# Scale-Up Preparation and Characterization of Collagen/Sodium Alginate Blend Films

Authors: Zhe Wang; Shuaifeng Hu; Huaiyu Wang
Journal: Journal of Food Quality
 (2017)

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## Abstract

In an effort to produce scale-up of edible films, collagen-based films including different amounts of sodium alginate (CS) were prepared by casting method. Films were characterized based on their rheological, thermal, and mechanical properties, water vapor permeability (WVP), and oxygen permeability (OP). The microstructures were also evaluated by scanning electron microscopy (SEM), atomic force microscopy (AFM), and Fourier transform-infrared spectroscopy (FTIR). Furthermore, the addition of sodium alginate effectively improved the viscosity and thermal stability, significantly increased TS, and decreasedE and WVP (P<0.05), but with no obvious effect on OP (P>0.05). SEM and AFM showed homogeneous matrix, with no signs of phase separation in the blends. Overall, films (CS2) produced using collagen (g) : sodium alginate (g) = 10 : 2 showed suitable rheological property (apparent viscosity was 4.87 m Pa s−1) and better TS (26.49 Mpa), E (64.98%), WVP (1.79 × 10−10g·cm−1·s−1·Pa−1), and OP (3.77 × 10−5cm3·m−2·d−1·Pa−1).


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## Body

## 1. Introduction

Food packaging is concerned with the preservation and protection of all types of foods, particularly from oxidative and microbial spoilage, and also extending their shelf-life characteristics. Increased use of synthetic packaging films has led to serious ecological problems due to their total nonbiodegradability [1, 2]. Thereby, the use of proper packaging materials and methods to minimize food losses and provide safe and wholesome food products had always been the main interest [3–7].Indeed, more and more attention has been paid to develop edible films in order to improve food safety and shelf-life [8–10]. Edible films need to possess the appropriate mechanical properties and barrier properties from initial product packing to final consumer usage [11, 12]. Meanwhile, the materials obtained from renewable natural sources that were used to prepare edible films mainly include proteins, lipids, polysaccharides, and their possible combinations [13, 14].Among them, collagen is one of the renewable natural polymers, which could be widely used as an important industrial raw material [15]. It gained more significance, which offers real potential for applications in the food industry due to its physicochemical properties, short time biodegradability, and nontoxicity. Several authors have developed films or coatings based on collagen to preserve food in laboratory scale [15–20]. Nevertheless, since now, scale-up collagen-based films were not successfully produced, as would limit their application in food preservation field.Alginate is a salt of alginic acid, a polymer ofd-mannuronic acid andl-guluronic acid, and isolated from brown algae, used as an edible coating because of its unique colloidal properties and its ability to form strong gels or insoluble polymers upon reaction with multivalent metal cations, such as calcium [6, 21]. As a stabilizer and a thickener, sodium alginate (SA), the main used form, is applied in various food products including drinks like chocolate milk and deserts like ice cream, jelly, sauces, and soups [22–25]. Particularly, edible films obtained from sodium alginates have obtained good mechanical characteristics and decreased oxygen transfer [26, 27].Therefore, SA was added to collagen, in order to obtain a suitable rheological behavior for the collagen-based solution, paving the way to a large scale-up preparation for collagen-based films. More importantly, hydrogen and/or electrostatic interactions between carboxylate groups of SA and hydroxyl groups of collagen can occur, forming a more dense and compact matrix.The objective of this paper was to prepare and evaluate the properties of different blending ratios of collagen-sodium alginate films in pilot scale. The films were characterized in terms of their rheological behavior, thermal stability, and mechanical properties, as well as their oxygen permeability and water vapor barrier property. Furthermore, their microstructure would be investigated by scanning electron microscopy, Fourier transform-infrared spectroscopy, and atomic force microscopy, respectively.


## 2. Materials and Methods

### 2.1. Materials

Fish skin collagen (MW: 2000–3000) was obtained from Shanghai Yuanye Bio-Technology Co., Ltd. Sodium alginate, glycerol, and glutaraldehyde were purchased from Sinopharm Chemical Reagent Co., Ltd. All of them were of analytical grade. Indeed, glutaraldehyde was added as a cross-linking agent, whereas glycerol was added as a plasticizer. The ultrapure water was used as a solvent for the solution preparation.


### 2.2. Film Preparation

Collagen/sodium alginate blend films were prepared using casting machine. Firstly, a collagen solution (10%, w/v) was prepared by dispersing collagen powder in distilled water at 65°C for 30 min under magnetic stirring. Subsequently, different weight of sodium alginate was added to collagen solution with mechanical stirring for 30 min at 60°C, to obtain the mixed solutions with different ratio of collagen to sodium alginate (10 : 0, 10 : 1, 10 : 2, 10 : 3, and 0 : 2). Then glycerol (20%, based on the content of dried matter) was added as plasticizer, and glutaraldehyde (0.5%, v/v) was added as cross-linking agent. The details could be shown in Table 1.Table 1
Rheological properties of film-forming solutions: index of consistency (K) and flow-behavior (n) calculated by the Ostwald de Waele model. Apparent viscosity values at 10 m S−1 shear rate (D).
Sample
Mass ratios of collagen to SA
Parameters of Ostwald de Waele model
Apparent viscosity(m Pa s−1)
K
N
R
2
D
=
10 m S−1
Collagen
10 : 0
0.107
0.888
0.947
0.005
CS1
10 : 1
0.354
0.844
0.999
0.33
CS2
10 : 2
1.083
0.582
0.988
4.87
CS3
10 : 3
1.874
0.384
0.964
18.65
SA
0 : 2
0.995
0.538
0.984
2.95The film-forming solutions were placed at vacuum condition for 60 min to remove bubbles at room temperature. Finally, the solution was cast onto the steel belt casting machine (TY7000, Zhaoqing Xintai Electromechanical Technology Co., Ltd.) at 60°C for 120 min. As could be presented in Figure1, the dried films were conditioned for 24 h at 50 ± 5% relative humidity (RH) and 25 ± 1°C before determination.Figure 1
Casting machine used for films produced: (a) film-forming solution, (b) film drying, and (c) finished film.
(a)
(b)
(c)


### 2.3. Rheological Analysis

Flow properties of film-forming solutions are useful for identifying the most appropriate coating system and optimizing operating conditions [23, 28]. The rheological properties of collagen, SA, and their blended film-forming solutions were characterized by a rheometer (Anton Paar, MCR302, Austria) equipped with a parallel-plate geometry (diameter = 25 mm and a gap = 0.2 mm). All measurements were conducted at 25°C. Before any measurement, samples rested for 2 min, to allow the stresses induced during sample loading to relax.Rheological characterization was carried out using stationary shear flow and oscillatory tests. The steady shear measurements (flow curves) were performed in an extended shear rate range (1 to 200 s−1).According to the rheological analysis model [29], the flow (n) and consistency indices (K) were determined after adjusting the empirical data according to the Ostwald de Waele rheological model (a.k.a. the Power-Law Model):(1)τ=KDnin which τ is the shear stress (Pa), K is the consistency index (Pa sn), D is shear rate, and n is the flow-behavior index.


### 2.4. Films Characterization

#### 2.4.1. Thickness

Thickness of the collagen-sodium alginate films was determined to the nearest 0.01 mm using a micrometer (Mitutoyo Manufacturing, Tokyo, Japan). Measurements were made in at least ten random locations on each film.


#### 2.4.2. Mechanical Properties

Mechanical properties of the films, such as tensile strength (TS, MPa) and elongation at break (E, %), were determined at 25 ± 1°C using a Testometric Machine (PARAM XLW (B) Auto Tensile Tester, Jinan, China) according to the ASTM standard method (D882-01). Films were cut into rectangular strips that were 120 mm long and 15 mm wide. Stripes were equilibrated at 50% RH and 25 ± 1°C for 48 hrs in a desiccator using saturated salt solutions of MgCl2 or Mg(NO3)2. The films were fixed with an initial grip separation of 80 mm and stretched at a cross-speed of 50 mm/min. A microcomputer was used to record the strength and elongation data. Tensile strength was calculated as the maximum load on the film before failure divided by the cross-sectional area of the specimen. Elongation was defined as the percent change in specimen length compared to the initial length between the grips. For each film, at least five replicate measurements were performed [30].


#### 2.4.3. Water Vapor Permeability (WVP)

Water vapor permeability tester (PERME TSY-TIL, Labthink Instruments Co., Ltd., Jinan, China) was used to determine the water vapor permeability (WVP, ×10−10 g·cm−1·s−1·Pa−1) of the films according to the ASTM standard method (D1653). Water vapor transmission rates were determined at 25 ± 1°C and 50% RH using saturated salt solutions of MgCl2 or Mg(NO3)2. The specimen was fixed to form a sealed environment with 2/3 distilled water in the vessel. The water vapor transmission rate and transmission coefficient were determined by measuring the decreasing weight of distilled water over time. For each film, at least five replicates were performed [30].


#### 2.4.4. Oxygen Permeability (OP)

A gas permeability tester (GDP-C) (Brugger Feinmechanik GmbH, Germany) was utilized to test the oxygen permeability (OP, ×10−5cm3·m−2·d−1·Pa−1) of the films according to the ASTM standard method (D3985-95). Oxygen transmission rates were determined at 25 ± 1°C and 50% RH using saturated salt solutions of MgCl2 or Mg(NO3)2. The sample was mounted in a gas transmission cell to form a sealed semibarrier between chambers. One chamber contained O2 at a specific high pressure and the other lower pressure chamber received the permeating O2. The lower pressure chamber was initially evacuated and the transmission of the gas through the test specimen was indicated by an increase in pressure [30]. The O2 stream was set to 100 mL/min and the oxygen transmission rate (OTR) was recorded. The OP was calculated by multiplying the OTR by the film thickness (FT) and then dividing by the partial pressure difference of oxygen (ΔP) as follows:(2)OP=OTR×FTΔP.For each film, at least five replicates were performed.


#### 2.4.5. Thermal Properties

The thermal properties of samples were characterized as reported previously using differential scanning calorimeter (DSC-Q20, TA Instruments, USA). The samples (3-4 mg) were heated with at 10°C/min in the swept temperature from 10 to 300°C [19].


### 2.5. Microstructure Characterization

#### 2.5.1. Fourier Transform-Infrared Spectroscopy (FTIR)

FT-IR was recorded on a Nicolet 360 spectrometer (Thermo Nicolet Corporation, American) from 400 to 4000 cm−1 with the KBr method.


#### 2.5.2. Scanning Electron Microscopy (SEM)

The SEM images were acquired on a ZEISS SUPRA 55 (Carl Zeiss, Germany) field-emission scanning electron microscopy. For cross section analysis, samples were cryofractured after immersion in liquid nitrogen. The cryofractured section and film surface were analyzed without further preparation. The images were taken at random positions of the films.


#### 2.5.3. Atomic Force Microscopy (AFM)

The surface morphology of collagen-SA films was studied using a Multimode atomic force microscope (Bruker Multimode 8, Bruker, Germany) equipped with a Nanoscope V controller. The equipment was operated in noncontacting mode using etched silicon tip (nominal radius 8 nm and cantilever length of 230μm) with a resonance frequency of about 267 kHz. AFM images were acquired in air at room temperature.


### 2.6. Statistical Analysis

All samples were analyzed in triplicate and one-way analysis of variance (ANOVA) was applied on the data followed by Duncan to distinguish the treatments atP<0.05. The statistical analyses were performed using SPSS version 17.0 (SPSS Inc., Chicago, IL, USA).


## 2.1. Materials

Fish skin collagen (MW: 2000–3000) was obtained from Shanghai Yuanye Bio-Technology Co., Ltd. Sodium alginate, glycerol, and glutaraldehyde were purchased from Sinopharm Chemical Reagent Co., Ltd. All of them were of analytical grade. Indeed, glutaraldehyde was added as a cross-linking agent, whereas glycerol was added as a plasticizer. The ultrapure water was used as a solvent for the solution preparation.


## 2.2. Film Preparation

Collagen/sodium alginate blend films were prepared using casting machine. Firstly, a collagen solution (10%, w/v) was prepared by dispersing collagen powder in distilled water at 65°C for 30 min under magnetic stirring. Subsequently, different weight of sodium alginate was added to collagen solution with mechanical stirring for 30 min at 60°C, to obtain the mixed solutions with different ratio of collagen to sodium alginate (10 : 0, 10 : 1, 10 : 2, 10 : 3, and 0 : 2). Then glycerol (20%, based on the content of dried matter) was added as plasticizer, and glutaraldehyde (0.5%, v/v) was added as cross-linking agent. The details could be shown in Table 1.Table 1
Rheological properties of film-forming solutions: index of consistency (K) and flow-behavior (n) calculated by the Ostwald de Waele model. Apparent viscosity values at 10 m S−1 shear rate (D).
Sample
Mass ratios of collagen to SA
Parameters of Ostwald de Waele model
Apparent viscosity(m Pa s−1)
K
N
R
2
D
=
10 m S−1
Collagen
10 : 0
0.107
0.888
0.947
0.005
CS1
10 : 1
0.354
0.844
0.999
0.33
CS2
10 : 2
1.083
0.582
0.988
4.87
CS3
10 : 3
1.874
0.384
0.964
18.65
SA
0 : 2
0.995
0.538
0.984
2.95The film-forming solutions were placed at vacuum condition for 60 min to remove bubbles at room temperature. Finally, the solution was cast onto the steel belt casting machine (TY7000, Zhaoqing Xintai Electromechanical Technology Co., Ltd.) at 60°C for 120 min. As could be presented in Figure1, the dried films were conditioned for 24 h at 50 ± 5% relative humidity (RH) and 25 ± 1°C before determination.Figure 1
Casting machine used for films produced: (a) film-forming solution, (b) film drying, and (c) finished film.
(a)
(b)
(c)


## 2.3. Rheological Analysis

Flow properties of film-forming solutions are useful for identifying the most appropriate coating system and optimizing operating conditions [23, 28]. The rheological properties of collagen, SA, and their blended film-forming solutions were characterized by a rheometer (Anton Paar, MCR302, Austria) equipped with a parallel-plate geometry (diameter = 25 mm and a gap = 0.2 mm). All measurements were conducted at 25°C. Before any measurement, samples rested for 2 min, to allow the stresses induced during sample loading to relax.Rheological characterization was carried out using stationary shear flow and oscillatory tests. The steady shear measurements (flow curves) were performed in an extended shear rate range (1 to 200 s−1).According to the rheological analysis model [29], the flow (n) and consistency indices (K) were determined after adjusting the empirical data according to the Ostwald de Waele rheological model (a.k.a. the Power-Law Model):(1)τ=KDnin which τ is the shear stress (Pa), K is the consistency index (Pa sn), D is shear rate, and n is the flow-behavior index.


## 2.4. Films Characterization

### 2.4.1. Thickness

Thickness of the collagen-sodium alginate films was determined to the nearest 0.01 mm using a micrometer (Mitutoyo Manufacturing, Tokyo, Japan). Measurements were made in at least ten random locations on each film.


### 2.4.2. Mechanical Properties

Mechanical properties of the films, such as tensile strength (TS, MPa) and elongation at break (E, %), were determined at 25 ± 1°C using a Testometric Machine (PARAM XLW (B) Auto Tensile Tester, Jinan, China) according to the ASTM standard method (D882-01). Films were cut into rectangular strips that were 120 mm long and 15 mm wide. Stripes were equilibrated at 50% RH and 25 ± 1°C for 48 hrs in a desiccator using saturated salt solutions of MgCl2 or Mg(NO3)2. The films were fixed with an initial grip separation of 80 mm and stretched at a cross-speed of 50 mm/min. A microcomputer was used to record the strength and elongation data. Tensile strength was calculated as the maximum load on the film before failure divided by the cross-sectional area of the specimen. Elongation was defined as the percent change in specimen length compared to the initial length between the grips. For each film, at least five replicate measurements were performed [30].


### 2.4.3. Water Vapor Permeability (WVP)

Water vapor permeability tester (PERME TSY-TIL, Labthink Instruments Co., Ltd., Jinan, China) was used to determine the water vapor permeability (WVP, ×10−10 g·cm−1·s−1·Pa−1) of the films according to the ASTM standard method (D1653). Water vapor transmission rates were determined at 25 ± 1°C and 50% RH using saturated salt solutions of MgCl2 or Mg(NO3)2. The specimen was fixed to form a sealed environment with 2/3 distilled water in the vessel. The water vapor transmission rate and transmission coefficient were determined by measuring the decreasing weight of distilled water over time. For each film, at least five replicates were performed [30].


### 2.4.4. Oxygen Permeability (OP)

A gas permeability tester (GDP-C) (Brugger Feinmechanik GmbH, Germany) was utilized to test the oxygen permeability (OP, ×10−5cm3·m−2·d−1·Pa−1) of the films according to the ASTM standard method (D3985-95). Oxygen transmission rates were determined at 25 ± 1°C and 50% RH using saturated salt solutions of MgCl2 or Mg(NO3)2. The sample was mounted in a gas transmission cell to form a sealed semibarrier between chambers. One chamber contained O2 at a specific high pressure and the other lower pressure chamber received the permeating O2. The lower pressure chamber was initially evacuated and the transmission of the gas through the test specimen was indicated by an increase in pressure [30]. The O2 stream was set to 100 mL/min and the oxygen transmission rate (OTR) was recorded. The OP was calculated by multiplying the OTR by the film thickness (FT) and then dividing by the partial pressure difference of oxygen (ΔP) as follows:(2)OP=OTR×FTΔP.For each film, at least five replicates were performed.


### 2.4.5. Thermal Properties

The thermal properties of samples were characterized as reported previously using differential scanning calorimeter (DSC-Q20, TA Instruments, USA). The samples (3-4 mg) were heated with at 10°C/min in the swept temperature from 10 to 300°C [19].


## 2.4.1. Thickness

Thickness of the collagen-sodium alginate films was determined to the nearest 0.01 mm using a micrometer (Mitutoyo Manufacturing, Tokyo, Japan). Measurements were made in at least ten random locations on each film.


## 2.4.2. Mechanical Properties

Mechanical properties of the films, such as tensile strength (TS, MPa) and elongation at break (E, %), were determined at 25 ± 1°C using a Testometric Machine (PARAM XLW (B) Auto Tensile Tester, Jinan, China) according to the ASTM standard method (D882-01). Films were cut into rectangular strips that were 120 mm long and 15 mm wide. Stripes were equilibrated at 50% RH and 25 ± 1°C for 48 hrs in a desiccator using saturated salt solutions of MgCl2 or Mg(NO3)2. The films were fixed with an initial grip separation of 80 mm and stretched at a cross-speed of 50 mm/min. A microcomputer was used to record the strength and elongation data. Tensile strength was calculated as the maximum load on the film before failure divided by the cross-sectional area of the specimen. Elongation was defined as the percent change in specimen length compared to the initial length between the grips. For each film, at least five replicate measurements were performed [30].


## 2.4.3. Water Vapor Permeability (WVP)

Water vapor permeability tester (PERME TSY-TIL, Labthink Instruments Co., Ltd., Jinan, China) was used to determine the water vapor permeability (WVP, ×10−10 g·cm−1·s−1·Pa−1) of the films according to the ASTM standard method (D1653). Water vapor transmission rates were determined at 25 ± 1°C and 50% RH using saturated salt solutions of MgCl2 or Mg(NO3)2. The specimen was fixed to form a sealed environment with 2/3 distilled water in the vessel. The water vapor transmission rate and transmission coefficient were determined by measuring the decreasing weight of distilled water over time. For each film, at least five replicates were performed [30].


## 2.4.4. Oxygen Permeability (OP)

A gas permeability tester (GDP-C) (Brugger Feinmechanik GmbH, Germany) was utilized to test the oxygen permeability (OP, ×10−5cm3·m−2·d−1·Pa−1) of the films according to the ASTM standard method (D3985-95). Oxygen transmission rates were determined at 25 ± 1°C and 50% RH using saturated salt solutions of MgCl2 or Mg(NO3)2. The sample was mounted in a gas transmission cell to form a sealed semibarrier between chambers. One chamber contained O2 at a specific high pressure and the other lower pressure chamber received the permeating O2. The lower pressure chamber was initially evacuated and the transmission of the gas through the test specimen was indicated by an increase in pressure [30]. The O2 stream was set to 100 mL/min and the oxygen transmission rate (OTR) was recorded. The OP was calculated by multiplying the OTR by the film thickness (FT) and then dividing by the partial pressure difference of oxygen (ΔP) as follows:(2)OP=OTR×FTΔP.For each film, at least five replicates were performed.


## 2.4.5. Thermal Properties

The thermal properties of samples were characterized as reported previously using differential scanning calorimeter (DSC-Q20, TA Instruments, USA). The samples (3-4 mg) were heated with at 10°C/min in the swept temperature from 10 to 300°C [19].


## 2.5. Microstructure Characterization

### 2.5.1. Fourier Transform-Infrared Spectroscopy (FTIR)

FT-IR was recorded on a Nicolet 360 spectrometer (Thermo Nicolet Corporation, American) from 400 to 4000 cm−1 with the KBr method.


### 2.5.2. Scanning Electron Microscopy (SEM)

The SEM images were acquired on a ZEISS SUPRA 55 (Carl Zeiss, Germany) field-emission scanning electron microscopy. For cross section analysis, samples were cryofractured after immersion in liquid nitrogen. The cryofractured section and film surface were analyzed without further preparation. The images were taken at random positions of the films.


### 2.5.3. Atomic Force Microscopy (AFM)

The surface morphology of collagen-SA films was studied using a Multimode atomic force microscope (Bruker Multimode 8, Bruker, Germany) equipped with a Nanoscope V controller. The equipment was operated in noncontacting mode using etched silicon tip (nominal radius 8 nm and cantilever length of 230μm) with a resonance frequency of about 267 kHz. AFM images were acquired in air at room temperature.


## 2.5.1. Fourier Transform-Infrared Spectroscopy (FTIR)

FT-IR was recorded on a Nicolet 360 spectrometer (Thermo Nicolet Corporation, American) from 400 to 4000 cm−1 with the KBr method.


## 2.5.2. Scanning Electron Microscopy (SEM)

The SEM images were acquired on a ZEISS SUPRA 55 (Carl Zeiss, Germany) field-emission scanning electron microscopy. For cross section analysis, samples were cryofractured after immersion in liquid nitrogen. The cryofractured section and film surface were analyzed without further preparation. The images were taken at random positions of the films.


## 2.5.3. Atomic Force Microscopy (AFM)

The surface morphology of collagen-SA films was studied using a Multimode atomic force microscope (Bruker Multimode 8, Bruker, Germany) equipped with a Nanoscope V controller. The equipment was operated in noncontacting mode using etched silicon tip (nominal radius 8 nm and cantilever length of 230μm) with a resonance frequency of about 267 kHz. AFM images were acquired in air at room temperature.


## 2.6. Statistical Analysis

All samples were analyzed in triplicate and one-way analysis of variance (ANOVA) was applied on the data followed by Duncan to distinguish the treatments atP<0.05. The statistical analyses were performed using SPSS version 17.0 (SPSS Inc., Chicago, IL, USA).


## 3. Results and Discussion

### 3.1. Rheological Analysis

The flow-behavior of film-forming solutions is an important property because it could affect the spread-ability, thickness, uniformity of the coating layer, the mechanical properties, and the application and processing design [28, 31]. Additionally, flow property modeling of film-forming solutions is useful technologically to identify the most appropriate coating system design and to optimize operating conditions [32].The variation of viscosity and shear stress of collagen-based film-forming solution could be shown in Figure2. Pure collagen solution showed Newtonian behavior between 0.1 and 200 s−1 shear rate range, whereas collagen/sodium alginate solution exhibited a shear-thinning behavior, confirming that the addition of SA enhanced the elastic behavior (w/v). As mentioned before, shear-thinning behavior is adequate for the production of films by tape casting.Figure 2
Characterization and rheological property evaluation for the films, (a) film-forming solution macrograph, (b) sheer stress versus shear rate, and (c) viscosity versus shear rate.
(a)
(b)
(c)As was presented in Table1, flow-behavior index (n) increased with increasing SA concentration; accordingly K values primarily increased and then decreased. As expected, higher SA concentration led to a higher apparent viscosity. It suggests that SA was the prime factor affecting apparent viscosity. This may be attributed to the intramolecular interaction of SA which was destroyed; then new hydrogen bonds were formed between collagen and SA. Regardless of this, some researchers have demonstrated that high viscosity makes it difficult to disperse the ingredients and eliminate visible air bubbles during the preparation of liquid films [23, 32, 33], leading to some discontinuities in the final films.


### 3.2. Films Characterization

#### 3.2.1. Thickness

Indeed, all films were yellowish and flexible and could be easily handled. The surfaces of the films looked very smooth, without visible cracks or pores. Greater details regarding film appearances are described in Table2.Table 2
Collagen-sodium alginate films properties: tensile strength (TS), elongation at break (E), water vapor permeability (WVP), and oxygen permeability (OP).
Films code
Thickness
TS
E
WVP
OP
(μm)
(Mpa)
(%)
×10−10g⋅cm−1⋅s−1⋅Pa−1
×10−5cm3⋅m−2⋅d−1⋅Pa−1
Collagen
30
±
2
a
17.46
±
1.13
a
78.49
±
3.59
a
3.43
±
0.38
a
3.87
±
0.28
a
CS1
31
±
1
a
20.38
±
2.24
b
70.15
±
3.14
b
2.2
±
0.28
b
3.56
±
0.57
a
b
CS2
32
±
2
a
26.49
±
2.67
c
64.98
±
2.69
c
1.7
±
0.26
b
c
3.77
±
0.37
a
CS3
33
±
2
a
34.17
±
2.48
d
58.11
±
2.78
d
2.92
±
0.22
a
b
3.85
±
0.42
a
SA
11
±
1
b
40.48
±
1.49
e
50.28
±
1.38
e
2.74
±
0.35
a
b
3.16
±
0.49
b
Values are expressed as mean ± standard deviation. Different letters in the same column indicate significant differences (P<0.05).Thickness of collagen films incorporated with SA at various concentrations is shown in Table2. Thickness of films incorporated with SA (1–3%, w/v) increased in comparison with the control. It ranged from 0.030 to 0.033 mm. However, no significant difference in thickness was observed between films incorporated with SA (P>0.05). Some authors also reported that the incorporation of SA had no effect on thickness of starch and pectin films [34, 35].


#### 3.2.2. Mechanical Properties

Mechanical properties of biopolymer films are often presented in terms of tensile strength (TS) and elongation at break (E). TS accounts for film’s mechanical resistance due to cohesion forces between chains, while E measures its plasticity, which is capacity of a film to extend before breaking [36–38].All test films showed significant (P<0.05) differences in TS and E (Table 2). Single collagen and SA films exhibited TS and E value of 17.46 and 40.48 MPa and 78.49% and 50.28%, respectively. In general, polysaccharide-based films had better TS compared with protein-based films while protein-based films possessed greater E than polysaccharide-based films [15, 17], agreeing well with the results of this study.When the ratio of collagen to SA varied from 10 : 0 (pure collagen film) to 10 : 3 (CS3), TS was enhanced from 17.46 to 34.17 MPa, nearly more than double; however,E decreased from 70.15% to 58.11%. As suggested by [39], usually films with higher TS values show lower E values, due to the structural nature of those attributes. This result was probably induced by a certain degree of cross-linking between the proteins of collagen and SA. As observed in the FTIR analysis, the hydrophobic interactions and hydrogen present bridges in proteins could be demonstrated (Section 3.3.1). It has been proved that lots of hydroxyl groups exist to allow formation of hydrogen bonds between side-by-side polymer chains, resulting in high TS of films made of protein or sodium alginate [6, 21, 40]. Moreover, it has been reported that the mechanical properties of films are greatly associated with distribution and of intra- and intermolecular interactions, depending on the arrangements, and orientation of polymer chains in the network [17]. According to the SEM analysis (Section 3.3.2), a uniformity appearance for the CS films is obtained, leading to a better mechanical property. Thus, SA could effectively improve the mechanical property of collagen films.


#### 3.2.3. Water Vapor Permeability (WVP)

Water vapor permeability (WVP) for the collagen, SA, and their blend films at relative humidity of 50% is shown in Table2. Obtained values ranged from 1.79 to 3.43 × 10−10g·cm−1·s−1·Pa−1. As it is reported that collagen is a hydrophilic polymer which has hydroxyl groups, thus, the water vapor could easily permeate through the film. In this study, films with lower content of SA showed significantly lower values comparing to the pure collagen films. This was in accordance with the fact that WVP values for blend films produced from protein and polysaccharide mixtures were lower in comparison to the WVP values of those films formed from protein alone [41].It is perhaps because more hydroxyl groups of SA could form more hydrogen bonds with water; thus water was trapped firmly in the polymer network. Similar results have been reported in the literature for feather keratin and SA blend films [21]. Further, it was discovered that SA could decrease the WVP probably through creating a tortuous pass for crossing water vapor through film, increasing the crystallinity of the biopolymer, or decreasing free hydrophilic groups (OH, NH) in biopolymer matrix [41, 42].It was also worth noting that further increase in SA (CS3) caused an increase in the WVP of CS films. This may attribute to the fact that both collagen and SA owing to their hydrophilic nature attract water molecules and create mobile regions with larger interchain distances. Additionally, these hydrophilic SA compete with water at the active sites of the polymer matrix causing water clustering which also forms microcavities in the network structure [43, 44]. The absorbed water molecules modify the film matrix, leading to a less dense structure where chain terminals are relatively more mobile, thus increasing water vapor transmission rate [45]. Therefore, the appropriate SA proportion could lead to a better barrier property for the blend films.


#### 3.2.4. Oxygen Permeability (OP)

Oxygen is responsible for many degradation processes in foods such as lipid oxidation, microorganism growth, enzymatic browning, and vitamin loss [46]. Consequently, oxygen permeability (OP) is a crucial property in food packaging and it could be used as an index to evaluate the ability to prohibit oxidation reaction [47].Although the collagen films were hydrophilic and exhibited poor water vapor barrier properties, collagen-based films were hypothesized to be excellent barriers against oxygen, as examined in Table2. Nevertheless, no significant differences (P>0.05) were obtained between all the estimated values and no specific trends could be observed. The OP value of the pure collagen and SA film was 3.87 and 3.16 × 10−5 cm3·m−2·d−1·Pa−1, indicating that the both films were good oxygen barrier. Similar results were obtained by Bonilla et al. [46]. It was also noted that films made from proteins and carbohydrates are excellent barriers to oxygen, because of their tightly packed, ordered hydrogen bonded network structure [48].From this result, it appears that the addition of SA slightly changed OP of CS films, but with no obvious effect (P>0.05). When the ratio of collagen to SA varied from 10 : 1 (CS1) to 10 : 3 (CS3), OP varied from 3.56 to 3.85 × 10−5cm3·m−2·d−1·Pa−1. Among them, the OP for CS1 was found to be lowest, but further increase in SA concentration led to an increase in OP of CS films. Generally SA possess a film-forming ability, which leads to modest or very good oxygen barrier properties depending on the structure [11]. However, the result was not as good as expected in this study; SA added in the collagen could not decrease the OP values for the blend films.


#### 3.2.5. Thermal Properties

Thermal properties of the samples were estimated using differential scanning calorimeter (DSC). It was known that DSC was a useful and rapid method to measure the interrelated thermodynamic profiles, and it was usually used to determine the temperature and enthalpy during endothermic or exothermic processes for an application in polymer materials [8]. The thermograms of DSC analysis and the related peak temperatures were given and illustrated in Figure 3.Figure 3
DSC thermograms of collagen, CS1, CS2, CS3, and SA films.It was reported that the first endothermic events were glass transition, followed by an endotherm associated with the melting of the ordered structures [20, 49]. As observed in Figure 3, the Tg value of the pure collagen film (55.63°C) is inferior to CS1 (85.31°C), CS2 (103.71°C), and CS3 (80.71°C). It suggested that the thermal stability of the CS films has been enhanced, owing to the addition of SA. That may be explained by the increase of interactions provided by SA, stabilizing the collagen structure against unfolding and requiring a higher temperature to degrade collagen [18, 20]. Nevertheless, the Tg value for the CS films initially increased and then decreased, with the SA concentration increase. As reported, Tg value of the collagen film is attributed to the hydrogen bonded networks and mediated by water molecules [50].Oppositely, as observed, compared to the collagen film (170.59°C), CS1 (153.13°C) and CS3 (158.29°C) presented a decrease inTc value associated with thermal stability. The lower Tc was related to the reduction in some weak intermolecular forces such as hydrogen bonds between water and the matrix. It could be explained that the hydrophobic feature was imparted into collagen and facilitated evaporation of water with SA added. Totally, the addition of SA effectively improved the thermal property for the CS blend films.


### 3.3. Microstructure Characterization

#### 3.3.1. FTIR

FTIR spectra of collagen, SA, and their blend films at selected concentrations were depicted in Figure4. A robust classification of FTIR spectra collagen could be obtained by using a combination of four spectral intervals [ν(C=O) absorption of amide I (1,700–1,600 cm−1), δ(CH2), and δ(CH3) absorptions (1,480–1,350 cm−1), ν(C–N), and δ(N–H) absorptions of amide III (1,300–1,180 cm−1), and (C–O) and (C–O–C) absorptions of carbohydrate moieties (1,100–1,005 cm−1)] [51]. Both collagen and CS3 spectra showed similar IR absorbance patterns.Figure 4
FTIR spectra of the different films (collagen, SA, and CS3) studied in all the range absorption.For CS3, the OH stretching and asymmetric COO stretching shift to a lower wavenumber (from 3435 to 3410 cm−1). Generally, the shift to the lower wavenumber indicated the existence of hydrogen bonds in collagen [50]. It also indicated that no other bonds except hydrogen bonds were formatted between collagen and SA.


#### 3.3.2. SEM

Scanning electron microscopy (SEM) observations were carried out to get a better insight into the homogeneity and the microstructure of the blend films (Figure5). SEM images of the surface of the collagen, SA, CS1, CS2, and CS3 films, and cross section of the CS2 films were presented. It was observed that collagen fiber was arranged in the film matrix, without pores and with excellent structural integrity (Figure 5(a)). SA exhibited rough surfaces with nonporous and heterogeneous morphologies due to some nonfully destructured alginate particles (Figure 5(b)). While more SA was added to the blend, the surface of CS2 and CS3 exhibited rougher and fluctuant matrix morphology (Figures 5(d) and 5(e)). Nevertheless, SEM images revealed that CS films had a smoother surface compared to pure SA films which became rougher upon drying. The cross section of CS2 had a compact and homogeneous structure and no distinct phase separation was observed (Figure 5(f)), indicating the integrity of the blend structure.Figure 5
SEM micrographs of the surface of the films based on (a) the pure collagen film, (b) SA film, (c) CS1, (d) CS2, and (e) CS3. SEM micrographs of the cross section appearance of the films based on (f) CS2.
(a)
(b)
(c)
(d)
(e)
(f)The above results lead to the following suggestions about the formation mechanism of the CS blend films. When SA were added to collagen films, the low molecular weight hydrophilic SA molecular movement was depressed by the formed strong cross-linking network structure, resulting in improved mechanical stability.


#### 3.3.3. AFM

AFM images were obtained in order to provide the information of surface morphology and roughness for the sample film. Figure6 shows surface morphologies and the corresponding results of roughness parameters (Rq, root mean square of roughness, and Ra, mean value of roughness) of the films. The surface morphology of SA film (Figure 6(a)) showed that bright protuberant parts were obviously observed due to SA molecule self-aggregation. Some significant differences between SA and CS films are exhibited. Obviously, the presence of collagen led to a marked decrease in the roughness of the films, as indicated by lower Ra and Rq values. The results were accordant with the SEM microstructure observations.Figure 6
AFM images of the films: (a) SA film, (b) CS1, (c) CS2, and (d) CS3.
(a)
(b)
(c)
(d)


## 3.1. Rheological Analysis

The flow-behavior of film-forming solutions is an important property because it could affect the spread-ability, thickness, uniformity of the coating layer, the mechanical properties, and the application and processing design [28, 31]. Additionally, flow property modeling of film-forming solutions is useful technologically to identify the most appropriate coating system design and to optimize operating conditions [32].The variation of viscosity and shear stress of collagen-based film-forming solution could be shown in Figure2. Pure collagen solution showed Newtonian behavior between 0.1 and 200 s−1 shear rate range, whereas collagen/sodium alginate solution exhibited a shear-thinning behavior, confirming that the addition of SA enhanced the elastic behavior (w/v). As mentioned before, shear-thinning behavior is adequate for the production of films by tape casting.Figure 2
Characterization and rheological property evaluation for the films, (a) film-forming solution macrograph, (b) sheer stress versus shear rate, and (c) viscosity versus shear rate.
(a)
(b)
(c)As was presented in Table1, flow-behavior index (n) increased with increasing SA concentration; accordingly K values primarily increased and then decreased. As expected, higher SA concentration led to a higher apparent viscosity. It suggests that SA was the prime factor affecting apparent viscosity. This may be attributed to the intramolecular interaction of SA which was destroyed; then new hydrogen bonds were formed between collagen and SA. Regardless of this, some researchers have demonstrated that high viscosity makes it difficult to disperse the ingredients and eliminate visible air bubbles during the preparation of liquid films [23, 32, 33], leading to some discontinuities in the final films.


## 3.2. Films Characterization

### 3.2.1. Thickness

Indeed, all films were yellowish and flexible and could be easily handled. The surfaces of the films looked very smooth, without visible cracks or pores. Greater details regarding film appearances are described in Table2.Table 2
Collagen-sodium alginate films properties: tensile strength (TS), elongation at break (E), water vapor permeability (WVP), and oxygen permeability (OP).
Films code
Thickness
TS
E
WVP
OP
(μm)
(Mpa)
(%)
×10−10g⋅cm−1⋅s−1⋅Pa−1
×10−5cm3⋅m−2⋅d−1⋅Pa−1
Collagen
30
±
2
a
17.46
±
1.13
a
78.49
±
3.59
a
3.43
±
0.38
a
3.87
±
0.28
a
CS1
31
±
1
a
20.38
±
2.24
b
70.15
±
3.14
b
2.2
±
0.28
b
3.56
±
0.57
a
b
CS2
32
±
2
a
26.49
±
2.67
c
64.98
±
2.69
c
1.7
±
0.26
b
c
3.77
±
0.37
a
CS3
33
±
2
a
34.17
±
2.48
d
58.11
±
2.78
d
2.92
±
0.22
a
b
3.85
±
0.42
a
SA
11
±
1
b
40.48
±
1.49
e
50.28
±
1.38
e
2.74
±
0.35
a
b
3.16
±
0.49
b
Values are expressed as mean ± standard deviation. Different letters in the same column indicate significant differences (P<0.05).Thickness of collagen films incorporated with SA at various concentrations is shown in Table2. Thickness of films incorporated with SA (1–3%, w/v) increased in comparison with the control. It ranged from 0.030 to 0.033 mm. However, no significant difference in thickness was observed between films incorporated with SA (P>0.05). Some authors also reported that the incorporation of SA had no effect on thickness of starch and pectin films [34, 35].


### 3.2.2. Mechanical Properties

Mechanical properties of biopolymer films are often presented in terms of tensile strength (TS) and elongation at break (E). TS accounts for film’s mechanical resistance due to cohesion forces between chains, while E measures its plasticity, which is capacity of a film to extend before breaking [36–38].All test films showed significant (P<0.05) differences in TS and E (Table 2). Single collagen and SA films exhibited TS and E value of 17.46 and 40.48 MPa and 78.49% and 50.28%, respectively. In general, polysaccharide-based films had better TS compared with protein-based films while protein-based films possessed greater E than polysaccharide-based films [15, 17], agreeing well with the results of this study.When the ratio of collagen to SA varied from 10 : 0 (pure collagen film) to 10 : 3 (CS3), TS was enhanced from 17.46 to 34.17 MPa, nearly more than double; however,E decreased from 70.15% to 58.11%. As suggested by [39], usually films with higher TS values show lower E values, due to the structural nature of those attributes. This result was probably induced by a certain degree of cross-linking between the proteins of collagen and SA. As observed in the FTIR analysis, the hydrophobic interactions and hydrogen present bridges in proteins could be demonstrated (Section 3.3.1). It has been proved that lots of hydroxyl groups exist to allow formation of hydrogen bonds between side-by-side polymer chains, resulting in high TS of films made of protein or sodium alginate [6, 21, 40]. Moreover, it has been reported that the mechanical properties of films are greatly associated with distribution and of intra- and intermolecular interactions, depending on the arrangements, and orientation of polymer chains in the network [17]. According to the SEM analysis (Section 3.3.2), a uniformity appearance for the CS films is obtained, leading to a better mechanical property. Thus, SA could effectively improve the mechanical property of collagen films.


### 3.2.3. Water Vapor Permeability (WVP)

Water vapor permeability (WVP) for the collagen, SA, and their blend films at relative humidity of 50% is shown in Table2. Obtained values ranged from 1.79 to 3.43 × 10−10g·cm−1·s−1·Pa−1. As it is reported that collagen is a hydrophilic polymer which has hydroxyl groups, thus, the water vapor could easily permeate through the film. In this study, films with lower content of SA showed significantly lower values comparing to the pure collagen films. This was in accordance with the fact that WVP values for blend films produced from protein and polysaccharide mixtures were lower in comparison to the WVP values of those films formed from protein alone [41].It is perhaps because more hydroxyl groups of SA could form more hydrogen bonds with water; thus water was trapped firmly in the polymer network. Similar results have been reported in the literature for feather keratin and SA blend films [21]. Further, it was discovered that SA could decrease the WVP probably through creating a tortuous pass for crossing water vapor through film, increasing the crystallinity of the biopolymer, or decreasing free hydrophilic groups (OH, NH) in biopolymer matrix [41, 42].It was also worth noting that further increase in SA (CS3) caused an increase in the WVP of CS films. This may attribute to the fact that both collagen and SA owing to their hydrophilic nature attract water molecules and create mobile regions with larger interchain distances. Additionally, these hydrophilic SA compete with water at the active sites of the polymer matrix causing water clustering which also forms microcavities in the network structure [43, 44]. The absorbed water molecules modify the film matrix, leading to a less dense structure where chain terminals are relatively more mobile, thus increasing water vapor transmission rate [45]. Therefore, the appropriate SA proportion could lead to a better barrier property for the blend films.


### 3.2.4. Oxygen Permeability (OP)

Oxygen is responsible for many degradation processes in foods such as lipid oxidation, microorganism growth, enzymatic browning, and vitamin loss [46]. Consequently, oxygen permeability (OP) is a crucial property in food packaging and it could be used as an index to evaluate the ability to prohibit oxidation reaction [47].Although the collagen films were hydrophilic and exhibited poor water vapor barrier properties, collagen-based films were hypothesized to be excellent barriers against oxygen, as examined in Table2. Nevertheless, no significant differences (P>0.05) were obtained between all the estimated values and no specific trends could be observed. The OP value of the pure collagen and SA film was 3.87 and 3.16 × 10−5 cm3·m−2·d−1·Pa−1, indicating that the both films were good oxygen barrier. Similar results were obtained by Bonilla et al. [46]. It was also noted that films made from proteins and carbohydrates are excellent barriers to oxygen, because of their tightly packed, ordered hydrogen bonded network structure [48].From this result, it appears that the addition of SA slightly changed OP of CS films, but with no obvious effect (P>0.05). When the ratio of collagen to SA varied from 10 : 1 (CS1) to 10 : 3 (CS3), OP varied from 3.56 to 3.85 × 10−5cm3·m−2·d−1·Pa−1. Among them, the OP for CS1 was found to be lowest, but further increase in SA concentration led to an increase in OP of CS films. Generally SA possess a film-forming ability, which leads to modest or very good oxygen barrier properties depending on the structure [11]. However, the result was not as good as expected in this study; SA added in the collagen could not decrease the OP values for the blend films.


### 3.2.5. Thermal Properties

Thermal properties of the samples were estimated using differential scanning calorimeter (DSC). It was known that DSC was a useful and rapid method to measure the interrelated thermodynamic profiles, and it was usually used to determine the temperature and enthalpy during endothermic or exothermic processes for an application in polymer materials [8]. The thermograms of DSC analysis and the related peak temperatures were given and illustrated in Figure 3.Figure 3
DSC thermograms of collagen, CS1, CS2, CS3, and SA films.It was reported that the first endothermic events were glass transition, followed by an endotherm associated with the melting of the ordered structures [20, 49]. As observed in Figure 3, the Tg value of the pure collagen film (55.63°C) is inferior to CS1 (85.31°C), CS2 (103.71°C), and CS3 (80.71°C). It suggested that the thermal stability of the CS films has been enhanced, owing to the addition of SA. That may be explained by the increase of interactions provided by SA, stabilizing the collagen structure against unfolding and requiring a higher temperature to degrade collagen [18, 20]. Nevertheless, the Tg value for the CS films initially increased and then decreased, with the SA concentration increase. As reported, Tg value of the collagen film is attributed to the hydrogen bonded networks and mediated by water molecules [50].Oppositely, as observed, compared to the collagen film (170.59°C), CS1 (153.13°C) and CS3 (158.29°C) presented a decrease inTc value associated with thermal stability. The lower Tc was related to the reduction in some weak intermolecular forces such as hydrogen bonds between water and the matrix. It could be explained that the hydrophobic feature was imparted into collagen and facilitated evaporation of water with SA added. Totally, the addition of SA effectively improved the thermal property for the CS blend films.


## 3.2.1. Thickness

Indeed, all films were yellowish and flexible and could be easily handled. The surfaces of the films looked very smooth, without visible cracks or pores. Greater details regarding film appearances are described in Table2.Table 2
Collagen-sodium alginate films properties: tensile strength (TS), elongation at break (E), water vapor permeability (WVP), and oxygen permeability (OP).
Films code
Thickness
TS
E
WVP
OP
(μm)
(Mpa)
(%)
×10−10g⋅cm−1⋅s−1⋅Pa−1
×10−5cm3⋅m−2⋅d−1⋅Pa−1
Collagen
30
±
2
a
17.46
±
1.13
a
78.49
±
3.59
a
3.43
±
0.38
a
3.87
±
0.28
a
CS1
31
±
1
a
20.38
±
2.24
b
70.15
±
3.14
b
2.2
±
0.28
b
3.56
±
0.57
a
b
CS2
32
±
2
a
26.49
±
2.67
c
64.98
±
2.69
c
1.7
±
0.26
b
c
3.77
±
0.37
a
CS3
33
±
2
a
34.17
±
2.48
d
58.11
±
2.78
d
2.92
±
0.22
a
b
3.85
±
0.42
a
SA
11
±
1
b
40.48
±
1.49
e
50.28
±
1.38
e
2.74
±
0.35
a
b
3.16
±
0.49
b
Values are expressed as mean ± standard deviation. Different letters in the same column indicate significant differences (P<0.05).Thickness of collagen films incorporated with SA at various concentrations is shown in Table2. Thickness of films incorporated with SA (1–3%, w/v) increased in comparison with the control. It ranged from 0.030 to 0.033 mm. However, no significant difference in thickness was observed between films incorporated with SA (P>0.05). Some authors also reported that the incorporation of SA had no effect on thickness of starch and pectin films [34, 35].


## 3.2.2. Mechanical Properties

Mechanical properties of biopolymer films are often presented in terms of tensile strength (TS) and elongation at break (E). TS accounts for film’s mechanical resistance due to cohesion forces between chains, while E measures its plasticity, which is capacity of a film to extend before breaking [36–38].All test films showed significant (P<0.05) differences in TS and E (Table 2). Single collagen and SA films exhibited TS and E value of 17.46 and 40.48 MPa and 78.49% and 50.28%, respectively. In general, polysaccharide-based films had better TS compared with protein-based films while protein-based films possessed greater E than polysaccharide-based films [15, 17], agreeing well with the results of this study.When the ratio of collagen to SA varied from 10 : 0 (pure collagen film) to 10 : 3 (CS3), TS was enhanced from 17.46 to 34.17 MPa, nearly more than double; however,E decreased from 70.15% to 58.11%. As suggested by [39], usually films with higher TS values show lower E values, due to the structural nature of those attributes. This result was probably induced by a certain degree of cross-linking between the proteins of collagen and SA. As observed in the FTIR analysis, the hydrophobic interactions and hydrogen present bridges in proteins could be demonstrated (Section 3.3.1). It has been proved that lots of hydroxyl groups exist to allow formation of hydrogen bonds between side-by-side polymer chains, resulting in high TS of films made of protein or sodium alginate [6, 21, 40]. Moreover, it has been reported that the mechanical properties of films are greatly associated with distribution and of intra- and intermolecular interactions, depending on the arrangements, and orientation of polymer chains in the network [17]. According to the SEM analysis (Section 3.3.2), a uniformity appearance for the CS films is obtained, leading to a better mechanical property. Thus, SA could effectively improve the mechanical property of collagen films.


## 3.2.3. Water Vapor Permeability (WVP)

Water vapor permeability (WVP) for the collagen, SA, and their blend films at relative humidity of 50% is shown in Table2. Obtained values ranged from 1.79 to 3.43 × 10−10g·cm−1·s−1·Pa−1. As it is reported that collagen is a hydrophilic polymer which has hydroxyl groups, thus, the water vapor could easily permeate through the film. In this study, films with lower content of SA showed significantly lower values comparing to the pure collagen films. This was in accordance with the fact that WVP values for blend films produced from protein and polysaccharide mixtures were lower in comparison to the WVP values of those films formed from protein alone [41].It is perhaps because more hydroxyl groups of SA could form more hydrogen bonds with water; thus water was trapped firmly in the polymer network. Similar results have been reported in the literature for feather keratin and SA blend films [21]. Further, it was discovered that SA could decrease the WVP probably through creating a tortuous pass for crossing water vapor through film, increasing the crystallinity of the biopolymer, or decreasing free hydrophilic groups (OH, NH) in biopolymer matrix [41, 42].It was also worth noting that further increase in SA (CS3) caused an increase in the WVP of CS films. This may attribute to the fact that both collagen and SA owing to their hydrophilic nature attract water molecules and create mobile regions with larger interchain distances. Additionally, these hydrophilic SA compete with water at the active sites of the polymer matrix causing water clustering which also forms microcavities in the network structure [43, 44]. The absorbed water molecules modify the film matrix, leading to a less dense structure where chain terminals are relatively more mobile, thus increasing water vapor transmission rate [45]. Therefore, the appropriate SA proportion could lead to a better barrier property for the blend films.


## 3.2.4. Oxygen Permeability (OP)

Oxygen is responsible for many degradation processes in foods such as lipid oxidation, microorganism growth, enzymatic browning, and vitamin loss [46]. Consequently, oxygen permeability (OP) is a crucial property in food packaging and it could be used as an index to evaluate the ability to prohibit oxidation reaction [47].Although the collagen films were hydrophilic and exhibited poor water vapor barrier properties, collagen-based films were hypothesized to be excellent barriers against oxygen, as examined in Table2. Nevertheless, no significant differences (P>0.05) were obtained between all the estimated values and no specific trends could be observed. The OP value of the pure collagen and SA film was 3.87 and 3.16 × 10−5 cm3·m−2·d−1·Pa−1, indicating that the both films were good oxygen barrier. Similar results were obtained by Bonilla et al. [46]. It was also noted that films made from proteins and carbohydrates are excellent barriers to oxygen, because of their tightly packed, ordered hydrogen bonded network structure [48].From this result, it appears that the addition of SA slightly changed OP of CS films, but with no obvious effect (P>0.05). When the ratio of collagen to SA varied from 10 : 1 (CS1) to 10 : 3 (CS3), OP varied from 3.56 to 3.85 × 10−5cm3·m−2·d−1·Pa−1. Among them, the OP for CS1 was found to be lowest, but further increase in SA concentration led to an increase in OP of CS films. Generally SA possess a film-forming ability, which leads to modest or very good oxygen barrier properties depending on the structure [11]. However, the result was not as good as expected in this study; SA added in the collagen could not decrease the OP values for the blend films.


## 3.2.5. Thermal Properties

Thermal properties of the samples were estimated using differential scanning calorimeter (DSC). It was known that DSC was a useful and rapid method to measure the interrelated thermodynamic profiles, and it was usually used to determine the temperature and enthalpy during endothermic or exothermic processes for an application in polymer materials [8]. The thermograms of DSC analysis and the related peak temperatures were given and illustrated in Figure 3.Figure 3
DSC thermograms of collagen, CS1, CS2, CS3, and SA films.It was reported that the first endothermic events were glass transition, followed by an endotherm associated with the melting of the ordered structures [20, 49]. As observed in Figure 3, the Tg value of the pure collagen film (55.63°C) is inferior to CS1 (85.31°C), CS2 (103.71°C), and CS3 (80.71°C). It suggested that the thermal stability of the CS films has been enhanced, owing to the addition of SA. That may be explained by the increase of interactions provided by SA, stabilizing the collagen structure against unfolding and requiring a higher temperature to degrade collagen [18, 20]. Nevertheless, the Tg value for the CS films initially increased and then decreased, with the SA concentration increase. As reported, Tg value of the collagen film is attributed to the hydrogen bonded networks and mediated by water molecules [50].Oppositely, as observed, compared to the collagen film (170.59°C), CS1 (153.13°C) and CS3 (158.29°C) presented a decrease inTc value associated with thermal stability. The lower Tc was related to the reduction in some weak intermolecular forces such as hydrogen bonds between water and the matrix. It could be explained that the hydrophobic feature was imparted into collagen and facilitated evaporation of water with SA added. Totally, the addition of SA effectively improved the thermal property for the CS blend films.


## 3.3. Microstructure Characterization

### 3.3.1. FTIR

FTIR spectra of collagen, SA, and their blend films at selected concentrations were depicted in Figure4. A robust classification of FTIR spectra collagen could be obtained by using a combination of four spectral intervals [ν(C=O) absorption of amide I (1,700–1,600 cm−1), δ(CH2), and δ(CH3) absorptions (1,480–1,350 cm−1), ν(C–N), and δ(N–H) absorptions of amide III (1,300–1,180 cm−1), and (C–O) and (C–O–C) absorptions of carbohydrate moieties (1,100–1,005 cm−1)] [51]. Both collagen and CS3 spectra showed similar IR absorbance patterns.Figure 4
FTIR spectra of the different films (collagen, SA, and CS3) studied in all the range absorption.For CS3, the OH stretching and asymmetric COO stretching shift to a lower wavenumber (from 3435 to 3410 cm−1). Generally, the shift to the lower wavenumber indicated the existence of hydrogen bonds in collagen [50]. It also indicated that no other bonds except hydrogen bonds were formatted between collagen and SA.


### 3.3.2. SEM

Scanning electron microscopy (SEM) observations were carried out to get a better insight into the homogeneity and the microstructure of the blend films (Figure5). SEM images of the surface of the collagen, SA, CS1, CS2, and CS3 films, and cross section of the CS2 films were presented. It was observed that collagen fiber was arranged in the film matrix, without pores and with excellent structural integrity (Figure 5(a)). SA exhibited rough surfaces with nonporous and heterogeneous morphologies due to some nonfully destructured alginate particles (Figure 5(b)). While more SA was added to the blend, the surface of CS2 and CS3 exhibited rougher and fluctuant matrix morphology (Figures 5(d) and 5(e)). Nevertheless, SEM images revealed that CS films had a smoother surface compared to pure SA films which became rougher upon drying. The cross section of CS2 had a compact and homogeneous structure and no distinct phase separation was observed (Figure 5(f)), indicating the integrity of the blend structure.Figure 5
SEM micrographs of the surface of the films based on (a) the pure collagen film, (b) SA film, (c) CS1, (d) CS2, and (e) CS3. SEM micrographs of the cross section appearance of the films based on (f) CS2.
(a)
(b)
(c)
(d)
(e)
(f)The above results lead to the following suggestions about the formation mechanism of the CS blend films. When SA were added to collagen films, the low molecular weight hydrophilic SA molecular movement was depressed by the formed strong cross-linking network structure, resulting in improved mechanical stability.


### 3.3.3. AFM

AFM images were obtained in order to provide the information of surface morphology and roughness for the sample film. Figure6 shows surface morphologies and the corresponding results of roughness parameters (Rq, root mean square of roughness, and Ra, mean value of roughness) of the films. The surface morphology of SA film (Figure 6(a)) showed that bright protuberant parts were obviously observed due to SA molecule self-aggregation. Some significant differences between SA and CS films are exhibited. Obviously, the presence of collagen led to a marked decrease in the roughness of the films, as indicated by lower Ra and Rq values. The results were accordant with the SEM microstructure observations.Figure 6
AFM images of the films: (a) SA film, (b) CS1, (c) CS2, and (d) CS3.
(a)
(b)
(c)
(d)


## 3.3.1. FTIR

FTIR spectra of collagen, SA, and their blend films at selected concentrations were depicted in Figure4. A robust classification of FTIR spectra collagen could be obtained by using a combination of four spectral intervals [ν(C=O) absorption of amide I (1,700–1,600 cm−1), δ(CH2), and δ(CH3) absorptions (1,480–1,350 cm−1), ν(C–N), and δ(N–H) absorptions of amide III (1,300–1,180 cm−1), and (C–O) and (C–O–C) absorptions of carbohydrate moieties (1,100–1,005 cm−1)] [51]. Both collagen and CS3 spectra showed similar IR absorbance patterns.Figure 4
FTIR spectra of the different films (collagen, SA, and CS3) studied in all the range absorption.For CS3, the OH stretching and asymmetric COO stretching shift to a lower wavenumber (from 3435 to 3410 cm−1). Generally, the shift to the lower wavenumber indicated the existence of hydrogen bonds in collagen [50]. It also indicated that no other bonds except hydrogen bonds were formatted between collagen and SA.


## 3.3.2. SEM

Scanning electron microscopy (SEM) observations were carried out to get a better insight into the homogeneity and the microstructure of the blend films (Figure5). SEM images of the surface of the collagen, SA, CS1, CS2, and CS3 films, and cross section of the CS2 films were presented. It was observed that collagen fiber was arranged in the film matrix, without pores and with excellent structural integrity (Figure 5(a)). SA exhibited rough surfaces with nonporous and heterogeneous morphologies due to some nonfully destructured alginate particles (Figure 5(b)). While more SA was added to the blend, the surface of CS2 and CS3 exhibited rougher and fluctuant matrix morphology (Figures 5(d) and 5(e)). Nevertheless, SEM images revealed that CS films had a smoother surface compared to pure SA films which became rougher upon drying. The cross section of CS2 had a compact and homogeneous structure and no distinct phase separation was observed (Figure 5(f)), indicating the integrity of the blend structure.Figure 5
SEM micrographs of the surface of the films based on (a) the pure collagen film, (b) SA film, (c) CS1, (d) CS2, and (e) CS3. SEM micrographs of the cross section appearance of the films based on (f) CS2.
(a)
(b)
(c)
(d)
(e)
(f)The above results lead to the following suggestions about the formation mechanism of the CS blend films. When SA were added to collagen films, the low molecular weight hydrophilic SA molecular movement was depressed by the formed strong cross-linking network structure, resulting in improved mechanical stability.


## 3.3.3. AFM

AFM images were obtained in order to provide the information of surface morphology and roughness for the sample film. Figure6 shows surface morphologies and the corresponding results of roughness parameters (Rq, root mean square of roughness, and Ra, mean value of roughness) of the films. The surface morphology of SA film (Figure 6(a)) showed that bright protuberant parts were obviously observed due to SA molecule self-aggregation. Some significant differences between SA and CS films are exhibited. Obviously, the presence of collagen led to a marked decrease in the roughness of the films, as indicated by lower Ra and Rq values. The results were accordant with the SEM microstructure observations.Figure 6
AFM images of the films: (a) SA film, (b) CS1, (c) CS2, and (d) CS3.
(a)
(b)
(c)
(d)


## 4. Conclusion

Scale-up collagen/sodium alginate (CS) films were successfully prepared and their physical, mechanical, and barrier properties were evaluated. SEM and AFM analysis verified the homogeneity of the blend films while FTIR indicated hydrogen bonds formed between collagen and sodium alginate. Also, DSC suggested that their thermal stability has improved, owing to the addition of SA.Furthermore, with increasing concentration of SA, TS increased andE decreased while WVP initially decreased and then increased. Relatively, no obvious difference on OP for the CS films was obtained (P>0.05). Results revealed that CS films with appropriate physical, mechanical, and barrier attributes could be effectively produced and successfully utilized in the food packaging industry.



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*Source: 4954259-2017-11-14.xml*