Grafting of Maleic Anhydride onto Poly(vinylidene fluoride) Using Reactive Extrusion

Poly(vinylidene fluoride) was grafted with maleic anhydride through reactive extrusion by using diisopropyl benzene peroxide as an initiator and 9-vinyl anthracene as a stabilizer. Effects of various parameters on grafting degree were investigated including the amounts of monomer, initiator and stabilizer. The maximum extent of grafting achieved was 0.74%. The graft polymers were characterized using FTIR, water contact angle, thermal, mechanical and XRD studies. Improved hydrophilic and mechanical properties were observed for graft polymers.


Introduction
Fluorinated polymers are niche macromolecules that exhibit unique and remarkable attributes, largely due to the properties of fluorine (including large electronegativity, low polarizability and small van-der-Waals radius (1.32 Å)) and the strong C-F bonds (485 kJ·mol −1 ) [1,2]. As a kind of semi-crystalline fluoropolymer, polyvinylidene fluoride (PVDF) has received wide attention in both academia and industry, as it shows outstandingly high chemical stability to solvents, acids and bases, weather resistance to oxidative and ultraviolet decomposition, as well as excellent ferroelectric, piezoelectric and other unique electrical properties [3][4][5][6][7]. However, PVDF is an inert polymer that lacks the presence of reactive functionality, and therefore shows poor adhesive properties with substrates and inferior compatibility with other polymers; this limits the application of PVDF in technological fields.
Recently, efforts have been made to improve the performance of PVDF by blending PVDF with other polymers/nanomaterials, chemically grafting functional molecules onto PVDF or copolymerizing it with vinylidene fluoride (VDF) and other monomers [8][9][10][11][12][13][14][15][16][17][18][19][20]. Chen et al. improved the interface compatibility between polypropylene (PP) and PVDF by using a styrene-maleic-anhydride copolymer as a compatibilizer [8]. By intermixing PVDF with maleic anhydride (MAH), Ye et al. found that MAH acts as a physical crosslinking point for PVDF macromolecules [9]. Naruke et al. found that the mixing ratio-dependent melting point depression exhibited by polymethyl methacrylate (PMMA)/PVDF blends is due to the size of their interface region, and that the complex thermophysical behavior of the solution-casting blends is caused by the presence of ultrafine PVDF crystals [10]. Tang et al. fabricated antifouling PVDF hollow fiber membranes through a zwitterionic graft copolymerization method [11]. Ameduri et al. summarized 2-trifluoromethacrylic acid, ω-trifluorovinyl and other macromonomers and their potential to react with VDF (including copolymerization kinetics), the properties of the resulting copolymers and their applications in daily life. At the same time, the effect of the crosslinking of this VDF copolymerization with special functions on this kind of fluorinated material is described [12]. Furthermore, the preparation and use of VDF copolymers are summarized [18]. Qiu et al. report the surface modification of PVDF microporous membranes by heat-induced grafting copolymerization with MAH/styrene (St) with a supercritical carbon dioxide (SCCO 2 ) solvent and a carrier agent. SCCO 2 can accelerate the mass transfer of the monomer in the polymer group, and then promote the grafting copolymerization at the membrane surface and in membrane pores. It was shown that significant and permanent hydrophilicity was obtained after grafting SMA and that the SMA-based PVDF membrane surface had excellent biocompatibility [19]. Although the studies of PVDF have gradually deepened, there are still few reports on a simple, fast and scalable approach to graft modified PVDF.
The reactive extrusion process is favorable due to its advantages such as fast reaction, continuous process, low cost and accessibility to industrialization, and has gained considerable interest compared to other grafting methods [21][22][23][24][25]. Iqbal et al. [21] modified low-density polyethylene with MAH by using benzoyl peroxide (BPO) as an initiator in a co-rotating twin-screw extruder. With the increase in BPO and MAH content, the MAH-grafting degree increased first and then decreased when reaching a certain value. Ismail prepared an ethylene-propylene-diene monomer (EPDM)-g-MAH by melting and mixing. The presence of EPDM-g-MAH can enhance interfacial interaction between EPDM matrix and bentonite [22]. Choi et al., fabricated MAH-EPDM grafted MWCNTs by reactive extrusion to enhance interfacial adhesion and mechanical properties of PP/MAH-EPDM composite [23]. Simonetti reported that the functional modified polyamide 6 (PA6) was performed through Michael addition between divinyl phenyl phosphine oxide and piperazine during the melt extrusion process of PA6 [24]. Through introducing silane-grafted lignin into polybutylene adipate-co-terephthalate (PBAT), a network structure between PBAT and modified lignin was formed by the reactive extrusion, which can enhance mechanical and biodegradable properties [25]. Arkema has already marketed PVDF-g-MAH, and patents have been reported for the fluoropolymer grafting method [26].
Herein, PVDF was grafted with MAH through reactive extrusion by using diisopropyl benzene peroxide (DCP) as an initiator and 9-vinyl anthracene (VAN) as a free-radical stabilizer, as shown in Scheme 1. Due to the introduction of an anhydride group of MAH onto the PVDF side chain, PVDF is normalized to improve the hydrophilicity of PVDF and its compatibility with other substances.
Molecules 2023, 28, x FOR PEER REVIEW 2 of 11 fluorinated material is described [12]. Furthermore, the preparation and use of VDF copolymers are summarized [18]. Qiu et al. report the surface modification of PVDF microporous membranes by heat-induced grafting copolymerization with MAH/styrene (St) with a supercritical carbon dioxide (SCCO2) solvent and a carrier agent. SCCO2 can accelerate the mass transfer of the monomer in the polymer group, and then promote the grafting copolymerization at the membrane surface and in membrane pores. It was shown that significant and permanent hydrophilicity was obtained after grafting SMA and that the SMA-based PVDF membrane surface had excellent biocompatibility [19]. Although the studies of PVDF have gradually deepened, there are still few reports on a simple, fast and scalable approach to graft modified PVDF. The reactive extrusion process is favorable due to its advantages such as fast reaction, continuous process, low cost and accessibility to industrialization, and has gained considerable interest compared to other grafting methods [21][22][23][24][25]. Iqbal et al. [21] modified lowdensity polyethylene with MAH by using benzoyl peroxide (BPO) as an initiator in a corotating twin-screw extruder. With the increase in BPO and MAH content, the MAHgrafting degree increased first and then decreased when reaching a certain value. Ismail prepared an ethylene-propylene-diene monomer (EPDM)-g-MAH by melting and mixing. The presence of EPDM-g-MAH can enhance interfacial interaction between EPDM matrix and bentonite [22]. Choi et al., fabricated MAH-EPDM grafted MWCNTs by reactive extrusion to enhance interfacial adhesion and mechanical properties of PP/MAH-EPDM composite [23]. Simonetti reported that the functional modified polyamide 6 (PA6) was performed through Michael addition between divinyl phenyl phosphine oxide and piperazine during the melt extrusion process of PA6 [24]. Through introducing silanegrafted lignin into polybutylene adipate-co-terephthalate (PBAT), a network structure between PBAT and modified lignin was formed by the reactive extrusion, which can enhance mechanical and biodegradable properties [25]. Arkema has already marketed PVDF-g-MAH, and patents have been reported for the fluoropolymer grafting method [26].
Herein, PVDF was grafted with MAH through reactive extrusion by using diisopropyl benzene peroxide (DCP) as an initiator and 9-vinyl anthracene (VAN) as a free-radical stabilizer, as shown in Scheme 1. Due to the introduction of an anhydride group of MAH onto the PVDF side chain, PVDF is normalized to improve the hydrophilicity of PVDF and its compatibility with other substances. Scheme 1. The preparation of PVDF-g-MAH through reactive extrusion.

FTIR Analysis
The FTIR results of pure PVDF, PVDF/MAH and PVDF-g-MAH are shown in Figure  1. For the pure PVDF, the strong absorption bands at 1405 cm −1 and 1175 cm −1 are attributed to the -CH2 deformation vibration and the -CF2 stretching vibration The visible absorption bands at 970 cm −1 , 763 cm −1 and 614 cm −1 are typical characteristics of the PVDF Scheme 1. The preparation of PVDF-g-MAH through reactive extrusion.

FTIR Analysis
The FTIR results of pure PVDF, PVDF/MAH and PVDF-g-MAH are shown in Figure 1. For the pure PVDF, the strong absorption bands at 1405 cm −1 and 1175 cm −1 are attributed to the -CH 2 deformation vibration and the -CF 2 stretching vibration The visible absorption bands at 970 cm −1 , 763 cm −1 and 614 cm −1 are typical characteristics of the PVDF nonpolar α phase [27]. Additionally, the position of PVDF absorption peaks in the PVDF/MAH and PVDF-g-MAH is similar to that of pure PVDF. In contrast to the pure PVDF and PVDF/MAH, two new absorption peaks can be observed at 1852 cm −1 and 1784 cm −1 , corresponding to the symmetric and asymmetric stretching of the two C=O groups in the resulting succinic anhydride group [27]. It therefore indicates that MAH was successfully grafted onto the PVDF molecule chains.
PVDF/MAH and PVDF-g-MAH is similar to that of pure PVDF. In contrast to the pure PVDF and PVDF/MAH, two new absorption peaks can be observed at 1852 cm −1 and 1784 cm −1 , corresponding to the symmetric and asymmetric stretching of the two C=O groups in the resulting succinic anhydride group [27]. It therefore indicates that MAH was successfully grafted onto the PVDF molecule chains.  Figure 2 shows the water contact angles of PVDF, PVDF/MAH and PVDF-g-MAH.

Wetting Properties
Pure PVDF demonstrates hydrophobic properties due to its low surface energy. After blending with MAH containing a hydrophilic group, the hydrophilicity of PVDF exhibits a certain improvement. However, this improvement is limited, which is due to MAH being mostly dissolved during purification. Compared to PVDF/MAH, the hydrophilicity of PVDF-g-MAH-1 has an obvious increase. Moreover, the increase in the VAN content can better promote the grafting MAH onto PVDF, thus improving the hydrophilicity of PVDF more significantly, with the water contact angle dropping down to 57° (PVDF-g-MAH-2). The surface contact angle results further suggest that the preparation of PVDFg-MAH was successful.  Figure 2 shows the water contact angles of PVDF, PVDF/MAH and PVDF-g-MAH.

Wetting Properties
Pure PVDF demonstrates hydrophobic properties due to its low surface energy. After blending with MAH containing a hydrophilic group, the hydrophilicity of PVDF exhibits a certain improvement. However, this improvement is limited, which is due to MAH being mostly dissolved during purification. Compared to PVDF/MAH, the hydrophilicity of PVDF-g-MAH-1 has an obvious increase. Moreover, the increase in the VAN content can better promote the grafting MAH onto PVDF, thus improving the hydrophilicity of PVDF more significantly, with the water contact angle dropping down to 57 • (PVDF-g-MAH-2). The surface contact angle results further suggest that the preparation of PVDF-g-MAH was successful.

Grafting Degree
In order to optimize the conditions for grafting of MAH onto PVDF, a series of contrast experiments were carried out by adjusting the amount of DCP, MAH and VAN. Figure 3 shows the changing trend of MAH-grafting degree under different variables. The effect of initiator concentration on grafting degree is illustrated in Figure 3a. The observed trend is typical for the graft polymerization reaction occurring via chain transfer. The initial increase in the percent grafting is caused by an increase in the concentration of radicals

Grafting Degree
In order to optimize the conditions for grafting of MAH onto PVDF, a series of contrast experiments were carried out by adjusting the amount of DCP, MAH and VAN. Figure 3 Molecules 2023, 28, 2246 4 of 11 shows the changing trend of MAH-grafting degree under different variables. The effect of initiator concentration on grafting degree is illustrated in Figure 3a. The observed trend is typical for the graft polymerization reaction occurring via chain transfer. The initial increase in the percent grafting is caused by an increase in the concentration of radicals formed through the decomposition of the initiator. Thus, the higher the concentration of radicals, the higher the chain transfer to the polymer backbone and the higher the percent grafting. Furthermore, an increase in initiator concentration decreases the average molecular weight of the side chains because of mutual termination reactions. As shown in Figure 3b, increasing the amount of MAH gives rise to an increase in the level of g-MAH, indicating that the content of MAH has a direct connection to the grafting degree. The role of VAN on the grafting degree of MAH onto PVDF is examined. Figure 3c shows that a higher concentration of VAN in the grafting system resulted in an increase in the grafting level. VAN is more resonance stabilized with the aromatic ring, leading to the observed continuous rate of the graft-polymerization reaction that results in an ultimately higher level of grafting. Thus, VAN acts as a promoter for the grafting reaction of MAH via an in situ co-grafting process resulting in a polymer containing highly grafted MAH. The possible grafting route is shown in Scheme 2.

Grafting Degree
In order to optimize the conditions for grafting of MAH onto PVDF, a series of con trast experiments were carried out by adjusting the amount of DCP, MAH and VAN. Fig  ure 3 shows the changing trend of MAH-grafting degree under different variables. Th effect of initiator concentration on grafting degree is illustrated in Figure 3a. The observe trend is typical for the graft polymerization reaction occurring via chain transfer. The in tial increase in the percent grafting is caused by an increase in the concentration of radica formed through the decomposition of the initiator. Thus, the higher the concentration radicals, the higher the chain transfer to the polymer backbone and the higher the percen grafting. Furthermore, an increase in initiator concentration decreases the average mole ular weight of the side chains because of mutual termination reactions. As shown in Fig  ure 3b, increasing the amount of MAH gives rise to an increase in the level of g-MAH indicating that the content of MAH has a direct connection to the grafting degree. The ro of VAN on the grafting degree of MAH onto PVDF is examined. Figure 3c shows that higher concentration of VAN in the grafting system resulted in an increase in the graftin level. VAN is more resonance stabilized with the aromatic ring, leading to the observe continuous rate of the graft-polymerization reaction that results in an ultimately high level of grafting. Thus, VAN acts as a promoter for the grafting reaction of MAH via an situ co-grafting process resulting in a polymer containing highly grafted MAH. The po sible grafting route is shown in Scheme 2.

Rheological Properties of PVDF, PVDF/MAH and PVDF-g-MAH
Usually, small molecules generally act as diluents and plasticizers of polymers [8]. As shown in Figure 4a, the blending of MAH and PVDF reduces the complex viscosity of PVDF. Compared with that of PVDF/MAH, the complex viscosity of PVDF-g-MAH decreases more obviously. As expected, the complex modulus and viscosity modulus are also decreased with the blending of MAH or the grafting of MAH, indicating that MAH has a plasticizing effect on PVDF.

Rheological Properties of PVDF, PVDF/MAH and PVDF-g-MAH
Usually, small molecules generally act as diluents and plasticizers of polymers [8]. As shown in Figure 4a, the blending of MAH and PVDF reduces the complex viscosity of PVDF. Compared with that of PVDF/MAH, the complex viscosity of PVDF-g-MAH decreases more obviously. As expected, the complex modulus and viscosity modulus are also decreased with the blending of MAH or the grafting of MAH, indicating that MAH has a plasticizing effect on PVDF.
Usually, small molecules generally act as diluents and plasticizers of polymers [8]. As shown in Figure 4a, the blending of MAH and PVDF reduces the complex viscosity of PVDF. Compared with that of PVDF/MAH, the complex viscosity of PVDF-g-MAH decreases more obviously. As expected, the complex modulus and viscosity modulus are also decreased with the blending of MAH or the grafting of MAH, indicating that MAH has a plasticizing effect on PVDF.

Mechanical Properties of PVDF, PVDF/MAH and PVDF-g-MAH
The effect of MAH on the mechanical properties was studied using tensile tests. The yield strength and elongation of pure PVDF, PVDF/MAH and PVDF-g-MAH are shown in Figure 5a. Due to the plastic effect of MAH, the addition of MAH gives rise to a slight reduction in the yield strength and modulus. However, the elongation of PVAD/MAH and PVDF-g-MAH increases significantly, especially for PVDF-g-MAH, indicating that the incorporation of MAH improves the ductility of PVDF. As expected, the higher grafting MAH level leads to the higher elongation at break (Figure 5b-d). Moreover, as shown in Figure 5c,d, the elongation rate of PVDF-g-MAH decreased again with the increasing amount of initiator and VAN used. This may be because as the amount of initiator and VAN increases, PVDF tends to break its chains and thus reduces its elongation rate. Figure 6 shows the effect of MAH co-blending with PVDF and MAH-grafted PVDF on the crystallization and melting behavior of PVDF. As can be seen in Figure 6a, MAH has a slight effect on the melting behavior of PVDF. The melting temperature of PVDF-g-MAH or PVDF/MAH varies very little. During the cooling process, the crystallinity was decreased with the addition of MAH (Figure 6b). It is possible that some forces were formed among the grafted chains of PVDF molecules, which affect the movement of the molecular chains. The crystallinity (χ c ) of PVDF in all samples was determined using Equation (1), as follows:

Analysis of the Crystallization and Melting Behavior
Formula (1): ∆H 0 m is the theoretical enthalpy of 100% crystalline polymer matrix (the ∆H 0 m for the PVDF is 104.7 J g −1 ) [28], and ∅ EMPTY is the weight fraction of the PVDF matrix. The results are shown in Table 1.
in Figure 5a. Due to the plastic effect of MAH, the addition of MAH gives rise to a slight reduction in the yield strength and modulus. However, the elongation of PVAD/MAH and PVDF-g-MAH increases significantly, especially for PVDF-g-MAH, indicating that the incorporation of MAH improves the ductility of PVDF. As expected, the higher grafting MAH level leads to the higher elongation at break (Figure 5b-d). Moreover, as shown in Figure 5c,d, the elongation rate of PVDF-g-MAH decreased again with the increasing amount of initiator and VAN used. This may be because as the amount of initiator and VAN increases, PVDF tends to break its chains and thus reduces its elongation rate.  Figure 6 shows the effect of MAH co-blending with PVDF and MAH-grafted PVDF on the crystallization and melting behavior of PVDF. As can be seen in Figure 6a, MAH has a slight effect on the melting behavior of PVDF. The melting temperature of PVDF-g-MAH or PVDF/MAH varies very little. During the cooling process, the crystallinity was decreased with the addition of MAH (Figure 6b). It is possible that some forces were formed among the grafted chains of PVDF molecules, which affect the movement of the molecular chains. The crystallinity (χc) of PVDF in all samples was determined using Equation (1), as follows:

Analysis of the Crystallization and Melting Behavior
(1) Formula (1): ∆ is the theoretical enthalpy of 100% crystalline polymer matrix (the ∆ for the PVDF is 104.7 J g −1 ) [28], and ⌀ is the weight fraction of the PVDF matrix. The results are shown in Table 1.

Thermal Stability
As shown in Figure 7, the thermal stability of PVDF, PVDF/MAH and PVDF-g-MAH was analyzed using TGA under a nitrogen atmosphere. The corresponding data are shown in Table 2. Normally, the initial decomposition temperature of MAH is very low, but pure PVDF has much better thermal stability than MAH [8]. The whole thermal degradation of pure PVDF only has one decomposition process with T10wt% of 444.7 °C, and Tmax of 467.6 °C. For PVDF/MAH or PVDF-g-MAH, the two separate degradation steps in Figure 7 correspond to the degradation of MAH and PVDF, respectively. Depending on the respective thermal stability, the first degradation step is due to the decomposition of MAH, and PVDF is degraded at higher temperatures. In the degradation process of MAH, the weight loss of MAH in PVDF/MAH and PVDF-g-MAH is 2.5 wt% and 5.7 wt%, respectively, which is lower than the added amount.

Thermal Stability
As shown in Figure 7, the thermal stability of PVDF, PVDF/MAH and PVDF-g-MAH was analyzed using TGA under a nitrogen atmosphere. The corresponding data are shown in Table 2. Normally, the initial decomposition temperature of MAH is very low, but pure PVDF has much better thermal stability than MAH [8]. The whole thermal degradation of pure PVDF only has one decomposition process with T 10wt% of 444.7 • C, and T max of 467.6 • C. For PVDF/MAH or PVDF-g-MAH, the two separate degradation steps in Figure 7 correspond to the degradation of MAH and PVDF, respectively. Depending on the respective thermal stability, the first degradation step is due to the decomposition of MAH, and PVDF is degraded at higher temperatures. In the degradation process of MAH, the weight loss of MAH in PVDF/MAH and PVDF-g-MAH is 2.5 wt% and 5.7 wt%, respectively, which is lower than the added amount.
As shown in Figure 7, the thermal stability of PVDF, PVDF/MAH and PVDF-g-MAH was analyzed using TGA under a nitrogen atmosphere. The corresponding data are shown in Table 2. Normally, the initial decomposition temperature of MAH is very low, but pure PVDF has much better thermal stability than MAH [8]. The whole thermal degradation of pure PVDF only has one decomposition process with T10wt% of 444.7 °C, and Tmax of 467.6 °C. For PVDF/MAH or PVDF-g-MAH, the two separate degradation steps in Figure 7 correspond to the degradation of MAH and PVDF, respectively. Depending on the respective thermal stability, the first degradation step is due to the decomposition of MAH, and PVDF is degraded at higher temperatures. In the degradation process of MAH, the weight loss of MAH in PVDF/MAH and PVDF-g-MAH is 2.5 wt% and 5.7 wt%, respectively, which is lower than the added amount.

Analysis of the Crystallization of PVDF, PVDF/MAH and PVDF-g-MAH
PVDF is a semi-crystalline polymer containing α, β, and γ crystal phases. Among them, the α phase is the most common and stable crystal type, which usually crystallizes from the melted PVDF [27]. Figure 8 shows the XRD patterns of PVDF, PVDF/MAH and PVDF-g-MAH. It is found that the peaks at 2θ = 18.5, 19.8, 26.3 and 27.9 are the characteristic diffraction peaks of the α phase crystal assigned to (020), (110), (021) and (100) reflections, respectively, indicating that the α phase plays a dominant role. After blending MAH with PVDF, the crystal peak of PVDF/MAH was significantly enhanced at 2θ = 27.9, suggesting that the blending of MAH can promote the crystal growth in (100) direction. However, the crystal peak of PVDF-g-MAH disappears here, demonstrating that g-MAH shows a different effect for the PVDF crystal growth compared to the blending of MAH.

Analysis of the Crystallization of PVDF, PVDF/MAH and PVDF-g-MAH
PVDF is a semi-crystalline polymer containing α, β, and γ crystal phases. Among them, the α phase is the most common and stable crystal type, which usually crystallizes from the melted PVDF [27]. Figure 8 shows the XRD patterns of PVDF, PVDF/MAH and PVDF-g-MAH. It is found that the peaks at 2θ = 18.5, 19.8, 26.3 and 27.9 are the characteristic diffraction peaks of the α phase crystal assigned to (020), (110), (021) and (100) reflections, respectively, indicating that the α phase plays a dominant role. After blending MAH with PVDF, the crystal peak of PVDF/MAH was significantly enhanced at 2θ = 27.9, suggesting that the blending of MAH can promote the crystal growth in (100) direction. However, the crystal peak of PVDF-g-MAH disappears here, demonstrating that g-MAH shows a different effect for the PVDF crystal growth compared to the blending of MAH.

Materials
PVDF was purchased from Hefei economic and technological development zone maga experimental supplies business department (Hefei economic and technological de-

Reactive Processing of PVDF with MAH
PVDF and MAH were first dried in an 80 • C vacuum drying tank for 24 h to remove the water. A certain amount of PVDF, MAH, DCP and VAN were introduced into a torque rheometer. Reactive processing was carried out at 190 • C for 5 min with a rotor speed of 50 rpm. The following Tables 3-5 show the specific compositions.

Purification of the Grafted PVDF
The product was dissolved in DMF to form a solution, then the solution was added into large quantities of methanol solvent under vigorous stirring. In this process, unreacted MAH was dissolved in methanol, while the PVDF-g-MAH powder was precipitated. At last, the powder was washed by abundant acetone and methanol, and then dried using vacuum for 24 h.

Determination of the Grafting Degree
The return titration method was used to test the grafting degree of MAH, and thymol blue-phenolphthalein was used as an indicator. The calculation formula is as follows: In Formula (2), G is the grafting degree, m is the relative molecular mass of MAH, V 1 is the volume of the base consumed by the test sample, V 0 is the volume of the base consumed by the blank sample, and C is the concentration of isopropanol sodium hydroxide solution [29].

Characterization
A contact angle measuring system (DSA30S) was used to measure the static contact angle between water and PVDF, PVDF/MAH or PVDF-g-MAH.
Differential scanning calorimetry (DSC) (DSC214) was used to measure the melting temperature (Tm), crystallization temperature (Tc), crystallization enthalpy (Hc) and melting enthalpy (Hm). The sample was heated to 250 • C at a heating rate of 10 K/min. After the heat history was removed, the sample was cooled to 30 • C at a cooling rate of 5 K/min, and then heated to 250 • C at a heating rate of 10 K/min.
Thermogravimetric analysis (TG) (Labsys Evo) was used to measure the thermogravimetric behavior of the samples in N 2 atmosphere with a nitrogen flow rate of 20 mL/min. The set temperature range was 25~800 • C, and the heating rate was 10 K/min.
A rotational rheometer (Bohlin Gemini HRnano 200) was used to measure the rheological properties of PVDF, PVDF/MAH and PVDF-g-MAH.
An X-ray diffractometer (XRD) (SmartLab 9 KW) was used to measure the crystal type of PVDF, PVDF/MAH and PVDF-g-MAH. The scanning speed was 2θ = 20 • /min. An electronic universal stretching machine (Instron 5967) was used to measure the mechanical properties of PVDF, PVDF/MAH and PVDF-g-MAH, according to GB/T10403-2006. The elongation rate was 20 mm/min.

Conclusions
In this work, PVDF-g-MAH was prepared using the simple fusion grafting method. The MAH-grafting degree can be enhanced with an increase in MAH, VAN and DCP contents to a certain extent. Then, the hydrophilicity and mechanical properties of PVDF-g-MAH were studied systematically. Compared to PVDF or PVDF/MAH, PVDF-g-MAH greatly improved the elongation at break of PVDF. More importantly, the hydrophilicity of PVDF was greatly improved, which can extend the application fields of PVDF.