3.1. Characterization of PVA Fibers
As a result of the strong hydrogen bonding existing among PVA chains, the melting temperature of PVA was very close to its decomposition temperature, and the melt spinning of PVA was still challenged. A practical method based on intermolecular complexation was proposed to realize the thermoplastic processing of PVA [
14,
15,
16]. Water as a strong polar molecule was introduced to realize the sufficiently stable melt spinning [
17]. The plasticization is reflected in
Figure 3a; the neat PVA exhibited two characteristic peaks at 2θ = 19.5° and 22.5° corresponding to the (110) and (200) reflections as the main crystalline range, respectively. Due to the excellent plasticization effect of water for PVA, the visible reduction in the main crystalline range, specifically the reduction in (110) reflection and the disappeared (200) reflection, was shown in the water-plasticized PVA [
18,
19]. The hydrogen bond changes between PVA molecules can be seen from
Figure 3b. There were a large number of hydrogen bonds among PVA chains, which made the hydroxyl vibration peak move to a lower wavenumber at 3349.8 cm
−1. With the addition of water, water molecules and the hydroxyl group of PVA reconstructed the hydrogen bond, destroying the hydrogen bond of the PVA molecule, causing the hydroxyl vibration peak to move to a higher wavenumber [
13], located at 3432.6 cm
−1. Based on the method of molecular complexation and plasticization, the thermal processing of PVA was realized.
It is well known that the cross-section is typically enlarged by the extrude swell during melt spinning, and the profiled cross-sectional shapes are changed from the original capillary shapes to circular shapes due to the surface tension of the polymer melt. The triangular PVA fibers were successfully prepared by adjusting the melt-spinning parameters, such as spinning speed and cooling speed. The cross-section morphology of triangular fiber with different draw ratios is shown in
Figure 4. The as-spun fibers basically maintained the cross-sectional morphology of the original spinneret, and had a compact structure without defects such as bubbles and micropores. As the draw ratio increased, the fibers became slender, and the fiber still maintained a good triangular shape. There were no defects found in the fibers, showing that hot drawing did not cause defects in the fibers.
It is noted that
Figure 4b–d has rough edges on the cross-section of fibers, because fiber bundles were fixed and then cut off in a vertical axial direction when making the sample of fiber section for SEM observation. The rough edges were caused by cutting during sample preparation, which had no great relationship with the sample itself. Compared with the equivalent circular cross-section fibers, triangular PVA fibers had a higher specific surface. Controlling the hot-drawing process, the mechanical properties of the fiber could be effectively improved while ensuring the characteristic triangular cross-section, and the high-performance triangular PVA fibers could be prepared.
The TG and DSC curves of triangular PVA fibers with different draw ratios are shown in
Figure 5. From the TG curves, it could be seen that the mass of as-spun fibers decreased with the increase in temperature, and the mass reduction to 90% at 130 °C was mainly the evaporation of plasticizer water. The water content of the as-spun fiber was higher than those of the stretched fibers, and with the fiber draw ratios increasing, the evaporation of water decreased obviously, because some of the water had been evaporated during the hot-drawing process. DSC curves also confirmed the above results. The enthalpy of water evaporation of the stretched fibers obviously decreased with the increase in draw ratio. The melt enthalpy of the PVA fibers increased obviously after hot-drawing, which indicated the amorphous region of profiled PVA fibers decreased and the crystalline region was more complete.
The characteristic diffraction peak at 2θ = 19.5°(101) of the stretched fibers was obviously sharper and stronger than that of the as-spun fiber, and some new crystal diffraction peaks appeared, such as diffraction peaks at 2θ = 11.0°(100), 15.8°(001) and 22.3°(200), as shown in
Figure 6a. Hot drawing made the arrangement of PVA molecular chains more regular, resulting in more perfect crystallization. The crystallinity of the fibers was quantitatively characterized by calculation. The crystallinity of as-spun triangle PVA fibers was 34.5%. The hot drawing increased the crystallinity of the fibers significantly. When it was stretched seven times, the crystallinity of the fibers was as high as 79%. During the hot-drawing process, a large amount of water evaporated, and the hydroxyl groups of PVA, originally combined with water to form hydrogen bonds, were released. The random PVA molecular chains stretched in the stretching direction during hot-drawing, and then hydrogen bonds were rebuilt, leading to the high regularity of PVA molecular chains and the crystallinity of fibers [
13].
The orientation and crystallization of macromolecules significantly affected the mechanical properties of the fibers. The elongation at break of as-spun triangular PVA fibers was 419%, as shown in
Figure 7b, indicating the potential of fibers for high ratio drawing. The as-spun PVA fibers contained more water that could form hydrogen bonds with PVA, which weakened the intra- and inter-molecular hydrogen bonds of PVA and caused PVA chains to move more easily under the action of forces, showing a larger elongation at break. After hot drawing, the tensile strength of PVA triangular fibers increased and the elongation at break decreased significantly. The tensile strength of PVA triangular fibers increased from 0.30 to 4.22 cN/dtex, and the elongation at break decreased from 419.0 to 14.7%. The improvement in the mechanical properties of PVA fibers was attributed to the hot drawing, which caused PVA chains to be arranged orderly along the stretching direction, and the crystal and orientation texture of PVA fibers tended to be perfect, thus increasing the tensile strength of PVA fibers. In this way, the PVA triangular fibers with good tensile strength were successfully prepared.
3.2. Characterization of PVA/EP Composites
Strength is the ability of a material to resist damage under external forces and a tensile test could show the strength of a material. The PVA triangular fibers with a draw ratio of seven times were used to reinforce and toughen epoxy resin. Circular PVA fibers with similar tensile strength reinforced and toughened epoxy composites and pure epoxy resin were prepared and compared with PVA triangular fibers/epoxy composites. The mechanical strength averages of composites are shown in
Table 1 and the tensile stress–strain curves of EP and PVA/EP composites with different fibers are shown in
Figure 8a. It can be observed from the curves that the stress of pure epoxy decreased rapidly after reaching the highest point during the stretching process, and the test bars broke directly. However, the fiber-reinforced and toughened epoxy composites had an obvious plastic deformation stage during the stretching process. The tensile strength of the composites was slightly stronger than that of the epoxy resin, while the tensile strength of the composites with circular fibers slightly lower. The elongation at break of fiber-reinforced and toughened epoxy materials with different cross-sections was greatly increased. EP resin exhibited elastic deformation while PVA fibers/EP composites exhibited plastic deformation during tensile test. The mechanical properties of composite materials were largely affected by the reinforcing phase. Compared with circular PVA fibers, triangular PVA fibers had larger specific surface area and larger contact surface with epoxy resin, causing stronger tensile strength of composites.
Stiffness is the ability of a material to resist elastic deformation under stress and a flexural test may indicate the stiffness of the material. The flexure stress–strain curves of EP and PVA/EP composites with different fibers are shown in
Figure 8b. The strain at yield of PVA/EP composites with different cross-sections increased, while the flexure strength of the composites decreased, but the flexure properties of triangular PVA fibers/EP composites were better than that of circular PVA fibers/EP composites. It was worth noting that during the bending test, the composite materials bars could only be bent and could not be crushed, while the pure epoxy resin bars directly bent and broke. The flexural strength was affected by the flexural modulus and flexural strength of each component of the materials, and the compatibility between the components. The modulus difference between fiber and epoxy resin was large, so the strain generated by load was different, which could easily cause the interface damage of composites. The triangle fiber had a large specific surface area and a strong binding force with epoxy resin, so the ability of triangle PVA fibers/EP composite to resist damage was stronger than that of circular PVA fibers/EP composites.
Toughness represents the ability of a material to absorb energy during plastic deformation and fracture and an impact test shows the toughness of the material. The impact properties of EP and PVA/EP composites with different fibers are shown in
Figure 8c. The cross-sections of epoxy resin bars were thicker than those of composites, so the impact absorbing energy of epoxy resin was greater than that of composites. However, the impact strength of the composites was obviously higher than that of epoxy resin, especially the triangular fibers/EP composites. Unlike pure epoxy resin, which was easy to break, the composites were not completely broken after being impacted; only the matrix was cracked and parts of the fiber layers were broken, and a small part of the fiber bundles was still connected compactly. In general, triangular fiber has great potential in strengthening and toughening epoxy due to its unique profiled structure.
In order to clearly understand the distribution of PVA fibers in the epoxy resin matrix, the cross-section structure of the materials was observed via SEM, as shown in
Figure 9. There was no obvious bubble or hole defect in the epoxy matrix, and no gap between the PVA triangular fibers and the epoxy contact surface, indicating the fibers were fully infiltrated in the epoxy solution. The fibers retained their profiled shape during the forming process. The profile structure enabled the fibers to be arranged and closely adhered. Triangular fibers were in contact with each other in a face, forming mechanical anchoring, the fiber interaction force was strong and the stress was more easily transferred between fibers when the materials were stretched. However, there was a clear gap between the PVA circular fibers and the epoxy resin matrix, the circular fibers were in line contact and the friction between the fibers was small. Compared with circular fibers, triangular fibers had a larger specific surface area, which increased the contact area with the epoxy resin matrix and increased the friction, making the fiber difficult to pull out. When the material was damaged, it was more resistant to fracture.
The mechanical properties of composite materials were affected by factors such as fibers and interfaces. Single-fiber pull-out testing (SFPOT) is an important method to evaluate the interface quality of composites. The embedded depth of the fiber in this test was 5 mm. The load–deflection curves of the triangular fibers and circular fibers are shown in
Figure 10. The maximum load of the PVA triangular fibers was 2.64 N, while the maximum load of the circular PVA fibers was 1.24 N. The circular PVA fibers had a high elongation rate. When they were pulled out from the epoxy resin, the fibers deformed seriously and were easy to pull out. This was also the reason for the high elongation at break of the composite materials. Profile degree affected the specific surface area of the fibers. Triangular fibers with high specific surface area increased the contact surface with epoxy resin. In the process of pulling out, the irregular shape of the triangular fibers surface increased the friction and made the fibers difficult to pull out. On the whole, the triangular PVA fibers had good mechanical properties, which ultimately made them more effective in strengthening and toughening epoxy resin.