key: cord-0858511-5vs445jt
authors: Han, Jin Soon; An, Gye Seok
title: Preparation of Dual-Layered Core–Shell Fe(3)O(4)@SiO(2) Nanoparticles and Their Properties of Plasmid DNA Purification
date: 2021-12-17
journal: Nanomaterials (Basel)
DOI: 10.3390/nano11123422
sha: 6d9b8c7421f5c42d9c1da7c50d92afaff1859432
doc_id: 858511
cord_uid: 5vs445jt

The rapid purification of biomaterials such as DNA, RNA, and antibodies has attracted extensive attention, and research interest has increased further with the COVID-19 pandemic. In particular, core–shell-structured superparamagnetic nanoparticles have been continuously studied for their application as biopurification materials. It has been reported that Fe(3)O(4)@SiO(2) nanoparticles are one of the most promising candidates for separating nucleic acids via a simple and rapid process. This study proposed a fabrication method for dual-layered Fe(3)O(4)@SiO(2) nanoparticles, in which the density of the SiO(2) shell was controlled using an intermediate surfactant during the SiO(2) coating. After the fabrication of dual-layered Fe(3)O(4)@SiO(2) nanoparticles, structural, morphological, and magnetic analyses were conducted. The results showed that the Fe(3)O(4) nanoparticles were surrounded by a dense layer 15.6~27.9 nm thick and a porous layer 24.2~44.4 nm thick, and had superparamagnetic properties with high saturated magnetization at room temperature (86.9 emu/g). Then, the optimal conditions for the biopurification material were suggested based on analysis of the selective separation of plasmid DNA.

Superparamagnetic nanoparticles are considered promising materials in various fields owing to their magnetic properties [1] [2] [3] [4] [5] [6] [7] . Biomedical engineering is one of the most promising fields, and it requires rapid processes for the separation and purification of biomaterials. Rapid RNA purification has become an urgent problem in the biomedical field, especially because of the COVID-19 pandemic. Therefore, superparamagnetic nanoparticles have been utilized for separating biomaterials as an advanced substitute for non-magnetic nanoparticles or membranes [8] [9] [10] [11] . To purify biomaterials using superparamagnetic nanoparticles, a surface functionalization process is necessary, and many related studies have been reported based on both basic research and practical applications [6, 8, 9] .

Since the core-shell structure could take advantage of both an Fe 3 O 4 core, which could control nanoparticles through its superparamagnetic properties, and an SiO 2 shell, which can be used for purifying biomaterials such as nucleic acid and antibodies, surface functionalization through silane grafting, and enhancing chemical and thermal stabilities, core-shell-structured Fe 3 O 4 @SiO 2 nanoparticles have received extensive attention, and a large number of studies have been conducted on the fabrication method and application of Fe 3 O 4 @SiO 2 nanoparticles [12] [13] [14] [15] [16] . Most fabrication studies of Fe 3 O 4 @SiO 2 nanoparticles have been conducted using the sol-gel method with silane precursors such as tetraethyl orthosilicate (TEOS) [6, 13] and tetramethyl orthosilicate (TMOS) [2, 3] . It has been reported that biomaterials, such as plasmid DNA, RNA, and antibodies, have been successfully purified using Fe 3 O 4 @SiO 2 nanoparticles in high-speed separation processes [17, 18] . Additionally, the SiO 2 shell acts as a protective layer, which protects the Fe 3 O 4 core (a relatively Nanomaterials 2021, 11, 3422 2 of 11 unstable structure) against chemical and heat effects. After initial research on the separation of biomaterials using Fe 3 O 4 @SiO 2 nanoparticles, studies have been focusing on applications based on their DNA-separating properties [9, 17, [19] [20] [21] [22] .

However, the demand for a higher efficiency of DNA purification is consistent, and studies have been carried out in order to enhance the concentration of separated DNA [8, 12, 23] . Owing to the above-mentioned advantages provided by the SiO 2 shell, many studies have been conducted to maximize DNA purification efficiency by extending the surface area of the SiO 2 shell [3, 8, 12, 23] . Most studies on the fabrication of complex Fe 3 O 4 @SiO 2 nanoparticles have reported mesoporous or hollow SiO 2 shell structures with nanosized pores [8, 12, 23] . Studies have also reported successful DNA purification and have shown an increase in the amount of purified DNA on the application of SiO 2 shells with extended surface areas [12] . However, among the increased surface area there must be some areas on which DNA could not be attached, and the efficiency of an increased surface area through porous SiO 2 shell structures has not been presented yet. Additionally, because the nanoscale pores could potentially decrease the stability of Fe 3 O 4 @SiO 2 nanoparticles by forming a channel in the SiO 2 shell [12] , the different structures of the SiO 2 shell have to be presented.

In this study, we proposed a preparation method based on the core-shell structure for dual-layered Fe 3 O 4 @SiO 2 . We validated the performance of plasmid DNA purification based on the structuring of nanoparticles on the SiO 2 shell surface. Various structures of the SiO 2 layer, including normal, porous, and dual-layered structures, were compared based on their surface characteristics to determine the relationship between surface characteristics and DNA purification efficiencies. In addition, we discuss the effects of the types of shell structures on the dispersion and magnetic properties of Fe 3 O 4 @SiO 2 nanoparticles, which could further affect the plasmid DNA purification.

Ferric chloride hexahydrate (FeCl 3 .6H 2 O, >97%, Sigma-Aldrich, Burlington, MA, USA), sodium acetate (NaOAc, 99.995%, Sigma-Aldrich, Burlington, MA, USA), and ethylene glycol (EG, >99.5% Samchun Chemical, Seoul, Korea) were used for Fe 3 O 4 synthesis. To build a coating layer on the surface of the Fe 3 O 4 , TEOS (98%, Sigma-Aldrich, Burlington, MA, USA) was prepared as a silica precursor, and hexadecyltrimethylammonium bromide (CTAB, >98%, Sigma-Aldrich, Burlington, MA, USA) was used as a surfactant. Additionally, ammonia solution (NH 4 OH, 28-30 wt% stock solution in water, Junsei, Tokyo, Japan) and ethyl alcohol were utilized for the sol−gel reaction of the silica precursor. To purify the plasmid DNA (Axygen, Union City, CA, USA), binding buffer (5 M Gu-HCl, 20 mM Tris-HCl, pH 6.6), washing buffer (10 mM Tris-HCl, pH 7.5; 80% ethanol buffer, pH 6.5), and elution buffer (10 mM Tris-HCl, pH 8.0) were prepared without further purification.

Synthesis of the Fe 3 O 4 nanoparticles was carried out based on a previously reported polyol method [24] , in which 0.01 mol of FeCl 3 ·6H 2 O was dissolved in 0.3 mL of distilled water, and 0.05 mol of NaOAc was dissolved in 0.7 mol of EG. Subsequently, these solutions were mechanically mixed at 130 RPM in a 3 L round-bottom flask. The mixture was heated at 70 • C for 24 h in order to induce the first-phase transformation of the iron precursor. Then, the mixture was heated to boiling point under reflux until the yellow color of the solution turned to reddish brown and for the last the color of the whole solution changed into black. This dark-colored solution was cooled naturally, and the synthesized nanoparticles were separated using a magnet on the outer wall. The separated nanoparticles were washed with ethanol and distilled water several times before use.

The prepared Fe 3 O 4 nanoparticles (1 g) were dispersed in 500 mL of distilled water and sonicated for 30 min. Additionally, 200 mL of ammonia solution was prepared as 5 wt% of the composition, and the magnetically collected Fe 3 O 4 nanoparticles were dispersed in the 200 mL of ammonia solution at room temperature. This solution was heated at 80 • C for 3 h with mechanical stirring at 300 RPM for surface treatment prior to SiO 2 fabrication. After the surface treatment had finished, the solution was naturally cooled to room temperature, and 3 mL of TEOS diluted in 20 mL of ethanol was prepared in the syringe. With the syringe pump, the TEOS solution was slowly injected into the mixture with a feeding rate of 0.08 mL/min and consistent mechanical stirring. This reaction was carried out for 15 h and the solution was magnetically collected and washed several times with ethanol and distilled water, with vigorous sonication for 10 min after the reaction was completed.

The surface treatment with ammonia solution mentioned in Section 2.3 was used on the as-prepared Fe 3 O 4 nanoparticles prior to this stage. An amount of 1 g of surfacetreated Fe 3 O 4 nanoparticles or dense Fe 3 O 4 @SiO 2 nanoparticles was dispersed in 80 mL of ethanol, and 1 wt% of CTAB solution was prepared with 100 mL of distilled water. These solutions were mixed to form a suspension in a 500 mL round-bottom flask with 300 RPM of mechanical stirring, and heated for 3 h at 80 • C. Then, the mixture was naturally cooled to room temperature. In total, 3 mL of TEOS diluted with 20 mL of ethanol was slowly injected into the mixture with a feeding rate of 0.08 mL/min via syringe pump. This reaction was carried out for 15 h and the solution was magnetically collected and washed several times with ethanol and distilled water, with vigorous sonication for 10 min after the reaction was completed.

To separate the plasmid DNA from the Fe 3 O 4 @SiO 2 nanoparticles, 30 µg of the plasmid DNA was mixed with the magnetic nanoparticles (5 mg/mL). A binding buffer was used as the solvent, and the solution was gently mixed for 5 min. Subsequently, the magnetic nanoparticles were magnetically separated and washed with 600 µL of washing buffer by gentle shaking. The attached plasmid DNA was desorbed from the magnetic nanoparticles using 100 µL of an elution buffer, and the supernatant was centrifuged with DNase-/RNasefree tubes after the nanoparticles were magnetically separated.

The surface functional groups of the prepared Fe 3 O 4 and Fe 3 O 4 @SiO 2 nanoparticles were determined using Fourier-transform infrared spectroscopy (FT-IR, IRAffinity-1 S, Shimadzu, Japan) with at least 15 times scan and 2 cm −1 resolution. The structures of the Fe 3 O 4 and Fe 3 O 4 @SiO 2 nanoparticles were measured using X-ray diffraction (XRD, UltimaIV, Rigaku, Tokyo, Japan) with CuKα radiation (λ = 1.54178 Å) at a 2θ range of 20-80 • . The sizes and morphologies of the Fe 3 O 4 nanoparticles and SiO 2 coating layer were observed using high-resolution transmission electron microscopy (HR-TEM, Tecnai G2 F30 S-Twin, FEI, Eindhoven, Netherlands). To measure the surface area, we conducted a surface area analysis based on the Brunauer−Emmett−Teller method (BET, ASAP 2010 M, Micromeritics, Norcross, GA, USA) with nitrogen gas under 77 K for the range P/P 0 = 0.05-0.3. The dispersion properties of Fe 3 O 4 and Fe 3 O 4 @SiO 2 nanoparticles were characterized using dynamic light scattering (DLS; Zetasizer Nano, Malvern Instruments, Malvern, UK). The magnetic hysteresis loops of the Fe 3 O 4 and Fe 3 O 4 @SiO 2 nanoparticles were determined using a vibrating sample magnetometer (VSM, #73002 VSM system, Lake Shore Cryotronics Inc., Westerville, OH, USA) to evaluate their magnetic characteristics. Absorbance monitoring (µQuant™ Microplate Spectrometer, BioTek Instruments Inc., Winooski, VT, USA) with agarose gel electrophoresis using a 3000-Xi power supply (Bio-Rad, Hercules, CA, USA) was used to analyze the DNA purification ability.

The FT-IR spectra of the prepared Fe 3 O 4 and Fe 3 O 4 @SiO 2 nanoparticles are shown in Figure 1 and the peak assignment between 500 and 2000nm are shown in Table 1 . In all the spectra, a specific bond was observed at 600 cm −1 , which corresponded to the Fe-O bonding. In the case of the dense Fe 3 O 4 @SiO 2 complex, an intense peak around 1250-950 cm −1 and a broad peak at 3700-3000 cm −1 were observed in the FT-IR spectrum, which corresponded to the Si-O-Si bonds and O-H stretching bonds [6, 13, 25] . In the spectra of the porous and dual Fe 3 O 4 @SiO 2 , the Si-O-Si bond peak was maintained, but two peaks at wavelength ranges of 3000-2840 cm −1 (attributed to the C-H stretching bond) and 1700-1500 cm −1 replaced the corresponding peak of the O-H stretching bond [12, 13] . The formation of these new bonds indicates that the CTAB affected the coating layer or remained intact after coating. determined using a vibrating sample magnetometer (VSM, #73002 VSM system, Lake Shore Cryotronics Inc., Westerville, OH, USA) to evaluate their magnetic characteristics. Absorbance monitoring (μQuant™ Microplate Spectrometer, BioTek Instruments Inc., VT, USA) with agarose gel electrophoresis using a 3000-Xi power supply (Bio-Rad, Hercules, CA, USA) was used to analyze the DNA purification ability.

The FT-IR spectra of the prepared Fe3O4 and Fe3O4@SiO2 nanoparticles are shown in Figure 1 and the peak assignment between 500 and 2000nm are shown in Table 1 . In all the spectra, a specific bond was observed at 600 cm −1 , which corresponded to the Fe-O bonding. In the case of the dense Fe3O4@SiO2 complex, an intense peak around 1250-950 cm −1 and a broad peak at 3700-3000 cm −1 were observed in the FT-IR spectrum, which corresponded to the Si-O-Si bonds and O-H stretching bonds [6, 13, 25] . In the spectra of the porous and dual Fe3O4@SiO2, the Si-O-Si bond peak was maintained, but two peaks at wavelength ranges of 3000-2840 cm −1 (attributed to the C-H stretching bond) and 1700-1500 cm −1 replaced the corresponding peak of the O-H stretching bond [12, 13] . The formation of these new bonds indicates that the CTAB affected the coating layer or remained intact after coating. [26] . In the case of the dense Fe 3 O 4 @SiO 2 , noise was observed under the 40 • area and the width of each peak increased, especially at lower angles. This occurred because the surface of the Fe 3 O 4 nanoparticles was under stress between the Fe 3 O 4 core and the SiO 2 shell, and the inter-planar distance was slightly increased [14, 27] . Additionally, this phenomenon occurred in the porous Fe 3 O 4 @SiO 2 and dual Fe 3 O 4 @SiO 2 . The noise in the 40 • area was stronger in these cases than that of the dense Fe 3 O 4 @SiO 2 . This noise indicates the possibility of an amorphous phase on the surface. The FT-IR spectra indicate the formation of an amorphous phase with Si-O-Si bonding on the surface of the Fe 3 O 4 nanoparticles as an SiO 2 coating layer [14] . XRD patterns of the prepared Fe3O4 nanoparticles and Fe3O4@SiO2 nanoparticles are shown in Figure 2 . The diffraction pattern of the prepared Fe3O4 showed significantly distinguished peaks at 35.4°, 30.1°, and 62.5°, which indicate the (311), (220), and (440) planes of the inverse spinel crystal structure, respectively. This diffraction pattern was almost the same as that of the JCPDS card for Fe3O4 nanoparticles. (JCPDS No. 19-0629) [26] . In the case of the dense Fe3O4@SiO2, noise was observed under the 40° area and the width of each peak increased, especially at lower angles. This occurred because the surface of the Fe3O4 nanoparticles was under stress between the Fe3O4 core and the SiO2 shell, and the interplanar distance was slightly increased [14, 27] . Additionally, this phenomenon occurred in the porous Fe3O4@SiO2 and dual Fe3O4@SiO2. The noise in the 40° area was stronger in these cases than that of the dense Fe3O4@SiO2. This noise indicates the possibility of an amorphous phase on the surface. The FT-IR spectra indicate the formation of an amorphous phase with Si-O-Si bonding on the surface of the Fe3O4 nanoparticles as an SiO2 coating layer [14] . The size and shape of the prepared Fe3O4 and Fe3O4@SiO2 nanoparticles are shown in the TEM images ( Figure 3 ). Their surface area was measured using the BET method, as shown in Table 2 . The size of the prepared Fe3O4 was approximately 237.9 nm, and its shape appeared to be almost spherical with a rough surface. Its surface area was measured to be 21.57 m 2 /g. In the case of the Fe3O4@SiO2 nanoparticles, an SiO2 layer (size range = 217.7-236.8 nm) was observed on the surface of the Fe3O4 core. This is the result of the condensation of hydrolyzed silane precursor (Si(OH)4) with itself and the activated site (Fe-OH) on the surface of the Fe3O4 core. The thickness of the SiO2 layer of the dense Fe3O4@SiO2 was the thinnest (24.7 nm), and those of the porous and dual Fe3O4@SiO2 were similar (66.8 nm for porous and ~52.1-60.0 nm for dual) to each other. Additionally, the SiO2 shell of the dual Fe3O4@SiO2 comprised a dual layer with a thickness of ~15.6-27.9 nm, and ~24.2-44.4 nm for the dense and porous layers, respectively. Almost spherical shapes were observed for the porous Fe3O4@SiO2 and dual Fe3O4@SiO2, and a slightly rougher structure was observed for the dense Fe3O4@SiO2. The surface areas were measured to be 24.86, 34.50, and 29.58 m 2 /g for the dense, porous, and dual Fe3O4@SiO2 nanoparticles, respectively. The TEM images show that the CTAB was successfully used to The size and shape of the prepared Fe 3 O 4 and Fe 3 O 4 @SiO 2 nanoparticles are shown in the TEM images ( Figure 3 ). Their surface area was measured using the BET method, as shown in Table 2 . The size of the prepared Fe 3 O 4 was approximately 237.9 nm, and its shape appeared to be almost spherical with a rough surface. Its surface area was measured to be 21.57 m 2 /g. In the case of the Fe 3 O 4 @SiO 2 nanoparticles, an SiO 2 layer (size range = 217.7-236.8 nm) was observed on the surface of the Fe 3 O 4 core. This is the result of the condensation of hydrolyzed silane precursor (Si(OH) 4 ) with itself and the activated site (Fe-OH) on the surface of the Fe 3 O 4 core. The thickness of the SiO 2 layer of the dense Fe 3 O 4 @SiO 2 was the thinnest (24.7 nm), and those of the porous and dual Fe 3 O 4 @SiO 2 were similar (66.8 nm for porous and~52.1-60.0 nm for dual) to each other. Additionally, the SiO 2 shell of the dual Fe 3 O 4 @SiO 2 comprised a dual layer with a thickness of~15.6-27.9 nm, and~24.2-44.4 nm for the dense and porous layers, respectively. Almost spherical shapes were observed for the porous Fe 3 O 4 @SiO 2 and dual Fe 3 O 4 @SiO 2 , and a slightly rougher structure was observed for the dense Fe 3 O 4 @SiO 2 . The surface areas were measured to be 24.86, 34.50, and 29.58 m 2 /g for the dense, porous, and dual Fe 3 O 4 @SiO 2 nanoparticles, respectively. The TEM images show that the CTAB was successfully used to build a porous-structured SiO 2 layer, which resulted in a thicker SiO 2 layer and a larger surface area with nanosized pores [12] . The SiO 2 shell of the porous Fe 3 O 4 @SiO 2 was thicker than that of the porous layer of the dual Fe 3 O 4 @SiO 2 and similar to the total thickness of the SiO 2 shell. The dual Fe 3 O 4 @SiO 2 had two structures for the SiO 2 coating layer; therefore, it exhibited the thickest SiO 2 layer. However, during the SiO 2 fabrication, Nanomaterials 2021, 11, 3422 6 of 11 two types of reaction were conducted: one formed an SiO 2 layer from the SiO 2 precursor using the Stöber method based on the sol-gel reaction, and the other layer was fabricated by etching the SiO 2 layer into the SiO 2 precursor with an ammonia solution [28] . Therefore, the total thickness of the SiO 2 layers on porous Fe 3 O 4 @SiO 2 and dual Fe 3 O 4 @SiO 2 was observed to be similar owing to a dynamic equilibrium between the SiO 2 precursor and the SiO 2 layer. build a porous-structured SiO2 layer, which resulted in a thicker SiO2 layer and a larger surface area with nanosized pores [12] . The SiO2 shell of the porous Fe3O4@SiO2 was thicker than that of the porous layer of the dual Fe3O4@SiO2 and similar to the total thickness of the SiO2 shell. The dual Fe3O4@SiO2 had two structures for the SiO2 coating layer; therefore, it exhibited the thickest SiO2 layer. However, during the SiO2 fabrication, two types of reaction were conducted: one formed an SiO2 layer from the SiO2 precursor using the Stöber method based on the sol-gel reaction, and the other layer was fabricated by etching the SiO2 layer into the SiO2 precursor with an ammonia solution [28] . Therefore, the total thickness of the SiO2 layers on porous Fe3O4@SiO2 and dual Fe3O4@SiO2 was observed to be similar owing to a dynamic equilibrium between the SiO2 precursor and the SiO2 layer. The particle size distributions of the prepared Fe3O4 and Fe3O4@SiO2 nanoparticles were analyzed using the DLS method and are shown in Figure 4 . In the case of the The particle size distributions of the prepared Fe 3 O 4 and Fe 3 O 4 @SiO 2 nanoparticles were analyzed using the DLS method and are shown in Figure 4 . In the case of the prepared Fe 3 O 4 nanoparticles, a bimodal parabola was observed with its first peak at 295 nm and second peak at 1106 nm, and it is implied that the particles aggregated along this bimodal parabola. However, all the parabolas of the Fe 3 O 4 @SiO 2 nanoparticles achieved a monomodal form, and the center axes of these parabolas were 338, 424, and 402 nm for the dense, porous, and dual Fe 3 O 4 @SiO 2 , respectively. The mean size of the prepared nanoparticles was measured to be 1122 nm, which was much larger than that of the actual particle size as observed from the TEM image. Assuming the second peak of size distribution to be due to aggregated particles, the size of the prepared Fe 3 O 4 was determined to be~295 nm, which was the center axis of the first peak. This was similar to 238 nm, which was the observed particle size on the TEM image. Assuming that only the SiO 2 layer was affected by the particle size, the increment in the mean size was double the timed shell thickness when the particle size distribution was compared with that of the TEM images. The increments in the mean sizes were 49, 121, and 107 nm for the dense, porous, and dual Fe 3 O 4 @SiO 2 nanoparticles, respectively. These were adequate for the thicknesses of the SiO 2 layers observed on the TEM images. Furthermore, at the point of dispersion, the parabolas of the porous Fe 3 O 4 @SiO 2 and dual Fe 3 O 4 @SiO 2 were observed to be very similar, but these parabolas were narrower than those of the dense Fe 3 O 4 @SiO 2 . To be more precise, the polydispersity indexes (PDI) were measured to be 0.617 for the prepared Fe 3 O 4 , 0.204 for dense, 0.159 for porous, and 0.152 for dual Fe 3 O 4 @SiO 2 . Therefore, it was confirmed that Fe 3 O 4 @SiO 2 had better dispersion properties than those of the prepared Fe 3 O 4 because a lower PDI results in better dispersion of the particles. The biggest difference in these dispersion properties was the aggregation of the prepared Fe 3 O 4 nanoparticles that resulted from the lack of repulsive force because of the neutral state of the surface charge. Contrarily, in the case of the Fe 3 O 4 @SiO 2 nanoparticles, a strong electrostatic repulsive force was provided by the coated SiO 2 , which is one of the most representative materials with a negative surface charge. The zeta potential was measured as −51.2 mV for the dense Fe 3 O 4 @SiO 2 , and −49.1 mV and −50.8 mV for the porous and dual Fe 3 O 4 @SiO 2 , respectively. Therefore, these nanoparticles had a stable dispersion solution with a strong repulsive force. To compare the Fe 3 O 4 @SiO 2 nanoparticles, some factors (including the structure of the nanoparticles and the amount of remaining trapped surfactant) that affected their dispersion properties were determined. With respect to the structure of the nanoparticles, the nanopores on the SiO 2 shell affected their dispersion properties by increasing the surface area of the particles. This increased surface area led to an increase in the repulsive force for particle dispersion, so the particles agglomerated easily. In terms of the repulsive force, the amount of trapped surfactant enhanced the steric force via a carbon chain, which was connected to the surface of the nanoparticles. However, these factors did not have a significant impact on the dispersion properties because the effect of the electrostatic repulsive force was much stronger than the effects of the structure of the nanoparticles and the amount of trapped surfactant.

prepared Fe3O4 nanoparticles, a bimodal parabola was observed with its first peak at 295 nm and second peak at 1106 nm, and it is implied that the particles aggregated along this bimodal parabola. However, all the parabolas of the Fe3O4@SiO2 nanoparticles achieved a monomodal form, and the center axes of these parabolas were 338, 424, and 402 nm for the dense, porous, and dual Fe3O4@SiO2, respectively. The mean size of the prepared nanoparticles was measured to be 1122 nm, which was much larger than that of the actual particle size as observed from the TEM image. Assuming the second peak of size distribution to be due to aggregated particles, the size of the prepared Fe3O4 was determined to be ~295 nm, which was the center axis of the first peak. This was similar to 238 nm, which was the observed particle size on the TEM image. Assuming that only the SiO2 layer was affected by the particle size, the increment in the mean size was double the timed shell thickness when the particle size distribution was compared with that of the TEM images. The increments in the mean sizes were 49, 121, and 107 nm for the dense, porous, and dual Fe3O4@SiO2 nanoparticles, respectively. These were adequate for the thicknesses of the SiO2 layers observed on the TEM images. Furthermore, at the point of dispersion, the parabolas of the porous Fe3O4@SiO2 and dual Fe3O4@SiO2 were observed to be very similar, but these parabolas were narrower than those of the dense Fe3O4@SiO2. To be more precise, the polydispersity indexes (PDI) were measured to be 0.617 for the prepared Fe3O4, 0.204 for dense, 0.159 for porous, and 0.152 for dual Fe3O4@SiO2. Therefore, it was confirmed that Fe3O4@SiO2 had better dispersion properties than those of the prepared Fe3O4 because a lower PDI results in better dispersion of the particles. The biggest difference in these dispersion properties was the aggregation of the prepared Fe3O4 nanoparticles that resulted from the lack of repulsive force because of the neutral state of the surface charge. Contrarily, in the case of the Fe3O4@SiO2 nanoparticles, a strong electrostatic repulsive force was provided by the coated SiO2, which is one of the most representative materials with a negative surface charge. The zeta potential was measured as −51.2 mV for the dense Fe3O4@SiO2, and −49.1 mV and −50.8 mV for the porous and dual Fe3O4@SiO2, respectively. Therefore, these nanoparticles had a stable dispersion solution with a strong repulsive force. To compare the Fe3O4@SiO2 nanoparticles, some factors (including the structure of the nanoparticles and the amount of remaining trapped surfactant) that affected their dispersion properties were determined. With respect to the structure of the nanoparticles, the nanopores on the SiO2 shell affected their dispersion properties by increasing the surface area of the particles. This increased surface area led to an increase in the repulsive force for particle dispersion, so the particles agglomerated easily. In terms of the repulsive force, the amount of trapped surfactant enhanced the steric force via a carbon chain, which was connected to the surface of the nanoparticles. However, these factors did not have a significant impact on the dispersion properties because the effect of the electrostatic repulsive force was much stronger than the effects of the structure of the nanoparticles and the amount of trapped surfactant. The magnetic properties of the prepared Fe 3 O 4 and Fe 3 O 4 @SiO 2 nanoparticles were determined as hysteresis loops at room temperature, as shown in Figure 5 . The hysteresis loops exhibited paramagnetic properties with low remanent magnetization and coercivity [29] . However, unlike other paramagnetic materials, saturated magnetization of each hysteresis loop was observed to be~80 emu/g, which was high enough for these nanoparticles to exhibit paramagnetic behavior. The saturated magnetization of the prepared Fe 3 O 4 nanoparticles was 121.7 emu/g (strongest magnetization), and it changed to 101.3, 91.3, and 86.9 emu/g for the dense, porous, and dual Fe 3 O 4 @SiO 2 , respectively. The reduction in the saturated magnetization of the dense Fe 3 O 4 @SiO 2 was smaller than that of the porous and dual Fe 3 O 4 @SiO 2 , which resulted from the thinner SiO 2 layer on the dense Fe 3 O 4 @SiO 2 . However, the porous Fe 3 O 4 @SiO 2 exhibited a higher saturated magnetization than that of the dual Fe 3 O 4 @SiO 2 , which had a thinner SiO 2 shell. The SiO 2 shell of the dual Fe 3 O 4 @SiO 2 had a higher density, which resulted in a lower proportionate weight of the Fe 3 O 4 core in the dual Fe 3 O 4 @SiO 2 compared with that of the porous Fe 3 O 4 @SiO 2 .

These results indicate that the reduction in the saturated magnetization of the Fe 3 O 4 @SiO 2 nanoparticles was derived from the weight proportion of these magnetic nanoparticles. Therefore, the saturated magnetization was reduced with the increasing thickness of the SiO 2 coating layer. However, their saturated magnetization was still high enough and the superparamagnetic properties were maintained, which were essential factors for their application.

The magnetic properties of the prepared Fe3O4 and Fe3O4@SiO2 nanoparticles were determined as hysteresis loops at room temperature, as shown in Figure 5 . The hysteresis loops exhibited paramagnetic properties with low remanent magnetization and coercivity [29] . However, unlike other paramagnetic materials, saturated magnetization of each hysteresis loop was observed to be ~80 emu/g, which was high enough for these nanoparticles to exhibit paramagnetic behavior. The saturated magnetization of the prepared Fe3O4 nanoparticles was 121.7 emu/g (strongest magnetization), and it changed to 101.3, 91.3, and 86.9 emu/g for the dense, porous, and dual Fe3O4@SiO2, respectively. The reduction in the saturated magnetization of the dense Fe3O4@SiO2 was smaller than that of the porous and dual Fe3O4@SiO2, which resulted from the thinner SiO2 layer on the dense Fe3O4@SiO2. However, the porous Fe3O4@SiO2 exhibited a higher saturated magnetization than that of the dual Fe3O4@SiO2, which had a thinner SiO2 shell. The SiO2 shell of the dual Fe3O4@SiO2 had a higher density, which resulted in a lower proportionate weight of the Fe3O4 core in the dual Fe3O4@SiO2 compared with that of the porous Fe3O4@SiO2. These results indicate that the reduction in the saturated magnetization of the Fe3O4@SiO2 nanoparticles was derived from the weight proportion of these magnetic nanoparticles. Therefore, the saturated magnetization was reduced with the increasing thickness of the SiO2 coating layer. However, their saturated magnetization was still high enough and the superparamagnetic properties were maintained, which were essential factors for their application. The plasmid DNA separation process was carried out based on the Fe3O4@SiO2 nanoparticles, and the DNA was separated using agarose gel electrophoresis to evaluate the efficiency of the plasmid DNA purification (Figure 6. ). The purity of the plasmid DNA extracted with every Fe3O4@SiO2 nanoparticle was sufficiently high for commercial applications (A260/A280 = 1.985 (dense), 1.924 (porous), and 1.952 (dual)). However, the amount of the separated plasmid DNA differed with the structure of the surface layer. The amounts of DNA separated using the dense Fe3O4@SiO2, porous Fe3O4@SiO2, and dual Fe3O4@SiO2 were measured to be 52.3 ± 10.8 ng/μL, 58.3 ± 5.2 ng/μL, and 61.2 ± 2.4 ng/μL, respectively. The amount of separated DNA increased with the changes in the shell structure of the Fe3O4@SiO2 nanoparticles (into porous and dual-layer structures). According to the surface area of the Fe3O4@SiO2 nanoparticles and the amount of the separated DNA, the DNA separation capability of the Fe3O4@SiO2 nanoparticles seems to be related to the surface area, which was at a maximum for the porous SiO2 fabrication. The surface area The plasmid DNA separation process was carried out based on the Fe 3 O 4 @SiO 2 nanoparticles, and the DNA was separated using agarose gel electrophoresis to evaluate the efficiency of the plasmid DNA purification (Figure 6. ). The purity of the plasmid DNA extracted with every Fe 3 O 4 @SiO 2 nanoparticle was sufficiently high for commercial applications (A260/A280 = 1.985 (dense), 1.924 (porous), and 1.952 (dual)). However, the amount of the separated plasmid DNA differed with the structure of the surface layer. The amounts of DNA separated using the dense Fe 3 O 4 @SiO 2 , porous Fe 3 O 4 @SiO 2 , and dual Fe 3 O 4 @SiO 2 were measured to be 52.3 ± 10.8 ng/µL, 58.3 ± 5.2 ng/µL, and 61.2 ± 2.4 ng/µL, respectively. The amount of separated DNA increased with the changes in the shell structure of the Fe 3 O 4 @SiO 2 nanoparticles (into porous and dual-layer structures). According to the surface area of the Fe 3 O 4 @SiO 2 nanoparticles and the amount of the separated DNA, the DNA separation capability of the Fe 3 O 4 @SiO 2 nanoparticles seems to be related to the surface area, which was at a maximum for the porous SiO 2 fabrication. The surface area of the porous Fe 3 O 4 @SiO 2 was larger than that of the dual Fe 3 O 4 @SiO 2 , and the separated amount of plasmid DNA was smaller than that of the dual Fe 3 O 4 @SiO 2 . Comparing with the surface area and the amount of separated DNA of the dense Fe 3 O 4 @SiO 2 , the surface areas of the porous Fe 3 O 4 @SiO 2 and dual Fe 3 O 4 @SiO 2 increased to 138.7% and 119.0%, respectively, whereas the amounts of separated DNA were 111.7% and 117.0%, respectively. In this comparison, increased surface area was not fully related to the DNA separation properties. This difference occurred because the surface areas, which were measured using the BET method, contained inaccessible areas for the plasmid DNA. In the case of the dual Fe 3 O 4 @SiO 2 , this inaccessible area for DNA was smaller than that of the porous dual Fe 3 O 4 @SiO 2 . Although the increased surface area was not fully utilized for DNA separation, plasmid DNA separation capabilities were enhanced in the porous and dual Fe 3 O 4 @SiO 2 . Furthermore, considering the point of efficiency between surface area and DNA separation capability, the dual Fe 3 O 4 @SiO 2 showed the most reasonable DNA separation property. of the porous Fe3O4@SiO2 was larger than that of the dual Fe3O4@SiO2, and the separated amount of plasmid DNA was smaller than that of the dual Fe3O4@SiO2. Comparing with the surface area and the amount of separated DNA of the dense Fe3O4@SiO2, the surface areas of the porous Fe3O4@SiO2 and dual Fe3O4@SiO2 increased to 138.7% and 119.0%, respectively, whereas the amounts of separated DNA were 111.7% and 117.0%, respectively. In this comparison, increased surface area was not fully related to the DNA separation properties. This difference occurred because the surface areas, which were measured using the BET method, contained inaccessible areas for the plasmid DNA. In the case of the dual Fe3O4@SiO2, this inaccessible area for DNA was smaller than that of the porous dual Fe3O4@SiO2. Although the increased surface area was not fully utilized for DNA separation, plasmid DNA separation capabilities were enhanced in the porous and dual Fe3O4@SiO2. Furthermore, considering the point of efficiency between surface area and DNA separation capability, the dual Fe3O4@SiO2 showed the most reasonable DNA separation property. 

This study proposed a fabrication method for complex-structured Fe3O4@SiO2 nanoparticles while controlling the density of the SiO2 shell. The resulting complexes were compared with respect to various properties. To build a dual-layered SiO2 shell with different densities, two types of SiO2 fabrication method were utilized on the surface of the Fe3O4 nanoparticles, and these types of coatings were varied by applying CTAB as a temporary structure. After fabrication, differently structured SiO2 coating layers were successfully formed on the surface of the Fe3O4 nanoparticles. In the case of the dual Fe3O4@SiO2, the thicknesses of the SiO2 shell were observed to be ~15.6-27.9 nm for the dense layer and ~24.2-44.4 nm for the porous layer. The dual-layered Fe3O4@SiO2 nanoparticles had good dispersion properties with a PDI value of 0.167, and their superparamagnetic properties with high saturated magnetization were also measured (86.9 emu/g). The surface area of the porous Fe3O4@SiO2 was observed to be the largest at 34.50 m 2 /g, which was 16% larger than that of the dual Fe3O4@SiO2 (29.58 m 2 /g). Nevertheless, the DNA separation capability of the dual Fe3O4@SiO2 was measured as 61.2 ng/μL which was a 4% higher amount than that of the porous Fe3O4@SiO2 without affecting the purity of the separated DNA. With this result, a possibility has been identified for applying the dual 

This study proposed a fabrication method for complex-structured Fe 3 O 4 @SiO 2 nanoparticles while controlling the density of the SiO 2 shell. The resulting complexes were compared with respect to various properties. To build a dual-layered SiO 2 shell with different densities, two types of SiO 2 fabrication method were utilized on the surface of the Fe 3 O 4 nanoparticles, and these types of coatings were varied by applying CTAB as a temporary structure. After fabrication, differently structured SiO 2 coating layers were successfully formed on the surface of the Fe 3 O 4 nanoparticles. In the case of the dual Fe 3 O 4 @SiO 2 , the thicknesses of the SiO 2 shell were observed to be~15.6-27.9 nm for the dense layer and 24.2-44.4 nm for the porous layer. The dual-layered Fe 3 O 4 @SiO 2 nanoparticles had good dispersion properties with a PDI value of 0.167, and their superparamagnetic properties with high saturated magnetization were also measured (86.9 emu/g). The surface area of the porous Fe 3 O 4 @SiO 2 was observed to be the largest at 34.50 m 2 /g, which was 16% larger than that of the dual Fe 3 O 4 @SiO 2 (29.58 m 2 /g). Nevertheless, the DNA separation capability of the dual Fe 3 O 4 @SiO 2 was measured as 61.2 ng/µL which was a 4% higher amount than that of the porous Fe 3 O 4 @SiO 2 without affecting the purity of the separated DNA. With this result, a possibility has been identified for applying the dual Fe 3 O 4 @SiO 2 , which exhibited maximum plasmid DNA separation ability with a higher surface area efficiency for the separation of biomaterials. However, since the stability of this nanocomposite has not been proven in this paper, there is also the necessity for further study into the stability of this nanocomposite.

Preparation, surface functionalization and application of Fe 3 O 4 magnetic nanoparticles

Design of Multifunctional Fluorescent Hybrid Materials Based on SiO 2 Materials and Core-Shell Fe 3 O 4 @SiO 2 Nanoparticles for Metal Ion Sensing

Silica coating of Fe 3 O 4 magnetic nanoparticles with PMIDA assistance to increase the surface area and enhance peptide immobilization efficiency

Synthesis of porous carbon matrix with inlaid Fe 3 C/Fe 3 O 4 micro-particles as an effective electromagnetic wave absorber from natural wood shavings

Photocatalytic degradation of MB dye by the magnetically separable 3D flower-like Fe 3 O 4 /SiO 2 /MnO 2 /BiOBr-Bi photocatalyst

Magnetic solid phase extraction based on PVA-TEOS/grafted Fe 3 O 4 @SiO 2 magnetic nanofibers for analysis of sulfamethoxazole and trimethoprim in water samples

Fe 3 O 4 Nanoparticles Coated with EDTA and Ag Nanoparticles for the Catalytic Reduction of Organic Dyes from Wastewater

Mesopourous Fe 3 O 4 @SiO 2 -hydroxyapatite nanocomposite: Green sonochemical synthesis using strawberry fruit extract as a capping agent, characterization and their application in sulfasalazine delivery and cytotoxicity

γ-Fe2O3@SiO 2 core-shell structured nanoparticle: Fabrication via surface treatment and application for plasmid DNA purification

New Interface for Purification of Proteins: One-Dimensional TiO 2 Nanotubes Decorated by Fe 3 O 4 Nanoparticles

Size-tunable carboxylic functionalized Fe 3 O 4 nanoparticle and evaluation of its magnetic and dispersion properties

Hollow-structured Fe 3 O 4 @SiO 2 nanoparticles: Novel synthesis and enhanced adsorbents for purification of plasmid DNA

In situ synthesis of Fe 3 O 4 @SiO 2 core-shell nanoparticles via surface treatment

Novel synthesis of core-shell structured Fe 3 O 4 @SiO 2 nanoparticles via sodium silicate

Composites of Fe 3 O 4 /SiO 2 from Natural Material Synthesized by Co-Precipitation Method

Synthesis and characterization of Fe 3 O 4 /SiO 2 composite with in-situ method: TEOS as SiO 2 NPs precursor

Fe 3 O 4 @SiO 2 Nanoparticles Functionalized with Gold and Poly (vinylpyrrolidone) for Bio-Separation and Sensing Applications

Superparamagnetic iron oxide nanoparticles-current and prospective medical applications

A new method of synthesis well-dispersion and dense Fe 3 O 4 @ SiO 2 magnetic nanoparticles for DNA extraction

Enzyme-free homogeneous electrochemical biosensor for DNA assay using toehold-triggered strand displacement reaction coupled with host-guest recognition of Fe 3 O 4 @ SiO 2 @ β-CD nanocomposites

A chemiluminescence biosensor based on the adsorption recognition function between Fe 3 O 4 @ SiO 2 @ GO polymers and DNA for ultrasensitive detection of DNA

Programmable DNA Circuits for Flexible and Robust Exciton-Plasmon Interaction-Based Photoelectrochemical Biosensing

Mesoporous magnetic silica particles modified with stimuli-responsive P(NIPAM-DMA) valve for controlled loading and release of biologically active molecules

Synthesis of Fe 3 O 4 nanoparticles of various size via the polyol method

Enhanced Electromagnetic Wave Absorption of Three-Dimensional Porous Fe 3 O 4 /C Composite Flowers

Synthesis and characterization of Fe 3 O 4 magnetic nanoparticles from iron ore

Synthesis and Characterization of Fe 3 O 4 /SiO 2 nanocomposites

Unraveling the growth mechanism of silica particles in the stöber method: In situ seeded growth model

Modification of polymer-magnetic nanoparticles by luminescent and conducting substances

The authors declare no conflict of interest.