T used in our experiments. It should also be noted that those clusters are spherically shaped aggregates of small spherical particles, in contrast to the rod-like structure of our NTs. However, in general, the r2/r1 values we obtained are in the range of clusters previously reported. Most importantly, however, it is significant to note the ability of the NT wall thickness to mediate the relaxivity values (with regard to T2), a topic warranting further investigation and ideal expansion of the tunability of these parameters as a function of template geometry and surface chemistry.

Conclusion

This work describes a straightforward process for the incorporation of superparamagnetic Fe3O4 NPs inside Si NTs, along with a necessary surface modification strategy for PEG functionalization. While the observed r2 values of these Fe3O4/Si NT composites are consistent with the clustering of Fe3O4 NPs in the NT interior, the ability to achieve ordered closest packed nanocrystal arrays is a unique attribute of this system. Further detailed evaluation of the ability of these materials to act as a negative contrast agent in vivo remain.