Sage Journals: Discover world-class research

Abstract

Ethylene vinyl alcohol (EVOH) with excellent barrier properties has insufficient thermomechanical properties. The introduction of magnesium chloride (MgCl₂) as an initiator in EVOH blends improved its properties by cross-linking. Torque behavior and gel experiment analysis indicated that a cross-linking in EVOH was formed. The cross-linking mechanism was confirmed through ¹³C nuclear magnetic resonance spectroscopy (¹³C NMR) and Fourier-transform infrared (FTIR) spectrometry. In ¹³C NMR spectra, the splitting peaks of CH carbon and CH₂ carbon tended to disappear, and the stretching vibration peak of –C=C– was observed in the FTIR spectra. The formation of hydrogen bond between MgCl₂ and EVOH destroyed the intramolecular and intermolecular hydrogen bonds of EVOH, which contributed to the dehydration of –OH to form –C=C–, and –C=C– was the basis for a cross-linking reaction. The thermal analysis of blends demonstrated that the melting temperature and crystallization temperature decreased, and the crystallinity gradually disappeared when the MgCl₂ content increased. Glass transition temperature significantly increased as the intermolecular force enhanced. Thermogravimetric analysis showed that a cross-linked structure could improve the thermostability of EVOH with an increase in the MgCl₂ content. Mechanical test results revealed a remarkable increase in the tensile strength of EVOH as the MgCl₂ content increased.

Keywords

EVOH cross-linking mechanical properties

Introduction

Studies have been conducted to preserve flavor components in food throughout their required shelf life, and most of them aim to determine and choose packaging materials that are a good fit for a given product.¹ Ethylene vinyl alcohol (EVOH) is a key material of interest because of its outstanding barrier properties to oxygen and carbon dioxide,^2–4 high resistance to hydrocarbons, and good processability.⁵ A random copolymer consists of ethylene units, which contribute to processability and flexibility, and vinyl alcohol units, which are responsible for high barrier properties.⁶ The barrier property of EVOH due to its small free volume in between molecules is from polyvinyl alcohol (PVA), which increases as vinyl alcohol content increases in terms of grade, and processing property is attributed to polyethylene.⁷ These materials have been widely used in the packaging industry as barrier layers to protect foods from the ingress of oxygen and losses of flavors and consequently to increase package shelf life. However, some drawbacks in the mechanical properties and thermal properties of EVOH and its brittleness limit its application. The hydrogen bond formed by hydroxyl groups in EVOH is insufficiently strong, causing an adverse effect on the mechanical and thermal properties of EVOH. Some efficient approaches must be used for probing to improve the properties of EVOH and further exploit its usefulness in more fields in the future.

Polymer blending technology is one of the major areas of research and development. Publications, patents, and research theses have shown that blending existing polymers has an added advantage over conventional polymers. In this study, blending technology involves the modification of physical, mechanical, and chemical properties of commodity to engineer a range of products.⁸ The methods of modifying EVOH by blending with other materials have been reported. The most common modification method is the addition of plasticizers^9–11; however, the mechanical and barrier performance of EVOH slightly decrease with the introduction of plasticizers. Active hydroxyl groups in EVOH can interact with other polymers that contain amino, carboxyl, acid anhydride, and epoxy groups.^12–14 In the present method, compatibility is important and can directly lead to a decreasing effect on the properties of EVOH.¹⁵

Recent studies have focused on the blending modification of EVOH. Li et al.¹⁶ prepared boric acid that induces cross-linked EVOH/graphene oxide nanocomposite films, but the preparation method is complicated and costly.

Accordingly, in the present study, cross-linking would be a simple way to overcome EVOH deficiencies. Thus, a cross-linked structure could improve the tensile strength and thermostability of EVOH. Magnesium chloride (MgCl₂), an inorganic substance, was selected as a catalyst for the cross-linking reaction. The cross-linked EVOH was discussed in terms of viscosity, thermal properties, and mechanical properties.

Experimental

Materials

EVOH (F101A) was purchased in a solid form from Kuraray Corporation, Japan, and it had an ethylene concentration of 32% and a melt flow index of 1.6 g 10 min⁻¹ (190°C, 2.16 kg). Anhydrous MgCl₂ was obtained from Shanghai Aladdin Biochemical Technology Co., Ltd, China. N, N-dimethylacetamide (DMAc) was also procured from Shanghai Aladdin Biochemical Technology Co., Ltd, China.

Preparation of neat EVOH and EVOH/MgCl₂ blends

EVOH was dried in a vacuum at 80°C for 8 h, and MgCl₂, Mg(OH)₂, CaCl₂, BaCl₂, CaO, and MgO were dried in an oven at 100°C for 4 h before blending. The blends of EVOH/metal compounds with compositions of 99/1 were prepared. Four samples of EVOH/MgCl₂ with compositions of 100/0, 99/1, 95/5, and 90/10 (w/w) were prepared and marked as M0, M1, M5, and M10, respectively. The blends were introduced to a mixer and blended at 100 r min⁻¹ for 6 min at 195°C. The torques during blending were automatically recorded to analyze processability and viscosity of the blends. After blending was completed, the samples were molded into a 0.5-mm-thick film by using a hot press and quenched to room temperature (25°C). The pressing temperature was 200°C, and the pressing time with a pressure of 10 MPa lasted 10 min.

Torque rheometry measurements

Torque during blending in the mixer was automatically recorded to analyze the rheological behavior of M0, M1, M5, and M10. In the internal mixer (XSS 300, Shanghai Kechuang Rubber & Plastic Machinery Equipment Co. Ltd., China), the mixing torque was continuously recorded as a function of the blending time.

Gel experiment

DMAc was selected as a suitable solvent to dissolve samples in a water bath at 85°C. Then, the dissolved samples were dried at 80°C and weighted.

The samples were boiled in water at 100°C, dried at 80°C, and weighed. The quantities of the samples before and after boiling were m₁ and m₂, respectively.

13C nuclear magnetic resonance spectroscopy

13C nuclear magnetic resonance (13C NMR) cross-polarization magic angle spinning spectra were recorded on a 500 MHZ/AVANCEIII spectrometer (Bruker, Switzerland). All the samples were solid. Analysis was performed using MestReNova software (Mestrelab Research, Spain).

Fourier-transform infrared spectroscopy

The Fourier-transform infrared (FTIR) spectra of the samples were recorded using a Nicolet 6700 spectrometer (Thermo Fisher, Waltham, Massachusetts, USA). Sample power was mixed with KBr powder and ground into fine powder. Subsequently, the mixtures were compressed into a round transparent tablet. The frequency range of FTIR was from 4000 cm⁻¹ to 400 cm⁻¹ against KBr as the background.

Thermal properties

Differential scanning calorimetry

The differential scanning calorimetry (DSC) of the blends was determined in a modulated DSC 2910 (TA Instruments, New Castle, Delaware, USA) under a nitrogen flow of 20 mL min⁻¹. The sample weights were approximately 8 mg. The scanning rate used throughout the investigation was 10°C min⁻¹. Pure EVOH and the blend samples were first heated from 25°C to 230°C and then held for 3 min to eliminate heat. The crystallization behavior was determined from the cooling step, and melting points were evaluated from the second heating run at a rate of 10°C min⁻¹.

Thermogravimetric analysis

The thermogravimetric analysis (TGA) measurements of the samples were performed in a TG209F1 TG/differential thermal analysis analyzer (Netzsch, Germany) under a nitrogen protective atmosphere. The samples were heated from 25°C to 600°C with a heating rate of 10°C min⁻¹ and a flow rate of 50 mL min⁻¹. Prior to the test, the samples were dried in a vacuum oven at 80°C for 24 h.

Dynamic mechanical analysis

Dynamic mechanical measurements at 1 Hz were made in a tensile mode by using a Q800 dynamic mechanical thermal analyzer (TA Instruments). Tests were performed at a heating rate of 5°C min⁻¹ from −60°C to 150°C. Rectangular specimens with a width of 5 mm and a length of 30 mm were used.

Mechanical properties

A tensile test was performed at 25°C and relative humidity of 52% by using a universal testing machine (CMT6104, Sans, China). The crosshead speed was set at 10 mm min⁻¹ with a gauge length of 50 mm in accordance with GB/T 1040-2006. Each sample included five tested replicates to obtain a reliable value of tensile strength and standard deviation.

Results and discussion

Torque behavior

Rheology is the theoretical basis for polymer processing, and most polymers are processed through melting and deformation. Through a rheological behavior test, information on the microstructure of polymers can be obtained, and the relationship between the microstructure and behavior can be established.

Torque is one characteristic of rheological behavior. The torque behavior of several common metal compounds is compared in Figure 1(a). A significant improvement in the torque behavior is observed via the addition of MgCl₂. Other metal compounds slightly affect torque that decreases when CaO is added. With experimental data in Figure 1, MgCl₂ is chosen to improve the properties of EVOH.

Figure 1.

Variation in the torque versus the mixing time of (a) several metal compounds and (b) M0, M1, M5, and M10.

Figure 1(b) shows the torque curves of M0, M1, M5, and M10 measured with the internal mixer at 195°C. The torque of melting polymer is related to the melt viscosity and the melt processability of the blends. Torque increases as the weight percent of MgCl₂ increases compared with that of pure EVOH.

Notably, the torques of M10 and M5 sharply increase at 150 and 300 s, respectively. The possible explanation for this behavior is that the cross-linking reaction of EVOH occurs when MgCl₂ is added. As the viscosity of M10 increases significantly, the cross-linked molecular chains easily break into multiple cross-linked structures by the shear force in the mixer. These structures have a weak chemical and physical interaction among them, but they have a strong internal interaction. Thus, the torque of M10 subsequently decreases as the part of the cross-linked structure is destroyed; however, the cross-linking degree is still high.

Cross-linking can lead to an increased effect on viscosity, which is indicated by an increase in torque. Accordingly, a cross-linking reaction in EVOH might occur through the addition of MgCl₂.

Gel experiment

DMAc was selected as a suitable solvent to dissolve the blends in a water bath at 85°C and to validate this hypothesis. The gel contents of M0, M1, M5, and M10 are 0%, 0%, 69.8%, and 74.4%, respectively. Notably, the gel gradually forms as the MgCl₂ content in the blends increases. Gel formation indicates that the cross-linking reaction occurs. The degree of cross-linking of the blends increases as the gel content increases.

The results after boiling are shown in Table 1. The variation in the quantities of M1, M5, and M10 after boiling is significantly reduced by nearly 1%, 5%, and 10%, respectively. The quantity of MgCl₂ may decrease, and MgCl₂ only participates in the cross-linking reaction as a catalyst.

Table 1.

Variations in the quantities of M0, M1, M5, and M10 before and after boiling.

Samples	m₁ (mg)	m₂ (mg)	Δ (%)
M0	80	82	+0.9
M1	104	103	−0.9
M5	98	93	−5.1
M10	102	92	−9.8

Cross-linking mechanism

The following assumptions are made on the basis of the variation in the torque and gel experiment: the cross-linking reaction occurs with the addition of MgCl₂, and MgCl₂ only as a catalyst participates in the cross-linking reaction. The cross-linking mechanism is analyzed to prove these hypotheses.

The structure of PVA is similar to that of EVOH. PVA is easily degraded, and the initial decomposition temperature is about 200°C, so the thermal decomposition mechanism of PVA is analyzed first. According to the TG and differential thermal gravity (DTG) of PVA, during the thermal degradation of PVA in the inert atmosphere, the shape of the mass loss curve is consistent with the generally accepted two-step mechanisms. The first step is the result of dehydration (elimination of water) accompanied with polyene formation, and the second one is pyrolization that produces some organic volatile products as shown in Figure 2.^17-19 The mechanism of the thermal degradation of PVA comprises two groups of reactions: the ones that only affect functional groups at about 200°C (inter- or intramolecular dehydration) and those accompanied with a scission or a modification of the main chain at a high temperature.²⁰

The processing temperature of EVOH is 195°C, so the first step of PVA thermal degradation is considered. Water elimination accompanied with polyene formation in EVOH involves the same hydroxyl structure as PVA likely occurs.^21,22 The cross-linking reaction of EVOH is based on the formation of –C=C–. With the addition of MgCl₂, the new hydrogen bond is formed between Cl in MgCl₂ and hydroxyl groups in EVOH, whereas the hydrogen bond in EVOH weakens, thereby contributing to dehydration accompanied with –C=C– formation. No interaction exists between Mg in MgCl₂ and EVOH. According to the boiling testing result, MgCl₂ as a catalyst may still remain in a molecular form. Then, the cross-linking reaction occurs with a –C=C– fracture at a high temperature, as shown in Figure 2.

Figure 2.

Cross-linking mechanism of EVOH.

The formation of –C=C– and cross-linking reaction was characterized through FTIR and 13C NMR to verify our assumptions.

¹³C NMR spectra of neat EVOH and EVOH/MgCl₂ blends

The ¹³C NMR spectra of M0, M1, M5, and M10 are shown in Figure 3. In ¹³C NMR spectra of pure EVOH, two regions of absorption are presented: 0–50 ppm related to all methylene carbons –CH₂–(C) and 50–80 ppm corresponding to all methine carbons CH–OH. The ¹³C NMR signal of CH₂ carbon shows three main peaks: the most downfield peak (peak I, 39.03 ppm), the central peak (peak II, 34.48 ppm), and the most upfield peak (peak III, 24.31 ppm). Three splitting peaks are observed at around 24.31 ppm. Similarly, the ¹³C NMR signal of CH carbon has one main peak (64.14 ppm), and three splitting peaks are caused by the differences in sequence distribution and stereo configuration.²³ The splitting of the peak is attributed to the formation of intramolecular hydrogen bonding.²⁴ With the addition of MgCl₂, the splitting peaks of CH carbon and CH₂ carbon tend to disappear. The hydrogen bond of EVOH is destroyed because of the formation of a new hydrogen bond between MgCl₂ and EVOH. Combined with the gel experiment, the ¹³C NMR signal indicates that the production of the cross-linking structure in EVOH reduces the differences in sequence distribution and stereo configuration when the MgCl₂ content increases. The ¹³C NMR signal of –C=C– between 100 ppm and 150 ppm is also observed in Figure 3, which can verify the proposed assumption.

Figure 3.

Solid-state ¹³C NMR of the samples: M0, M1, M5, and M10.

FTIR spectra of pure EVOH and EVOH/MgCl₂ blends

The infrared absorption peak of the free –OH (no hydrogen bond) is between 3610 cm^–1 and 3640 cm^–1, and the shape of peak is sharp. When a hydrogen bond forms, the infrared absorption peak shifts to a lower wave number, and the peak widens. The intensity of the hydrogen bond can be indicated by the variation in a hydrogen bond peak. When the hydrogen bond strengthens, the infrared absorption peak shifts to a lower wave number; conversely, this peak shifts to a higher wave number when the hydrogen bond weakens.

As shown in Figure 4, an intense broad band centered at approximately 3390 cm⁻¹ that corresponds to hydroxyl stretching is found in the spectra of EVOH specimens, which are attributed to the intermolecular and intramolecular hydrogen bonds in EVOH. After 1% MgCl₂ in EVOH is blended, the peak wave number of the absorption bands that correspond to the hydroxyl stretching of EVOH shifts from 3385 cm⁻¹ to 3379 cm⁻¹, which illustrates that the hydrogen bond strengthens upon the addition of MgCl₂. Conversely, the absorption peak of –OH shifts to a higher wave number as the MgCl₂ content increases, indicating that the hydrogen bond weakens. Thus, the weakened hydrogen bond inter- and intramolecular hydrogen bonding between the hydroxyl groups of EVOH and the characteristic peaks appear at 1650 cm⁻¹, which is attributed to the –C=C– stretching vibration and confirmed the aforementioned assumption. No absorbance is noted above 3000 cm⁻¹ for the double bond possibly because the peaks of –OH and –CH overlap with the –C=C– peak.

Figure 4.

FTIR spectra of the samples: M0, M1, M5, and M10.

Thermal behavior of EVOH and EVOH/MgCl₂ blends

Crystallization characteristics and DSC curves

M0, M1, M5, and M10 were subjected to thermal characterization through DSC measurement. Figure 5(a) and (b) shows the cool and second heat scans of the DSC thermograms of four samples. The experimental data in Table 2 indicate that the crystallization temperature (T_c) and melting temperature (T_m) of EVOH are at 160.3°C and 183.4°C, respectively. T_m and T_c significantly decrease as MgCl₂ is introduced, and they cannot be detected when the weight percent of MgCl₂ increases. So does the crystallinity (χ_c). The cross-linking structure in EVOH upon MgCl₂ addition from M0 to M1 may not be inferred precisely; however, decreasing trends in T_m, T_c, and χ_c can illustrate that crystallization and interactions between EVOH molecules are destroyed by the addition of MgCl₂. These phenomena may be the result of slight cross-linking. The missing peaks of M5 and M10 can be used as a support for cross-linking in EVOH.

Figure 5.

DSC curves of M0, M1, M5, and M10: (a) cooling curve and (b) second heating.

Table 2.

DSC results of M0, M1, M5, and M10.

Samples	T_m (°C)	T_c (°C)	ΔH_m (J g⁻¹)	χ_c (%)
M0	183.4	160.3	65.51	41.5
M1	179.5	153.5	57.95	37.1
M5	—	—	—	—
M10	—	—	—	—

DSC: differential scanning calorimetry; T_m: melting temperature; T_c: crystallization temperature; χ_c: crystallinity.

The possible explanation for the abovementioned behavior is that strong intermolecular interactions form, and molecular chain movement is restricted when MgCl₂ is added; as a result, no significant variation in crystal enthalpy is observed.²⁵ The results agree with the NMR and FTIR spectra, implying that the cross-linking reaction occurs when MgCl₂ is added to EVOH.

Thermogravimetric analysis

The TG and DTG curves of M0, M1, M5, and M10 are shown in Figure 6. Three degradation processes occur upon heating from 25°C to 600°C. The first step is dehydration to form –C=C–. The second one is the breakage of the main chains to produce some polymers with a low molecular weight, and the final one is carbonization. MgCl₂ addition leads to the acceleration of the first reaction step. Then, the second reaction step occurs at a higher temperature than that of pure EVOH; therefore, the possible explanation for this behavior is that a cross-linked structure is present to improve the thermostability of EVOH. The result of this work clearly states that the cross-linking reaction contributes to the thermal properties of EVOH.

Figure 6.

Thermogravimetric curves of M0, M1, M5, and M10.

Dynamic mechanical analysis

A series of storage modulus curves and loss factor (tan δ) as a function of temperature that ranges from −50°C to 150°C for M0, M1, M5, and M10 are depicted in Figure 7. It shows obvious platforms for rubber in M5 and M10, which can prove the formation of the cross-linked structure. Figure 7(b) shows a dynamic relaxation peak that appears in all the samples. According to Ishak and Berry,²⁶ the α relaxation peak is believed to be related to the breakage of the hydrogen bond between polymer chains that induce long-range segmental chain movement in an amorphous area. This area is assigned to the glass transition (T_g) temperature of the blends. Notably, T_g is significantly higher when the MgCl₂ content increases. This result indicates that the interaction between the molecular chains of the blend remarkably enhances, and the movement of the molecular chain is restricted and leads to an increase in T_g. This result can be attributed to a cross-linking reaction.²⁷

Figure 7.

DMA curves of M0, M1, M5, and M10: (a) storage modulus-temperature curve and (b) tan δ-temperature curve.

Mechanical properties

Figure 8 shows the behavior of M0, M1, M5, and M10 under tensile loading, and Figure 9 presents their values. The tensile strength of EVOH increases as the MgCl₂ content increases. However, the elongation of M10 decreases drastically.

Figure 8.

Stress–strain curves of M0, M1, M5, and M10.

Figure 9.

Tensile strength and elongation at break of M0, M1, M5, and M10.

As explained in the above section, the amount of cross-linking increases as the MgCl₂ content increases, resulting in an increase in tensile strength. A dense network structure that results in the restriction of EVOH chain movement leads to a more brittle behavior. Since toughness is calculated by integrating the area under the stress–strain curve, a drastic increase in the elongation of M1 and M5 results in an increase in toughness; however, M10 decreases. Therefore, cross-linking moderation can improve the mechanical properties of EVOH.

Conclusion

In this study, cross-linked EVOH was prepared through MgCl₂ introduction, and MgCl₂ was used only as a catalyst. The properties of EVOH were improved via the cross-linking reaction. An abnormally increased torque was revealed in the torque behavior, which could explain the presence of a cross-linked structure, as shown by the gel experiment analysis. The cross-linking reaction of EVOH was based on the formation of –C=C–. With MgCl₂ addition, the hydrogen bond of EVOH could be destroyed, while a new hydrogen bond was formed between Cl in MgCl₂ and hydroxyl groups in EVOH. Such formation contributed to dehydration accompanied with –C=C– formation, which promoted the formation of the cross-linked structure. The mechanism of a cross-linking reaction was confirmed through ¹³C NMR and FTIR. The cross-linked structure destroyed the ordered arrangement of EVOH molecules, thereby causing the gradual disappearance of crystals from DSC curves. Thermal analysis showed that the cross-linked structure enhanced the intermolecular force. Therefore, T_g significantly increased when the MgCl₂ content increased. Tensile tests indicated that tensile strength improved when the MgCl₂ content increased. Therefore, this test proposed an effective and practical way to form the cross-linked structure to improve the tensile strength and thermostability of EVOH and provided a broad application area.

Supplemental Material

sj-pdf-1-jtc-10.1177_0892705720913313 – Supplemental Material for Effects of cross-linking by MgCl₂ as an initiator on the properties of EVOH

Supplemental Material, sj-pdf-1-jtc-10.1177_0892705720913313 for Effects of cross-linking by MgCl₂ as an initiator on the properties of EVOH by Bin Wang, Chong Lu, Jing Hu and Weixin Lu in Journal of Thermoplastic Composite Materials

Footnotes

Funding

The author(s) received no financial support for the research, authorship, and/or publication of this article.

ORCID iD

Bin Wang

Chong Lu

Supplemental material

Supplemental material for this article is available online.

References

Cheon

Jung

Shim

, et al. Development and evaluation of organic vapour permeation system for packaging applications. Packag Technol Sci 2019; 32: 297–308.

Faisant

Ait-Kadi

Bousmina

, et al. Morphology, thermomechanical and barrier properties of polypropylene-ethylene vinyl alcohol blends. Polym 1998; 39: 533–545.

Demarquette

Kamal

. Influence of maleation of polypropylene on the interfacial properties between polypropylene and ethylene-vinyl alcohol copolymer. J Appl Polym Sci 2015; 70: 70–75.

Maes

Luyten

Herremans

, et al. Recent updates on the barrier properties of ethylene vinyl alcohol copolymer (EVOH): a review. Polym Rev 2017; 58: 209–246.

Kalfoglou

Samios

Papadopoulou

. Compatibilization of poly(ethylene-co-vinyl alcohol) (EVOH) and EVOH/HDPE blends with ionomers. Structure and properties. J Appl Polym Sci 1998; 39: 3863–3870.

Maes

Junior Y, Mitsuyoshi

, et al. Ethylene vinyl alcohol copolymer (EVOH) as a functional barrier against surrogate components migrating from paperboard. J Chem 2019; 2019: Article ID 4180708.

Artzi

Narkis

Siegmann

. Review of melt-processed nanocomposites based on EVOH/organoclay. J Appl Polym Sci Part B Polym Phys 2005; 43: 1931–1943.

Tavakoli Anaraki

Saeb

Rastin

, et al. A probe into the status quo of interfacial adhesion in the compatibilized ternary blends with core/shell droplets: selective versus dictated compatibilization. J Appl Polym 2019; 134: 10.

Cabedo

Giménez

Lagaron

, et al. Development of EVOH-kaolinite nanocomposites. Polym 2004; 45: 5233–5238.

10.

Jeong

Kim

. Structure and properties of EVOH/organoclay nanocomposites. J Mater Sci 2005; 40: 3783–3787.

11.

Lee

Hur

Yang

, et al. Effect of interfacial attraction on intercalation in polymer/clay nanocomposites. J Appl Polym Sci 2006; 101: 2749–2753.

12.

Abad

Ana

Luis

, et al. Influence of the ethylene-(methacrylic acid)-Zn²⁺ ionomer on the thermal and mechanical properties of blends of poly(propylene) (PP)/ethylene-(vinyl alcohol) copolymer (EVOH). Polym Int 2010; 54: 673–678.

13.

Zhong

Lin

, et al. Space charge distribution and crystalline structure in polyethylene blended with EVOH. Eur Polym J 2004; 40: 1987–1995.

14.

Montoya

Abad

Barral

, et al. Mechanical and fracture behavior of polypropylene/poly(ethylene-co-vinyl alcohol) blends compatibilized with ionomer Na⁺. Eur Polym J 2006; 42: 265–273.

15.

Salehi-Mobarakeh

Yadegari

Didehvar

, et al. Polyamide grafting onto ethylene-vinyl alcohol copolymer. J Polym Eng 2013; 33: 843–850.

16.

Bandyopadhyay

Guo

, et al. Enhanced gas barrier and anticorrosion performance of boric acid induced cross-linked poly(vinyl alcohol-co-ethylene)/graphene oxide film. Carbon 2018; 133: 150–161.

17.

Budrugeac

. Kinetics of the complex process of thermo-oxidative degradation of poly (vinyl alcohol). J Therm Anal Calorim 2008; 92: 291–296.

18.

Tsuchiya

Sumi

. Thermal decomposition products of polyisobutylene. Polym Sci Part A Polym Chem 1969; 7: 3151–3158.

19.

Popa

Vasile

Schneider

. Thermoxidative degradation of poly(vinyl alcohol) under dynamic thermogravimetric conditions I. Influence of heating rate and of molecular weight. J Polym Sci Part A Polym Chem 1972; 10: 3679–3684.

20.

Fernandes

Hechenleitner

AAW

Gómez Pineda

. Kinetic study of the thermal decomposition of poly(vinyl alcohol)/kraft lignin derivative blends. Thermochim Acta 2006; 441: 101–109.

21.

Sonker

Wagner

Bajpai

, et al. Effects of tungsten disulphide nanotubes and glutaric acid on the thermal and mechanical properties of polyvinyl alcohol. Compos Sci Technol 2016; 127: 47–53.

22.

Jain

Verma

Singh

. Dynamic mechanical analysis and creep-recovery behaviour of polyvinyl alcohol based cross-linked biocomposite reinforced with basalt fiber. Mater Res Exp 2019; 6: 105373.

23.

Moritani

Iwasaki

. Carbon-13 nuclear magnetic resonance study on sequence distribution and anomalous linkage in ethylene-vinyl alcohol copolymers. Macromolecules 1978; 11: 1251–1259.

24.

Kuwabara

Kaji

Horii

, et al. Solid-state ¹³C NMR analyses of the crystalline-noncrystalline structure for metallocene-catalyzed linear low-density polyethylene. Macromolecules 1997; 30: 7516–7521.

25.

Bersanetti

da Cruz

LGI

Carlstron

, et al. DSC characterization of enzymatic digestion of corneas treated with plant extracts rich in polyphenols. J Therm Anal Calorim 2019; 138: 3797–3802.

26.

Ishak

ZAM

Berry

. Hygrothermal aging studies of short carbon fiber reinforced nylon 6.6. J Appl Polym Sci 1994; 51: 2145–2155.

27.

Jin

Sima

Weng

, et al. Simultaneously reinforcing and toughening of poly (propylene carbonate) by epoxy-terminated hyperbranched polymer (EHBP) through micro-crosslinking. Polym Bull 2019; 76: 5733–5749.

Supplementary Material

Please find the following supplemental material available below.

For Open Access articles published under a Creative Commons License, all supplemental material carries the same license as the article it is associated with.

For non-Open Access articles published, all supplemental material carries a non-exclusive license, and permission requests for re-use of supplemental material or any part of supplemental material shall be sent directly to the copyright owner as specified in the copyright notice associated with the article.

0.00 MB

0.30 MB

Effects of cross-linking by MgCl 2 as an initiator on the properties of EVOH

Abstract

Keywords

Introduction

Experimental

Materials

Preparation of neat EVOH and EVOH/MgCl2 blends

Torque rheometry measurements

Gel experiment

13C nuclear magnetic resonance spectroscopy

Fourier-transform infrared spectroscopy

Thermal properties

Differential scanning calorimetry

Thermogravimetric analysis

Dynamic mechanical analysis

Mechanical properties

Results and discussion

Torque behavior

Gel experiment

Cross-linking mechanism

13C NMR spectra of neat EVOH and EVOH/MgCl2 blends

FTIR spectra of pure EVOH and EVOH/MgCl2 blends

Thermal behavior of EVOH and EVOH/MgCl2 blends

Crystallization characteristics and DSC curves

Thermogravimetric analysis

Dynamic mechanical analysis

Mechanical properties

Conclusion

Supplemental Material

sj-pdf-1-jtc-10.1177_0892705720913313 – Supplemental Material for Effects of cross-linking by MgCl2 as an initiator on the properties of EVOH

Footnotes

Funding

ORCID iD

Supplemental material

References

Supplementary Material

Preparation of neat EVOH and EVOH/MgCl₂ blends

¹³C NMR spectra of neat EVOH and EVOH/MgCl₂ blends

FTIR spectra of pure EVOH and EVOH/MgCl₂ blends

Thermal behavior of EVOH and EVOH/MgCl₂ blends

sj-pdf-1-jtc-10.1177_0892705720913313 – Supplemental Material for Effects of cross-linking by MgCl₂ as an initiator on the properties of EVOH