Fabrication of Poly (Acrylonitrile-Co-Methyl Methacrylate) Nanoﬁbers Containing Boron via Electrospinning Method: A Study on Size Distribution, Thermal, Crystalline, and Mechanical Strength Properties

: Electrospun polymeric nanoﬁbers have attracted great attention in ﬁltration systems and protective clothes. One of them is polyacrylonitrile (PAN) nanoﬁbers, which are a suitable choice for the fabrication of protective clothes in the defense industry, due to their good ﬁber formation and easy optimization with chemical reagents. They do not possess adequate properties for protection against chemical, biological, and radiological agents. In this research, poly (acrylonitrile-co-methyl methacrylate) (PANMM) nanoﬁbers and PANMM nanoﬁbers containing 10 B were fabricated via the electrospinning method. The study of the morphology of nanoﬁbers, using scanning electron microscopy (SEM), revealed that smooth and knotted ﬁbers with an average diameter of 259 ± 64 nm were obtained, using 12% ( w / v ) of PANMM in the solution as the optimal concentration for the electrospinning process. This sample was doped with boron (10%, 30%, and 50% ( w / w )) to fabricate the samples of PANMM + boric acid (BA) nanoﬁbers. The results demonstrated an increasing trend in the diameter of the nanoﬁbers with an increase in BA up to 50%. At this concentration, smooth ﬁbers were formed with lower knots. Furthermore, the presence of B-O and O-H groups was observed using Fourier transform infrared (FTIR) spectroscopy. To study the tensile properties, the nanoﬁbrous web was tested, and the results showed that introducing 10 B to PANMM nanoﬁber structures reduced the strength of the nanoﬁbers. Thermal gravimetric analysis (TGA) showed that BA-modiﬁed PANMM nanoﬁbers had lower thermal degradability, as compared with pure PANMM.

Carbon fiber reinforced polymers are an important kind of versatile reinforcement structure for polymeric fibers [11]. Polyacrylonitrile (PAN) is one of the main precursors for manufacturing carbon fibers because of its high quality and the fact that it is high-tech material [12]. PAN-based carbon fibers (CFs) are greatly used in aerospace and defense industries, due to their excellent mechanical properties, such as low density (1.7-2.2 g cm-3), high tensile strength (3)(4)(5)(6)(7), and high Young's modulus value (200-700 GPa) [13,14]. PAN fibers are important synthetic fibers in the textile industry; they are spun from acrylonitrile copolymers containing more than 85% of PAN with outstanding properties, such as excellent warmth retention, good elasticity, etc. [5,15]. Furthermore, they are known as one of the most combustible synthetic fibers, which produce heavy smoke and toxic hydrogen cyanide when on fire. Consequently, the developments of PAN fibers' applications, particularly imparting PAN fibers with flame retardant properties, have become significantly important [16].
The production of flame-retardant PAN fibers can be carried out through surface modification, blending, and copolymerization methods [17]. In the latter method, flameretardant elements are introduced to acrylonitrile macromolecular chains through a covalent bond, resulting in durable flame-retardant performance. The main drawback of this method is that the cost of production significantly increases. In addition, acrylonitrile has high molecular weight due to the relatively high molecular weight of the copolymers [18]. Surface modification is used as a simple and cost-effective method to introduce flame retardancy. In this method, there are disadvantages, such as the yellow or brown color of fibers, that limit its broad range applications and poor mechanical properties [19].
Boron and its compounds are applied extensively in the nuclear industry, such as in control/shut off rods in nuclear reactors, sensors for neutron counting, shapes for neutron shielding, etc., due to their high neutron absorption cross section. The neutron absorption of enriched 10 B is sufficiently high at 1 barn for 1 MeV neutron energy. Boric acid (BA) and boron carbide as neutron absorbers in the nuclear industry are two principal compounds of boron materials. BA is used in the moderator/coolant of research reactors and developed due to its high absorption cross sections [20]. Several studies have shown the protective characteristics of 10 B against ultraviolet (UV) radiation; therefore, investigations have been carried out for the modification of the textiles' structure in order to increase their UV protection factor [16]. Commonly, protection provided by normal clothing is insufficient to protect skin from UV radiation damage. Thus, attempts on improving UV protection have increased, and several methods have been proposed and compared for doping 10 B onto CFs, such as the (1) dissolution-reprecipitation of carbon for the formation-decomposition of carbides and/or the (2) oxidative stabilization method, which makes a tunable balance between the reaction rates of cyclization and oxidation during stabilization [21]. In these two methods, the heterogeneous nature of boron distribution inside the CFs has demonstrated difficulty in the diffusion of BA and placing boron on the surface. The most promising methods of CF production with B precursors have been reported in the form of immersing fibers in solutions containing boron, such as boron carbide (B 4 C), boron trioxide (B 2 O 3 ), or BA (H 3 BO 3 ) [18,20]. On the other hand, boron compounds, such as BA, are toxic to all species at a high dosage, but they are not mutagenic or carcinogenic. However, the toxicity mechanisms of boron remain unclear [22]. The major chronic toxicities are related to growth and reproduction. Due to the exposure of industries and consumers to boron, awareness of its toxicity is essential [23].
To overcome the problems mentioned above, researchers have carried out the modification of PAN fibers [24]. According to the results, BA could also be doped to the fibers, before drying, in the spinning process. Grassie et al. also mentioned that BA had an inhibitory role in the reaction [25]. Considering the possible ways for industrialization, immersion determined as an appropriate and easy method is performed by immersing fibers in a BA solution, using existing equipment without adding an excess process or a new machine for higher production [17]. According to the surface structures, and properties of the pure PAN fibers' structure, it can also be concluded that BA could be cross-linked to PAN fibers [26]. More results demonstrated that the content of boron (B) in polymer fibers is dependent on polymer solution concentration [17,27].
In this paper, pure poly (acrylonitrile-co-methyl methacrylate) (PANMM)and PANMM nanofibers containing BA were fabricated. The effect of PANMM and BA concentrations on the diameter of the fibers was investigated by SEM. The effects of doping BA on the chemical structure, thermal, crystalline, and mechanical properties of the nanofibers were investigated.

Materials
PAN was supplied by Polyacryl Iran Company (IRI), and then PANMM (94 wt% acrylonitrile and 6 wt% methyl acrylate), with the average molecular weight of around 1.7 million g/mole was synthesized using emulsion copolymerization at a low temperature in a closed reactor. Dimethylformamide (DMF) as a solvent and BA were supplied from Merck (GER).

Polymer Solution Preparation
The PANMM solutions were prepared at the concentrations of 5%, 12%, and 20% (w/v) by the PANMM nanofibers' dissolution in DMF, as a solvent. All PANMM solutions were mixed for 24 h on a magnetic stirrer until a homogeneous distribution was obtained. In the next step, BA was used for the electrospinning process in order to create nanofibers containing boron. For this purpose, three different polymer solutions were selected for the electrospinning process, and the samples were prepared with boron doping equal to 10%, 30%, and 50% (w/w) of the PANMM nanofibers. This means that the surface of the PANMM fibers is coated with 0.25, 0.75, and 1.25 wt% of boron. Thus, BA can be introduced onto the PANMM fibers' surface to improve the homogeneity of the structure of the PANMM fibers during the thermal treatment. First, BA was dissolved in DMF, and then the PANMM nanofibers were added to this solution. The dissolution process was performed using a magnetic stirrer for 24 h, in combination with an ultrasonic mixing method for 6 min, to obtain a clear solution. After dissolution, electrospinning of the solutions was performed. BA could inhibit the cyclization process, which can then occur at a higher temperature. It should be noted that electrospinning was performed at room temperature. This was intended to test the effect of the concentration of PANMM nanofibers and BA on the fibers' diameter after electrospinning. The solutions' concentrations and the electrospinning process parameters are presented in Table 1. Table 1. Different concentrations of the prepared solutions and the parameters of the electrospinning processes.

Electrospinning
After obtaining a clear solution of the polymer, electrospinning was performed under the conditions as follows: the voltage of around 14 kV, 15 cm distance from the needle tip to the collector plate, and the polymer feed rate of 1 mL/h fitted with a steel needle of 337 µm inner diameter. The fiber samples were electrospun, and the nanofibers were collected on aluminum foil and stored in a desiccator to investigate their properties.

Thermal Stabilization of PANMM Fibers
The samples of the pure PANMM were heated in an oven at 200 • C for 1 h (from room temperature to 200 • C with the rate of 3 • C/min). The process was carried out in a pure inner air flow flux.

Characterization
SEM images are often used to determine the diameter of fibers. Therefore, PANMM fibers were coated with gold for 120 s under a flow of 10 mA, and then the fibers were observed at a voltage of 20 kV. By examining the SEM images of the samples obtained from the electrospinning of polymer solutions, the best concentration for producing fibers from PANMM solutions in DMF was obtained. A dynamic light scattering (DLS) technique (Zetasizer, Malvern, UK) was used to measure the average particle size of the prepared nanocomplexes. The samples were diluted with distilled water (the pH of the distilled water was adjusted according to the pH of the samples), and the average volumetric diameter was applied for the determination of the average particle size. X-ray diffraction (XRD, GBC MMA instrument) in the range of 2θ = 10 − 70 • was applied for the characterization of the crystallinity of the materials. In order to study the thermal changes of nanofibers before and after the introduction of BA, TGA was used to plot the changes in the samples weight against temperature. The samples were studied by a TAQ50 instrument and heated with the rate of 10 • C/min under argon gas from 25 • C to 840 • C. In order to measure the mechanical properties, samples with dimensions of 50 × 10 mm 2 and a thickness of 0.69 nm were prepared. It should be mentioned that the thickness of the fibers increases obviously by increasing boron content. Then, the mechanical properties were measured using the Instron instrument, using the weight of 10 N at a speed of 10 mm/min. The number of replications for each experiment was 5 samples, and the averages of the results were reported as strength and elongation of the sample.

Investigation of the SEM of the Nanofibers
As shown in Figure 1a, at the concentration of 5% (w/v), due to the low viscosity of the polymer solution, the fibers are not formed, and the polymer particles are spread on the collector. This phenomenon can be explained by the fact that the polymer chains are not able to accumulate and form a fibrous structure, due to the low concentration of the polymer solution. As a result, the spherical particles of the polymer are charged, accelerated, and thrown toward the collector [28].

Thermal Stabilization of PANMM Fibers
The samples of the pure PANMM were heated in an oven at 200 °C for 1 h (from room temperature to 200 °C with the rate of 3 °C/min). The process was carried out in a pure inner air flow flux.

Characterization
SEM images are often used to determine the diameter of fibers. Therefore, PANMM fibers were coated with gold for 120 s under a flow of 10 mA, and then the fibers were observed at a voltage of 20 kV. By examining the SEM images of the samples obtained from the electrospinning of polymer solutions, the best concentration for producing fibers from PANMM solutions in DMF was obtained. A dynamic light scattering (DLS) technique (Zetasizer, Malvern, UK) was used to measure the average particle size of the prepared nanocomplexes. The samples were diluted with distilled water (the pH of the distilled water was adjusted according to the pH of the samples), and the average volumetric diameter was applied for the determination of the average particle size. X-ray diffraction (XRD, GBC MMA instrument) in the range of 2θ = 10 − 70° was applied for the characterization of the crystallinity of the materials. In order to study the thermal changes of nanofibers before and after the introduction of BA, TGA was used to plot the changes in the samples weight against temperature. The samples were studied by a TAQ50 instrument and heated with the rate of 10 °C/min under argon gas from 25 °C to 840 °C. In order to measure the mechanical properties, samples with dimensions of 50 × 10 mm 2 and a thickness of 0.69 nm were prepared. It should be mentioned that the thickness of the fibers increases obviously by increasing boron content. Then, the mechanical properties were measured using the Instron instrument, using the weight of 10 N at a speed of 10 mm/min. The number of replications for each experiment was 5 samples, and the averages of the results were reported as strength and elongation of the sample.

Investigation of the SEM of the Nanofibers
As shown in Figure 1a, at the concentration of 5% (w/v), due to the low viscosity of the polymer solution, the fibers are not formed, and the polymer particles are spread on the collector. This phenomenon can be explained by the fact that the polymer chains are not able to accumulate and form a fibrous structure, due to the low concentration of the polymer solution. As a result, the spherical particles of the polymer are charged, accelerated, and thrown toward the collector [28].  As illustrated in Figure 1b, by increasing the concentration of the polymer solution to 12% (w/v), a desired electrospinning condition is obtained, and smooth and knotted fibers with an average diameter of 259 ± 64 nm are also obtained (Figure 2a). By increasing the concentration of the solution to 20% (w/v), it is observed that the diameter of fibers increases significantly (Figure 1c), and the average diameter of the fibers reaches 1400 ± 482 nm (Figure 2b). To justify this, it can be said that by increasing the concentration of the polymer solution, the viscosity of the solution increases and the polymer projectile in the electric field between two electrodes undergoes fewer rotations and bends; consequently, the polymer is less stretched, and thus, the diameter of the fibers increases [29]. Figure 3 shows an average diameter of the unmodified nanofibers at different concentrations of PANMM.
to 12% (w/v), a desired electrospinning condition is obtained, and smooth and knotted fibers with an average diameter of 259 ± 64 nm are also obtained (Figure 2a). By increasing the concentration of the solution to 20% (w/v), it is observed that the diameter of fibers increases significantly (Figure 1c), and the average diameter of the fibers reaches 1400 ± 482 nm (Figure 2b). To justify this, it can be said that by increasing the concentration of the polymer solution, the viscosity of the solution increases and the polymer projectile in the electric field between two electrodes undergoes fewer rotations and bends; consequently, the polymer is less stretched, and thus, the diameter of the fibers increases [29]. Figure 3 shows an average diameter of the unmodified nanofibers at different concentrations of PANMM.   to 12% (w/v), a desired electrospinning condition is obtained, and smooth and knotted fibers with an average diameter of 259 ± 64 nm are also obtained (Figure 2a). By increasing the concentration of the solution to 20% (w/v), it is observed that the diameter of fibers increases significantly (Figure 1c), and the average diameter of the fibers reaches 1400 ± 482 nm (Figure 2b). To justify this, it can be said that by increasing the concentration of the polymer solution, the viscosity of the solution increases and the polymer projectile in the electric field between two electrodes undergoes fewer rotations and bends; consequently, the polymer is less stretched, and thus, the diameter of the fibers increases [29]. Figure 3 shows an average diameter of the unmodified nanofibers at different concentrations of PANMM.   According to the results obtained from SEM images, the optimal concentration for electrospinning is 12% (w/v) of PANMM. At this concentration, smooth fibers with smaller diameters are formed. According to the studies performed on electrospinning of the PANMM solution, it can be said that under the conditions used in the electrospinning process, this polymer is electrospun well, and suitable fibers at optimal concentrations are produced.
By obtaining the appropriate concentration for the fabrication of PANMM nanofibers, the fabrication of PANMM nanofibers modified with BA was performed. As shown in Figure 1d, in PANMM nanofibers +10% (w/w) of BA, the entry of boron into the polymer structure increases the diameter of the fibers by approximately 100 nm (Figure 2c), and almost smooth fibers, without any depressions on their surface, are produced. By increasing the concentration of boron in the nanofibers (Figure 1d,f), the fibers' average diameter increases from 375 nm (Figure 2c) in PANMM nanofibers + 10% of BA to 430 nm (Figure 2d) in PANMM nanofibers +30% BA, and finally, to 618 nm (Figure 2e) in PANMM nanofibers +50% BA. The trend of increasing the diameter of nanofibers with increasing the concentration of BA is clearly illustrated in Figure 4. The increase in the fibers' diameter is due to the increase in the viscosity of the solution, because by increasing viscosity, the rotations and bends of the electrospray projectile inside the electric field between two electrodes decrease, and the fiber diameter increases due to the reduction in the fibers' elongation [30]. In addition, it can be seen that the distribution of the fibers' diameter increases. The reason is that by increasing the concentration of BA in the electrospinning solution, the charge of the solution increases, and the electric field tension on the polymer projectile in some parts of the field becomes more than in other parts. Therefore, the average diameter of the fibers is smaller.
electrospinning is 12% (w/v) of PANMM. At this concentration, smooth fibers with smaller diameters are formed. According to the studies performed on electrospinning of the PANMM solution, it can be said that under the conditions used in the electrospinning process, this polymer is electrospun well, and suitable fibers at optimal concentrations are produced.
By obtaining the appropriate concentration for the fabrication of PANMM nanofibers, the fabrication of PANMM nanofibers modified with BA was performed. As shown in Figure 1d, in PANMM nanofibers +10% (w/w) of BA, the entry of boron into the polymer structure increases the diameter of the fibers by approximately 100 nm ( Figure  2c), and almost smooth fibers, without any depressions on their surface, are produced. By increasing the concentration of boron in the nanofibers (Figure 1d,f), the fibers' average diameter increases from 375 nm (Figure 2c) in PANMM nanofibers + 10% of BA to 430 nm (Figure 2d) in PANMM nanofibers +30% BA, and finally, to 618 nm (Figure 2e) in PANMM nanofibers +50% BA. The trend of increasing the diameter of nanofibers with increasing the concentration of BA is clearly illustrated in Figure 4. The increase in the fibers' diameter is due to the increase in the viscosity of the solution, because by increasing viscosity, the rotations and bends of the electrospray projectile inside the electric field between two electrodes decrease, and the fiber diameter increases due to the reduction in the fibers' elongation [30]. In addition, it can be seen that the distribution of the fibers' diameter increases. The reason is that by increasing the concentration of BA in the electrospinning solution, the charge of the solution increases, and the electric field tension on the polymer projectile in some parts of the field becomes more than in other parts. Therefore, the average diameter of the fibers is smaller.

Investigation of Chemical Structure of the Nanofibers
In this study, FTIR spectroscopy was applied to detect different chemical groups in the structure of the nanofibers. First, the FTIR spectrum was recorded for pure BA pow-

Investigation of Chemical Structure of the Nanofibers
In this study, FTIR spectroscopy was applied to detect different chemical groups in the structure of the nanofibers. First, the FTIR spectrum was recorded for pure BA powder and PANMM nanofibers. It can be seen from Figure 5 that the peak at 1190 cm −1 is related to the bending of the BOH group, and the relatively strong peak at 1450 cm −1 is also attributed to the bending vibration of the B-O and O-H groups. Another intense peak at the position of 3210 cm −1 can be related to the vibration of the B-O and O-H groups in the BA structure [31]. the peaks at 2938 cm −1 (attributed to stretching in CH, CH2, and CH3 groups), 2245 cm −1 (related to C ≡ N stretching), 2361 cm −1 (related to the presence of CO2), 1732 cm −1 (related to the stretching of the carbonyl group (C = O)), 1452 cm -1 (related to bending CH2), and 1375 cm -1 (associated to bending CH) [32]. The peak in the range of 1000 − 1300 cm −1 is related to the ester group, which confirms that the polymer is a copolymer of acrylonitrile and methyl methacrylate. The FTIR spectra of PANMM nanofibers with different percentages of BA were recorded and compared with the spectra of pure BA and PANMM. As shown in Figure  5, pure PANMM nanofibers do not show any peaks in the range of 3000-4000 cm −1 , which indicates the absence of O-H or B-O groups in its structure. By increasing BA in the structure of PANMM nanofibers, the peak intensity related to B-O and C-H vibrations increases and a strong peak is observed at 3223 cm −1 , which is related to the stretching vibrations of the O-H and B-O groups. There is a weak peak at 2930 cm −1 related to the stretching strength of CH, CH2, and CH3 groups that can also be seen in pure PANMM nanofibers. The intensity of these peaks in BA-modified PANMM nanofibers is also very low. The peak recorded at 1452 cm −1 is attributed to the bending of C-H, which is overlapped with the peaks related to the bending of B-O and O-H, and its intensity increases by increasing the percentage of BA in PANMM nanofibers [33]. It should be noted that the nitrile groups' cyclization is an intramolecular electron transfer reaction. A nucleophilic attack on the carbon atom of an adjacent nitrile group is made by the cyano N atom that carries a partial negative charge owing to the high polarity of the nitrile group, causing the C ≡ N groups conversion to a conjugated C = N structure [34]. A pair of electrons can be accepted by BA (as a typical Lewis acid). Thus, the electron-withdrawing ability of BA may cause the effect of retardation on the cyclization re- The FTIR spectrum of pure PANMM nanofibers is shown in Figure 5. It indicates the peaks at 2938 cm −1 (attributed to stretching in CH, CH 2 , and CH 3 groups), 2245 cm −1 (related to C ≡ N stretching), 2361 cm −1 (related to the presence of CO 2 ), 1732 cm −1 (related to the stretching of the carbonyl group (C = O)), 1452 cm −1 (related to bending CH 2 ), and 1375 cm −1 (associated to bending CH) [32]. The peak in the range of 1000 − 1300 cm −1 is related to the ester group, which confirms that the polymer is a copolymer of acrylonitrile and methyl methacrylate.
The FTIR spectra of PANMM nanofibers with different percentages of BA were recorded and compared with the spectra of pure BA and PANMM. As shown in Figure 5, pure PANMM nanofibers do not show any peaks in the range of 3000-4000 cm −1 , which indicates the absence of O-H or B-O groups in its structure. By increasing BA in the structure of PANMM nanofibers, the peak intensity related to B-O and C-H vibrations increases and a strong peak is observed at 3223 cm −1 , which is related to the stretching vibrations of the O-H and B-O groups. There is a weak peak at 2930 cm −1 related to the stretching strength of CH, CH 2 , and CH 3 groups that can also be seen in pure PANMM nanofibers. The intensity of these peaks in BA-modified PANMM nanofibers is also very low. The peak recorded at 1452 cm −1 is attributed to the bending of C-H, which is overlapped with the peaks related to the bending of B-O and O-H, and its intensity increases by increasing the percentage of BA in PANMM nanofibers [33]. It should be noted that the nitrile groups' cyclization is an intramolecular electron transfer reaction. A nucleophilic attack on the carbon atom of an adjacent nitrile group is made by the cyano N atom that carries a partial negative charge owing to the high polarity of the nitrile group, causing the C ≡ N groups conversion to a conjugated C = N structure [34]. A pair of electrons can be accepted by BA (as a typical Lewis acid). Thus, the electron-withdrawing ability of BA may cause the effect of retardation on the cyclization reaction and the prevention of the electron transfer among nitrile groups. It should be mentioned that BA has an inhibitory role in the cyclization reaction. Proceeding with the cyclization reaction during the stabilization leads to the gradual conversion of the C ≡ N groups to C = N groups [35]. The FTIR spectra show a decrease in the band intensity of the C ≡ N groups. In the meantime, the band at 1445 cm −1 increases. According to the spectra, it is clear that in the modified nanofibers, increasing the concentration of BA does not cause the production of a new peak. Only one peak is removed, and the intensity of other peaks is increased owing to BA. These results are somewhat similar to the results in the spectra obtained from the electrospun nanofibers of organic and natural polymers. When there is no chemical reaction between the two components in the nanofiber structure, the functional groups of both components appear independently. In these cases, the component added to the substrate polymer is actually trapped between the polymer chains and appears separately in the existing nanofibers [36]. The same process is observed in cases where the nanocomposite is produced from a combination of nanoparticles and nanofibers. The nanoparticles that settle on the fibers have a spectrum corresponding to their functional groups and appear without interfering with the spectrum of the functional groups of the substrate polymer nanofibers. The results of FTIR studies show a slight reaction of BA with the substrate polymer.

Investigation of the Thermal Properties of the Nanofibers
TGA was used to study the effect of BA introduced to the nanofibers structure. Figure 6 shows the TGA curve of the pure and modified PANMM nanofibers. The pure nanofibers are decomposed in the temperature range of 312-484 • C, while the nanofibers containing BA are degraded between 298 and 470 • C. These results show that the entry of BA into the PANMM nanofibers' structure reduces the thermal resistance of the nanofibers. The placement of BA molecules between the polymer chains increases the rate of degradation of the polymer, and thermal degradation begins at lower temperature [37,38]. It is also possible that the O-group of ionized BA also attacks the C ≡ N group, converting it to the C-O group. As can be seen in the FTIR spectra, the C ≡ N peaks in pure PANMM nanofibers are partially eliminated, and the intensity of C-O peaks is increased. The results of the TGA confirm the FTIR results.

Investigation of the Structure of BA, PAN Nanofibers and PAN + BA
As shown in Figure 7a, in the XRD pattern of BA powder, a very strong peak is observed at 2θ = 15°, which is related to the tetragonal structure of BA. A peak with lower intensity is observed at 2θ = 28°, which is related to the scattering of light from single BA plates. The XRD pattern of BA powder shows that this compound has a complete crystalline structure [39]. To study the crystal structure of PANMM nanofibers, its XRD pattern was investigated, and the result in Figure 7b shows that PANMM nanofibers have a  intensity is observed at 2θ = 28 • , which is related to the scattering of light from single BA plates. The XRD pattern of BA powder shows that this compound has a complete crystalline structure [39]. To study the crystal structure of PANMM nanofibers, its XRD pattern was investigated, and the result in Figure 7b shows that PANMM nanofibers have a semi-crystalline or amorphous structure, and no strong peaks can be observed in the pattern. In the case of PANMM nanofibers containing BA (Figure 7c), the amorphous pattern of the polymer nanofibers is seen as compared with Figure 7b. The strongest peak of BA powder entirely vanished, and two new peaks were formed in the composite, suggesting a complete reaction or staying of some parts of BA in the amorphous phase, which could not be distinguished by the XRD analysis. It is reasonable to conclude that the oxidized PANMM nanofibers could also be crosslinked by BA. It can also be concluded that BA on the fiber surface has little influence on the free radical cyclization reactions of nitrile groups and obviously retards the stabilization process of PANMM.

Investigation of the Mechanical Strength of the Modified Nanofibers
The mechanical behavior of polymers is expressed by examining the changes in stress to strain, and these changes can be shown in a diagram. Figure 8 shows a graph of the changes in the stress to strain of fibers before and after the introduction of BA. Table 2 shows the changes in mechanical strength of the nanofibers after modification and optimization with BA. Mechanical strength decreases after modification. The amount of this reduction is 14% in modulation and 6% in strength. In addition, the elongation and work of rupture increase to 4% and 10%, respectively, which show a slight reduction in strength due to the reduction in the molecular weight of the polymer and the possible distance between the polymer chains, and also, a reduction in interactions between chains. An increase in length could be due to the sliding of the chains on top of each other [40]. The overall results show that the mechanical properties are maintained to an acceptable level.

Investigation of the Mechanical Strength of the Modified Nanofibers
The mechanical behavior of polymers is expressed by examining the changes in stress to strain, and these changes can be shown in a diagram. Figure 8 shows a graph of the changes in the stress to strain of fibers before and after the introduction of BA. Table 2 shows the changes in mechanical strength of the nanofibers after modification and optimization with BA. Mechanical strength decreases after modification. The amount of this reduction is 14% in modulation and 6% in strength. In addition, the elongation and work of rupture increase to 4% and 10%, respectively, which show a slight reduction in strength due to the reduction in the molecular weight of the polymer and the possible distance between the polymer chains, and also, a reduction in interactions between chains. An increase in length could be due to the sliding of the chains on top of each other [40]. The overall results show that the mechanical properties are maintained to an acceptable level. Sustainability 2021, 13, x FOR PEER REVIEW 11 of 13

Conclusions
The purpose of this research was the fabrication of PANMM nanofibers containing 10 B. The study of the morphology of the nanofibers using SEM revealed that 12% (w/v) of PANMM is the optimal concentration for the electrospinning process, which could fabricate smooth and knotted fibers with an average diameter of 259 ± 64 nm. The XRD pattern of PANMM showed a semi-crystalline or amorphous structure of the nanofibers. The XRD pattern of the nanofibers containing BA showed that the strongest peak of BA powder entirely vanished, and two new peaks were formed in the composite, suggesting a complete reaction or staying of some parts of BA in the amorphous phase, which could not be distinguished by the XRD analysis. Mechanical properties decreased after the modification of PANMM. A 14% reduction in modulation and a 6% reduction in strength were obtained. In addition, the elongation increased to 4%, and the work of rupture increased to 10%. According to the results obtained in this study, it can be said that PANMM nanofibers modified with BA can be a suitable choice for use in protective clothes of power plants and places where there is neutron pollution.

Conclusions
The purpose of this research was the fabrication of PANMM nanofibers containing 10 B. The study of the morphology of the nanofibers using SEM revealed that 12% (w/v) of PANMM is the optimal concentration for the electrospinning process, which could fabricate smooth and knotted fibers with an average diameter of 259 ± 64 nm. The XRD pattern of PANMM showed a semi-crystalline or amorphous structure of the nanofibers. The XRD pattern of the nanofibers containing BA showed that the strongest peak of BA powder entirely vanished, and two new peaks were formed in the composite, suggesting a complete reaction or staying of some parts of BA in the amorphous phase, which could not be distinguished by the XRD analysis. Mechanical properties decreased after the modification of PANMM. A 14% reduction in modulation and a 6% reduction in strength were obtained. In addition, the elongation increased to 4%, and the work of rupture increased to 10%. According to the results obtained in this study, it can be said that PANMM nanofibers modified with BA can be a suitable choice for use in protective clothes of power plants and places where there is neutron pollution.

Data Availability Statement:
The authors declare that all data supporting this study's findings are available within the article.