[picture] | Journal of Renewable Materials | [picture]

DOI: 10.32604/jrm.2022.022996

ARTICLE

The Promoting Effect of Multifunctional Groups on the Thermal and Mechanical Properties of PVC Materials

Mei Wang¹,*, Xinzhu Fan¹, Xianghai Song² and Quan Bu¹,*

1 School of Agricultural Engineering, Jiangsu University, Zhenjiang, 212013, China
2 Institute of the Green Chemistry and Chemical Technology, School of Chemistry and Chemical Engineering, Jiangsu University, Zhenjiang, 212013, China
Corresponding Authors: Mei Wang. Email: 1000004927@ujs.edu.cn; Quan Bu. Email: qbu@ujs.edu.cn
Received: 04 April 2022; Accepted: 06 June 2022

Abstract: The development of PVC materials grafted with mannich base originated from myrcene (P-MAM-g, where the mannich base derived from myrcene is abbreviated as MAM) via green and effective synthetic methods is a good strategy to avoid unacceptable discoloration and deterioration of thermal and mechanical properties caused by autocatalytic dehydrochlorination (DHC) during PVC processing. In this study, MAM with double bonds, amino groups, ester groups, and phospholipid groups was introduced into the chains of PVC to improve the thermal stability of PVC. The experimental results showed that the covalent attachment of MAM to PVC enhanced both the initial and the long-term stability of PVC. The enhanced performance of P-MAM-g compared with unmodified PVC is attributed to the simultaneous introduction of double bonds and amino groups into the PVC structure. The double bonds trapped the unstable chlorine atoms originated from the degradation of the PVC chain and reacted with the labile macromolecular radicals originated from PVC, thus inhibiting the radical degradation of the PVC chain. Furthermore, the amino groups absorbed the HCl produced in the degradation of PVC, inhibiting the adverse effects of HCl. P-MAM-g displayed better intrinsic flexibility and anti-migration ability of organic functional components compared with the control PVC materials. A possible stabilizing mechanism of the P-MAM-g was also presented.

Keywords: Myrcene; poly(vinyl chloride); covalent grafting; self-stabilization

Nomenclature

Term 1: | Interpretation 1
Term 2: | Interpretation 2
e.g.
∅ : | Porosity
s: | Skin factor

1  Introduction

Poly(vinyl chloride) (PVC) has been widely applied in various fields; however, it degrades easily at processing temperatures due to autocatalytic dehydrochlorination (DHC) [1,2]. This degradation occurs because of the elimination of HCl and the production of conjugated unsaturated double bonds [3], which remarkably decreases the color, thermal and mechanical properties [4,5]. Previous studies have shown that adding thermal stabilizers is an effective and practical method to inhibit the degradation of PVC [6].

Metallic soaps, organic tin/lead salts, and nitrogenous compounds have been recently used as thermal stabilizers and color retention reagents for PVC [7–9]. Though lead salts and organic tin can effectively stabilize PVC, the toxicity limits their application in PVC products. CaSt2/ZnSt2 (calcium stearate/zinc stearate) composite heat stabilizers have been extensively investigated attributing to their synergistic effect in stabilizing PVC. However, zinc chloride (ZnCl2) with strong Lewis acidity is formed in the manufacturing process of PVC materials thermally stabilized by CaSt2/ZnSt2, causing an unfavorable “zinc burning” phenomenon [1,10]. Organic thermal stabilizers show great potential attributing to their advantages including high efficiency, low environmental impact, good compatibility, and strong universality. However, existing organic thermal stabilizers fail to inhibit long-term discoloration of PVC and need to be used in conjunction with other thermal stabilizers for further enhancing thermal stability [11].

PVC materials are currently prepared by physically blending thermal stabilizers with PVC, causing uneven dispersion of the thermal stabilizers and the migration of organic functional components [12]. This process deteriorates their thermal stability [13]. Therefore, the development of non-toxic and green, uniformly dispersed and anti-precipitated organic thermal stabilizers is of great significance to the development of thermally stable PVC materials.

In comparison with physical blending, the introduction of organic functional groups into the structure of PVC via chemical grafting is expected to significantly improve the migration resistance abilities and mechanical properties of PVC. For example, Jia et al. [14] prepared cardanol butyl ester mannich base with cardanol and grafted it onto PVC via a substitution reaction. The as-obtained PVC sample displayed good plasticizing and mechanical properties and a migration rate almost of 0. Although PVC materials grafted with organic compounds present improved long-term thermal stability compared with pure PVC, it is still difficult to simultaneously delay “zinc-burning” and inhibit the initial degradation and coloring of PVC materials. For instance, Zhu et al. [15] successfully inhibited the first stage of thermal degradation of PVC by grafting phenol to PVC under microwave irradiation, resulting in improved long-term thermal stability of the PVC. However, the initial color and prolonged long-term thermal stability of the as-prepared PVC products were still not sufficient compared with commercial PVC samples. In addition, the flexibility of the PVC sample was not satisfactory due to the rigid structure of phenol, thus the sample exhibited poor mechanical properties. Therefore, it is still urgent to develop novel organic thermal stabilizers by means of a grafting strategy to further facilitate the initial stability, long-term stability, and mechanical properties of PVC materials.

Recently, it was reported that Ca/Zn stabilizers with multifunctional groups such as amino groups, double bonds, and ester groups were reported to endow PVC with good long-term stability [16,17]. These functional groups can trap the labile chlorine atoms removed from the PVC chain, react with the unstable macromolecular radical of PVC, and act as HCl absorbers at subsequent stages of degradation, demonstrating a significant thermal stabilizing effect on PVC. Thus, PVC samples grafted with organic compounds containing amino groups, double bonds, and ester groups are expected to display enhanced stability and thus improved mechanical properties. Myrcene, an oily liquid, contains conjugated double bonds in its structure and thus is an ideal raw material for the preparation of multifunctional PVC materials. The conjugated double bond of myrcene enables it to react easily with dienophiles via the Diels–Alder reaction to introduce other functional groups into its structure. The as-obtained products from this reaction of myrcene have been widely applied in coatings, epoxy curing agents, and vinyl ester resin [18–20]. Similarly, the introduction of lauraldehyde derivatives into the PVC chains via covalent bonds is a promising choice for constructing self-stabilized PVC polymers.

Accordingly, this study describes the development of a myrcene-based organic thermal stabilizer containing double bonds, amino groups, ester groups, and phospholipid groups in its structure and its application in stabilizing PVC via chemical grafting. A series of MAM grafted PVC samples (P-MAM-g, where the mannich base derived from myrcene is abbreviated as MAM) were successfully prepared by the replacement reaction of the chlorine group in PVC with a mannich base derived from myrcene. To date, there are no reports of PVC materials simultaneously incorporating double bonds, amino groups, ester groups, and phospholipid groups into their structure.

2  Experimental Section

2.1 Materials

Myrcene was purchased from Jiangxi Global Natural Spices Co. (China), containing about 79% of myrcene. Acrolein (98%, Aladdin), diethyl phosphite (99%, Aladdin), dioctyl phthalate (DOP, 98%, Aladdin) diethylenetriamine (99%, Aladdin), pure PVC (suspension grade, S-1000 ZnCl2 (95%, Nanjing Chemical Reagent), sodium chloride (99%, Nanjing Chemical Reagent), sodium bicarbonate (99%, Nanjing Chemical Reagent), anhydrous magnesium sulfate (99%, Nanjing Chemical Reagent), tetrahydrofuran (THF, 99%, Nanjing Chemical Reagent), N,N-dimethyl-formamide (DMF, 99%, Nanjing Chemical Reagent), methanol (99%, Nanjing Chemical Reagent), and n-hexane (97%, Nanjing Chemical Reagent) were used as purchased.

2.2 Synthesis of Myrac Aldehyde (MA)

First, myrcene (55.85 g, 0.410 mol) and zinc chloride (3.41 g, 0.025 mol) were added into 250 mL flask equipped with the magnetic stirrer and reflux condenser. After the temperature was raised to 55°C, acrolein (27.47 g, 0.49 mol) was added drowsily and, maintained the temperature at approximately 55°C. The resulting suspension was aging at 60°C for 6 h. The obtained product was washed by 10% sodium chloride solution, 5% sodium bicarbonate, dried with anhydrous magnesium sulfate and removed the excess acrolein by a rotary evaporator to get a light yellow liquid (MA, Fig. 1).

Figure 1: Preparation of mannich base originated from myrcene (MAM) grafted PVC (PVC-MAM-g)

2.3 Synthesis of Mannich Base Derived from Myrcene (MAM)

First, MA (28.85 g, 0.15 mol) was added dropwise to a flask containing diethylenetriamine (15.48 g, 0.15 mol) solution. The mixture was stirred at 20°C for 2 h and then raised to 90°C. Thereafter, the resulting mixture was raised to 90°C. Then diethyl phosphite (20.72 g, 0.15 mol) was added drop-wise to the above mixture and kept at 90°C for 4 h. After the reaction, the product was raised to 120°C to remove water. Finally, a light-yellow slimy product was obtained (MAM).

2.4 Synthesis of MAM Grafted PVC (P-MAM-g)

A mixture (7 g) of PVC and MAM was dissolved in 80 mL of DMF, the resulted solution was washed with methanol several times and dried in a drybox at 60°C. The obtained product (5 g) was dissolved in THF (60 mL), then poured into a glass dish and dried at room temperature for 2 days to get the self-plasticization PVC materials (P-MAM-g) [21]. All the P-MAM-g (P-MAM-1, P-MAM-2, P-MAM-3, and P-MAM-4) were synthesized by the same reaction conditions as described above, except that the mass ratios of PVC and MAM were 5:1, 5:2, 5:3, 5:4, respectively. Pure PVC and PVC/40DOP [m(PVC):m(DOP) = 2.5] samples were prepared by the same method.

2.5 Molecular Structure Characterization

Fourier transform infrared (FT-IR) spectra were achieved from Nicolet iS10 FT-IR (Nicolet Instrument Crop., USA) infrared spectrophotometer by the KBr disc method.

1H NMR test was performed on a Bruker 400 MHz spectrometer (Bruker, Rheinstetten, Germany). CDCl3 was used as a solvent to dissolve the samples of MA and MAM, respectively. Deuterated dimethyl sulfoxide (DMSO) was used as a solvent to dissolve the samples of PVC P-MAM-2 and P-MAM-4, respectively.

Weight-average molecular weight and dispersity were measured using a gel permeation chromatograph (GPC) made by Waters, USA at 30°C (flow rate: 1 mL min–1, column: mixed PL gel 300 × 718 mm and 25 μm, HPLC-grade DMF as solvent) using. All PVC materials were dissolved in THF solutions to form a concentration of 1∼5 mg mL–1.

2.6 Thermal Stability Analysis

The static thermal aging test was performed according to ISO 305-1990 (E) (Plastics. 1990). The PVC sheet was cut into 20 mm × 20 mm pieces and put in a thermal aging test box at 180°C. The color of the sample was recorded every 5 min, and then the thermal stability of the sample could judge by the degree of color change.

The thermogravimetric analysis (TGA) was also performed by a TA Q600 instrument (NetzschInstrument Crop., Germany). Typically, 4 mg of samples were heated from 40 to 600°C at a heating rate of 10 °C min–1, under nitrogen flow (100 mL min–1).

2.7 Mechanical Properties Analysis

Differential scanning calorimetry (DSC) measurement was measured on a TA Instrument (NETZSCCH DSC 200 PC) in a nitrogen atmosphere. The measurement temperature range is from –50 to 120°C with a heating rate of 20°C min–1. Approximately 5∼10 mg of PVC and self-plasticization PVC materials were weighed and sealed in a 40 μL aluminum crucible and immediately detected using DSC measurement. The DSC data was collected from the first cycle of heating.

Tensile strength and elongation at break were carried out according to the American Society for testing and materials (ASTM D638-03), and recorded on a CMT4303 universal test machine (Sans, China). The cross head speed was 50 mm min–1. The samples used in the tensile test were 0.47 mm thick, 3.98 mm wide and 25 mm long. At least five tests were repeated for each sample.

DMTA Q800 (TA Instruments, USA) was used to analyze the dynamic mechanical behavior of the PVC sample under the tension mode. The oscillatory frequency used in the dynamic test was 1 Hz. The temperature range was within –80–120°C with a temperature rate of 3 °C min–1.

2.8 Migration Properties Analysis

The migration resistance ability of the samples was investigated via the leaching experiment according to the ASTM D5227. Typically, the PVC sample (2 × 2 × 0.45 cm3) with precise mass was immersed in n-hexane and kept at 50°C for 2 h. And PVC sample (2 × 2 × 0.45 cm3) with precise mass was immersed in deionized water and kept at 25°C for 24 h. Subsequently, the above sample was thoroughly washed with deionized water, dried and weight for a second time. Degree of migration (%) = Wbefore−WafterWbefore×100 . Wbefore is the weight of the sample before test. Wafter is the weight of the sample after the test. Besides, the Tg of extracted samples were determined by DSC from –50 to 120°C at a heating rate of 20 °C min–1.

3  Results and Discussion

3.1 Synthesis and Characterization

The structures of the as-prepared products were characterized and confirmed by FT-IR and 1H-NMR spectroscopy. Fig. 2a shows the FT-IR spectra of myrcene, MA, and MAM. After the reaction of myrcene and acrolein, the absorption peaks representing conjugated double bonds (1594 cm−1) and the terminal vinyl group of myrcene (3086 and 1796 cm−1) disappeared. In addition, the resulting product showed the peaks for aldehyde groups (1725 cm−1) and C–H bonds in the hexatomic ring (2706 and 1311 cm−1). The double bond absorption peak (1644 cm−1) was retained, indicating the successful preparation of MA. In the FTIR spectrum of the mannich reaction adduct, the peaks representing aldehyde groups (1725 cm−1) disappeared and the peaks representing P=O, C–N and P–O (1439, 1027 and 950 cm−1) appeared after the reaction of MA, diethyl phosphite and diethylenetriamine, suggesting successful preparation of MAM. A deep insight into the chemical structures of MA and MAM was further obtained by 1H NMR characterization [Fig. 2b]. In comparison with MA, the MAM spectrum showed several new peaks in the approximately 4.5–2.5 ppm range (peaks 11, 12, 14, and 16–19), attributing to the hydrogen in the methylene connected to N or O containing groups such as −CH−NH−, P−O−CH2−, and −NH−CH2−CH2−NH−. This indicates that diethyl phosphite and diethylenetriamine were successfully introduced into the structure of MA. Moreover, other characteristic peaks of MA such as methyl (peaks 1 and 2) and methylene (peaks 3 and 6) were well-preserved. The FT-IR and 1H NMR results demonstrate successful preparation of MAM.

Figure 2: (a) FT-IR spectra of myrcene, MA, and MAM; (b) 1H NMR spectra of MA and MAM

MAM was covalently bonded to PVC via nucleophilic replacing the unstable chlorine atoms of PVC chains. The functional groups of the as-prepared samples were investigated by FT-IR spectroscopy. The peaks at 2977, 2912, 2837, 1668, 1026, 950, and 690 cm−1 (Fig. 3a) were assigned to the C−H (sp), C−H (sp3), C−H (sp2), N−H stretching vibrations, C−N, P−O, and N−H rocking vibrations, respectively. The intensity of the peaks at 1668, 1026, 950, and 690 cm−1 increased with the increasing replacement of chlorine atoms with MAM in PVC. In addition, the intensity of the peaks at approximately 627 cm−1, assigned to the C−Cl stretching vibration of PVC, gradually decreased with increasing replacement of chlorine atoms with MAM, indicating successful preparation of P-MAM-g. The chemical structures of PVC and P-MAM-g were also investigated by 1H NMR. As shown in Fig. 3b, P-MAM-2 and P-MAM-4 show several new peaks in the ranges of 2.0–5.5 ppm (peaks 11, 12, 14, and 16−19) in comparison with PVC. These typical peaks are also be found in MAM, indicating the successful introduction of MAM into the PVC structure. Moreover, the intensity of these signals increased with the increasing displacement of chlorine in the PVC structure, while the intensity of other characteristic peaks such as −CH−Cl (peak 1’) and CH2 (peak 2’) gradually decreased, indicating successful preparation of P-MAM-g.

Figure 3: (a) FT-IR spectra of pure PVC and P-MAM-g; (b) 1H NMR spectra of pure PVC, P-MAM-2, and P-MAM-4

The number average molecular weight (Mn) of the as-prepared P-MAM-g samples was studied by gel permeation chromatography (GPC), as displayed in Fig. S1 and Table S1. The Mn increased from 28,048 to 28,851 g/mol with increasing replacement of chlorine atoms. These results demonstrate that the chlorine atoms in PVC were successfully substituted with mannich base derived from myrcene.

3.2 Thermal Stability Evaluated by Discoloration

In the process of heating treatment, the DHC of PVC unavoidably results in unacceptable discoloration. To comprehensively investigate the thermal stability of the PVC materials described above, the color stability was measured with a thermal aging test at 180°C (Table 1). The pure PVC strips initially exhibited excellent color, but turned dark brown in 5 min, and absolute black within 15 min. This phenomenon is derived from the degradation of pure PVC in the thermal treatment process. During this process, the chloride anions originating from the C–Cl bond breaking can extract protons from the adjacent C–H bond, eliminating HCl from the PVC chains. The loss of HCl forms conjugated unsaturated double bonds sequences, causing the color change of the polymer from white to slight yellow, dark brown, and finally absolute black [22]. The initial color of the P-MAM-g materials was tan or light brown. The thermal aging tests of the P-MAM-g samples show that at 5 min, all four P-MAM-g materials had a tawny brown color, lighter than the dark brown displayed by pure PVC at 5 min. The sample with the smallest change in color was P-MAM-3. Moreover, after 15 min, P-MAM-3 remained dark brown instead of turning completely black, unlike pure PVC or the other P-MAM-g materials. These results indicated that the covalent attachment of MAM to PVC improved the initial and long-term stability of PVC. This phenomenon can potentially be attributed to the double bonds of P-MAM-g, replacing active chlorine atoms and reacting with the unstable macromolecular radical of PVC, thus enhancing stability. In addition, the multiple double bonds of P-MAM-g assisted the formation of stable conjugated polyene compounds, further restraining the deterioration of PVC samples.

3.3 Thermal Stability Evaluated by TGA

The additional insight into the thermal stability and thermal degradation behavior of pure PVC and P-MAM-g was obtained by thermogravimetric analysis (TGA) in an N2 atmosphere. Fig. 4 shows that the thermal decomposition behavior of all PVC materials can be divided into two stages in good agreement with previously reported results [23,24]. The first stage (200–400°C) is mainly attributed to the release of hydrogen chloride leading to the generation of conjugated polyene structures. The second stage (400–560°C) is caused by the formation of aromatic compounds due to the cyclization of conjugated polyene sequences. All the relevant information is listed in Table 2. T5 is the temperature at 5% weight loss, Tmax1 and Tmax2 correspond to the temperatures at the maximum weight loss rate in the first and second degradation stages, respectively, while W300 and W600 are associated with the yields of residue at 300 and 600°C, respectively. The T5 and W600 values of pure PVC were 154.2°C and 10.53%, respectively, while the T5 and W600 values for P-MAM-g were 179.2–194.2°C and 15.44%–16.23%, respectively. Compared to the PVC samples, the grafted PVC samples show higher T5, the maximum weight loss rate of the first degradation, and W600. These results demonstrate that P-MAM-g has enhanced initial and long-term thermal stability compared with pure PVC. Moreover, P-MAM-3 demonstrates enhanced thermal stability among the P-MAM-g materials. These results match those of the thermal aging test at 180°C.

Figure 4: TGA curves of pure PVC and P-MAM-g

3.4 Thermal Stabilization Mechanism of P-MAM-g

Pure PVC sample tends to degrade under the processing temperature of 180°C. A potential degradation mechanism can be described as follows: the chloride anion produced by the C–Cl bond breaking extracts hydrogen from the adjacent C–H bond, eliminating HCl from the PVC chain. The loss of HCl results in the formation of conjugated double bonds sequences, causing the color change of the polymer from white to light yellow, dark brown, and finally completely black. As illustrated in Fig. 5, the generally accepted stabilization mechanism is based on the phenomena of P-MAM-g double bonds acting as radical trap reagents. In addition, the amino groups can absorb HCl to improve the stabilization of P-MAM-g. During the induction period of degradation (i.e., 0, 10, 20, 30, and 40 min), the Cl radicals originated from P-MAM-g degradation react with the double bond of P-MAM-g to form the radical III. Next, III captures the P-MAM-g radicals (I) to produce IV. Subsequently, IV captures the HCl eliminated from PVC. The process of capturing radicals and HCl continues until large amounts of conjugated polyene appear in the P-MAM-g molecules.

Figure 5: Proposed stabilization mechanism of P-MAM-g

3.5 Mechanical Properties

In addition to thermal aging, the thermal DHC of PVC materials can also deteriorate their mechanical properties [25]. The Tg of P-MAM-g was studied by DSC and compared with the Tg of pure PVC and a non-covalent mixture of PVC/40DOP. As displayed in Fig. 6, the Tg values of PVC/40DOP, P-MAM-1, P-MAM-2, P-MAM-3 and P-MAM-4 were 39.2°C, 36.4°C, 32.7°C, 28.5°C, and 33.0°C, respectively, far lower than the Tg value of pure PVC (84.4°C) [17]. P-MAM-g demonstrated an improved plasticization ability in comparison to PVC/40DOP and pure PVC. Grafting ester group, hexatomic ring and longer alkyl chains simultaneously onto PVC decreased the polymer-polymer interaction and enhanced the free volume between polymer molecules, which is helpful for decreasing the Tg of P-MAM-g [26–28]. The above analysis verifies that the introduction of multifunctional mannich base derived from myrcene into PVC is an effective strategy for providing PVC with intrinsic plasticization abilities.

Figure 6: DSC curves of P-MAM-g

The tensile strength of P-MAM-g was characterized to evaluate its mechanical properties. Fig. 7 shows that the tensile strength of P-MAM-g tends to decrease with increasing levels of MAM. This phenomenon may originate from the fact that MAM acts as a lubricant in PVC, weakening the internal friction between the PVC chains. Among the grafted PVC, P-MAM-2 exhibited the largest elongation at break (304.1%), which is 1.54 times higher than that of pure PVC. This may be attributed to the covalent bond between MAM and PVC, which can maintain the uniform and optimal structure of the material under tensile, preventing crack propagation and enabling the molecular chains to extand maximally [29]. These results further indicate that the covalent bond between MAM and PVC plays an important role in obtaining PVC materials with high flexibility and extensibility. This characterization is in strong agreement with the DSC results.

Figure 7: Tensile properties of P-MAM-g

3.6 Migration Resistance Properties

The migration resistance ability is an important criterion for assessing the performance of PVC materials [30] and was investigated via the leaching test in this study according to ASTM procedures. As illustrated in Fig. 8, PVC/40DOP displayed 13.21% and 0.22% of the migration ability of compounds, respectively, indicating its poor anti-migration ability. However, the leaching tests showed that the migration of all P-MAM-g samples was almost negligible, indicating the outstanding anti-migration ability of P-MAM-g ascribed to the covalent bond between PVC and MAM [31]. As shown in Fig. 9, no considerable changes in the Tg of the P-MAM-g were observed, and the Tg values were below 38°C after the leaching experiment. Under the same experimental conditions, the Tg of PVC/40DOP remarkably raised from 39.2 to 49.9°C. Therefore, compared with PVC/40DOP, P-MAM-g films demonstrated improved organic functional component anti-migration ability and retained their flexibility at room temperature.

Figure 8: Weight loss of PVC/40DOP and P-MAM-g migration after the leaching test

Figure 9: Tg of the P-MAM-g before and after leaching test in n-Hexane

4  Conclusion

A series of self-stabilized PVC materials (P-MAM-g) were obtained by replacing chlorine in PVC with a mannich base derived from myrcene. The thermal stability, mechanical properties, and migration resistance ability of P-MAM-g were determined by TGA, thermal aging, DSC, and tensile tests. The thermal aging tests demonstrate that the best-performing P-MAM-3 material showed significantly less discoloration than the pure PVC after 15 min at 180°C, turning brown instead of completely black. In the TGA experiments, the temperature at 5% weight loss was 154.2°C and the residue yield at 600°C was 10.53%, whereas the two parameters for P-MAM-g were in the range 179.2–194.2°C and 15.44%–16.23%. These results demonstrate that covalent attachment of MAM to PVC improved the initial and long-term stability of PVC materials. This enhanced performance was attributed to the grafting of the double bonds and amino groups, that can simultaneously trap PVC radicals and HCl resulting from PVC deterioration onto the architecture of P-MAM-g. The DSC results revealed that P-MAM-g had improved plasticization performance compared with a non-covalent mixture of PVC and DOP. P-MAM-g also demonstrated an improved anti-migration ability of organic functional components compared with PVC/40DOP and retained their flexibility at room temperature. In the tensile tests, P-MAM-2 exhibited the highest elongation at break value (304.08%), 1.54 times higher than that of pure PVC. The tensile experiments further showed that the covalent bond between MAM and PVC plays an important role in obtaining PVC materials with self-stabilization, high flexibility, and stretch ability.

Acknowledgement: This study was financially supported by the National Natural Science Foundation of China (21905117) and the Priority Academic Program Development of Jiangsu Higher Education Institutions (PAPD).

Funding Statement: This work was subsidized for the National Natural Science Foundation of China (21905117) and the Priority Academic Program Development of Jiangsu Higher Education Institutions (PAPD).

Conflicts of Interest: The authors declare that they have no conflicts of interest to report regarding the present study.

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Supporting Information

Figure S1: GPC spectra of pure PVC and of P-MAM-g

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