1. Introduction
Use of polymers in biomedical applications has been continuously growing in recent decades [
1,
2,
3,
4,
5,
6]. These materials are used to restore, replace or activate specific biological response [
7,
8,
9,
10,
11,
12]. Polymers can be combined with other types of biomaterials, such as ceramics, or with other polymers to form a composite with advanced performance [
13,
14,
15,
16,
17,
18].
Polymers include two major subgroups: biostable (i.e., non-resorbable in the body) and bioresorbable (i.e., materials that are completely dissolved and excreted from the body over time) polymers. Aliphatic polyesters, such as polylactide (PLA), polyglycolide (PGA), and their derivatives, are the most widely spread category of the bioresorbable polymers for medical applications [
19,
20,
21,
22,
23,
24]. Aliphatic polyesters are commercially used, for instance, in pins, screws, and plates. The use of bioresorbable fracture fixation plates made of these materials has good potential in musculoskeletal reconstructions due to their unique advantages. In general, they have good biocompatibility. In turn, gradual degradation of the plate’s material over time allows stepwise redistribution of the load-bearing function from the plate back to the bone, thus reducing the risk of stress-shielding and favoring the bone formation, which is important, for example, in the cases of elderly and pediatric patients. After the completion of its function, the plate is entirely resorbed and excreted from the body; thus, the need for the plate removal is eliminated. Moreover, in pediatric applications, bioresorbable bone fixation less hinder the natural growth of the skeleton than their biostable counterparts [
25,
26].
The degradation rate and mechanical properties of aliphatic polyesters are versatile to some extent and can be tailored to a particular application. This is achieved by adjusting, for example, the average molecular mass, ratio of stereoisomers (e.g.,
l- and
d- isomers in PLA) or copolymers (e.g., lactides/glycolides) in the final polymer [
27]. Despite that, the maximum achievable strength and stiffness are insufficient for many load-bearing applications. The thermoplastic nature of polyesters determines their susceptibility to creep under non-critical, but continuous load [
28,
29,
30]. Contouring of polyester plates is possible, but usually requires additional manipulations, such as heating in a hot water bath up to the glass transition temperature (40–60 degrees) [
31,
32]. Moreover, the degradation of a massive bulk of polyester increases the acidity in the surrounding tissues and may lead to adverse tissue reactions [
33,
34,
35].
In this study, an alternative for conventional thermoplastic polyesters for the use in load-bearing fracture fixation applications was suggested—functionalized thermosetting polyesters.
Functionalized thermosetting polyesters have been previously studied from the prospective of tissue engineering [
36,
37,
38,
39]. Based on the preceding research, we proposed a straightforward synthesis route of PLA functionalized with diMethAcrylate (PLAMA). At normal conditions, PLAMA represents a liquid viscous resin. From the widely used acrylic dental restoration materials, such as bisphenol-A-glycidylmethacrylate (bisGMA), the photoinitiation system was adopted [
40,
41,
42]. This allowed curing (i.e., hardening) of PLAMA in situ using the standard dental equipment. Considering the advantages of PLAMA, we proposed a special concept of the in situ curable bioresorbable bioactive load-bearing fiber reinforced composite (FRC) fracture fixation plate. In those plates, PLAMA will be used as the matrix phase of FRC. Fibers made of bioactive glass (BG) [
43,
44,
45,
46,
47,
48] will be used to increase the mechanical properties and provide the bioactive properties for the whole plate to compensate for possible adverse effects caused by the products of the degradation of PLAMA [
49,
50,
51,
52]. The light curing will be used to harden the plate in situ after contouring it against the shape of a bone. The thermosetting character of PLAMA will provide more stable mechanical properties during the bone healing than in thermoplastic polyesters [
28].
The present work is the first stage in the systematic investigation of PLAMA and its application in the concept of the in situ curable bioresorbable bioactive load-bearing FRC fracture fixation plate. Considering the proposed concept, in this study PLAMA was investigated from the standpoints of its chemical and physical properties and the biological safety.
Clinical Concept
The proposed concept FRC fracture fixation plate comprises the matrix phase, the reinforcement phase, and the shell (
Figure 1).
The matrix phase is represented by PLAMA with addition of a photoinitiation agent, which allows curing of the resin in situ using standard dental light-curing equipment.
The reinforcement phase is made of bioresorbable fibers, such as BG fibers. The reinforcement is formed using tailored fiber placement (TFP) technology. In this textile technique, a continuous fiber roving is placed, according to a pattern optimized for a particular application considering stress distribution [
53,
54,
55,
56]. This allows bypassing of the areas for screw holes and minimizes cutting of the reinforcement phase. TFP is widely used in aerospace and automotive industries; however, to the authors’ knowledge, has never been applied for load-bearing implantable devices. The use of TFP in an FRC plate maintains the structural integrity on all steps of the manufacturing process and reduces the need for mechanical processing of the composite.
Finally, the shell of the implant is a film made of a fast-resorbing polymer, such as oxidized cellulose-based materials. It encloses the constituents of the composite together so that the uncured implant can be handled in situ.
Prior to a surgery, the shell containing the reinforcement phase is put onto a fractured bone, contoured against the bone surface, and fixed with screws. Next, the shell is filled with the resin resulting in a pre-impregnated (“prepreg”) composite. Further, the prepreg is cured with light.
The concept is flexible. Thus, the concrete choice of materials for each of the components of the plate may vary, and is defined by the required mechanical and bioactive properties of the plate, provided that matrix-to-fibers adhesion is adequate.
2. Results
2.1. Overview of the Study
The present study comprised four stages (
Figure 2). The goal was to investigate PLAMA from the standpoints of its chemical and physical properties and the biological safety.
In Stage 1, two modifications of PLAMA with different molecular masses (PLAMA-500 and PLAMA-1000) were synthesized in the form of liquid light-curable resins. A basic light curing protocol was applied to obtain hardened polymers. The efficiency of the curing was assessed by the degree of conversion (DC) of double bonds during the cross-linking reaction. In turn, DC was measured by means of Fourier-transform infrared (FTIR) spectroscopy.
In Stage 2, basic mechanical and thermomechanical properties of PLAMA were determined in a standardized tensile test under normal conditions and in the thermomechanical analysis (TMA). Elastic modulus, Poisson’s ratio, ultimate tensile strength (UTS), and the corresponding strain were determined in the tensile test. Glass transition temperature (Tg) and coefficient of thermal expansion (CTE) were found in TMA.
In Stage 3, basic features of the biodegradation behavior of PLAMA were studied in vitro by immersion of PLAMA specimens in simulated body fluid (SBF). The mass changes in the PLAMA specimens, change of the pH value of SBF, and change in the flexural properties of PLAMA specimens (flexural modulus, ultimate flexural strength and strain, strength and strain at break) were analyzed.
In Stage 4, the biocompatibility of the novel polymer was analyzed using osteoblast-like cells seeded on PLAMA specimens. The change of the cells’ morphology was evaluated by fluorescence microscopy. The cells’ proliferation was assessed by measuring the metabolic activity of cells by one of the standardized Water-Soluble Tetrazolium salts -based assays, WST-8.
The materials used in each stage, including the controls, are summarized in
Table 1.
2.2. Stage 1: Preparation and Chemical Characterization
Three groups were used in the Stage (PLAMA-500, PLAMA-1000 and bisGMA). BisGMA served as a control since the functional group, which provides the cross-linking of PLAMA, and the photoinitiation system, which starts the cross-linking reaction, had been adopted from bisGMA. The photoinitiation system consisted of camphorquinone (CQ) and 2-dimethylaminoethyl methacrylate (DMAEMA). The efficiency of the curing protocol and, thus, the cross-linking was assessed by DC of double bonds during the cross-linking reaction.
2.2.1. Visual Characterization of Uncured Resins
Both PLAMA-500 and PLAMA-1000 resins represented transparent colorless viscous liquids. After blending with the photoinitiation system components, the liquids obtained yellow color. Visually, it was impossible to distinguish both PLAMA modifications and bisGMA resins from each other. The cross-linking of the resins resulted in light yellow transparent glassy materials. Whereas cross-linked PLAMA-500 and bisGMA were rigid, PLAMA-1000 was notably more flexible and less elastic when bent, resembling the behavior of a relatively hard elastomer.
2.2.2. Measurement of the Degree of Conversion
Examples of the FTIR spectra used in the measurement of DC are given in
Figure 3. Measured values of DC are presented in
Table 2 and in
Figure 4. Immediately after curing, both PLAMA-500 and PLAMA-1000 had significantly higher DC than bisGMA (128.2% and 132.0% from DC of bisGMA, correspondingly;
p < 0.001 in both cases), whereas there was no significant difference between PLAMAs. Significant post-curing was detected in all groups between days 0 and 1 (108.1% from the value at day 0,
p = 0.007; 106.0%,
p = 0.001, and 126.8%,
p = 0.002 in PLAMA-500, PLAMA-1000, and bisGMA, correspondingly). Between days 1 and 3, significant post-curing occurred in group PLAMA-500 only (103.8% from the value at day 3,
p = 0.041). No further significant post-curing was found in all groups after day 3. On day 28, the difference between DC in groups PLAMA-500 and PLAMA-1000 was insignificant, whereas both groups had DC significantly higher than in bisGMA (111.3% from DC of bisGMA,
p = 0.048 and 113.1% from DC of bisGMA,
p = 0.011, correspondingly).
2.3. Stage 2: Physical Characterization
Four groups of specimens were used in the stage: PLAMA-500, PLAMA-1000, bisGMA, and poly (
l-/
dl-) lactide (PLDL). BisGMA served as a control since it is a thermoset that has a similar cross-linking mechanism as PLAMA, and since it has been successfully studied as a matrix phase of FRC implants for skeletal reconstruction [
58,
59]. PLDL was the second control since it has similar repeating units as PLAMA, but at the same time, it is a thermoplastic.
2.3.1. Tensile Test
The groups PLAMA-500, PLAMA-1000, and bisGMA showed inelastic behavior (
Figure 5). The stress-vs-strain curves of PLAMA-500 (
Figure 5A) demonstrated the most ductile character, i.e., had strain softening before the break point. PLAMA-1000 had a flat curve resembling that of elastomers (
Figure 5B), which was in line with subjective observations. The shape of the curves of BisGMA (
Figure 5C) were similar to those of PLAMA-500, but demonstrated brittle fracture.
Contrary to expectations, the group PLDL demonstrated extremely brittle behavior (
Figure 5D) with low strength. In three out of five specimens, fracture occurred before the onset of the nonlinear region of the stress-vs-strain curve; in the other two, the proportional limit was barely passed. Supposedly, the applied manufacturing method (vacuum molding by melting granules directly in a mold) was not appropriate for obtaining maximum possible mechanical properties; however, other methods were not feasible for our group at that moment.
Compared to bisGMA (
Table 3,
Figure 6A), the modulus of PLAMA-500 was insignificantly lower, whereas significantly higher than in PLAMA-1000 (83.9% of the bisGMA value for PLAMA-500 and 23.1%,
p < 0.001 for PLAMA-1000). The modulus of PLDL was significantly higher than that of bisGMA (129.4% of bisGMA,
p = 0.015).
Poisson’s ratio (
Table 3,
Figure 6B) of PLAMA-1000 was significantly higher than that of PLAMA-500 (93.1% of bisGMA,
p = 0.018), bisGMA (
p = 0.035), and PLDL (134.5% of the bisGMA value;
p < 0.001). Differences in other pairs were insignificant. In all groups, the oscillations of the measured Poisson’s ratio value were uniformly decreasing with the growth of strain (
Figure 7). In PLAMA-500 and bisGMA, the shapes of the Poisson’s ratio curves were similar, with slightly increasing average value (
Figure 7A,C), while in a more elastomeric PLAMA-1000 there was an opposite tendency (
Figure 7B). In PLDL, a barely seen decrease of the curve was detected (
Figure 7D).
UTS was significantly different in all materials (
Table 3,
Figure 6C) with
p < 0.001 in all pairs. BisGMA demonstrated the highest strength, whereas UTS of PLAMA-500 was 81.4% of bisGMA, in PLDL it was 62.2% and 16.6% in PLAMA-1000. In bisGMA and PLAMA-1000, UTS point corresponded to the break point on the engineering stress-vs-strain curve. In PLAMA-500, UTS corresponded to the highest point on the curve with some decline of that afterwards.
Ranking by strain at UTS was reversal with respect to the ranking by UTS itself (
Table 3,
Figure 6D). In PLAMA-500, this value was 117.7% from bisGMA, 112.8% of bisGMA in PLAMA-1000, and 36.1% of bisGMA in PLDL. Only strain value of PLDL was significantly different from the other groups (
p < 0.001 in all pairs); between other groups, the difference was insignificant.
2.3.2. Thermomechanical Analysis
The shapes of the thermograms obtained in the single cycle TMA were in line with the expectation for, correspondingly, the thermoset groups (PLAMA-500, PLAMA-1000, and bisGMA;
Figure 8A–C) and the thermoplastic group (PLDL;
Figure 8D). The glass transition point (
Tg) was clearly detected in all materials (
Table 4).
In the multicyclic TMA, the resulting curves showed some progressive contraction of the specimens on each cycle (
Figure 9). The numerical results averaged for the three full cycles were in line with the corresponding values measured in the single heating cycle TMA (
Table 5).
2.4. Stage 3: SBF Immersion Test
2.4.1. Visual Characterization
The specimens from the group PLAMA-500 had no apparent signs of degradation after 84 days. On the contrary, specimens from the PLAMA-1000 group had cavities within the bulk material, as well as some spots of corrosion on the surface.
2.4.2. Mass Changes in Specimens
Before the immersion, the difference in average mass of specimens between the two groups was insignificant (
Table 6,
Figure 10A). After drying of the specimens removed from SBF, the average mass of PLAMA-1000 was significantly lower than that of PLAMA-500 (92.2% of the PLAMA-1000 mass,
p < 0.001;
Figure 10B). Mass losses within the groups were significant in both cases (97.0% of the initial value,
p = 0.008 and 90.2%,
p < 0.001 in PLAMA-500, and PLAMA-1000, correspondingly;
Figure 10C).
2.4.3. Changes in pH Value of SBF
Measurements of the pH value of SBF taken after the immersion test were compared by one sample
t test with the pH value measured in the fresh SBF (
Table 7). The temperature at which all measurements were done was slightly lower than the temperature during the test (33 ± 0.5 °C). The average pH value in the group PLAMA-1000 was significantly lower than in PLAMA-500 (95.7% of the PLAMA-500 value;
p < 0.001;
Figure 11A). Significant drop compared with the initial level of the fresh SBF was detected also in the group PLAMA-1000 (95.9% of the initial value,
p < 0.001;
Figure 11B) while no drop was observed in PLAMA-500.
2.4.4. Changes in the Flexural Properties of Materials
Numerical results of the three-point bending test are summarized in
Table 8. The test demonstrated different flexural behavior of the two modifications of PLAMA in both time points, which, in general, was in line with the behavior of the corresponding materials detected in the tensile tests (
Figure 12A,B). Both materials exhibited inelastic response; PLAMA-500 specimens had a softening portion of stress-strain curves (
Figure 12A). For dry PLAMA-1000, in the conditions of the experimental setup, a break point was not obtained in two out of five cases due to the flexibility of the material (
Figure 12B). After the immersion, both materials became more brittle, and all PLAMA-1000 specimens reached a break point (
Figure 12D).
At both time points, PLAMA-1000 was significantly less stiff than PLAMA-500 (13.5% and 19.5% of PLAMA-500, correspondingly) with
p < 0.001 (
Figure 13A,B). After the immersion, the stiffness within both groups significantly increased (112.8% and 162.2% from the initial value in PLAMA-500 and in PLAMA-1000, correspondingly; both
p < 0.001;
Figure 13C). The ultimate flexural strength at both time points was significantly lower in PLAMA-1000 than in PLAMA-500 (21.3% and 21.4% from PLAMA-500, correspondingly; both
p < 0.001;
Figure 13D,E). After the test, the strength increased within both groups with
p = 0.002 for PLAMA-500 (111.6% from the initial value) and
p = 0.049 for PLAMA-1000 (112.2% from the initial value;
Figure 13F).
At both time points, PLAMA-1000 was significantly more flexible than PLAMA-500 (strain at break was 171.2% of that in PLAMA-500,
p < 0.001 and 128.2%,
p = 0.017, correspondingly;
Figure 14A,B). After the immersion, both materials became less flexible than in their initial condition (strain at break was 82.6% of the initial value,
p = 0.013 for PLAMA-500 and 61.9%,
p < 0.001 for PLAMA-1000;
Figure 14C).
The ultimate flexural strength and the stress at break were not equal in dry PLAMA-500. After the immersion, the material became more brittle, and both points coincided. Thus, the stress at break significantly increased (113.8% of the initial value,
p = 0.004;
Figure 14D) while the corresponding strain decreased (68.4% of the initial value,
p = 0.009;
Figure 14E).
2.5. Stage 4: Biocompatibility Evaluation
Four groups of specimens were prepared: PLAMA-500, PLAMA-1000, PLDL, and stainless steel (SS). PLDL was used as a control since it has similar degradation mechanism as PLAMA and, thus, may have similar effect on the surrounding tissues. SS was used as the second control as a typical bioinert implantable orthopedic material.
2.5.1. Cell Morphology Test
At all time points, angular shaped cells having bundles of actin filaments (stress fibers) were found on specimens in each group (
Figure 15,
Figure 16 and
Figure 17).
No substantial variations in the surface area were found among different groups at all time points (
Table 9,
Figure 18). Within the groups, only in PLAMA-500, a significant increase was detected between the time points 4 and 8 h (155.2% of the initial value,
p = 0.015); by 24 h this rise was insignificantly compensated.
Similarly, the aspect ratio did not vary significantly among the groups (
Table 10,
Figure 19). Only at the time point 8 h, statistical analysis confirmed a significant difference between PLAMA-1000 and PLDL (194.1% of the PLDL value,
p = 0.020). Within the groups of the novel polymer, some tendency of the aspect ratio to increase over time, i.e., a tendency to a more elongate shape of a cell, was observed. However, these changes were insignificant; in PLDL, there was a significant drop between 4 h and 8 h (70.8% of the initial value;
p = 0.015), which was compensated by 24 h (147.1% of the value at 8 h,
p = 0.017).
2.5.2. Cell Viability Test
Absorbance at 450 nm measured in the cell viability test was proportional to the amount of living cells in a well. At the initial point, absorbance was significantly different only in PLAMA-1000 compared to PLDL (53.4% of the control PLDL value,
p = 0.007). At 96 h point, absorbance in PLAMA-500 (74.2% of the PLDL value) was significantly lower than in the SS group (146.1% of PLDL,
p = 0.022); absorbance in PLAMA-1000 was significantly lower than in PLDL (52.9% of PLDL,
p = 0.023) and in SS (
p < 0.001). Statistically significant growth of absorbance and, thus, of the amount of living cells was detected in all groups of materials (170.4% of the initial value,
p = 0.029 for PLAMA-500; 133.5%,
p = 0.020 for PLAMA-1000; 134.7%,
p = 0.015 for PLDL; 307.8%,
p < 0.001 for SS;
Table 11,
Figure 20C).
3. Discussion
In this study, a concept of the in situ curable bioresorbable bioactive load-bearing FRC plate for musculoskeletal reconstruction was proposed. A concept plate possesses the advantages of a less-rigid bioresorbable fixation plate, and at the same time, can be contoured to bone as a conventional metal plate. As the first milestone in the development of the concept, a candidate light-curable bioresorbable polymer for the use as the matrix phase of the composite, named PLAMA, was synthesized. In a combination of pilot experiments, its basic chemical and physical properties and the biological safety were investigated. The results of the study showed potential of PLAMA for the intended applications.
Introduction of a new treatment solution into the real medical practice requires optimal functioning of it from the standpoints of the biological safety and biomechanical efficiency, whereas the production costs remain reasonable. We believe that the selected format of a pilot overview study is highly important and useful for planning of deeper investigations of particular aspects of the proposed concept. This format limited, to some extent, the time frames and group sizes. Particularly, a limitation of this study was the small sample size in TMA, which did not allow performing statistical tests on the corresponding results. However, we consider that the obtained results gave the general preliminary understanding of the basic chemical and physical properties and the biological safety of PLAMA. In future studies, the number of specimens in each experiment should provide the possibility to perform necessary statistical tests.
Beside the major requirements of the biological safety and efficiency, in the choice of the composition of a polymer, we aimed at the simplicity, reproducibility, and minimization of the costs of the synthesis process. Hence, a straightforward route applying commercially available PLA diols was employed to prepare the basic oligomer mixtures and, consequently, light-curable resins. Thermosetting polyester oligomers have been previously obtained by functionalization of polyester polyols with unsaturated methacrylate [
36,
37,
39,
60], acrylate [
38], or fumarate [
61] groups. In the present study, the methacrylate group, used in approved dental and orthopedic materials, such as bisGMA or polymethyl methacrylate (PMMA), was chosen for the functionalization of PLA. The efficiency of the curing and, thus, the formation of cross-links between functional groups, measured by DC, in turn, largely depends on the composition of the photoinitiation system and the selected light curing protocol and strongly affects the physical properties of the cured polymers [
62,
63]. For PLAMA, a combination of CQ and DMAEMA was selected as a photoinitiation system. That combination is also widely used in dental polymers, such as bisGMA, and provides effective cross-linking reaction [
40,
41,
42]. Moreover, it has been shown that the effectiveness of the cross-linking in FRC based on dimethacrylic matrix with CQ/DMAEMA photoinitiation system is not significantly affected by the presence of bone tissues and blood [
64], which is important for the suggested plate concept. Additionally, a wide range of already existing and easily available light-curing equipment can be used to cure a plate in situ. It is worthy of note that the DC obtained in the present study for PLAMA was higher than that in the prototype dimethacrylic resin bisGMA. In turn, among the values of DC for bisGMA found in the literature [
40,
65,
66,
67], the highest DC (80.6% on day 7 after curing) was obtained exactly with CQ/DMAEMA photoinitiation system.
Preparation of two modifications of PLAMA from the precursor diols with different molecular masses (500 and 1000 Da) allowed observation of the change in the properties as a function of the molecular mass of the polymer. Analogously to the observation found in the literature [
39], all experiments conducted in the study showed significant difference in most of the properties between PLAMA-500 and PLAMA-1000. Supposedly, by mixing of the diols in different proportions, the average molecular mass of the obtained PLAMA can be gradually altered in between the two initial masses of the applied diols. This can be used to smoothly adjust the properties of PLAMA, and, therefore, the mechanical and biodegradation properties of the whole plate can be tailored according to a particular clinical application and the corresponding demands of a surgeon. For example, the mechanical properties of PLAMA-500 were significantly higher than that of PLAMA-1000. On the other hand, the degradation rate, which can be indirectly assessed by the mass losses in polymer specimens and the effect on the pH value of SBF after the immersion test, was significantly higher in PLAMA-1000. Both observations might be attributed to the opposite effects of one phenomenon: the increase in the polymer’s crosslinks density and the corresponding decrease in the chain length leads to higher stiffness and strength [
68], while a lower crosslinks density and a higher chain length results in faster degradation [
68,
69]. It should be noted that only the starting degradation of the two PLAMA modifications was examined in the framework of the present study. Further experiments are needed to investigate the period of complete degradation.
In terms of the mechanical performance of the novel polymer, the highest stiffness and strength values shown by PLAMA-500 were close to those of bisGMA, which, in turn, has been studied in vivo as a matrix phase in load-bearing composite implants reinforced with conventional E-glass fibers [
58,
59]. Thus, one may expect sufficient mechanical performance from PLAMA-based FRCs for load-bearing applications. Provided that the experimental data for the reinforcing fibers of FRC are available, the data achieved in the mechanical testing of PLAMA may serve for the preliminary simulation of the mechanical behavior of novel FRC implants by means of finite element modelling (FEM).
From the standpoint of the biological safety, two main aspects related to the chemical structure of PLAMA should be taken into account. First, the main mechanism of the degradation of PLAMA in the body is provided by the cleavage of the bonds between repeating LA units and release of those into surrounding fluids and tissues similarly to the degradation of conventional PLA [
68]. This leads to a drop of the pH value of the fluids [
70,
71,
72]. Possible reactions of the organism to the increased acidity are well documented and may lead to the formation of osteolytic zones in the damaged bone [
33,
34,
35]. Nevertheless, the in vitro biocompatibility evaluation conducted within the present study showed the significant proliferation of osteoblast-like MG-63 cells in the presence of PLAMA. This cell line is widely used in biocompatibility studies of materials for orthopedic applications [
73,
74,
75]. In the present study, angular shape and formation of stress fibers in the cells were visually detected, which is important for confirmation of normal morphogenesis, adhesion, and migration of cells. The aspect ratio and the cells’ surface area in all groups, including the control stainless steel and PLDL groups did not differ significantly. Thus, one may conclude that PLAMA did not affect the morphology of cells differently from the conventional materials. In general, the present study confirmed that normal functioning and development of cells in the presence of PLAMA was possible in vitro. Together with similar cytotoxicity experiments reported for analogous PLA-based cross-linkable resins studied from the prospective of tissue engineering [
36,
37,
38], the biocompatibility of PLAMA looks promising. Nevertheless, more detailed studies, such as analysis of the degradation products and the correlation of their release with the results of in vitro experiments, are desirable.
Nevertheless, in the next step of the research of the proposed concept, BG fibers will be used [
43,
44,
45,
46,
47,
48] as the reinforcement phase of a bioresorbable bioactive FRC. Being in contact with body fluids, BG is capable of increasing the fluids’ pH value due to the release of alkali ions through a cascade of chemical reactions [
76,
77]. This would buffer the expected local drop in pH value caused by acidic degrading polymers such as PLAMA.
In addition to the pH compensatory effect, the use of BG as a bioactive agent can stimulate bone growth [
49,
50,
51,
52] and provide antimicrobial effect [
78,
79]. Hence, BG and other bioactive ceramics have been logically scrutinized as a bioactive filler within a polyester matrix in composite implants and scaffolds in multiple studies [
76,
80,
81,
82,
83,
84,
85,
86]. Thus, in the suggested novel plate concept, the reinforcement phase made of BG fibers will provide both load-bearing and bioactive functions. By varying the composition of BG, amount, and distribution of fibers, the degradation rate and the bioactivity of the reinforcement phase can be adjusted in accordance with the clinical requirements providing the favorable biological response during all steps of the healing process.
The second aspect of the biological safety of PLAMA is the effect of the functional methacrylate groups presented on the ends of the molecular chains. Structural acrylate-based biomaterials have been in clinical practice for decades since the introduction of PMMA in the middle of the 20th century. Therefore, the adverse effects of acrylates are well studied in dentistry and orthopedics and include skin allergic reactions [
87,
88,
89,
90], cytotoxicity of acrylate free radicals [
91], inflammatory reaction, and osteolysis caused by wearing particles of a bulk acrylate [
92,
93,
94]. However, acrylates are still in demand, and studies on novel acrylate-based biomaterials are still being reported [
95,
96,
97]. Acrylic materials used for decades in orthopedic and dental restoration, such as PMMA and bisGMA, have even been used in such sensitive applications as cranial implants [
98,
99,
100].