A systematic study of core size and coating thickness on manganese-doped nanocrystals for high T2 relaxivity as magnetic resonance contrast agent

Abstract

We describe a systematic study of coating thickness and their effect on different core sizes for the optimized preparation of highly sensitive manganese-doped magnetic nanocrystals (MnMNCs) to be served as magnetic resonance (MR) contrast agent. From these efforts, MnMNCs with 12 nm core and DA-PEG2k coating demonstrated that T2 relaxivity (r2) was increased by 7.29-fold (r2 value: 452 mM⁻¹ s⁻¹) compare to conventional iron oxide (CLIO) and remarkable colloidal stability in various physiological conditions. Further in vitro cellular MR imaging results showed that MnMNC-PEGs were biocompatible and well suited for medical applications. This study will provide a useful synthetic strategy for the development of highly effective MR contrast agents.

Background

Magnetic nanocrystals (MNCs) are emerging research areas for their potential applications in biomedical sciences such as magnetic resonance imaging, cancer treatment and micro-NMR sensors [1–3]. Researchers are aiming to make high sensitive magnetic materials by means of increasing size, engineering magnetism, and surface coating variations [4–6]. Manganese-doped magnetic nanocrystals (MnMNCs) are one of the most important material because of relatively simple preparation method and increased mass magnetization value compare to conventional iron oxides [7]. However MnMNCs are coated with hydrophobic ligands and eventually they need to be encapsulated in hydrophilic ligands to disperse them in water phase. Our group reported a method to make highly water dispersible MnMNCs, they are still in suboptimal potency of sensitivity because magnetic field surrounding a magnetic nanocrystals would be fallen as the distance go far from the core material. And the coating molecules are important factor that would affect the nuclear relaxation of water protons by forming hydrogen bond. Therefore, it is necessary work to study the affect of coating materials even if their iron oxide core sizes are similar [8–11].

Herein, we report on an optimized design for manganese-doped magnetic nanocrystals (MnMNCs), capable of achieving maximal r2 and colloidal stability (Figure 1). These synthesized MnMNCs with different coating thickness can exhibit quite different r2 even if their MnMNC core sizes remain similar. These constructions could approach the maximum r2 coefficient for a given material. As a specific example in the present study, we synthesized MnMNCs for T2-weighted magnetic resonance (MR) imaging contrast agent and encapsulated into a various PEG shell. The resultant MnMNCs with 12 nm core size encapsulated with dodecanoic acid-PEG2K Da (MnMNC12-PEG2K) exhibited most high r2 relaxivity (452 mM⁻¹ s⁻¹ [metal]), 7.29-fold higher compared to conventional iron oxide (CLIO), and showed excellent colloidal stability. The prepared MnMNC12-PEG2K was subsequently applied to an intra-cellular imaging system to demonstrate their use in identifying target cells in vitro.

Methods

Materials

Iron(III) acetylacetonate, manganese (II) acetylacetonate, 1,2-hexadecanediol, dodecanoic acid, dodecylamine, benzyl ether, anhydrous dichloromethane, monomethylpolyethylene glycol (mPEG; Mw 1 k, 2 k, 5 k, 10 k, 20 k Da)were purchased from Sigma-Aldrich. All other chemicals and reagents were of analytical grade.

Synthesis of 6 nm MnFe₂O₄ Magnetic Nanocrystals

MnFe₂O₄ nanocrystals were synthesized by seed-mediated growth method [5]. Typically, 2 mmol iron (III) acetylacetonate, 1 mmol manganese (II) acetylacetonate, 10 mmol 1,2-hexadecanediol, 6 mmol dodecanoic acid, 6 m moldodecylamine, and 20 mL of benzyl ether were mixed under a nitrogen atmosphere. The mixture was preheated to 200°C for 120 min and then refluxed at 300°C for 60 min. After being cooled to room temperature, the products were purified with an excess of pure ethanol [12].

Synthesis of 12 nm MnFe₂O₄ Magnetic Nanocrystals

2 mmol iron (III) acetylacetonate, 1 mmol manganese (II) acetylacetonate, 10 mmol 1,2-hexadecanediol, 2mmoldodecanoic acid, 2 mmol dodecylamine, and 20 mL of benzyl ether were mixed and magnetically stirred under a flow of N₂. Eighty four milligram sample of pre-synthesized 6 nm MnFe₂O₄ nanoparticles dispersed in hexane (1 mL) was added into the mixture. The mixture was first heated to 110°C for 30 min to remove hexane, then further to 200°C for 1 h. Under a blanket of nitrogen, the mixture was further heated to reflux (300°C) for 30 min. The black-colored mixture was cooled to room temperature by removing the heat source. After being cooled to room temperature, the products were purified with an excess of pure ethanol [12].

Synthesis of DA-PEG Block Copolymers

DA-PEG block copolymer was synthesized as described previously [6,7].As reported, a solution of 30 mmol dodecanoic acid (DA) and 10 mmol mPEG dissolved in 40 mL of anhydrous dichloromethane was activated by adding 30 mmol of N,N’-dicyclohexylcarbodiimide (DCC) and 4-dimethylaminopyridine (DMAP). The reaction was carried out for 48 h at room temperature under a nitrogen atmosphere. The resulting product was filtered using a cellulose acetate syringe filter (pore size ≈ 200 nm) and dialyzed for two weeks against 10 mM sodium phosphate buffer (pH 7.4) using dialysis tube.

Surface coating of MnFe₂O₄nanocrystals with DA-PEG

30 mg of MnFe₂O₄nanocrystals was dissolved in 4 mL of chloroform. This organic phase was added to 20 mL of sodium phosphate buffer containing 200 mg of DA-PEG with various sizes of mPEG (1 K, 2 K, 5 K, 10 K and 20 K molecular weight), respectively. After mutual saturation of the organic and continuous phases, the mixture was emulsified for 15 min with an ultrasonicator (ULH700S, Ulssohitech, Korea) at 300 W. After solvent evaporation in 4 h, the product was purified 3 times with centriprep at 3,000 rpm for 30 min to remove excess DA-PEG molecules [9].

Colloidal Stability

The colloidal stability of the prepared MnMNC-PEGs was determined from their resistance to pH-induced nanoparticle aggregation. A 100 μL nanoparticle suspension (20 mg/mL) was added to 2 mL (pH 2, 4, 74, 9) at room temperature and then size of the suspension was measured using laser scattering (ELS-Z, Otsuka electronics).

Cell viability assay by MTT

The biocompatibility of the prepared MNC6-PEG1K and MNC12-PEG2K for macrophage cells was quantified by a colorimetric assay based on the mitochondrial oxidation of 3-(4,5-dimethylthiazolyl-2)-2,5-diphenyltetrazolium bromide (MTT). RAW 264.7 cells were harvested at a density of 10⁴ cells/200 μL in a 96-well plate and incubated at 37°C under 5% CO₂ atmosphere. The cells were incubated for 24 h with prepared MnMNCs, rinsed with 100 μL PBS (pH 7.4, 1 mM), and then treated with freshly prepared MTT solution (10 μL) and incubated for an additional 4 h before adding 100 μL dimethylsulfoxide. After 24 h, the plates were assayed using an enzyme-linked immunosorbent assay (Spectra Max 340, Molecular Devices, USA) and the results were measured at an absorbance wavelength of 575 nm and a reference wavelength of 650 nm [9].

MR imaging

We performed MR imaging experiments with a 1.5-T clinical MRI instrument with a micro-47 surface coil (Intera; Philips Medical Systems, Best, the Netherlands). R2 relaxivities of MnMNC6-PEG(1 k ~20 k) and MnMNC12-PEG (1 k ~20 k) were measured using the Carr-Purcell-Meiboom-Gill sequence at room temperature: TR = 10 s, 32 echoes with 12 ms even echo space, number of acquisition = 1, point resolution of 156 × 156 μm, section thickness of 0.6 mm. R2 was defined as 1/T2 with units of s⁻¹. For T2-weighted MR imaging of cells in vitro at 1.5 T, the following parameters were used: point resolution: 156 × 156 μm, section thickness of 0.6 mm, TE = 60 ms, TR = 4000 ms, number of acquisitions = 1. For T2 mapping of cells in vitro, the following parameters were used: point resolution of 156 × 156 μm, section thickness of 0.6 mm, TE = 20, 40, 60, 80, 100, 120, 140, 160 ms, TR = 4000 ms, number of acquisitions =2.

Prussian blue stain

RAW 264.7 cells (5.0 × 10⁵ cells/well) were seeded onto six-well plates and incubated for 24 h at 37°C. Prepared MnMNC6-PEG1K and MnMNC12-PEG2K (100 μg of MnFe/mL) were added to Dulbecco’s modified eagle medium (DMEM, Gibco®, Invitrogen, USA). After incubation for 24 h at 37°C, the cells with MnMNC6-PEG1K and MnMNC12-PEG2K were detached, centrifuged and washed three times with PBS (pH 7.4, 1 mM). The detached cells were fixed and immersed in iron staining solution (20% hydrochloric acid: potassium ferrocyanate =1: 1) for 30 min at room temperature after being fixed in 95% alcohol for 5 min. Then, the samples were rinsed three times in deionized water to remove the residual staining solution. Subsequently, the samples were stained with the nuclear staining solution (Nuclear Fast Red) for 15 min, followed by three washes with deionized water, and were finally fixed in increasing concentrations of alcohol and xylene [13].

Characterization

The morphologies and the sizes of the prepared MnMNCs were analyzed using high resolution transmission electron microscopy (HR-TEM, JEM-2100 LAB6, JEOL Ltd., Japan) and laser scattering (ELS-Z, Otsuka electronics, Japan). X-ray diffraction measurement was performed by a Rigaku D/max-RB (Tokyo, Japan) powder diffractometer and image-plate photography using graphite-monochromatized Cu Kα radiation (λ =1.542 Å) to determine the lattice of the MnFe₂O₄. Data were collected from 20° to 80° with a step size of 0.05° and step time of 5 s. The amounts of metal ions were quantified using inductively coupled plasma atomic emission spectrometry (ICP-AES, Thermo electron corporation, USA).

Results and discussion

Manganese-doped magnetic nanocrystal cores (MnFe₂O₄; MnMNCs) exhibiting high saturation of magnetization were selected as a core material and synthesized first as reported [12]. Briefly, the particles were prepared by thermally decomposing a mixture of Fe(acac)₃ and Mn(acac)₂ in 1,2-hexadecanediol. The as-synthesized particles were then mixed and reacted with additional precursors to allow for particle growth. Using this procedure, we obtained highly monodisperse 6 nm MnMNCs (MnMNC6, size variation <5%) and 12 nm MnMNCs (MnMNC12, size variation <8.9%), respectively (Figure 2). The XRD patterns of the samples were very similar and showed characteristic reflection peaks due to the presence of a nanocrystalline inverse spinel structure (Figure 3a). The peak intensities increased from MnMNC6 to MnMNC12, indicating a progressive increase in the average particle size, also in agreement with TEM observation. The average particle sizes as determined by the Scherrer equation from line broadening of the (311) reflection (2θ =35.5) were of 5.5 and 11.6 nm for the sample of MnMNC6 and MnMNC12, respectively. The magnetic hysteresis loops of the MnMNC6 and MnMNC12 were observed at 300 K (Figure 3b) and both exhibited superparamagnetic behavior without remnant magnetic hysteresis at zero field. In addition, their saturation of magnetization values were 87.7 and 48.3 emu/g, respectively, on the basis of dried weight at 1.0 T. Due to the presence of organic components (DA-PEGs), the saturation of magnetization of MnMNC-PEGs was relatively lower than that of previously reported MnFe₂O₄ nanocrystals as expected.

Figure 1

Schematic illustration of optimal coating thickness on different sizes of MnFe ₂ O ₄ (6 nm and 12 nm). The color bar represents the magnitude of the magnetic field strength of the MnMNC cores. Solid and dashed lines represent the boundaries of PEG coating layers, respectively. Starting from the center, the lines indicate PEG1k, PEG2k, PEG5k, PEG10k, and PEG20k.

Figure 2

TEM images of MnFe ₂ O ₄ magnetic nanocrystals (MnMNCs) at the same magnification. The average diameters of the MnMNC, obtained by measuring about 50 particles for each sample, (a) MnMNC6 (b) MnMNC12. All scale bars are 20 nm.

Figure 3

Characterization of MnMNCs. (a) X-ray powder diffraction patterns and (b) mass magnetization (M) as a function of applied external field (H) measured at 300 K for MnMNC6 (blue) and MnMNC12 (red).

The as-synthesized MnMNC cores were enveloped by oleic acid/oleylamine and dispersed in chloroform. For water dispersible MnMNCs, amphiphilic block copolymer was synthesized using hydrophobic dodecanoic acid (DA) and various sizes of hydrophilic monomethylpolyethyleneglycol (mPEG, 1 K, 2 K, 5 K, 10 K and 20 K) [9]. Because of the hydrophobic interaction of MnMNCs with the DA component of amphiphilic block copolymer, the PEG-coated MnMNCs were successfully dispersed in aqueous phase. As we expected, the use of PEGs with higher molecular masses resulted in larger hydrodynamic diameters. More specifically, we calculated the series of PEG layer thicknesses and compared with our experimental data. First, we hypothesize the thickness of the hydrophobic layers, formed by oleic acid/oleylamine with DA interaction, are supposed to be the same as that of the cell membrane (3 nm), the statistical length of a PEG monomer (=0.39 nm) and the density of DA-PEG on a micelle (0.59 PEG/nm²) [14,15]. MnMNC6-PEG systems are quite well matched with calculated model systems approving the thickness of PEG variation ~ <2 nm. MnMNC12-PEG systems are slightly larger than ~ >6 nm as PEG molecular weight increase. The difference of the hydrodynamic diameters might be caused by the presence of a tiny amount of small particle clusters (e.g., dimers or trimers). This may be attributed to the strong interactions between MnMNC12 hydrophobic surfaces. The calculated and measured MnMNC-PEG layer thicknesses are listed in Table 1.

Table 1 Calculated [ 14 ] and measured thickness of different core and PEG sizes

To determine the optimized thickness of various PEG coated MnMNCs listed in Table 1 for MR contrast agents, we have experimentally measured their relaxivity coefficient values of r2, defined as relaxation rates at unit concentration (1 mM metal ions, R2 = T2⁻¹) which were obtained from the relaxation time versus [Fe + Mn] concentration plots (Figure 4). The data clearly showed a dependency of proton relaxivity on their particle sizes (magnetic domain size). MnMNC12 exhibited consistently higher relaxation rate than the MnMNC6 for all 5-series PEG coatings. For instance, MnMNC12 with PEG2k coating showed 2.16-fold higher r2 value than that of the MnMNC6 coated with identical PEG size. As previously mentioned, this size dependency is due to the effect of surface spin anisotropy which is more pronounced for smaller magnetic domain sizes due to larger surface area to volume ratio. An interesting feature is that at the same particle core size, the measured proton relaxivity depends on the nature of PEG coating thickness, leading to different values of relaxivity. The r2 coefficient of the MnMNC12 increased by 1.54-fold as the PEG molecular weight decreased from 20 to 2 K; however, it did not increase further as the PEG size further decreased to 2 and 1 K. MnMNC6 has a similar tendency; its r2 coefficient increased by 1.30-fold as the PEG molecular weight decreased from 20 to 1 K. Interestingly, both cores (6 and 12 nm) would have a critical PEG size, at which the r2 coefficient can be optimized through surface coating thickness. For instance, 12 nm MnMNCs core with DA-PEG2K exhibited the highest r2 coefficient of 452 ± 7.4 mM⁻¹ s⁻¹, which is 7.29- and 4.10-folds higher than those of CLIO and Feridex, respectively. Consequently, from the optimal combination of the core size and coating thicknesses, r2 value maximized MnMNC design could be determined and therefore, MnMNC12-PEG2K and MnMNC6-PEG1K as optimized MnMNC candidates were selected for further physiological condition tests for MR contrast agents.

Figure 4

Dependency of relaxivity coefficient (r2, mM ⁻¹ S ⁻¹ ) values on the core size and the PEG chain length of (a) MnMNC6, (b) MnMNC12. Comparison of r2 values of conventional iron oxide nanoparticles (dotted black line: Feridex, dotted gray line: CLIO).

We next investigated colloidal stability of aqueous MnMNCs to be served as a MR contrast agents (Figure 5). The colloidal stabilities of MnMNCs in aqueous solution over a wide range of pH (2, 4, 7.4, and 9) are tested using laser scattering and their results were plotted against pH. We observed that their sizes were not changed indicating successful enveloping of PEG chains on the surface of MnMNCs preventing aggregation and their zeta potential values of the MnMNCs were also well maintained around at 0 ~ 2 mV (Figure 5). Although PEG coated MnMNCs exhibiting nearly neutral surface charge, excellent colloidal stability was maintained even after repeated centrifugations. This result indicates that PEG segment dispersed from the core surface into the aqueous exterior shielding overall surface charge. Further colloidal stability experiments were performed by measuring transverse relaxation time (T2) of PEG coated MnMNCs in certain period dispersed in PBS. Figure 6 showed that their relaxation time values remained unchanged and showed excellent stability for 2 week observation.

Figure 5

Photographs of colloidal stability tests and hydrodynamic sizes and zeta-potential values of (a) MnMNC6-PEG1K, (b) MnMNC12-PEG2K on various pH conditions. (pH 2, 4, 7.4 and 9).

Figure 6

Time dependent (days) evaluation of transverse relaxation time (R2) of MnMNC6-PEG1K (blue) MnMNC12-PEG2K (red) in PBS ([Fe + Mn] concentration: 25 μM/ 200 μL).

To assess the biocompatibility of MnMNCs as a MR contrast agent, cytotoxicity of MnMNCs was investigated using the MTT assay and the results showed no cytotoxicity toward RAW 264.7cells even at high concentration (400 μg/mL) (Figure 7).

Figure 7

Cytotoxicity test of RAW 264.7 cells treated with MnMNC6-PEG1K (black) and MnMNC12-PEG2K (Gray), respectively.

Finally, we performed cellular imaging experiments with optimized MnMNC-PEG samples (MnMNC6-PEG1K and MnMNC12-PEG2K) against RAW 264.7 macrophage cells (Figure 8). Prussian blue and ferric ions of the MNCs rapidly exchange electrons thereby producing dark blue colors in the intra-cellular region. The microscope image shows that stained MnMNC12-PEG2K with RAW 264.7 cells were observed as a dotted blue color compared to non-treated cells. Moreover, the relative MR signal intensity ratio (relaxivity difference between MnMNCs treated cells and non-treated cells = △R2/R2_{non-treatment}, where R2 - R2_{non-treatment} = △R2 and R2 = T2⁻¹) showed a remarkably high MR signal sensitivity with MnMNC12-PEG2K (157.2 ± 9.2%) and less but fairly high signal enhancement was also achieved with MnMNC6-PEG1K (87.04 ± 8.5%) compared to control cells (non-treated RAW 264.7).

Figure 8

Prussian blue staining images of RAW 264.7 cells treated with (a) MnMNC12-PEG2K, (b) non-treatment (Scale bars: 5 μm), and (c) relative MR signal enhancement graph of ΔR2/R2 _{non-treatment} value.

Conclusion

In summary, we developed an efficient coating method on different core size MnFe₂O₄ magnetic nanocrystals (MnMNCs) using dodecanoic acid (DA)-PEG amphiphilic block copolymers by solvent evaporation method, and determined r2 value maximized MnMNCs based MR probes as MRI contrast agents compared to conventional iron oxide nanoparticles (Feridex and CLIO). In addition, DA-PEG coating of MnMNCs was stable and offered an optimal shell/core to achieve successful colloidal stability as well as low cytotoxicity. The study on the combination of optimal PEG layer thickness and magnetic core size for producing maximal r2 coefficient revealed that MnMNCs with 12 nm core coated with DA-PEG2K (MnMNC12-PEG2K) provided the highest r2 coefficient for MR imaging. Consequently, these advantageous features of optimized PEG coated MnMNCs allowed us to obtain outstanding MR imaging results demonstrating the utility of this MR contrast agent design in future diagnostic MR imaging applications.