Effects of Chitosan and Cellulose Derivatives on Sodium Carboxymethyl Cellulose-Based Films: Study from Rheological Properties of Film-Forming Solutions

1. Introduction

With increasing importance of sustainable development, bio-based packaging materials and efficient drug delivery systems are gaining attention as viable options [1,2]. Cellulose has attracted particular interest for its advantages, such as reproducibility, biodegradability, non-cytotoxicity, thermostability, and chemical stability [3]. However, the water-insolubility of cellulose greatly restricts its wide application. To address this limitation, cellulose is often modified to make it water-soluble. Sodium carboxymethyl cellulose (CMC) is one of most water-soluble cellulose derivatives. In addition to being water soluble, CMC inherits all the advantages of cellulose and is widely used in food packaging and drug delivery [4].

While pure CMC films show promise as food packaging materials and efficient drug delivery systems, they often lack of sufficient mechanical properties [5]. Large number of studies has demonstrated that the incorporation of polymers or polymer-based nanomaterials, such as chitosan and cellulose derivatives, can improve the mechanical properties of CMC films, as well as their thermodynamic stability [6,7,8]. It is due to the electrostatic interaction and hydrogen bonding between polymer additives and CMC. Rheological tests are commonly used to analyze the interaction between polymeric materials [2,9].

The rheological properties of polymeric solution depend on various factors such as molecular weight ($M_w$), distribution of molecular weight, degree of substitution (DS), and concentration (C_CMC). For example, at fixed concentration and DS, CMC solutions exhibit shear-thinning behavior, Newtonian fluid behavior and shear-thickening behaviors with $M_w$ increasing from 9×10⁴ to 25×10⁴, and 70×10⁴ [10]. While the concentration is increased from 0.5, 2.0 and then 3.0 g/L, CMC solutions exhibit Newtonian fluid behavior, shear-thinning, and shear-thickening behaviors, respectively [11]. The apparent viscosity of CMC solutions increases with increasing $M_w$, DS, and C_CMC. CMC with large $M_w$ shows more notable influence on rheological properties. The variation of these rheological properties depends on the interaction between carboxymethyl cellulose molecules [12].

In this paper, the effect of chitosan and cellulose derivatives on rheological properties of CMC-based film-forming solutions were comparatively studied. The molecular structure and content of the derivatives, and temperature were investigated. Based on the results of rheology, selected CMC-based films were prepared and their properties including wettability, transparency, hydrophilicity, mechanical properties, degradation and toxicity were studied. This work will provide an idea from the design of film-forming solution to the targeted preparation of food packaging and effective drug delivery materials with specific properties.

2. Experimental

2.1. Materials

Sodium carboxymethyl cellulose (UPS grade, CMC) and O-carboxymethylated chitosan (O-CMCh, with a degree of degradation ≥ 80% and a viscosity of 80 mPa.s) were purchased from Shanghai Aladdin Biochemical Technology Co., Ltd. Hydroxypropyltrimethyl ammonium chloride chitosan (HACC) with a degree of substitution (DS) of ≥ 98% was provided by Shanghai Macklin Biochemical Co., Ltd. N-2-hydroxypropyl-3-trimethylammonium-O-carboxymethyl chitosan (HTCMCh), cellulose nanofibers (CNF), and cellulose nanocrystals (CNC) were synthesized according to our previous works [13,14,15].

2.2. Preparation of film-forming solutions

Take the preparation of CMC/HTCMCh solution as an example. Mother solutions of CMC (4% w/v) and HTCMCh (2% w/v) were prepared at 80°C and 60°C by magnetic stirring (600 rpm) for 4 hours, then cooled to room temperature naturally. A film-forming solution consisting of 12.5 g CMC mother solution, certain amounts of HTCMCh and deionized water, the total weight of the film-forming solution was 25 g. The solution was then kept at 60°C and magnetically stirred (600 rpm) for 4 hours, followed by cooling to 25°C for later use. The mass ratios of HTCMCh to CMC (m_HTCMCh/m_CMC) were 1:99, 5:95, and 10:90, and abbreviated as CMC/HTCMCh_1%, CMC/HTCMCh_5%, CMC/HTCMCh_10%, respectively.

The film-forming solutions of CMC/O-CMCh, CMC/HACC, CMC/CNC and CMC/CNF were also prepared, and the abbreviations were similar to those of CMC/HTCMCh.

2.3. Preparation of CMC-based films

Each film-forming solution (25 g) was poured into a polytetrafluoroethylene mold with 5.5 cm in diameter and 0.7 cm in height. The molds were then placed in a drying oven at 40 °C for 48 hours to evaporate the water.

2.4. Characterization of CMC-based films

The thickness of the films was measured using an electronic digital Vernier caliper (Shenzhen Duliang Precision Machinery Co., Ltd.) with an accuracy of 0.001 mm. During the measurement, five points were randomly selected for each film, and the values were averaged.

The wettability of the films was evaluated by measuring the contact angles using a KRUSS DSA 100 analyzer through the sessile drop method.

The whiteness and transmittance of the films were tested using a YQ-Z-48B whiteness tester (Hangzhou Qingtong Brocade Automation Technology Co., Ltd., China). A R457 whiteboard with a whiteness of 84.5 was used as the calibration sample. The transparency and transmittance were measured using a white board with a Ry of 84% and a black background.

Thermogravimetric analysis (TGA) of the films was performed using a thermo-gravimetric analyzer (Mettler Toledo, Switzerland) in the range of 25ºC to 500ºC. The heating rate was 10ºC·min^-1, and a nitrogen flow was 100mL·min^-1.

The tensile strength (TS), elongation at break (EB) and Young’s moduli (E) were measured using an electronic universal testing machine (Jinan Teson Machinery Co. Ltd.). The films were cut into 4.0×1.0 cm strips, and the crosshead speed was set at 0.2 cm/min.

2.5. Rheological measurement

The rheological properties were measured using the method we previously reported [14]. In brief, a DHR-2 rheometer with a parallel plate geometry of 45.0 mm in diameter, and a gap of 1.0 mm between the plate and sample stage was used. Prior to the measurement of the dynamic moduli, a linear viscoelastic region was determined at an angular frequency of 1.0 rad/s. The dynamic moduli, including the storage (G') and loss moduli (G''), were determined with the angular frequency of 0.1 to 100 rad/s. The temperature was maintained at 25 °C unless otherwise specified. The apparent viscosity was measured within the shear rate range of 0.1 to 100 s^-1 at 25°C.

2.6. Biodegradability of films

To study the final aerobic biodegradability of the films, the methodology of the UNE-EN ISO 17556 standard was adapted [16]. In summary, this assay was carried out under controlled composting conditions to determine the total biodegradability of the films. A constant rate of N₂-O₂ (78/23 v/v) mixture was blown into the containers with the films for every 24 h, and the CO₂ was collected with NaOH solution and titrated. After 35 days of testing, the biodegradability of each film was calculated based on the amount of CO₂.

2.7. In-vitro cytotoxicity

The cytotoxicity of the CMC-based films to Human foreskin fibroblast cells (HFF-1) was evaluated by the 3-(4,5-dimethylthiazol-2-yl)-2,5-diphenyltetrazolium bromide (MTT) (Sigma, USA) method. The initial concentration of HFF-1 cell in cultural medium was 104 HFF-1 cells/mL, and the cells were cultured for 24 h in 96-well plates. The HFF-1celles were treated with the 100 μL of the film-forming solution for another 24 h, before 10 μL MTT with concentration of 5 mg/mL was added into each well of the 96-well plate, and incubated at 37 °C for 4 h. Subsequently, the cells were rinsed with phosphate-buffered saline (PBS), and dissolved in 100 μL of dimethyl sulfoxide (DMSO). The absorbance was measured at 540 nm on a microplate reader (SpectraMax M5; Molecular Devices, USA).

3. Results and discussion

3.1. Effect of chitosan and cellulose derivative structures on rheological properties

To investigate the effect of molecular structure on the rheological properties of CMC-based solutions, chitosan derivatives of HTCMCh, O-CMCh, HACC and cellulose derivatives of CNC and CNF with mass content of 1% were selected.

CMC solution exhibits Newtonian behavior at shear frequencies below 1 s^-1 and shear thinning behavior at frequencies above 1 s^-1, as shown in Figure 1A. The Newtonian behavior corresponds to the insistence of hydrogen bonding and entanglement network between CMC molecular chains. With increasing shear rate, the hydrogen bonding is destroyed, as well as the entanglement network, leading to shear thinning behavior [7,11].

The introduction of HTCMCh, O-CMCh, HACC, CNC and CNF resulted in the variation of the CMC solution viscosity, however, they did not affect the Newtonian-shear thinning behavior of the solutions (Figure 1A). All the chitosan and cellulose derivatives, except for O-CMCh, increased the viscosity of the CMC solution (the insert in Fig.1A). CNF showed the greatest enhancement to CMC solution viscosity, followed by HTCMCh, and CNC showed the least enhancement. It ascribed to the largest aspect ratio of CNF, except for large amount of hydrogen bonds, however, CNC possess the smallest one [17]. It is noteworthy that the addition of HTCMCh resulted in an increase in the viscosity, while O-CMCh led to a slight decrease. This can be attributed to the different forces between O-CMCh and HTCMCh and CMC. The repulsion between CMC and O-CMCh may weaken the hydrogen bonds between CMC molecules, as a result the viscosity of CMC/O-CMCh solution decreases. HTCMCh is a kind of amphiphilic chitosan derivatives, quaternary ammonium salt groups in HTCMCh interact with the carboxyl groups in CMC, forming entanglement and increasing solution viscosity [18].

The relationship between the shear rate and shear stress of CMC film-forming solutions was analyzed and fitted using a power-law model (Equation (1)).

$$\sigma =k_{PL}{\dot{\gamma }}^n$$

(1)

Where $\mathsf{\sigma }$,$k_{PL}$, $\dot{\gamma }$ and n are shearing stress, consistency coefficient, shear rate and power-law exponent, respectively. When the value of n is less than 1, the solution exhibits shear thinning behavior.

The fitted parameters are consistent with the experimental data, such as all the power-law exponent values are less than 1, confirming the shear thinning behavior of the film-forming solutions. The consistency coefficient, viscosity at 1s^-1 of CMC/CNF_1% system is the largest, and those of CMC/CNC_1% system is the lowest.

Table 1. Parameters of CMC-based film-forming solutions fitted with power law model.

Samples	$k_{PL}$(Pa. s)	n	${\mathsf{\eta }}_1$(Pa·s)	${\mathsf{\eta }}_{10}$(Pa·s)	${\mathsf{\eta }}_{100}$(Pa·s)
CMC	6.9559	0.5321	1.8681	1.5866	0.8476
CMC/O-CMCh1%	7.0044	0.5243	1.7254	1.5840	0.8279
CMC/O-CMCh5%	6.2411	0.5459	1.7680	1.4569	0.8067
CMC/O-CMCh10%	6.8765	0.5391	1.9459	1.5886	0.8636
CMC/HTCMCh1%	6.7830	0.5249	2.2382	1.5275	0.8043
CMC/HTCMCh5%	7.0774	0.5316	2.0604	1.6338	0.8595
CMC/HTCMCh10%	6.4761	0.5434	1.8805	1.5285	0.8260
CMC/HACC1%	7.1250	0.5195	2.0952	1.6355	0.8237
CMC/HACC5%	10.5533	0.4723	4.1827	2.4424	0.9936
CMC/HACC10%	10.1251	0.4630	5.0657	2.4074	0.9069
CMC/CNC1%	5.7862	0.5361	1.9923	1.3922	0.7148
CMC/CNC5%	7.6036	0.5203	2.3339	1.7777	0.8841
CMC/CNC10%	8.8637	0.5168	2.5765	1.9835	1.0099
CMC/CNF1%	9.4362	0.5096	2.8358	2.1238	1.0484
CMC/CNF5%	8.8237	0.5054	2.6472	1.9926	0.9598
CMC/CNF10%	6.8930	0.5299	2.1640	1.6343	0.8308

Note: ${\mathsf{\eta }}_1$, ${\mathsf{\eta }}_{10}$and ${\mathsf{\eta }}_{100}$ represent the apparent viscosity of the CMC film-forming solution at shear rates of 1, 10, and 100 rad/s, respectively, and the R² of the fitted data are all greater than 0.99.

Table 1. Parameters of CMC-based film-forming solutions fitted with power law model.

Samples	$k_{PL}$(Pa. s)	n	${\mathsf{\eta }}_1$(Pa·s)	${\mathsf{\eta }}_{10}$(Pa·s)	${\mathsf{\eta }}_{100}$(Pa·s)
CMC	6.9559	0.5321	1.8681	1.5866	0.8476
CMC/O-CMCh1%	7.0044	0.5243	1.7254	1.5840	0.8279
CMC/O-CMCh5%	6.2411	0.5459	1.7680	1.4569	0.8067
CMC/O-CMCh10%	6.8765	0.5391	1.9459	1.5886	0.8636
CMC/HTCMCh1%	6.7830	0.5249	2.2382	1.5275	0.8043
CMC/HTCMCh5%	7.0774	0.5316	2.0604	1.6338	0.8595
CMC/HTCMCh10%	6.4761	0.5434	1.8805	1.5285	0.8260
CMC/HACC1%	7.1250	0.5195	2.0952	1.6355	0.8237
CMC/HACC5%	10.5533	0.4723	4.1827	2.4424	0.9936
CMC/HACC10%	10.1251	0.4630	5.0657	2.4074	0.9069
CMC/CNC1%	5.7862	0.5361	1.9923	1.3922	0.7148
CMC/CNC5%	7.6036	0.5203	2.3339	1.7777	0.8841
CMC/CNC10%	8.8637	0.5168	2.5765	1.9835	1.0099
CMC/CNF1%	9.4362	0.5096	2.8358	2.1238	1.0484
CMC/CNF5%	8.8237	0.5054	2.6472	1.9926	0.9598
CMC/CNF10%	6.8930	0.5299	2.1640	1.6343	0.8308

Note: ${\mathsf{\eta }}_1$, ${\mathsf{\eta }}_{10}$and ${\mathsf{\eta }}_{100}$ represent the apparent viscosity of the CMC film-forming solution at shear rates of 1, 10, and 100 rad/s, respectively, and the R² of the fitted data are all greater than 0.99.

The viscoelastic moduli of CMC and CMC/additives1% solutions are shown in Figure 1B, which shows that all the storage moduli (G″) is higher than that of elastic moduli (G′). According to previous work, the viscoelastic properties of CMC solutions are mainly related to the changes of CMC concentration [19]. Benchabane et al. [20] also revealed that CMC solutions showed viscous properties at concentrations of 1 wt% and 3 wt%. Additives can alter the properties of solutions, but they typically do not affect the fundamental characteristics of the liquid, such as the viscosity and elasticity modulus [21]. These two parameters are important for describing the flow and deformation behavior of liquids, and are related to the intermolecular interactions within the liquid [22]. When the angular frequencies were 50.12 rad/s, the elastic moduli of CMC/HTCMCh_1% and CMC/O-CMCh_1% film-forming solutions exceed the viscous ones, which can be attributed to intermolecular interactions.

3.2. Effect of derivative concentration on rheological properties

The rheological behaviors of CMC-based film-forming solutions with different content of chitosan and cellulose derivatives are shown in Figure 2. The content of HACC shows notable influence on viscosity of CMC/HACC film-forming solutions within shear rate of 0.1-100 s^-1. When the concentration of HACC is increased from 1% to 10%, the viscosity of the solution increased rapidly from 2.09 to 5.07 Pa·s (Figure 2A). The contents of CNC and CNF show small influence on rheological properties of film-forming solutions (Figure 2G,I), and those of HTCMCh and O-CMCh only a little influence (Figure 2C,E). As is known that HACC is a kind of cationic chitosan derivatives, which can interact with CMC through electrostatic forces, however, O-CMCh is a kind of anionic chitosan derivatives, which has very strong electrostatic repulsion with CMC. HTCMCh is a kind of amphiphilic chitosan derivatives, and there are intra- and inter-molecular electrostatic interactions at a large content. In short, HACC increases the viscosity of the film-forming solutions through electrostatic interactions and hydrogen bonding, which also results in the lowest onset rate of shear thinning behavior among all the film-forming solutions [18]. Similar phenomena have been observed in other systems [17,23]. For HTCMCh and O-CMCh, there is a balance between the hydrogen bond between HTCMCh and O-CMCh and CMC, and the shielding effect of –COO^- groups [24]. In this work, the two effects are evenly matched. CNC and CNF influence the viscosity of CMC-based film-forming solution through their physical obstacles and forming a large number of hydrogen bonds with CMC [25].

The viscoelasticity of the CMC/HACC film-forming solution is significantly affected by the content of HACC within the angular frequency from 0.1 to 100 rad/s. When the content of HACC increased from 1% to 10%, the storage modulus increased from 4.06 to 11.93 Pa (Figure 2B). This is due to the strong electrostatic interaction between the quaternary ammonium groups in HACC and carboxyl groups in CMC, making the physical interactions between molecules stronger [26]. Small amount of HACC could induce CMC aggregate, which increases the strength of the interactions and enhances the physical correlation effect between the aggregates [27]. As a result, the storage modulus of CMC/HACC film-forming solution increases. The addition of O-CMCh and HTCMCh, as well as CNC and CNF, had little effect on the storage moduli (Figure 2D,F,H,J). On the one hand, it is due to the presence of electrostatic repulsion between the macromolecules, and on the other hand, it is the competition between the additives and CMC molecules, decreasing the intramolecular hydrogen bonding of CMC molecules [28,29].

3.3. Effect of temperature on rheological properties

Figure 3 demonstrates that the viscosities and dynamic moduli of CMC-based film-forming solutions decrease with an increase in temperature, which are typical temperature-dependent behaviors [30,31]. As temperature increases, the decrease in viscosity can be attributed to an increase in molecular free volume and a corresponding decrease in intermolecular interactions [32,33]. The increase in temperature raises the average kinetic energy of molecules, which in turn increases the average distance between them, leading to an increase in their free volume [34]. This temperature-dependent behavior also influences the viscoelastic properties. At lower temperatures, CMC molecules are mainly in a condensed state, and the intermolecular interactions between them are strong, resulting in a higher storage modulus [35]. However, as temperature increases, a large amount of thermal energy is input into the system, resulting in enhanced molecular vibrations and increased molecular freedom for CMC molecules [36]. Therefore, the intermolecular interaction forces decrease, leading to a decrease in storage modulus of CMC. In addition, under high temperature conditions, CMC molecules are more prone to rheological instability, which may also contribute to the decrease in storage modulus [37]. CMC may undergo chemical degradation under different temperature, which may further affect the change in storage modulus [38].

Table 2. Rheological parameters of CMC-based film-forming solutions were calculated at different temperatures using the power law.

Samples	$k_{PL}$(Pa. s)	n	${\mathsf{\eta }}_1$(Pa·s)	${\mathsf{\eta }}_{10}$(Pa·s)	${\mathsf{\eta }}_{100}$(Pa·s)	T (℃)
CMC/O-CMCh10%	8.7973	0.5099	2.7071	2.0333	0.9783	15
CMC/O-CMCh10%	6.8765	0.5391	1.9459	1.5886	0.8636	25
CMC/O-CMCh10%	5.5768	0.5362	1.5683	1.2776	0.6837	35
CMC/HTCMCh10%	9.2297	0.5082	2.9375	2.1512	1.0171	15
CMC/HTCMCh10%	6.4761	0.5434	1.8805	1.5285	0.8260	25
CMC/HTCMCh10%	5.2879	0.5415	1.4607	1.2248	0.6657	35
CMC/HACC10%	11.1922	0.4578	6.2172	3.0673	1.1879	15
CMC/HACC10%	10.1251	0.4631	5.0656	2.4074	0.9069	25
CMC/HACC10%	5.6527	0.4937	2.8466	1.3937	0.5750	35
CMC/CNC10%	11.5919	0.4808	3.6063	2.5182	0.8147	15
CMC/CNC10%	8.8637	0.5168	2.5765	1.9835	1.0099	25
CMC/CNC10%	7.1385	0.5287	1.9328	1.6053	0.8605	35
CMC/CNF10%	8.0515	0.5042	2.7048	1.8902	0.8744	15
CMC/CNF10%	6.8930	0.5299	2.1640	1.6343	0.8308	25
CMC/CNF10%	5.2780	0.5327	1.5827	1.2078	0.6411	35

Table 2. Rheological parameters of CMC-based film-forming solutions were calculated at different temperatures using the power law.

Samples	$k_{PL}$(Pa. s)	n	${\mathsf{\eta }}_1$(Pa·s)	${\mathsf{\eta }}_{10}$(Pa·s)	${\mathsf{\eta }}_{100}$(Pa·s)	T (℃)
CMC/O-CMCh10%	8.7973	0.5099	2.7071	2.0333	0.9783	15
CMC/O-CMCh10%	6.8765	0.5391	1.9459	1.5886	0.8636	25
CMC/O-CMCh10%	5.5768	0.5362	1.5683	1.2776	0.6837	35
CMC/HTCMCh10%	9.2297	0.5082	2.9375	2.1512	1.0171	15
CMC/HTCMCh10%	6.4761	0.5434	1.8805	1.5285	0.8260	25
CMC/HTCMCh10%	5.2879	0.5415	1.4607	1.2248	0.6657	35
CMC/HACC10%	11.1922	0.4578	6.2172	3.0673	1.1879	15
CMC/HACC10%	10.1251	0.4631	5.0656	2.4074	0.9069	25
CMC/HACC10%	5.6527	0.4937	2.8466	1.3937	0.5750	35
CMC/CNC10%	11.5919	0.4808	3.6063	2.5182	0.8147	15
CMC/CNC10%	8.8637	0.5168	2.5765	1.9835	1.0099	25
CMC/CNC10%	7.1385	0.5287	1.9328	1.6053	0.8605	35
CMC/CNF10%	8.0515	0.5042	2.7048	1.8902	0.8744	15
CMC/CNF10%	6.8930	0.5299	2.1640	1.6343	0.8308	25
CMC/CNF10%	5.2780	0.5327	1.5827	1.2078	0.6411	35

The increase in temperature also results in a slight increase in the values of n, and a notable decrease in $k_{PL}$ [12]. This suggests that an increase in temperature can reduce the degree of shear thinning and viscosity. Both the shear thinning behavior and viscosity depend on intermolecular and intramolecular interactions. The CMC/HACC_10%,15℃ system exhibits the highest ${\eta }_1$ value, which may be attributed to the strong electrostatic interaction between HACC and CMC. According to Yang et al., the strong interaction between HACC/CMC and the reorganization of the chains allows the apparent viscosity of the hybrid system to be preserved even as the temperature increases [18].

3.4. Morphology, thickness, whiteness, transmittance, and wettability of CMC-based films

The film-forming solutions with chitosan and cellulose were used to prepared CMC-based films. Take the films of CMC/HTCMCh and CMC/CNF films as examples (Figure 4), the films are good at transparency. The results are similar to those polysaccharide-based films, which is attributed to the good compatibility of CMC with chitosan and cellulose derivatives [39]. Zhang and Jin also reported that the microstructure (cross section) of CMC/cationic chitosan derivative film showed a rough structure, while the CMC/cellulose derivative film showed small amount of cracks [39,40]. The rough structures are attributed to the aggregates of CMC-cationic chitosan derivative resulted from the electrostatic interaction between cationic groups in chitosan derivative and ${-\mathrm{COO}}^{-}$ groups in CMC [41]. The small amount of cracks in CMC/cellulose derivative film is caused by hydrogen bonding effect and nanoparticle effect [14]. In addition, the microscopic morphology of CMC-based films can be influenced by various factors, including film-forming conditions, plasticizers, degree of substitution, molecular weight of CMC, and the interaction between CMC and additives [42].

The thickness of CMC film is listed in Table 3, where one can find that both the HTCMCh and HACC decrease the thickness of the films, on the contrary, HACC, CNC and CNF increase the thickness.

It is reported that film thickness depends on the natural properties of film-forming materials, the alignment/interaction between these materials, and the concentration of additives [41]. CMC and HTCMCh are both water-soluble and contain groups with opposite charges in the two macromolecules. In other words, strong electrostatic interactions between these two macromolecules dominate their arrangement, and HACC is the same [43]. Under a high mass ratio of HTCMCh and HACC (e.g., 10%), the electrostatic interactions between the molecules and hydrogen bonding induce tight cross-linking between the two macromolecules. Therefore, the thickness of CMC/HTCMCh and CMC/HACC films decreases with the increase of additives. CMC and O-CMCh, CNC, CNF contain the same negative charge groups. Therefore, with the increase of O-CMCh, CNC, and CNF content, the electrostatic interactions between the molecules weaken, resulting in an increase in film thickness.

The intermolecular interaction and arrangement of the macromolecules in the films also affect the surface properties, including wettability and water vapor permeability. The contact angles of the films are listed in Table 3. All the CMC-based films are hydrophilic, and with the increase of HTCMCh and HACC contents, the contact angles of CMC-based films increase. However, with increasing O-CMCh, CNC, and CNF content, the contact angle of CMC-based films decreases. This was ascribed to the different intermolecular interactions as the thickness changes. These results are consistent with those in the N-(2-hydroxypropyl)-3-trimethylammonium chitosan (HTCC)/CMC film [18] and the tea polyphenol/hydroxypropyl starch film [44].

The whiteness and transmittance of the control CMC film are 35.34±0.13 and 92.72±0.16, respectively. The addition of chitosan derivatives and cellulose has almost no effect on the whiteness and transparency of CMC-based films (Table 3), which is confirmed from the optical appearance in Figure 4. This means there is good compatibility of the two biomacromolecules.

3.5. Thermodynamic properties of CMC-based films

The intermolecular interactions of CMC-based films are also reflected in the TGA curves. The thermal gravimetric results of CMC-based films are shown in Figure 5. DTG curves are more sensitive than that of TGA ones. The DTG curve of pure CMC film exhibits three distinct peaks corresponding to the evaporation of bound water and the dissociation of hydrogen bonds (111℃), the evaporation of internal water (173℃), and the decomposition of the cellulose chain (288℃), respectively. [40].

The interaction between the additives and CMC, such as hydrogen bonding and electrostatic interaction, can improve the thermal stability of composite films. However, the destruction of intramolecular and intermolecular hydrogen bonds and the formation of discontinuous structures can decrease the thermal stability properties of CMC. The addition of 10% HTCMCh did not have a significant effect on the thermal stability of CMC, while the presence of 10% nanocellulose (CNC and CNF) enhanced the encapsulation of water by the composite film, resulting in a higher evaporation temperature of the encapsulated water. The CMC/CNF_10% and CMC/CNC_10% films exhibit a higher maximum decomposition temperature (292.48℃ and 294.60℃, respectively). The addition of nanocellulose can effectively increase the maximum decomposition temperature of CMC composite films, which may be due to a small specific surface area and size of nanocellulose [40]. The filling effect of nanocellulose on CMC and the strong hydrogen bond with CMC may hinder the relative motion between molecules, thereby increasing the maximum decomposition temperature of the composite films [14]. The electrostatic interaction between CMC and cationic polymers can effectively improve the thermodynamic properties of CMC films. For example, HACC can effectively increase the maximum decomposition temperature of CMC films [18] and HTCMCh can improve the glass transition temperature of CMC films from 56.5℃ to 90.2℃ [41]. Electrostatic repulsive interactions between CMC and CNC and CNF can result in the formation of pinholes and occasional slits in CMC-based films.

The stronger intermolecular interaction between CMC and 10% CNF, as well as the denser structure of the resulting CMC/CNF_10% film, contribute to a higher maximum decomposition temperature compared to 10% CNC. This finding is consistent with the results of the rheology.

3.6. Mechanical properties of CMC-based films

Table 4 displays the tensile strength (TS), elongation at break (EB), and Young's modulus (E) of CMC-based films. The neat CMC film exhibits a tensile strength of 13.57 MPa and an elongation at break of 44.41±0.61%. The mechanical properties of CMC films are influenced by various factors, including the source of CMC, its molecular mass and distribution, and the conditions under which the film is formed [41]. The addition of chitosan and cellulose derivatives results in an increase in the tensile strength of CMC-based films compared to pure CMC film (Table 4). Among the CMC-based films, the maximum tensile strength is observed in CMC/CNF_10% (42.41 MPa), followed by CMC/CNC_10% (32.22 MPa), while the minimum is observed in pure CMC (13.57 MPa). Additives typically interact with film-forming substrates through hydrogen bonds, which can enhance the tensile strength of the film [45]. Tarrés et al. [46] reported that CNF significantly improved the strength of paper due to its high surface area. The carboxylate and carboxymethyl groups in dense and layered fibers form more hydrogen bonds between nanofibers, thereby increasing the tensile strength.

In the current study, it is found that the tensile strength and elongation at break of CMC-based films are enhanced with the incorporation of O-CMCh and HTCMCh. According to previous reports [41], the increase in tensile strength and elongation at break can be attributed to the biocompatibility, strong electrostatic interactions, and hydrogen bonding between O-CMCh and CMC. With the addition of HACC, CNC, and CNF, the elongation at break of CMC-based films decreases. This ascribes to the hydrogen bonds between the additive and the film-forming substrate limit their relative sliding possibility, leading to a decrease in elongation at break.

Young's modulus is a typical characteristic of material stiffness, the larger the Young's modulus is, the less deformability [47]. The incorporation of O-CMCh and HTCMCh in CMC-based films results in a lower Young's modulus, which translates to better toughness, superior processability, and wider applicability. The CMC/CNF film exhibits a tensile strength of 42.41 MPa and a Young's modulus of 121.17 MPa, which are 13.57 MPa and 30.84 MPa higher than those of CMC film, respectively. These findings suggest that CMC/CNF film possesses superior mechanical properties and deformation resistance. Similar results were observed in CMC/HACC films [48], CMC/CNC films [49], and graphene oxide/carboxymethylcellulose/alginate composite blend films [50].

3.7. Biodegradability of CMC-based films

The films produced by adding chitosan and cellulose derivatives into CMC are suitable for various applications, including food packaging and drug delivery. However, the films should also be biodegradable to maintain its usability. This prompts us to evaluate the biodegradability of pure CMC film and CMC film containing chitosan and cellulose derivatives. CMC can be made more biodegradable by adding natural plasticizers [51]. In the current, bio-based polylactic acid (PLA) was used as a control to evaluate if the level of biodegradability of our films was optimal compared to other materials already described as biodegradable [52]. After 35 days of testing, the accumulated CO₂ (mg) values obtained were: 264.92 for CMC film, 281.45 for CMC/O-CMCh film, 287.78 for CMC/HTCMCh film, 289.08 for CMC/HACC film, 290.46 for CMC/CNC, 296.12 for CMC/CNF and 108.83 for PLA. Therefore, after 35 days, some of our films have already biodegraded more than PLA. The results obtained indicate that the biodegradability of our films was optimal. Furthermore, these findings support the use of the studied composites as a replacement for non-biodegradable, environmentally unfriendly plastics that can have additional harmful effects on both health and the economy.

3.8. Cytotoxicity of CMC-based films

When considering the application of CMC-based films in food packaging and drug delivery, it is essential to evaluate their biocompatibility. The in-vitro cytotoxicity of CMC-based films was determined by MTT assay, with a concentration range of 0 (control sample) to 2.0 mg/mL. As shown in Figure 7, the viability of cells on all films was greater than 90%, meaning that all CMC-based films were non-toxic and independent of the type of additive. This result is consistent with previous reports [53,54,55], confirming the CMC-based films can be safely used as food packaging and drug delivery materials.

4. Conclusions

The rheological properties of CMC-based film-forming solutions were studied. The additives were O-CMCh, HTCMCh, HACC, CNC, and CNF. The results showed that all CMC-based film-forming solutions exhibited shear thinning behavior. The CMC-based film-forming solutions showed Newtonian plateau before 1s^-1 followed by slight shear thinning behavior. The interaction between CMC and additives depends on the charge of the additives, for example, HACC and HTCMCh interact with CMC primarily through electrostatic interaction except for hydrogen bonds. O-CMCh, CNC and CNF interact with CMC mainly through hydrogen bonds. Both HTCMCh and CNF had a significant thickening effect on CMC solutions. The strong electrostatic force between HACC and CMC resulted in the loss of the original Newtonian plateau of CMC solutions at low shear frequencies. When HACC content reached to 5% and 10%, CMC solutions exhibited shear thinning behavior throughout the shear rate range of 0.1-100 s^-l. The rheological properties showed that CMC and all the additives have good biocompatibility.

The films prepared from selected CMC-based film-forming solutions showed very high transmittance, hydrophilicity, improved thermal stability, enhanced tensile strength, good biocompatibility. These results also confirmed the good biocompatibility between CMC and the additives. The non-toxicity of the films suggest that the CMC-based films are potential food-packaging and drug delivery systems.