Silk-Based Magnetic Materials: History
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Silk fibroin protein materials have shown excellent tensile strength, flexibility and biocompatibility. Natural silk fibers are composed of sericin coating and silk fibroin proteins. Sericin as a protective gel coat wraps the silk fibroin, which can be removed by a degumming process. Silk fibroin protein contains 18 amino acids, of which simple glycine (Gly), alanine (Ala) and serine (Ser) account for above 70%.

  • silk fibroin protein
  • composite material
  • magnetic nanoparticles
  • secondary structure
  • film

1. Introduction

Magnetic nanoparticles have been widely used in the biomedical fields such as targeted drug delivery, biosensors, cancer treatment and medical imaging, due to their small size, tunable surface chemistry and controllable magnetization. Their magnetic properties mainly depend on the size, shape and particle distribution, which may be significantly different from those of their bulk counterparts. Magnetic particles can be easily functionalized with other biopolymer materials such as proteins to improve their mechanical flexibility and biocompatibility. BaFe12O19 is a hexagonal magnetoplumbite-type ferrite material [1,2], which has a remarkably high intrinsic coercivity, saturation magnetization and Curie temperature [3]. These unusual properties give it great potential for use in biological science applications. Cobalt is another broadly used magnetic material, which has stable chemical properties at room temperature, with a Curie temperature of up to 1121 °C [4]. Fe3O4 has been used in the biomedicine field recently, specifically with applications on magnetic resonance imaging, targeted drug delivery and tumor hyperthermia [5,6,7,8,9]. Magnetic Fe3O4 nanoparticles have high biocompatibility and low cytotoxicity [6,8], while their production method is simple and low-cost. Due to the existence of various free radical groups in human body fluids, the direct use of magnetic particles in the body can be largely limited and even cause harm to the human body. Therefore, a functional composite material that combines magnetic particles and biocompatible protein materials can significantly enhance the advantages of the two components and expand their scope of application.

Silk fibroin protein materials have shown excellent tensile strength, flexibility and biocompatibility [10,11,12]. Natural silk fibers are composed of sericin coating and silk fibroin proteins. Sericin as a protective gel coat wraps the silk fibroin, which can be removed by a degumming process [13]. Silk fibroin protein contains 18 amino acids, of which simple glycine (Gly), alanine (Ala) and serine (Ser) account for above 70% [14,15]. The secondary structure of silk fibroin includes β-sheets, random coils and α-helices [16,17,18], which greatly control the physical properties. For instance, the mechanical properties of silk fiber can be enhanced by a high content of β-sheet crystals [19,20]. The highly crosslinked silk fibril network structure through β-sheet crystals is believed to also cause the insolubility of the regenerated silk materials in water and many mild organic solvents [10,21]. Different forms of silk materials, such as films, gels, particles and fibers, have shown great potential in biomedical applications [22,23,24,25], and by manipulating their secondary structure, one can control the release time and dose during targeted drug delivery [18,26]. A high content of β-sheet crystals, which can be stimulated through alcohol solutions or water annealing, also helps to improve cell adhesion and tissue growth [25,27,28]. In addition, the hydrophilic functional groups on the network composed of the protein chain and its crosslinked structure can make the material absorb water while still maintaining its shape and structure well, permitting its use for bone reconstruction, bioelectronics, and in vivo tumor models [29,30,31].

In this study, three magnetic nanoparticles, M-type hexaferrite BaFe12O19 (BaM), Fe3O4, and cobalt (Co) particles were blended with silk fibroin (SF) proteins to form robust composite films (denoted as BaM-SF, Fe3O4-SF and Co-SF, respectively) by a wet-pressing method (Figure 1). Performance of the obtained silk-magnetic functional films were comparatively evaluated at various concentrations of different magnetic particles. The effect of particle concentration on the secondary structure of silk fibroins was studied by FTIR analysis. TGA and DSC were used to study the thermal stability and transitions of silk-magnetic composite films, and SEM with EDS was used to characterize the morphology of the silk films and the distribution of the particles while the magnetization was studied by magnetometry. This comparative study helps us better understand the interactions between the organic matrix and the inorganic inclusions in composites, which have a variety of potential uses as sustainable or biomedical materials.

Figure 1. Procedures to prepare magnetic silk fibroin composite films.

2. Results and Discussion

2.1. Structural Analysis

FTIR is an effective tool to characterize the secondary structure and functional group of silk protein materials [16,17] (Figure 2). For Fe3O4-SF samples, there is a sharp peak at 1622 cm−1, suggesting the β-sheet crystal structures are dominant. However, the peak shoulder at 1646 cm−1 (random coils structures) increased with Fe3O4 content, indicating that relative fraction of β-sheet crystals decreased. All BaM-SF samples also showed a sharp peak at 1620 cm−1, indicating a predominant β-sheet secondary structure due to the wet-pressing method. The peak at 1650 cm−1 slightly increased when more nanoparticles were present, suggesting that the BaM particles in the silk matrix can also slightly enhance the formation of α-helix or random coils structures. However, this structural change is not as significant for the Fe3O4-SF samples. Compared to the FTIR patterns of BaM-SF and Fe3O4-SF, Co-SF samples showed much sharper peaks at 1622 cm−1, suggesting it has the highest β-sheet crystal content among the three types of magnetic inclusions. In addition, the shoulder at 1651 cm−1 decreased with the increase in Co particle content. In the amide II region, all three types of composite films showed peaks around 1515 cm−1, which suggests Tyr side chains structure.

Figure 2. FTIR spectra of (a) Fe3O4-silk fibroin (SF), (c) BaM-SF and (e) Co-SF composite films. Secondary structure contents of (b) Fe3O4-SF, (d) BaM-SF and (f) Co-SF calculated from a Fourier self-deconvolution curve fitting method.

A quantitative analysis of the secondary structure contents was performed with a Fourier self-deconvolution (FSD) curve fitting method (Figure 2b,d,f) [16]. It shows that β-sheet content of SF sample is around 39% composed of mainly inter-molecular β-sheets [10]. The β-sheet content of the Fe3O4-SF samples decreases with Fe3O4 content, reaching 33% at 30 wt%, while the random coils content increased slightly by 29–32%. Similar behavior was found in BaM-SF samples, where the β-sheet content decreased with an increase in BaM weight fraction, while the random coils content nominally increased. In contrast, for the Co-SF samples, the secondary structure remained almost unchanged with a slight increase in β-sheet content.

2.2. Morphology Analysis

Surface and cross-section morphology of SF and magnetic silk composite films are shown in Figure 3. Lamellar patterns evenly spread out across the cross section of SF and 20% BaM-SF films (Figure 3a,g). Cross section of 20% Fe3O4 (Figure 3d) showed a rougher morphology with wrinkles and densely distributed particles. Cross section of 20% Co-SF (Figure 3j) showed evenly distributed holes with connected wrinkles. When comparing the surface samples to the cross-sectional, the surface seems to be much more homogenous, containing fewer aggregates and wrinkles. SF film shows a smooth and uniform surface (Figure 3b). A 20% BaM-SF sample (Figure 3h) showed a relatively rough surface, and BaM particles distribute homogenously instead of forming big aggregates. Compared to the surface morphology of 20% BaM-SF film, 20% Fe3O4 (Figure 3e) and 20% Co-SF (Figure 3k) films showed smooth and uniform surface morphology with shallow pits. EDS spectra and analyses of the SF, 20% Fe3O4-SF, 20% BaM-SF and 20% Co-SF films are shown in Figure 3c,f,i,l, respectively. As mentioned above, most CaCl2 residue has been washed out of the pure SF film after the water annealing process (Figure 3c). The EDS spectra of various elements in the composites also showed evidence of Fe (6.403 keV and 0.705 keV, Figure 3f), Ba (4.465 keV and 0.779 keV, Figure 3i) and Co (6.929 keV and 0.776 keV, Figure 3l) elements in their respective composite films.

Figure 3. (a,d,g,j) The cross section of SF film, 20% Fe3O4-SF, 20% BaM-SF and 20% Co-SF composite, respectively; (b,e,h,k) are the surface morphology of SF film, 20% Fe3O4-SF, 20% BaM-SF and 20% Co-SF composite, respectively; (c,f,i,l) display the EDS spectra for the SF, 20% Fe3O4-SF, 20% BaM-SF and 20% Co-SF films, respectively.

2.3. Thermal Analysis

Thermal stability of the silk magnetic composite films was characterized by TGA (Figure 4Table 1). All three types of magnetic particles are thermally stable with no degradation for all of them up to 800 °C. All Fe3O4-SF composite films showed a small degradation in the range of 209~226 °C (Td1), a major degradation between 296 and 303 °C (Td2) and a third degradation around 650 °C (Td3). The residual weight of Fe3O4-SF samples at 800 °C was between 26.6 and 48.2%, which generally increased with Fe3O4 content. All BaM-SF composite films showed a small degradation between 238 and 251 °C (Td1) and a major degradation between 301 and 309 °C (Td2). When the BaM concentration was 10% or above, a third degradation (Td3) was found around 700 °C (Figure 4c,d). The residual weight of BaM-SF samples at 800 °C was between 27.1 and 46.1%, and the residual weight increased with BaM content. All Co-SF composite films showed a small degradation at 214~233 °C (Td1) and a major degradation at 300~307 °C (Td2). The residual weight of Co-SF samples at 800 °C is between 27.1 and 55.1%, and increased with Co content. However, no third degradation peak (Td3) was observed around 600~700 °C for any of Co-SF samples. The first small degradation is mainly from the unstable part of silk proteins [32,33,34]. BaM-SF samples showed a higher Td1 than that of the other two types of composites, suggesting that BaM particles were able to best protect silk materials. The third degradation for Fe3O4-SF and BaM-SF samples is probably from a stable phase that formed when the Fe combined with the silk protein.

Figure 4. Thermogravimetric curves of (a) Fe3O4-SF, (c) BaM-SF and (e) Co-SF composite films. The 1st derivative TG (DTG) curves of (b) Fe3O4-SF, (d) BaM-SF and (f) Co-SF composite films.

Table 1. Thermal properties of Fe3O4-SF, BaM-SF and Co-SF composite films *.

  Tw (°C) Td1 (°C) Td2 (°C) Td3 (°C)
SF 48 245 308 -
5% Fe3O4-SF 49 219 303 657
10% Fe3O4-SF 52 226 297 659
20% Fe3O4-SF 46 209 296 641
30% Fe3O4-SF 50 215 303 650
5% BaM-SF 63 250 308 -
10% BaM-SF 64 251 309 708
20% BaM-SF 60 250 306 697
30% BaM-SF 61 238 301 696
5% Co-SF 52 233 300 -
10% Co-SF 54 234 307 -
20% Co-SF 50 223 307 -
30% Co-SF 52 214 303 -

* Data was obtained from TGA. The weight derivative peak position was used as the degradation temperature. All temperature values have an error bar within ± 0.5 °C.

Heat flow and reversing heat capacity of magnetic silk composite films measured from DSC are shown in Figure 5. Heat flow analysis shows that all three type composite films have a major degradation about 260 °C, which is from the decomposition of silk proteins. The amorphous part of the polymer has a greater mobility with increasing temperature, which is defined as the glass transition. The glass transition is gradual and reversible, and the heat capacity of the polymer changes dramatically during this transition [35]. All Fe3O4-SF samples showed a similar glass transition temperature around 172 °C. The glass transition temperature of BaM-SF composite films increased from 172 °C for SF, to 192 °C for 30% BaM-SF, suggesting that the mobility of the amorphous structure in BaM-SF composites can be tuned by the BaM particles. All Co-SF composite films showed a glass transition temperature around 180 °C.

Figure 5. Heat flow of (a) Fe3O4-SF, (c) BaM-SF and (e) Co-SF composite films. Reversing heat capacity of (b) Fe3O4-SF, (d) BaM-SF and (f) Co-SF.

2.4. Magnetization Analysis

Magnetization of the three types of composite films showed typical ferromagnetic behavior with coercive field of about 128 Oe (Fe3O4), 3660 Oe (BaM) and 165 Oe (Co), respectively (Figure 6a–c). The dependence of the magnetization on weight fraction of magnetic particles are shown in Figure 6d. The saturation magnetization Ms of Fe3O4, BaM and Co nanoparticles is about 61 emu/g, 68 emu/g and 156 emu/g, respectively. Since silk protein matrix has magnetic susceptibility near zero, it can be assumed that the moment of the composite films depends only on the net weight of the magnetic particles. Therefore, one would anticipate that the Ms value of the composite should be about xMs, where x is the weight fraction of magnetic particles. All samples display a linear dependence of Ms on weight fraction; however, note that neither line intercepts the origin. Presumably, all three types of magnetic particles partially dissolved in the formic acid solution, saturating the solution at about 3.7 wt%, 3.4 wt% and 1.1 wt% (horizontal intercept of the graph) for Fe3O4, BaM and Co particles, respectively. These results are consistent with the study of the secondary structure of SF matrix. In any case, at sufficient loading, of three types of composite films maintain a sizable magnetization for potential use in MRI imaging or targeted drug delivery.

Figure 6. Magnetization and hysteresis loops of (a) Fe3O4-SF, (b) BaM-SF and (c) Co-SF composite films at room temperature. (d) Saturation moment of Fe3O4-SF, BaM-SF and Co-SF composite films as a function of the magnetic particle content.

2.5. Self-Assembly Mechanism

With the experimental evidence and analysis provided above, we can confirm that Fe3O4 and BaM particles can slightly prevent the β-sheet crystal formation, suggesting that the Fe3O4-SF and BaM-SF composite films have more noncrystalline structures (Figure 7). This is probably caused by the strong coordination bonding between Fe3+ ions and carboxylate ions on silk fibroin chains [36,37,38] due to the dissolved Fe found from the magnetization studies. Most β-sheet crystals usually formed during the water annealing and wet pressing process. However, when the Fe3O4 and BaM particles were present, the strong coordination bonding limited the mobility of silk fibroin chain and further prohibited the β-sheet crystal formation (Figure 7). The unique high temperature degradation (Td3) of Fe3O4-SF and BaM-SF samples found in TG analysis may be another indicator of this stable phase, which is formed when Fe is combined with silk protein. On the other hand, the amount of dissolved Co is minimal as compared to that of the Fe, so the addition of Co nanoparticles has less effect on the secondary structure. Since a large amount of Co particles will occupy more space in the Co-SF film, the silk protein chains are able to be closer to each other, resulting in a slight increase in β-sheet crystals (Figure 7).

Figure 7. The effect of iron-based (Fe3O4 or BaM) and cobalt-based (Co) magnetic particles on the secondary structures of silk fibroin material.

This entry is adapted from the peer-reviewed paper 10.3390/ijms21207583

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