# Fabrication and Characterization of Regenerated Cellulose Films Using Different Ionic Liquids

Authors: Jin-Hui Pang; Xin Liu; Miao Wu; Yu-Ying Wu; Xue-Ming Zhang; Run-Cang Sun
Journal: Journal of Spectroscopy
 (2014)

---

## Abstract

The demand for substitution of fossil-based materials by renewable bio-based materials is increasing with the fossil resources reduction and its negative impacts on the environment. In this study, environmentally friendly regenerated cellulose films  were successfully prepared using 1-allyl-3-methylimidazolium chloride (AmimCl), 1-butyl-3-methylimidazolium chloride (BmimCl), 1-ethyl-3-methylimidazolium chloride (EmimCl), and 1-ethyl-3-methylimidazolium acetate (EmimAc) as solvents, respectively. The results of morphology from scanning electron microscopy (SEM) and atomic force microscopy (AFM) showed that all the cellulose films possessed smooth, highly uniform, and dense surface. The solid-state cross-polarization/magic angle spinning (CP/MAS)13C NMR spectra and X-ray diffraction (XRD) corroborated that the transition from cellulose I to II had occurred after preparation. Moreover, it was shown that the ionic liquid EmimAc possessed much stronger dissolubility for cellulose as compared with other ionic liquids and the cellulose film regenerated from EmimCl exhibited the most excellent tensile strength (119 Mpa). The notable properties of regenerated cellulose films are promising for applications in transparent biodegradable packaging and agricultural purpose as a substitute for PP and PE.


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## Body

## 1. Introduction

With the development of modern society and industry, there is growing demand for development of renewable and biodegradable materials as substitutes for petroleum-derived synthetic polymers [1]. Cellulose is the most abundant natural polymer in nature and it will become one of the most promising polymeric resources, which is renewable, biodegradable, and biocompatible [2, 3]. However, chemical processing of cellulose is extremely difficult in general because it is neither meltable nor soluble in water or common solvents due to its partially crystalline structure and close chain packing via numerous inter- and intramolecular hydrogen bonds [4, 5].Over the past decades, several cellulose solvent systems have been available for dissolving cellulose, such as viscose process (CS2) [6, 7], LiCl/N,N-dimethylacetamide (DMAc) [8], DMSO/paraformaldehyde (PF) [9], and some aqueous solutions of metal complexes [10]. However, these conventional cellulose solvent systems have disadvantages, such as limited dissolving capability, toxicity, high cost, solvents recovery, uncontrollable side reaction, and instability during cellulose processing and/or derivatization. The recently developed Lyocell process [11], which uses N-methylmorpholine N-oxide (NMMO) to dissolve cellulose directly, also has some disadvantages including the formation of byproducts, the degradation of cellulose, and high cost [12]. In recent years, Zhang et al. [13, 14] have developed a green and efficient method for dissolution of cellulose in NaOH/urea aqueous solution, in which the cellulose can be rapidly dissolved as precooled to −12°C within 2 min. However, the dissolution process is limited in terms of cellulose concentration and degree polymerization (DP). More recently, ionic liquids (ILs) have attracted much attention due to their high electrochemical and thermal stability, nonflammability, and tunable solubility properties [15]. Ionic liquids are often fluid at room temperature and consist entirely of ionic species and represent a new class of solvents with high polarity. Since no toxic or explosive gases are formed due to their low vapor pressure, ionic liquids are considered as “green solvents.” Moreover, ionic liquids exhibited outstanding dissolving capability for cellulose [16], which will broaden the comprehensive utilization for cellulose. It has been shown that the ability to dissolve cellulose is not an inherent property of this broad class of compounds [17]. Among the vast number of ILs reported so far, only a minority dissolve cellulose. In order to compare the dissolubility and processability of different ionic liquids on cellulose, four ILs including 1-allyl-3-methylimidazolium chloride (AmimCl), 1-ethyl-3-methylimidazolium chloride (EmimCl), 1-butyl-3-methylimidazolium chloride (BmimCl), and 1-ethyl-3-methylimidazolium acetate (EmimAc) were chosen as solvents to dissolve cellulose and elaborate regenerated cellulose films. The morphology, chemical structure, and mechanical properties of cellulose films were investigated to evaluate the desirability of their applications in the packaging and functional materials fields.


## 2.  Materials and Methods

### 2.1. Materials

Cotton linter, supplied by Silver Hawk Fiber Corporation (Shandong province, China), was used as cellulose sample with the degree of polymerization (DP) 920. The degree of polymerization was measured by TAPPI test method using cupriethylenediamine (CED) as a solvent and a capillary viscometer, to give an indication of the average degree of polymerization of the cellulose materials. The viscosities determined as centipoises (cP) were converted to degree of polymerization (DP) based on the following formula:(1)
D
P
0.905
=
0.75
×
[
954
×
log
⁡
(
X
)
-
325
]
,
where X = TAPPI viscosity in cP.The cellulose sample used was dried in vacuum at 105°C for 24 h before using. The ILs 1-ethyl-3-methylimidazolium acetate (EmimAc), 1-allyl-3-methylimidazolium chloride (AmimCl), 1-ethyl-3-methylimidazolium chloride (EmimCl), and 1-butyl-3-methylimidazolium chloride (BmimCl), used as solvents for dissolution of the cellulose, were purchased from Chengjie Chemistry Corporation.


### 2.2. Preparation of Regenerated Cellulose Films

In a typical procedure for preparation of regenerated cellulose film, 5 g cotton linter sample was dispersed in 100 g ILs of EmimAc, AmimCl, EmimCl, and BmimCl, respectively. The mixture was heated at different temperatures in the range of 80°C–120°C under magnetic stirring until cellulose dissolved in ILs completely. After dissolution, the resulting transparent solution was cast on a glass plate and then immediately coagulated in the water to obtain transparent regenerated cellulose gel. The regenerated cellulose gel was washed with running distilled water and then air dried. All films were kept in a conditioning cabinet at 50% relative humidity (RH) and 25°C to ensure the stabilization of their water content before characterization.


### 2.3. Thickness Measurements

A micrometer (Lorentzen & Wettre, precision 1μm) was used to measure film thickness. Measurement was taken at six different locations on each film, and the mean value was used in the calculations of the mechanical test.


### 2.4. Scanning Electron Microscopy Analysis

Scanning electron micrographs (SEM) were taken on a HITACHI S-3400N scanning electron microscope with 10 kV acceleration voltage and at a magnification of 2000. The free surface and the fracture surface of the films were sputtered with gold-palladium on a HITACHI E-1010 and then observed and photographed.


### 2.5. Atomic Force Microscopy Analysis

Atomic force microscopy (AFM) (SPM-9600, Shimadzu) was used to study the morphology of film surface. In AFM scanning, two to four interest locations on each sample were tested. Small pieces of films were glued onto metal disks and attached to a magnetic sample holder located on the top of the scanner tube. Phase images were recorded under ambient air conditions. All of the images were recorded in contact mode using silicon cantilevers.


### 2.6. X-Ray Diffraction

Crystallinity of the regenerated cellulose film samples was determined by X-ray diffraction patterns using XRD-6000 instrument (Shimidzu, Japan). The method was the same as that at literature [13].


### 2.7. Thermal Analysis

Thermal analysis was determined by using thermogravimetric analysis (TGA) and differential thermal analysis (DTA) on a simultaneous thermal analyzer (SDT Q600 TGA/DSC, TA Instrument). The samples weighed around 10 mg were heated from room temperature to 600°C at a heating rate of 10°C/min under an inert atmosphere of N2.


### 2.8. Fourier Transform Infrared Spectra Analysis

Infrared spectra of cellulose film samples were recorded with a Fourier transform IR spectrometer (FT-IR TENSOR27, Germany) in ATR mode. The specimens were measured directly with a scan range from 400 cm−1 to 4000 cm−1.


### 2.9. CP/MAS13C NMR Spectra

Solid-state cross-polarization/magic angle spinning (CP/MAS)13C NMR spectra of the regenerated cellulose film samples were recorded on a Bruker AV-III 400 M spectrometer (Germany) operated at a 13C frequency of 100.6 MHz. A 4 mm zirconia (ZrO2) rotor was used to pack cellulose films, and the measurement was performed using a CP pulse program with a 2 ms contact time and a 2 s delay between transitions. The spinning speed was set at 5 kHz for all samples.


### 2.10. Contact Angle Measurements

Contact angles of the cellulose films were measured to calculate the surface free energies of the cellulose films. The measurements were performed at room temperature by the sessile drop method using a goniometer equipped with a high-speed camera (OCA 20, Data physics Ltd., Germany).


### 2.11. Tensile Strength Testing

The tensile strength of the regenerated cellulose films was measured by using a tensile testing machine (Zwick Universal testing machine Z005) at a speed of 5 mm/min. The samples were cut in the rectangular specimens with a width of 20 mm and length of 60 mm, and eight replicate specimens were tested from each film type. A grip distance of 20 mm was maintained. The measurements were performed at 25°C and relative humidity of 50%.


## 2.1. Materials

Cotton linter, supplied by Silver Hawk Fiber Corporation (Shandong province, China), was used as cellulose sample with the degree of polymerization (DP) 920. The degree of polymerization was measured by TAPPI test method using cupriethylenediamine (CED) as a solvent and a capillary viscometer, to give an indication of the average degree of polymerization of the cellulose materials. The viscosities determined as centipoises (cP) were converted to degree of polymerization (DP) based on the following formula:(1)
D
P
0.905
=
0.75
×
[
954
×
log
⁡
(
X
)
-
325
]
,
where X = TAPPI viscosity in cP.The cellulose sample used was dried in vacuum at 105°C for 24 h before using. The ILs 1-ethyl-3-methylimidazolium acetate (EmimAc), 1-allyl-3-methylimidazolium chloride (AmimCl), 1-ethyl-3-methylimidazolium chloride (EmimCl), and 1-butyl-3-methylimidazolium chloride (BmimCl), used as solvents for dissolution of the cellulose, were purchased from Chengjie Chemistry Corporation.


## 2.2. Preparation of Regenerated Cellulose Films

In a typical procedure for preparation of regenerated cellulose film, 5 g cotton linter sample was dispersed in 100 g ILs of EmimAc, AmimCl, EmimCl, and BmimCl, respectively. The mixture was heated at different temperatures in the range of 80°C–120°C under magnetic stirring until cellulose dissolved in ILs completely. After dissolution, the resulting transparent solution was cast on a glass plate and then immediately coagulated in the water to obtain transparent regenerated cellulose gel. The regenerated cellulose gel was washed with running distilled water and then air dried. All films were kept in a conditioning cabinet at 50% relative humidity (RH) and 25°C to ensure the stabilization of their water content before characterization.


## 2.3. Thickness Measurements

A micrometer (Lorentzen & Wettre, precision 1μm) was used to measure film thickness. Measurement was taken at six different locations on each film, and the mean value was used in the calculations of the mechanical test.


## 2.4. Scanning Electron Microscopy Analysis

Scanning electron micrographs (SEM) were taken on a HITACHI S-3400N scanning electron microscope with 10 kV acceleration voltage and at a magnification of 2000. The free surface and the fracture surface of the films were sputtered with gold-palladium on a HITACHI E-1010 and then observed and photographed.


## 2.5. Atomic Force Microscopy Analysis

Atomic force microscopy (AFM) (SPM-9600, Shimadzu) was used to study the morphology of film surface. In AFM scanning, two to four interest locations on each sample were tested. Small pieces of films were glued onto metal disks and attached to a magnetic sample holder located on the top of the scanner tube. Phase images were recorded under ambient air conditions. All of the images were recorded in contact mode using silicon cantilevers.


## 2.6. X-Ray Diffraction

Crystallinity of the regenerated cellulose film samples was determined by X-ray diffraction patterns using XRD-6000 instrument (Shimidzu, Japan). The method was the same as that at literature [13].


## 2.7. Thermal Analysis

Thermal analysis was determined by using thermogravimetric analysis (TGA) and differential thermal analysis (DTA) on a simultaneous thermal analyzer (SDT Q600 TGA/DSC, TA Instrument). The samples weighed around 10 mg were heated from room temperature to 600°C at a heating rate of 10°C/min under an inert atmosphere of N2.


## 2.8. Fourier Transform Infrared Spectra Analysis

Infrared spectra of cellulose film samples were recorded with a Fourier transform IR spectrometer (FT-IR TENSOR27, Germany) in ATR mode. The specimens were measured directly with a scan range from 400 cm−1 to 4000 cm−1.


## 2.9. CP/MAS13C NMR Spectra

Solid-state cross-polarization/magic angle spinning (CP/MAS)13C NMR spectra of the regenerated cellulose film samples were recorded on a Bruker AV-III 400 M spectrometer (Germany) operated at a 13C frequency of 100.6 MHz. A 4 mm zirconia (ZrO2) rotor was used to pack cellulose films, and the measurement was performed using a CP pulse program with a 2 ms contact time and a 2 s delay between transitions. The spinning speed was set at 5 kHz for all samples.


## 2.10. Contact Angle Measurements

Contact angles of the cellulose films were measured to calculate the surface free energies of the cellulose films. The measurements were performed at room temperature by the sessile drop method using a goniometer equipped with a high-speed camera (OCA 20, Data physics Ltd., Germany).


## 2.11. Tensile Strength Testing

The tensile strength of the regenerated cellulose films was measured by using a tensile testing machine (Zwick Universal testing machine Z005) at a speed of 5 mm/min. The samples were cut in the rectangular specimens with a width of 20 mm and length of 60 mm, and eight replicate specimens were tested from each film type. A grip distance of 20 mm was maintained. The measurements were performed at 25°C and relative humidity of 50%.


## 3.  Results and Discussion

### 3.1. Topography of Films

The topography of produced films was analyzed by SEM and AFM. SEM and AFM micrographs of the regenerated films are shown in Figures1 and 2. The SEM images indicated that all the regenerated films displayed smooth, highly uniform, and dense surface, indicating a complete regeneration of cellulose. The small nodules especially in the cellulose film obtained from ionic liquid EmimAc (sample d) were possibly caused by the presence of bubbles in processes of casting and coagulation. AFM images with higher resolution were recorded to determine the surface structural information of the films, whereas the height images were generated for the additional morphology and surface roughness of the films. AFM images (Figure 2) revealed that the surface of the regenerated cellulose films displayed typical granular morphology.SEM images of regenerated films, (a) AmimCl, (b) BmimCl, (c) EmimCl, and (d) EmimAc.
(a)
(b)
(c)
(d)AFM images of regenerated films, (a) AmimCl, (b) BmimCl, (c) EmimCl, and (d) EmimAc.
(a)
(b)
(c)
(d)


### 3.2. Crystallinity

The X-ray diffraction patterns of cotton linter and cellulose films regenerated from AmimCl, BmimCl, EmimCl, and EmimAc are shown in Figure3. The value of crystallinity and diffraction planes of cellulose films are presented in Table 1. It was shown that the XRD profiles of cotton linter exhibited typical diffraction cellulose I angles (2
θ) around at 15.0°, 16.4°, and 22.6°, which corresponded to the diffraction planes of (−110), (110), and (200), respectively [18]. The diffraction patterns of the regenerated films (spectra b, c, d, and e) from the four ILs showed a broad peak at 2
θ
=
20.2
° (110), 21.2° (020) and a small broad peak at 2
θ
=
12.8
° (−110), which correspond to the crystalline form of cellulose II [19–21]. These results indicate that the transformation from cellulose I to cellulose II occurred after the dissolution and regeneration process in ILs. Compared to the original cellulose, the crystallinity of the regenerated cellulose films was lower than that of the cotton linter (Table 1). These results meant that the inter- and intramolecular hydrogen bonds between cellulose molecule were rapidly broken during the dissolution process, thus destroying the original crystalline form [22, 23]. Moreover, the coagulation process was unfavorable to the cellulose crystallization [24]. In addition, it was noteworthy that the regenerated film fabricated with EmimAc had relatively higher hydrophilicity as the contact angle was the lowest (34.18°) as well as crystallinity (34.04%), which demonstrated that EmimAc exhibited much stronger dissolubility for cellulose as compared with other ILs.Table 1
Crystallinity, peak positions in X-ray diffractograms, and contact angle of cellulose films.
Sample
Crystallinity (%)
Diffraction angle2
θ
Contact angle/θ°
(−110)
(110)
(200)
(020)
Cotton linter
54.01
15.0
16.4
22.6
—
—
AmimCl
38.41
12.8
20.2
—
21.2
38.48
BmimCl
39.25
12.6
20.2
—
21.2
40.08
EmimCl
39.24
12.8
20.6
—
21.2
54.12
EmimAc
34.04
12.8
20.2
—
21.2
34.18Figure 3
XRD images of films, (a) cotton linter, (b) AmimCl, (c) BmimICl, (d) EmimCl, and (e) EmimAc.


### 3.3. FT-IR

FT-IR spectroscopy was used to obtain direct information on chemical changes in cellulose during dissolution and regeneration. Figure4 illustrates the FT-IR spectra of the regenerated films prepared from AmimCl (spectrum a), BmimCl (spectrum b), EmimCl (spectrum c), and EmimAc (spectrum d). The peak at 3331 cm−1 is originated from the stretching of –OH groups and the signal at 2896 cm−1 is assigned to CH– stretching [25]. The band at 1643 cm−1 could be due to water in the amorphous region [26]. The peak at 1369 cm−1 is attributed to the O–H bending vibration and the strong band at 1022 cm−1 is attributed to the characteristic C–O–C stretching. The band at 1430 cm−1 in all spectra indicated that all samples contained a mixture of crystallized cellulose II and amorphous cellulose [27]. The bands due to C–O antisymmetric bridge stretching and C–O–C pyranose ring skeletal vibration were detected at 1157 cm−1. A small sharp band at 894 cm−1 corresponds to the glycosidic C–H deformation with ring vibration contribution and O–H bending, which is characteristic of β-glycosidic linkages between glucose in cellulose [28]. Moreover, the intensity of this band is relatively higher as compared with cellulose I, which corroborated the transition from cellulose I to II [29]. The bands at 1375, 1315, and 1156 cm−1 are assigned to CH-stretching, CH2 wagging, and C–O stretching in cellulose II, respectively [30]. Furthermore, it could be observed that these spectra were quite similar and no new peaks appeared in the regenerated samples, which indicated that no chemical reaction between the ILs and the cellulose had occurred during the dissolution and regeneration process. In other words, AmimCl, BmimCl, EmimCl, and EmimAc were nonderivatizing solvents for cellulose, which was consistent with the literature [7, 27].Figure 4
FT-IR images of films, (a) AmimCl, (b) BmimCl, (c) EmimCl, and (d) EmimAc.


### 3.4. Thermal Properties

Thermal degradability is affected by the chemical composition of the material. The typical TGA and DSC curves of the regenerated cellulose films are shown in Figures5 and 6. As shown in Figure 5, the thermal decomposition of the original cellulose and the regenerated cellulose was divided into two weight loss stages, corresponding to the slow pyrolysis and fast pyrolysis stages, respectively. At the first stage, the mass loss was associated with the volatilization of water. At the fast pyrolysis stage, the onset decomposition temperatures of the regenerated cellulose films were all lower than that of the original cellulose, especially the cellulose films regenerated from BmimCl (sample c) and EmimCl (sample d). The maximum decomposition rate (T
max
⁡, the decomposition temperature corresponding to the maximum weight loss rate) is shown in Figure 6. It was noted that thermal stabilities of the regenerated cellulose films were lower than that from original cellulose, which was probably caused by the lower crystallinity of regenerated cellulose as the previous work has shown that lower crystallinity and lower cellulose crystallite size can accelerate the degradation process and reduce the wood thermal stability [31].Figure 5
TGA of films, (a) virgin fibers, (b) AmimCl, (c) BmimCl, (d) EmimCl, and (e) EmimAc.Figure 6
DSC of films, (a) virgin fibers, (b) AmimCl, (c) BmimCl, (d) EmimCl, and (e) EmimAc.


### 3.5.13C CP/MAS NMR Spectra

The13C CP/MAS NMR spectra of cotton linter and different film samples are shown in Figure 7. The major signals at 105.8, 89.2, 75.3, 72.9, 71.7, and 65.4 ppm in the spectrum of cotton linter are attributed to the C-1, C-4, C-5, C-3, C-2, and C-6, respectively, which correspond to the cellulose I structure [32]. Compared with native cellulose, the C-6 signal of the regenerated cellulose film shifted from 65.4 to 62.8 ppm as a single peak, suggesting that the “t-g” conformation (ca. 66 ppm for C-6) of the C6-OH group for the crystalline parts of cellulose I had changed into a “g-t” conformation (ca. 61–63 ppm for C-6) of cellulose II [33]. For the regenerated cellulose films, the C-4 peaks located at 87.9 ppm shifted to higher magnetic field than the native cellulose (89.2 ppm), and the intensity was significantly lower, which suggested the dramatic decrease in the crystallinity due to the dissolution and regeneration process.Figure 7
13C CP-MAS spectra of films, (a) virgin fibers, (b) AmimCl, (c) BmimCl, (d) EmimCl, and (e) EmimAc.


### 3.6. Mechanical Properties

To examine the suitability of the cellulose films for industry applications, the mechanical properties of the regenerated cellulose films were determined. The typical stress-strain curves of regenerated films prepared in AmimCl (a), BmimCl (b), EmimCl (c), and EmimAc (d) are shown in Figure8. It can be seen from Figure 8 that the cellulose film regenerated from EmimCl caused the most excellent tensile strength, which was suggested by the highest tensile stress (119 Mpa). Moreover, it was noted that the tensile strain of regenerated film prepared by EmimCl was the highest (8.8%). In addition, all the samples showed thermoplastic like behavior with stress increasing rapidly at small strains and more slowly after a yield point. In comparison, although the tensile strength value for the regenerated cellulose films obtained from AmimCl was lowest, it was still slightly higher than those of the largely used commercial polyolefin films, such as polyethylene (PE) and polypropylene (PP) with tensile strength in the range of 20–40 Mpa [34]. Therefore, these results indicated that the environmentally friendly regenerated cellulose films had the potential to replace both nonbiodegradable PE and PP for packaging and agricultural purpose.Figure 8
Strength of films, (a) AmimCl, (b) BmimCl, (c) EmimCl, and (d) EmimAc.


## 3.1. Topography of Films

The topography of produced films was analyzed by SEM and AFM. SEM and AFM micrographs of the regenerated films are shown in Figures1 and 2. The SEM images indicated that all the regenerated films displayed smooth, highly uniform, and dense surface, indicating a complete regeneration of cellulose. The small nodules especially in the cellulose film obtained from ionic liquid EmimAc (sample d) were possibly caused by the presence of bubbles in processes of casting and coagulation. AFM images with higher resolution were recorded to determine the surface structural information of the films, whereas the height images were generated for the additional morphology and surface roughness of the films. AFM images (Figure 2) revealed that the surface of the regenerated cellulose films displayed typical granular morphology.SEM images of regenerated films, (a) AmimCl, (b) BmimCl, (c) EmimCl, and (d) EmimAc.
(a)
(b)
(c)
(d)AFM images of regenerated films, (a) AmimCl, (b) BmimCl, (c) EmimCl, and (d) EmimAc.
(a)
(b)
(c)
(d)


## 3.2. Crystallinity

The X-ray diffraction patterns of cotton linter and cellulose films regenerated from AmimCl, BmimCl, EmimCl, and EmimAc are shown in Figure3. The value of crystallinity and diffraction planes of cellulose films are presented in Table 1. It was shown that the XRD profiles of cotton linter exhibited typical diffraction cellulose I angles (2
θ) around at 15.0°, 16.4°, and 22.6°, which corresponded to the diffraction planes of (−110), (110), and (200), respectively [18]. The diffraction patterns of the regenerated films (spectra b, c, d, and e) from the four ILs showed a broad peak at 2
θ
=
20.2
° (110), 21.2° (020) and a small broad peak at 2
θ
=
12.8
° (−110), which correspond to the crystalline form of cellulose II [19–21]. These results indicate that the transformation from cellulose I to cellulose II occurred after the dissolution and regeneration process in ILs. Compared to the original cellulose, the crystallinity of the regenerated cellulose films was lower than that of the cotton linter (Table 1). These results meant that the inter- and intramolecular hydrogen bonds between cellulose molecule were rapidly broken during the dissolution process, thus destroying the original crystalline form [22, 23]. Moreover, the coagulation process was unfavorable to the cellulose crystallization [24]. In addition, it was noteworthy that the regenerated film fabricated with EmimAc had relatively higher hydrophilicity as the contact angle was the lowest (34.18°) as well as crystallinity (34.04%), which demonstrated that EmimAc exhibited much stronger dissolubility for cellulose as compared with other ILs.Table 1
Crystallinity, peak positions in X-ray diffractograms, and contact angle of cellulose films.
Sample
Crystallinity (%)
Diffraction angle2
θ
Contact angle/θ°
(−110)
(110)
(200)
(020)
Cotton linter
54.01
15.0
16.4
22.6
—
—
AmimCl
38.41
12.8
20.2
—
21.2
38.48
BmimCl
39.25
12.6
20.2
—
21.2
40.08
EmimCl
39.24
12.8
20.6
—
21.2
54.12
EmimAc
34.04
12.8
20.2
—
21.2
34.18Figure 3
XRD images of films, (a) cotton linter, (b) AmimCl, (c) BmimICl, (d) EmimCl, and (e) EmimAc.


## 3.3. FT-IR

FT-IR spectroscopy was used to obtain direct information on chemical changes in cellulose during dissolution and regeneration. Figure4 illustrates the FT-IR spectra of the regenerated films prepared from AmimCl (spectrum a), BmimCl (spectrum b), EmimCl (spectrum c), and EmimAc (spectrum d). The peak at 3331 cm−1 is originated from the stretching of –OH groups and the signal at 2896 cm−1 is assigned to CH– stretching [25]. The band at 1643 cm−1 could be due to water in the amorphous region [26]. The peak at 1369 cm−1 is attributed to the O–H bending vibration and the strong band at 1022 cm−1 is attributed to the characteristic C–O–C stretching. The band at 1430 cm−1 in all spectra indicated that all samples contained a mixture of crystallized cellulose II and amorphous cellulose [27]. The bands due to C–O antisymmetric bridge stretching and C–O–C pyranose ring skeletal vibration were detected at 1157 cm−1. A small sharp band at 894 cm−1 corresponds to the glycosidic C–H deformation with ring vibration contribution and O–H bending, which is characteristic of β-glycosidic linkages between glucose in cellulose [28]. Moreover, the intensity of this band is relatively higher as compared with cellulose I, which corroborated the transition from cellulose I to II [29]. The bands at 1375, 1315, and 1156 cm−1 are assigned to CH-stretching, CH2 wagging, and C–O stretching in cellulose II, respectively [30]. Furthermore, it could be observed that these spectra were quite similar and no new peaks appeared in the regenerated samples, which indicated that no chemical reaction between the ILs and the cellulose had occurred during the dissolution and regeneration process. In other words, AmimCl, BmimCl, EmimCl, and EmimAc were nonderivatizing solvents for cellulose, which was consistent with the literature [7, 27].Figure 4
FT-IR images of films, (a) AmimCl, (b) BmimCl, (c) EmimCl, and (d) EmimAc.


## 3.4. Thermal Properties

Thermal degradability is affected by the chemical composition of the material. The typical TGA and DSC curves of the regenerated cellulose films are shown in Figures5 and 6. As shown in Figure 5, the thermal decomposition of the original cellulose and the regenerated cellulose was divided into two weight loss stages, corresponding to the slow pyrolysis and fast pyrolysis stages, respectively. At the first stage, the mass loss was associated with the volatilization of water. At the fast pyrolysis stage, the onset decomposition temperatures of the regenerated cellulose films were all lower than that of the original cellulose, especially the cellulose films regenerated from BmimCl (sample c) and EmimCl (sample d). The maximum decomposition rate (T
max
⁡, the decomposition temperature corresponding to the maximum weight loss rate) is shown in Figure 6. It was noted that thermal stabilities of the regenerated cellulose films were lower than that from original cellulose, which was probably caused by the lower crystallinity of regenerated cellulose as the previous work has shown that lower crystallinity and lower cellulose crystallite size can accelerate the degradation process and reduce the wood thermal stability [31].Figure 5
TGA of films, (a) virgin fibers, (b) AmimCl, (c) BmimCl, (d) EmimCl, and (e) EmimAc.Figure 6
DSC of films, (a) virgin fibers, (b) AmimCl, (c) BmimCl, (d) EmimCl, and (e) EmimAc.


## 3.5.13C CP/MAS NMR Spectra

The13C CP/MAS NMR spectra of cotton linter and different film samples are shown in Figure 7. The major signals at 105.8, 89.2, 75.3, 72.9, 71.7, and 65.4 ppm in the spectrum of cotton linter are attributed to the C-1, C-4, C-5, C-3, C-2, and C-6, respectively, which correspond to the cellulose I structure [32]. Compared with native cellulose, the C-6 signal of the regenerated cellulose film shifted from 65.4 to 62.8 ppm as a single peak, suggesting that the “t-g” conformation (ca. 66 ppm for C-6) of the C6-OH group for the crystalline parts of cellulose I had changed into a “g-t” conformation (ca. 61–63 ppm for C-6) of cellulose II [33]. For the regenerated cellulose films, the C-4 peaks located at 87.9 ppm shifted to higher magnetic field than the native cellulose (89.2 ppm), and the intensity was significantly lower, which suggested the dramatic decrease in the crystallinity due to the dissolution and regeneration process.Figure 7
13C CP-MAS spectra of films, (a) virgin fibers, (b) AmimCl, (c) BmimCl, (d) EmimCl, and (e) EmimAc.


## 3.6. Mechanical Properties

To examine the suitability of the cellulose films for industry applications, the mechanical properties of the regenerated cellulose films were determined. The typical stress-strain curves of regenerated films prepared in AmimCl (a), BmimCl (b), EmimCl (c), and EmimAc (d) are shown in Figure8. It can be seen from Figure 8 that the cellulose film regenerated from EmimCl caused the most excellent tensile strength, which was suggested by the highest tensile stress (119 Mpa). Moreover, it was noted that the tensile strain of regenerated film prepared by EmimCl was the highest (8.8%). In addition, all the samples showed thermoplastic like behavior with stress increasing rapidly at small strains and more slowly after a yield point. In comparison, although the tensile strength value for the regenerated cellulose films obtained from AmimCl was lowest, it was still slightly higher than those of the largely used commercial polyolefin films, such as polyethylene (PE) and polypropylene (PP) with tensile strength in the range of 20–40 Mpa [34]. Therefore, these results indicated that the environmentally friendly regenerated cellulose films had the potential to replace both nonbiodegradable PE and PP for packaging and agricultural purpose.Figure 8
Strength of films, (a) AmimCl, (b) BmimCl, (c) EmimCl, and (d) EmimAc.


## 4. Conclusion

The regenerated cellulose films were successfully prepared using different ionic liquids including AmimCl, BmimCl, EmimCl, and EmimAc as solvents. It was shown that the regenerated cellulose films displayed smooth, highly uniform, and dense morphology properties.13C CP/MAS NMR spectra and XRD corroborated that the transition from cellulose I to II had occurred after preparation. In comparison, the ionic liquid EmimAc possessed much stronger dissolubility for cellulose and the cellulose film regenerated from ionic liquid EmimCl exhibited the most excellent tensile strength. The notable properties of the regenerated cellulose films are promising for applications in transparent, biodegradable packaging and agricultural purpose as a substitute for PP and PE.



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*Source: 214057-2014-06-09.xml*