# Organic/Inorganic Superabsorbent Hydrogels Based on Xylan and Montmorillonite

Authors: Shuang Zhang; Ying Guan; Gen-Que Fu; Bo-Yang Chen; Feng Peng; Chun-Li Yao; Run-Cang Sun
Journal: Journal of Nanomaterials
 (2014)

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## Abstract

The unique organic/inorganic superabsorbent hydrogels based on xylan and inorganic clay montmorillonite (MMT) were prepared via grafting copolymerization of acrylic acid (AA) and 2-acrylamido-2-methylpropanesulfonic acid (AMPS) withN,N-methylenebisacrylamide (MBA) as a cross-linking agent and potassium persulfate (KPS) as an initiator. The effect of variables on the swelling capacity of the hydrogels, such as the weight ratios of MMT/xylan, MBA/xylan, and AMPS/AA, was systematically optimized. The results indicated that the superabsorbent hydrogels comprised a porous cross-linking structure of MMT and xylan with side chains that carry carboxylate, carboxamide, and sulfate. The hydrogels exhibit the high compressive modulus (E), about 35–55 KPa, and the compression strength of the hydrogels increased with an increment of the MMT content. The effect of various cationic salt solutions (LiCl, CaCl2, and FeCl3) on the swelling has the following order: Li+ > Ca2+ > Fe3+. Furthermore, the influence of pH values on swelling behaviors showed that the superabsorbent composites retained around 1000 g g−1 over a wide pH range of 6.0–10.0. The xylan-based hydrogels with the high mechanical and swelling properties are promising for the applications in the biomaterials area.


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## Body

## 1. Introduction

Superabsorbent hydrogels are slightly cross-linked hydrophilic polymers with a three-dimensional network structure. They can absorb water in the amount from 10% up to thousands of times based on their dry weight and retain large amounts of aqueous fluids even under some pressure. Due to the special characteristics, these materials have been widely applied in various fields, such as agriculture [1, 2], biomedical area [3, 4], waste-water treatment [5, 6], biosensors [7], and tissue engineering [8, 9].Polysaccharide-based hydrogels are currently attracting much interest for their unique properties, that is, biocompatibility, biodegradability, renewability, and nontoxicity. Various polysaccharides, such as chitosan [10], starch [11], cellulose [12], alginate [13], carrageenan [14], and gellan gum [15], have been investigated on hydrogel formulations. Typically, hemicelluloses are the second most abundant polysaccharides in biomass, which are commonly defined as cell wall heterogeneous polysaccharides. Compared with other polysaccharides, hemicelluloses have been somewhat neglected in research and are normally disposed as organic waste from the forest industry side streams. While recent research has shown that hemicelluloses have significant potential as a material resource for hydrogel preparation. A series of hemicelluloses-based hydrogels were synthesized from galactoglucomannans, via introducing functional monomers with unsaturated bonds to the backbone of hemicelluloses and chemically cross-linking the modified hemicelluloses [16–20]. The hydrogels, presenting good biodegradability, nontoxicity, and controllable swelling capacity, were fully developed for drug delivery systems. In addition, xylan-based hydrogels have also shown potential applications as pH-sensitive controlled drug delivery vehicles by blending aspen hemicelluloses and chitosan in acidic conditions [21]. Furthermore, xylan-rich hemicelluloses-based hydrogels were prepared and used as a novel porous bioabsorbent by graft copolymerization of acrylic acid and hemicelluloses for absorption of heavy metal ions from aqueous solutions [22, 23]. Therefore, the applications of hemicelluloses in hydrogels field are gradually expanding.Arabinoxylans (AXs) are the main hemicelluloses of Gramineae, which have been generally present in a variety of tissue of the main cereals of commerce: wheat, rye, barley, oat, rice, corn, and sorghum, as well as other plants: pangola grass, bamboo shoot, and ray grass [24]. Gramineae is similar to hardwood xylan, but the amount of L-arabinose is higher. Hydrogels have been prepared from AXs extracted from wheat bran as controlled release matrices, which were synthesized via the oxidative cross-linking using either chemical (ferulic chloride and ammonium persulphate) or enzymatic (laccase/O2 and peroxidase/H2O2) free radical-generating agents [25–27]. The gels present interesting properties like neutral taste and odor, high water absorption capability (up to 100 g of water per gram of dry polymer), and absence of pH, electrolyte, and temperature susceptibility [28]. However, the water absorption capacity and mechanical strength of the AXs hydrogels are much lower than those of petroleum-based hydrogels such as poly(acrylic acid) and poly(acrylamide) hydrogels. Furthermore, the absence of multistimulus response properties severely restricts their applications. Therefore, more research attention should be paid to develop new approaches for modifying and cross-linking AXs to improve the properties of the hydrogels, such as absorption capacity, mechanical strength, and stimuli-responsive physical properties (normally temperature-, pH-, salt-, or osmosis-controlled changes).Recently, much attention has been focused on inorganic materials for preparation of superabsorbent composites, such as attapulgite [29], kaolin [30], and sodium silicate [31]. The introduction of inorganic clay into polysaccharides not only reduces production costs but also improves the properties (e.g., swelling ability, gel strength, and mechanical and thermal stability) of hydrogels and accelerates the generation of new materials for special application [32]. Among the clays, montmorillonite (MMT), a layered aluminum silicate with exchangeable cations and reactive –OH groups on the surface, has been widely used to improve the properties of hydrogels, due to its good absorption, extensive swelling in water and cation exchange capacity [33]. Yet, to the best of our knowledge, there has been no report on the preparation of superabsorbent hydrogels based on xylan and inorganic clays.Acrylic acid (AA) and 2-acrylamido-2-methylpropanesulfonic acid (AMPS) are important monomers that are widely used for the preparation of functional hydrogels. AMPS is hydrophilic monomer containing nonionic and anionic groups; meanwhile, AA is anionic monomer. The incorporation of ionic groups in the superabsorbent is known to increase their swelling capacity, while the nonionic groups can improve their salt tolerance. In this paper, a unique organic/inorganic hydrogel was prepared by grafting copolymerization of AA and AMPS monomers along the chains of AXs in the presence of MMT. The intermolecular interaction and morphological change of the hydrogels were characterized by FT-IR spectra and scanning electron microscope (SEM). Moreover, the swelling properties and behaviors under different pH and salt concentrations were investigated.


## 2. Experimental

### 2.1. Materials

Xylan was isolated from bamboo (Phyllostachys pubescens) holocellulose obtained by using 3% NaOH at 75°C for 3 h with a solid to liquid ratio of 1 : 25 (g·mL−1). The holocellulose was obtained by delignification of the extractive-free bamboo (40–60 mesh) with 6% sodium chlorite in acidic solution (pH 3.6–3.8, adjusted by 10% acetic acid) at 75°C for 2 h. The composition of neutral sugars and uronic acids and the molecular weights of the hemicellulosic samples were determined according to the literature [34]. The sugar composition of the xylan (83.5% xylose, 5.1% arabinose, 4.2% glucose, 0.4% galactose, and 6.8% glucuronic acid (relatively molar percent)) was tested by high performance anion exchange chromatography (HPAEC). The molecular weights obtained by gel permeation chromatography (GPC) showed that the native xylan had a weight average molecular weight (Mw) of 13,420 g·mol−1 and a polydispersity of 4.1, corresponding to a degree of polymerization of 88. 2-Acrylamido-2-methyl-1-propanesulfonic acid (AMPS) and montmorillonite (MMT) were purchased from A Johnson Mattey Company. N,N-Methylenebisacrylamide (MBA) and potassium persulfate (KPS) were purchased from Tianjin Jinke Refined Chemical Engineering Research Institute, China. All of these chemicals were used without any further purification. AA (Beijing Yili Fine Chemical Co., Ltd., China) was purified by distillation under reduced pressure to remove the inhibitor hydroquinone before use. All other reagents used were analytical grade, and all solutions were of prepared with distilled water.


### 2.2. Preparation of Hydrogels

Xylan (1.0 g) was dissolved in 35.0 mL of distilled water in a three-neck reactor equipped with a mechanical stirrer, a reflux condenser, and a nitrogen line at 85°C until a homogeneous solution was obtained. Then appropriate amounts (0.00–0.12 g) of MMT were added to this solution with stirring to form a uniform sticky solution under nitrogen. After cooling the reactant to 70°C, 0.08 g of KPS were added, stirred, and kept for 10 min to generate radicals. Subsequently, the mixture of AA (1.43–2.86 g, neutralization degree of 70% with sodium hydroxide solution), AMPS (1.14–2.57 g), and MBA (0.05–0.25 g) was added to the flask. All the reactions were carried out under nitrogen, and the reaction mixture was continuously stirred for 4 h. At the end of the propagation reaction, the gel product was poured into excess ethanol (200 mL) and remained for 48 h to dewater. Then, the dewatered product was dried to constant mass at 70°C, grounded, and passed through 100-mesh sieve. Finally, the powdered products were stored away from moisture, heat, and light. The feed compositions of all samples are listed in Table1.Table 1
The reaction conditions for xylan-g-poly(AA-AMPS)/MMT hydrogels.
Sample codes
MMT/xylan (g g−1)
AMPS (g)
MBA (g)
AA (g)
1
—
1.00
0.10
2.00
2
0.03
1.00
0.10
2.00
3
0.05
1.00
0.10
2.00
4
0.08
1.00
0.10
2.00
5
0.11
1.00
0.10
2.00
6
0.08
2.00
0.05
2.00
7
0.08
2.00
0.10
2.00
8
0.08
2.00
0.15
2.00
9
0.08
2.00
0.20
2.00
10
0.08
2.00
0.25
2.00
11
0.08
1.14
0.10
2.28
12
0.08
1.78
0.10
2.22
13
0.08
2.00
0.10
2.00
14
0.08
2.33
0.10
1.67
15
0.08
2.57
0.10
1.43


### 2.3. Method of Characterization

#### 2.3.1. FT-IR Spectroscopy

FT-IR spectra of the MMT, xylan, xylan-g-poly(AA-AMPS), and xylan-g-poly(AA-AMPS)/MMT hydrogels were recorded using a Thermo Scientific Nicolet iN 10 FT-IR Microscopy (Thermo Nicolet Corporation, Madison, WI) equipped with a liquid nitrogen cooled MCT detector. Dried samples were grounded and palletized using BaF2 and their spectra were recorded from 4000 to 650 cm−1 at a resolution of 4 cm−1 and 128 scans per sample.


#### 2.3.2. Surface Morphology of the Hydrogels

The equilibrium-swollen samples of the hydrogels in deionized water at room temperature were quickly frozen and then freeze-dried for morphological analysis. Scanning electron microscopy (SEM) of the hydrogel samples was carried out with a Hitachi S-3400N II (Hitachi, Japan) instrument at 15 kV. Prior to taking pictures, the samples were sputter-coated with a thin layer of gold. Images were obtained at magnifications ranging from 200x to 5000x, which was dependent on the feature to be traced.


#### 2.3.3. Swelling Measurements

The preweighted dry hydrogels were immersed into excessive distilled water to reach a state of equilibrium swelling. The swollen superabsorbent was filtered using 100-mesh sieve and drained for 20 min until no free water remained. After weighing the swollen hydrogels, the equilibrium water absorption was calculated by using the following equation:(1)
Q
eq
=
W
2
-
W
1
W
1
,
where Q
eq is the equilibrium water absorption defined as grams of water per gram of sample; W
1 and W
2 are the mass of sample before and after swelling, respectively.


#### 2.3.4. Mechanical Measurement

Dynamic mechanical analysis (DMA, TA Instruments Q800 Series) was used to determine the compressive modulus of the swollen hydrogel samples. To reach swelling equilibrium, hydrogels were incubated in distilled water for 24 h at room temperature before test. The disk-shaped samples were1
cm
×
0
.
5 cm (diameter
×
height) in dimension and were tested in compression mode at 25°C. Rheological measurements were carried out at 25°C on ARES-RFS III rheometer (TA Instruments, USA). The mixture of xylan (1.0 g), KPS (0.08 g), AA (1.0 or 2.0 g), MBA (0.05–0.25 g), and MMT (0.00–0.12 g) was stirred to form a homogeneous solution. This hybrid system was quickly transferred into rheometer for testing.


#### 2.3.5. Swelling in Various Salt Solutions

The swelling capacity of the hydrogels was measured in different concentrations (0.5, 1.0, 1.5, 2.0, and 2.5 mol·L−1) of LiCl, CaCl2, and FeCl3 salt solutions according to the above method described for swelling measurement in distilled water.


#### 2.3.6. Swelling at Various pHs

Individual solutions with acidic and basic pHs were prepared by the dilution of NaOH (pH 12.0) and HCl (pH 2.0) solutions to achievepH
≥
6.0 and <6.0, respectively. The pH values were precisely checked by a pH meter (PB-10, Sartorius). Then, the preweighted dried hydrogels were used for the swelling measurements according to the above method described for swelling measurement in distilled water.


#### 2.3.7. Water Retention Measurement

The water retention (WR) was determined by centrifuging the water-swollen hydrogels at 2000 rpm. The weight of the hydrogels was determined every 30 s. The WR of the hydrogels was calculated according to(2)
WR
(
%
)
=
m
2
m
1
×
100
%
,
where m
1 is the weight of the fully swollen hydrogel and m
2 is the weight of the hydrogel centrifuged for different times at 2000 rpm.


## 2.1. Materials

Xylan was isolated from bamboo (Phyllostachys pubescens) holocellulose obtained by using 3% NaOH at 75°C for 3 h with a solid to liquid ratio of 1 : 25 (g·mL−1). The holocellulose was obtained by delignification of the extractive-free bamboo (40–60 mesh) with 6% sodium chlorite in acidic solution (pH 3.6–3.8, adjusted by 10% acetic acid) at 75°C for 2 h. The composition of neutral sugars and uronic acids and the molecular weights of the hemicellulosic samples were determined according to the literature [34]. The sugar composition of the xylan (83.5% xylose, 5.1% arabinose, 4.2% glucose, 0.4% galactose, and 6.8% glucuronic acid (relatively molar percent)) was tested by high performance anion exchange chromatography (HPAEC). The molecular weights obtained by gel permeation chromatography (GPC) showed that the native xylan had a weight average molecular weight (Mw) of 13,420 g·mol−1 and a polydispersity of 4.1, corresponding to a degree of polymerization of 88. 2-Acrylamido-2-methyl-1-propanesulfonic acid (AMPS) and montmorillonite (MMT) were purchased from A Johnson Mattey Company. N,N-Methylenebisacrylamide (MBA) and potassium persulfate (KPS) were purchased from Tianjin Jinke Refined Chemical Engineering Research Institute, China. All of these chemicals were used without any further purification. AA (Beijing Yili Fine Chemical Co., Ltd., China) was purified by distillation under reduced pressure to remove the inhibitor hydroquinone before use. All other reagents used were analytical grade, and all solutions were of prepared with distilled water.


## 2.2. Preparation of Hydrogels

Xylan (1.0 g) was dissolved in 35.0 mL of distilled water in a three-neck reactor equipped with a mechanical stirrer, a reflux condenser, and a nitrogen line at 85°C until a homogeneous solution was obtained. Then appropriate amounts (0.00–0.12 g) of MMT were added to this solution with stirring to form a uniform sticky solution under nitrogen. After cooling the reactant to 70°C, 0.08 g of KPS were added, stirred, and kept for 10 min to generate radicals. Subsequently, the mixture of AA (1.43–2.86 g, neutralization degree of 70% with sodium hydroxide solution), AMPS (1.14–2.57 g), and MBA (0.05–0.25 g) was added to the flask. All the reactions were carried out under nitrogen, and the reaction mixture was continuously stirred for 4 h. At the end of the propagation reaction, the gel product was poured into excess ethanol (200 mL) and remained for 48 h to dewater. Then, the dewatered product was dried to constant mass at 70°C, grounded, and passed through 100-mesh sieve. Finally, the powdered products were stored away from moisture, heat, and light. The feed compositions of all samples are listed in Table1.Table 1
The reaction conditions for xylan-g-poly(AA-AMPS)/MMT hydrogels.
Sample codes
MMT/xylan (g g−1)
AMPS (g)
MBA (g)
AA (g)
1
—
1.00
0.10
2.00
2
0.03
1.00
0.10
2.00
3
0.05
1.00
0.10
2.00
4
0.08
1.00
0.10
2.00
5
0.11
1.00
0.10
2.00
6
0.08
2.00
0.05
2.00
7
0.08
2.00
0.10
2.00
8
0.08
2.00
0.15
2.00
9
0.08
2.00
0.20
2.00
10
0.08
2.00
0.25
2.00
11
0.08
1.14
0.10
2.28
12
0.08
1.78
0.10
2.22
13
0.08
2.00
0.10
2.00
14
0.08
2.33
0.10
1.67
15
0.08
2.57
0.10
1.43


## 2.3. Method of Characterization

### 2.3.1. FT-IR Spectroscopy

FT-IR spectra of the MMT, xylan, xylan-g-poly(AA-AMPS), and xylan-g-poly(AA-AMPS)/MMT hydrogels were recorded using a Thermo Scientific Nicolet iN 10 FT-IR Microscopy (Thermo Nicolet Corporation, Madison, WI) equipped with a liquid nitrogen cooled MCT detector. Dried samples were grounded and palletized using BaF2 and their spectra were recorded from 4000 to 650 cm−1 at a resolution of 4 cm−1 and 128 scans per sample.


### 2.3.2. Surface Morphology of the Hydrogels

The equilibrium-swollen samples of the hydrogels in deionized water at room temperature were quickly frozen and then freeze-dried for morphological analysis. Scanning electron microscopy (SEM) of the hydrogel samples was carried out with a Hitachi S-3400N II (Hitachi, Japan) instrument at 15 kV. Prior to taking pictures, the samples were sputter-coated with a thin layer of gold. Images were obtained at magnifications ranging from 200x to 5000x, which was dependent on the feature to be traced.


### 2.3.3. Swelling Measurements

The preweighted dry hydrogels were immersed into excessive distilled water to reach a state of equilibrium swelling. The swollen superabsorbent was filtered using 100-mesh sieve and drained for 20 min until no free water remained. After weighing the swollen hydrogels, the equilibrium water absorption was calculated by using the following equation:(1)
Q
eq
=
W
2
-
W
1
W
1
,
where Q
eq is the equilibrium water absorption defined as grams of water per gram of sample; W
1 and W
2 are the mass of sample before and after swelling, respectively.


### 2.3.4. Mechanical Measurement

Dynamic mechanical analysis (DMA, TA Instruments Q800 Series) was used to determine the compressive modulus of the swollen hydrogel samples. To reach swelling equilibrium, hydrogels were incubated in distilled water for 24 h at room temperature before test. The disk-shaped samples were1
cm
×
0
.
5 cm (diameter
×
height) in dimension and were tested in compression mode at 25°C. Rheological measurements were carried out at 25°C on ARES-RFS III rheometer (TA Instruments, USA). The mixture of xylan (1.0 g), KPS (0.08 g), AA (1.0 or 2.0 g), MBA (0.05–0.25 g), and MMT (0.00–0.12 g) was stirred to form a homogeneous solution. This hybrid system was quickly transferred into rheometer for testing.


### 2.3.5. Swelling in Various Salt Solutions

The swelling capacity of the hydrogels was measured in different concentrations (0.5, 1.0, 1.5, 2.0, and 2.5 mol·L−1) of LiCl, CaCl2, and FeCl3 salt solutions according to the above method described for swelling measurement in distilled water.


### 2.3.6. Swelling at Various pHs

Individual solutions with acidic and basic pHs were prepared by the dilution of NaOH (pH 12.0) and HCl (pH 2.0) solutions to achievepH
≥
6.0 and <6.0, respectively. The pH values were precisely checked by a pH meter (PB-10, Sartorius). Then, the preweighted dried hydrogels were used for the swelling measurements according to the above method described for swelling measurement in distilled water.


### 2.3.7. Water Retention Measurement

The water retention (WR) was determined by centrifuging the water-swollen hydrogels at 2000 rpm. The weight of the hydrogels was determined every 30 s. The WR of the hydrogels was calculated according to(2)
WR
(
%
)
=
m
2
m
1
×
100
%
,
where m
1 is the weight of the fully swollen hydrogel and m
2 is the weight of the hydrogel centrifuged for different times at 2000 rpm.


## 2.3.1. FT-IR Spectroscopy

FT-IR spectra of the MMT, xylan, xylan-g-poly(AA-AMPS), and xylan-g-poly(AA-AMPS)/MMT hydrogels were recorded using a Thermo Scientific Nicolet iN 10 FT-IR Microscopy (Thermo Nicolet Corporation, Madison, WI) equipped with a liquid nitrogen cooled MCT detector. Dried samples were grounded and palletized using BaF2 and their spectra were recorded from 4000 to 650 cm−1 at a resolution of 4 cm−1 and 128 scans per sample.


## 2.3.2. Surface Morphology of the Hydrogels

The equilibrium-swollen samples of the hydrogels in deionized water at room temperature were quickly frozen and then freeze-dried for morphological analysis. Scanning electron microscopy (SEM) of the hydrogel samples was carried out with a Hitachi S-3400N II (Hitachi, Japan) instrument at 15 kV. Prior to taking pictures, the samples were sputter-coated with a thin layer of gold. Images were obtained at magnifications ranging from 200x to 5000x, which was dependent on the feature to be traced.


## 2.3.3. Swelling Measurements

The preweighted dry hydrogels were immersed into excessive distilled water to reach a state of equilibrium swelling. The swollen superabsorbent was filtered using 100-mesh sieve and drained for 20 min until no free water remained. After weighing the swollen hydrogels, the equilibrium water absorption was calculated by using the following equation:(1)
Q
eq
=
W
2
-
W
1
W
1
,
where Q
eq is the equilibrium water absorption defined as grams of water per gram of sample; W
1 and W
2 are the mass of sample before and after swelling, respectively.


## 2.3.4. Mechanical Measurement

Dynamic mechanical analysis (DMA, TA Instruments Q800 Series) was used to determine the compressive modulus of the swollen hydrogel samples. To reach swelling equilibrium, hydrogels were incubated in distilled water for 24 h at room temperature before test. The disk-shaped samples were1
cm
×
0
.
5 cm (diameter
×
height) in dimension and were tested in compression mode at 25°C. Rheological measurements were carried out at 25°C on ARES-RFS III rheometer (TA Instruments, USA). The mixture of xylan (1.0 g), KPS (0.08 g), AA (1.0 or 2.0 g), MBA (0.05–0.25 g), and MMT (0.00–0.12 g) was stirred to form a homogeneous solution. This hybrid system was quickly transferred into rheometer for testing.


## 2.3.5. Swelling in Various Salt Solutions

The swelling capacity of the hydrogels was measured in different concentrations (0.5, 1.0, 1.5, 2.0, and 2.5 mol·L−1) of LiCl, CaCl2, and FeCl3 salt solutions according to the above method described for swelling measurement in distilled water.


## 2.3.6. Swelling at Various pHs

Individual solutions with acidic and basic pHs were prepared by the dilution of NaOH (pH 12.0) and HCl (pH 2.0) solutions to achievepH
≥
6.0 and <6.0, respectively. The pH values were precisely checked by a pH meter (PB-10, Sartorius). Then, the preweighted dried hydrogels were used for the swelling measurements according to the above method described for swelling measurement in distilled water.


## 2.3.7. Water Retention Measurement

The water retention (WR) was determined by centrifuging the water-swollen hydrogels at 2000 rpm. The weight of the hydrogels was determined every 30 s. The WR of the hydrogels was calculated according to(2)
WR
(
%
)
=
m
2
m
1
×
100
%
,
where m
1 is the weight of the fully swollen hydrogel and m
2 is the weight of the hydrogel centrifuged for different times at 2000 rpm.


## 3. Results and Discussion

### 3.1. Synthesis and Spectral Characterization

The superabsorbent hydrogel was prepared by the graft copolymerization of acrylic acid (AA) and 2-acrylamido-2-methyl-1-propanesulfonic acid (AMPS) onto xylan in the presence of a cross-linking agent (MBA), powdery montmorillonite (MMT), and potassium persulfate (KPS) as an initiator. The persulfate initiator was decomposed under heating to produce sulfate anion radicals that abstract hydrogen atoms from the hydroxyl groups of the xylan backbones. Therefore, this redox system resulted in active centers capable of radically initiating the polymerization of AA and AMPS, leading to a graft copolymer. Since a cross-linking agent (MBA) was present in this system, the copolymer comprised a cross-linked structure. The MMT in the polymerization reaction can also be considered as a cross-linking agent [35]. The proposed mechanism for the grafting and chemically cross-linking reactions is outlined in Figure 1.Figure 1
Proposed reaction mechanism for synthesis of xylan-g-poly(AA-AMPS)/MMT superabsorbent hydrogels.Infrared spectroscopy was carried out to confirm the chemical structure of the superabsorbent hydrogel. FT-IR spectra of MMT, xylan, xylan-g-poly(AA-AMPS), and xylan-g-poly(AA-AMPS)/MMT superabsorbent hydrogel are shown in Figure 2. In the spectrum (see Figure 2(c)) of xylan, the region between 3500 cm−1 and 1800 cm−1 presents two major peaks at about 3411 cm−1 (corresponding to the absorption of stretching of the hydroxyl groups) and at 2911 cm−1 (corresponding to the C–H stretching of the CH2 groups). The absorption peak at 1600 cm−1 is related to the uronic acid carboxylate [36]. The bands at the range of 1452 and 1048 cm−1 are assigned to the C–H and C–O bond stretching frequencies. The low intensity of the peaks at 990 and 1166 cm−1 suggests the presence of arabinosyl units, which have been reported to be attached only at position 3 of the xylopyranosyl constituents [37]. A sharp band at 895 cm−1 is due to β-glycosidic linkages between the sugar units. On comparing the spectra of xylan and xylan-g-poly(AA-AMPS) (see Figure 2(d)), new characteristic absorption bands at 1651, 1558, and 1442 cm−1 are assigned to the stretching vibration of C=O, asymmetrical stretching vibration of COO−, and symmetrical stretching vibration of COO−, respectively [38]. Moreover, the characteristic absorption peaks of AMPS units are shown at 1400, 1040, and 627 cm−1, which are attributed to C–N stretching vibration of the amide, S–O stretching vibration of –SO3H, and C–S stretching vibration, respectively [39]. These bands indicated that AA and AMPS monomers were actually grafted onto the backbone of xylan.Figure 2
FT-IR of (a) xylan-g-poly(AA-AMPS)/MMT, (b) MMT, (c) xylan and (d) xylan-g-poly(AA-AMPS).In the spectrum (see Figure2(a)) of MMT, the characteristic vibration bands are shown at 3400 and 3630 cm−1, which correspond to –OH stretching band for absorbed interlayer water and –OH stretching band for Al–OH, respectively. The absorption peaks at 1631 and 1423 cm−1 are attributed to the deformation vibration of the hydroxyl groups. The characteristic peaks at 1150 and 1090 cm−1 are due to Si–O stretching (out-of plane) for MMT and Si–O stretching (in plane) vibration for layered silicates, respectively. The peaks at 915, 845, and 796 cm−1 are assigned to Al–Al–OH, Al–Mg–OH, and Si–O–Al bending vibrations, respectively [40–42]. As can be seen, compared to the spectrum of MMT (Figure 2(b)), the intensities of absorption bands at 3630 cm−1 ascribed to –OH of MMT disappeared in the spectrum of xylan-g-poly(AA-AMPS)/MMT (Figure 2(a)). In addition, the intensity of the absorption peaks due to Si–O stretching also decreased. These results indicated that MMT participated in polymerization reaction through its active –OH groups and chemically cross-linked with polymer chains. Therefore, it could be concluded that the superabsorbent hydrogel product comprised a cross-linking structure of xylan and MMT with side chains carrying carboxylate, carboxamide, and sulfate.


### 3.2. Morphological Analysis

The morphologies of the freeze-dried xylan-g-poly(AA-AMPS) and xylan-g-poly(AA-AMPS)/MMT composites are depicted in Figure 3, respectively. Obviously, the surface morphology of the xylan-g-poly(AA-AMPS)/MMT hydrogel is different from that of xylan-g-poly(AA-AMPS). It could be observed that the cross-linked xylan-g-poly(AA-AMPS) (Figure 3(a)) displayed a porous structure with many large pores. However, for hydrogel containing MMT (Figure 3(b)), the pore size became smaller and it showed a sheet-like structure with significant interconnection forming a three-dimensional network, which was beneficial for the diffusion of aqueous fluid into the superabsorbent polymer and increasing the water absorption rate [43, 44]. In addition, the degree of dispersion of clay micropowder in the polymer matrix is more important for an organic-inorganic composite [45, 46]. As can be seen from Figures 3(c) and 3(d), the microstructure of pure MMT clay was flaky (Figure 3(c)), while these clays were randomly dispersed in the polymer matrix and almost embedded within xylan-g-poly(AA-AMPS) in the composites (Figure 3(d)), and no flocculation of MMT particles could be observed. These SEM results confirmed that the MMT was finely dispersed in the composite to form a homogeneous composition.SEM images of (a) xylan-g-poly(AA-AMPS), (b) xylan-g-poly(AA-AMPS)/MMT at low magnification and (c) MMT, (d) xylan-g-poly(AA-AMPS)/MMT at high magnification.
(a)
(b)
(c)
(d)


### 3.3. Mechanical Properties of Hydrogels

The mechanical properties of the xylan-based hydrogels with different ratios of MMT to xylan have been determined. Figure4(a) presents the typical compressive modulus-strain curves of xylan-based hydrogels at room temperature. Obviously, all the samples exhibited the high compressive modulus (E), about 35–55 KPa. This indicated that the hydrogels had excellent mechanical properties. As expected, the compressive modulus of the hydrogels increased with the increment of the MMT content in the hydrogels, in the order Gel 5> Gel 4> Gel 3> Gel 2> Gel 1. The results strongly demonstrated that MMT contributed to the enhancement of the mechanical properties of the hydrogels. On the other hand, the strains of hydrogels decrease from 92% to 66%, when the MMT content was increased in the hydrogel.Compressive stress-strain curves for hydrogels with different MMT contents (a). The time dependence of storage modulus (G′) for hydrogels with different MMT contents (b) and different MBA contents (c).
(a)
(b)
(c)To monitor the gelation process, a time sweep measurement for viscoelastic properties of each sample was carried out at 25°C [47]. Figures 4(b) and 4(c) show the storage modulus (G′) of hydrogels with different MMT concentrations and various MBA contents, respectively. Apparently, a significant increase of G′ values at about 300 s in Figure 4(b) indicated that the rapid gelation process and phase separation occurred during the initial stage. Moreover, the maximum storage modulus of the hydrogels increased with the increase of the MMT/xylan weight ratios from 0.00 to 0.11. It was further proved that the MMT played an important role in improving the strength of hydrogels. Meanwhile, Figure 4(c) shows the time dependence of the storage modulus of the hydrogels with different MBA contents. Cross-linking agent induced a stable network with the polymers by covalent bonds; thus, the increment of MBA content led to the regular increase of the maximum storage modulus of the hydrogels.


### 3.4. Effect of MMT Content on Swelling Capacity

The influence of MMT/xylan weight ratio on water absorbency of the superabsorbent hydrogels is shown in Figure5. It is obvious that MMT content is an important factor influencing water absorbency of the hydrogels. Increasing MMT/xylan weight ratios from 0.00 to 0.08 caused an increment in water absorbency. The maximum water absorbency (1423 g g−1) was obtained at weight ratio of MMT/xylan (0.08). This trend was attributed to the fact that the active –OH groups of MMT could react with the –OH, –SO3H, and –COOH groups of the polymeric chains, as indicated by FT-IR spectra (Figure 2). Hence, it can relieve the entanglement of graft polymeric chains and weaken the hydrogen-bonding interaction among hydrophilic groups, which decreases the physical cross-linking degree and improves polymeric network. As a result, the water absorbency can be enhanced by introducing moderate amount of MMT. However, a further increase of MMT caused a decrease in water absorbency. This phenomenon may be attributed to the fact that the MMT can act as an additional cross-linking point in the polymeric network to decrease the elasticity of polymers. Additionally, the excess of MMT would also decrease the hydrophilicity as well as the osmotic pressure difference, resulting in shrinkage of the composite [48].Figure 5
Effect of MMT contents on water absorbency of the hydrogels.


### 3.5. Effect of MBA Content on Swelling Capacity

The amount of cross-linking agent determines the cross-linking density of the hydrogel network, which is an important swelling-control element. The effect of cross-linker (MBA) to xylan weight ratio on the swelling capacity of the superabsorbent hydrogels was investigated. As shown in Figure6, the swelling ratio rose from 585 to 864 g g−1 when the MBA/xylan weight ratio increased from 0.05 to 0.2, while it decreased with a further increase in the weight ratio. The hydrophilic polymer chains would dissolve in an aqueous environment with just a few cross-linkers. Therefore, the network cannot be formed efficiently, and the water molecules cannot be held, which results in a decrease in the water absorbency. Contrarily, the excess cross-linking concentration causes the higher cross-linking density and decreases the space of polymer three-dimensional network, and consequently, it would not be beneficial to expand the structure and hold a large quantity of water.Figure 6
Effect of MBA contents on water absorbency of the hydrogels.


### 3.6. Effect of Monomer Ratio on the Swelling Capacity

The swelling capacity of hydrogels prepared with various weight ratios of AMPS/AA is shown in Figure7. As can be seen, increasing the AMPS concentration at monomer feed composition, the swelling capacity increased. Swelling and absorption properties are attributed to the presence of hydrophilic groups, such as –OH–, CONH–, –CONH2–, and –SO3H in the network. –S
O
3
- groups associated to AMPS present better affinity than –COO− group of AA. Moreover, the nonionic groups such as CONH– can improve their salt tolerance.Figure 7
Effect of monomer ratios on water absorbency of the hydrogels.


### 3.7. Equilibrium Swelling at Various pH Values

The xylan-g-poly(AA-AMPS)/MMT, containing carboxylate, carboxamide, and sulfonate groups, are the majority of anionic-type hydrogels. Ionic superabsorbent hydrogels exhibit swelling changes for a wide range of pHs. Since the swelling capacity of all “ionic” hydrogels is strongly influenced by ionic strength, no buffer solutions are used. Hence, stock NaOH (pH 13.0) and HCl (pH 1.0) solutions were diluted with distilled water to reach desired basic and acidic pH values, respectively. These results are illustrated in Figure 8. The swelling ratios of the superabsorbent hydrogels were finely preserved around 1000 g g−1 in a wide range of pH (6.0–10.0). However, swelling capacity was significantly decreased at pH lower than 6.0 and higher than 10.0, which reached to 108 g g−1 at pH 2.0 and 148 g g−1 at pH 12.0, respectively. In acidic media, the carboxylate and sulfonate anions were protonated. Moreover, the hydrogen-bonding interactions among carboxylate and sulfonate groups were strengthened, which generated the additional physical cross-linking. At higher pH (6.0–10.0), nearly all of the –COOH and –SO3H groups were converted to –COO− and –S
O
3
-. Consequently, the hydrogen-bonding interaction was eliminated and the electrostatic repulsion among the anionic groups increased. Therefore, the polymer network tended to swell more. At pHs greater than 10, the excess Na+ cations from NaOH shielded the –COO− and –S
O
3
- groups, which prevented effective anion-anion repulsion.Figure 8
Effect of external pH on the water absorbency of the hydrogels.


### 3.8. Swelling in Salt Solutions

The characteristics of external solution such as salt concentration and charge valency greatly influence the swelling behavior of the superabsorbent hydrogels. The swelling ratios of hydrogels in aqueous solution of LiCl, CaCl2, and FeCl3 with various concentrations are shown in Figure 9. Obviously, the swelling ratio decreased with increasing the concentration of external salt solutions. This well-known undesired swelling loss is often attributed to a “charge screening effect” of the additional cations causing a nonperfect anion-anion electrostatic repulsion [49]. Therefore, the osmotic pressure generating from the mobile ion concentration difference between the gel and aqueous phases decreased and resulted in shrinkage of the network. In addition, as shown in Figure 9, the swelling ratio in multivalent cationic saline (CaCl2 and FeCl3) solution was almost close to zero at the concentration above 0.1 mol L−1, while it reached 31 g g−1 (0.1 mol L−1) and 21 g g−1 (0.25 mol L−1) in monovalent cationic solution (LiCl), which are probably due to the complexation of the carboxylate and sulfonate groups with the multivalent cations inducing the formation of the additional cross-link points at the surface of particles. Hence, the network cross-link density was enhanced, resulting in the shrinkage of the network. As a result, the water absorbency was decreased considerably (LiCl > CaCl2 > FeCl3).Figure 9
Effect of different salt solution on the water absorbency of the hydrogels.


### 3.9. Effect of MMT Content on Water Retention

The water retention ability is an important parameter for hydrogels, especially used in dry and desert regions. The water retention abilities of the hydrogels with different MMT/xylan weight ratios are shown in Figure10. From this figure, the water retention of the hydrogels was rapidly decreased within 30 s, while small changes in the water retention occurred with prolonging the time. This behavior may be explained as follows: absorbed water in the network of hygrogels can exist in three states: bound, half bond, and free water. Free water is the easiest to remove, compared with bound and half-bond water. Additionally, the water retention of the hydrogels with various MMT/xylan weight ratios of 0.00, 0.03, 0.05, 0.08, and 0.11 was 65, 69, 74, 60, and 53%, respectively, centrifuged at 2000 rpm for 360 seconds. It can be concluded that the water retention can be enhanced with the moderate amount of MMT. This may be explained by the barrier effect of polymer/MMT hydrogels [50]. The nano-dispersed MMT in the composite, acted as an additional crosslinking point, impeded the diffusion of the water molecules, and made the diffuse path for water vapor longer. However, a further increase of MMT caused a decrease in water retention, which was probably due to that it was difficult to disperse MMT in the homogeneous network solution at higher MMT content, resulted in decreasing the water retention ability.Figure 10
Effect of MMT contents on water retention of the hydrogels.


## 3.1. Synthesis and Spectral Characterization

The superabsorbent hydrogel was prepared by the graft copolymerization of acrylic acid (AA) and 2-acrylamido-2-methyl-1-propanesulfonic acid (AMPS) onto xylan in the presence of a cross-linking agent (MBA), powdery montmorillonite (MMT), and potassium persulfate (KPS) as an initiator. The persulfate initiator was decomposed under heating to produce sulfate anion radicals that abstract hydrogen atoms from the hydroxyl groups of the xylan backbones. Therefore, this redox system resulted in active centers capable of radically initiating the polymerization of AA and AMPS, leading to a graft copolymer. Since a cross-linking agent (MBA) was present in this system, the copolymer comprised a cross-linked structure. The MMT in the polymerization reaction can also be considered as a cross-linking agent [35]. The proposed mechanism for the grafting and chemically cross-linking reactions is outlined in Figure 1.Figure 1
Proposed reaction mechanism for synthesis of xylan-g-poly(AA-AMPS)/MMT superabsorbent hydrogels.Infrared spectroscopy was carried out to confirm the chemical structure of the superabsorbent hydrogel. FT-IR spectra of MMT, xylan, xylan-g-poly(AA-AMPS), and xylan-g-poly(AA-AMPS)/MMT superabsorbent hydrogel are shown in Figure 2. In the spectrum (see Figure 2(c)) of xylan, the region between 3500 cm−1 and 1800 cm−1 presents two major peaks at about 3411 cm−1 (corresponding to the absorption of stretching of the hydroxyl groups) and at 2911 cm−1 (corresponding to the C–H stretching of the CH2 groups). The absorption peak at 1600 cm−1 is related to the uronic acid carboxylate [36]. The bands at the range of 1452 and 1048 cm−1 are assigned to the C–H and C–O bond stretching frequencies. The low intensity of the peaks at 990 and 1166 cm−1 suggests the presence of arabinosyl units, which have been reported to be attached only at position 3 of the xylopyranosyl constituents [37]. A sharp band at 895 cm−1 is due to β-glycosidic linkages between the sugar units. On comparing the spectra of xylan and xylan-g-poly(AA-AMPS) (see Figure 2(d)), new characteristic absorption bands at 1651, 1558, and 1442 cm−1 are assigned to the stretching vibration of C=O, asymmetrical stretching vibration of COO−, and symmetrical stretching vibration of COO−, respectively [38]. Moreover, the characteristic absorption peaks of AMPS units are shown at 1400, 1040, and 627 cm−1, which are attributed to C–N stretching vibration of the amide, S–O stretching vibration of –SO3H, and C–S stretching vibration, respectively [39]. These bands indicated that AA and AMPS monomers were actually grafted onto the backbone of xylan.Figure 2
FT-IR of (a) xylan-g-poly(AA-AMPS)/MMT, (b) MMT, (c) xylan and (d) xylan-g-poly(AA-AMPS).In the spectrum (see Figure2(a)) of MMT, the characteristic vibration bands are shown at 3400 and 3630 cm−1, which correspond to –OH stretching band for absorbed interlayer water and –OH stretching band for Al–OH, respectively. The absorption peaks at 1631 and 1423 cm−1 are attributed to the deformation vibration of the hydroxyl groups. The characteristic peaks at 1150 and 1090 cm−1 are due to Si–O stretching (out-of plane) for MMT and Si–O stretching (in plane) vibration for layered silicates, respectively. The peaks at 915, 845, and 796 cm−1 are assigned to Al–Al–OH, Al–Mg–OH, and Si–O–Al bending vibrations, respectively [40–42]. As can be seen, compared to the spectrum of MMT (Figure 2(b)), the intensities of absorption bands at 3630 cm−1 ascribed to –OH of MMT disappeared in the spectrum of xylan-g-poly(AA-AMPS)/MMT (Figure 2(a)). In addition, the intensity of the absorption peaks due to Si–O stretching also decreased. These results indicated that MMT participated in polymerization reaction through its active –OH groups and chemically cross-linked with polymer chains. Therefore, it could be concluded that the superabsorbent hydrogel product comprised a cross-linking structure of xylan and MMT with side chains carrying carboxylate, carboxamide, and sulfate.


## 3.2. Morphological Analysis

The morphologies of the freeze-dried xylan-g-poly(AA-AMPS) and xylan-g-poly(AA-AMPS)/MMT composites are depicted in Figure 3, respectively. Obviously, the surface morphology of the xylan-g-poly(AA-AMPS)/MMT hydrogel is different from that of xylan-g-poly(AA-AMPS). It could be observed that the cross-linked xylan-g-poly(AA-AMPS) (Figure 3(a)) displayed a porous structure with many large pores. However, for hydrogel containing MMT (Figure 3(b)), the pore size became smaller and it showed a sheet-like structure with significant interconnection forming a three-dimensional network, which was beneficial for the diffusion of aqueous fluid into the superabsorbent polymer and increasing the water absorption rate [43, 44]. In addition, the degree of dispersion of clay micropowder in the polymer matrix is more important for an organic-inorganic composite [45, 46]. As can be seen from Figures 3(c) and 3(d), the microstructure of pure MMT clay was flaky (Figure 3(c)), while these clays were randomly dispersed in the polymer matrix and almost embedded within xylan-g-poly(AA-AMPS) in the composites (Figure 3(d)), and no flocculation of MMT particles could be observed. These SEM results confirmed that the MMT was finely dispersed in the composite to form a homogeneous composition.SEM images of (a) xylan-g-poly(AA-AMPS), (b) xylan-g-poly(AA-AMPS)/MMT at low magnification and (c) MMT, (d) xylan-g-poly(AA-AMPS)/MMT at high magnification.
(a)
(b)
(c)
(d)


## 3.3. Mechanical Properties of Hydrogels

The mechanical properties of the xylan-based hydrogels with different ratios of MMT to xylan have been determined. Figure4(a) presents the typical compressive modulus-strain curves of xylan-based hydrogels at room temperature. Obviously, all the samples exhibited the high compressive modulus (E), about 35–55 KPa. This indicated that the hydrogels had excellent mechanical properties. As expected, the compressive modulus of the hydrogels increased with the increment of the MMT content in the hydrogels, in the order Gel 5> Gel 4> Gel 3> Gel 2> Gel 1. The results strongly demonstrated that MMT contributed to the enhancement of the mechanical properties of the hydrogels. On the other hand, the strains of hydrogels decrease from 92% to 66%, when the MMT content was increased in the hydrogel.Compressive stress-strain curves for hydrogels with different MMT contents (a). The time dependence of storage modulus (G′) for hydrogels with different MMT contents (b) and different MBA contents (c).
(a)
(b)
(c)To monitor the gelation process, a time sweep measurement for viscoelastic properties of each sample was carried out at 25°C [47]. Figures 4(b) and 4(c) show the storage modulus (G′) of hydrogels with different MMT concentrations and various MBA contents, respectively. Apparently, a significant increase of G′ values at about 300 s in Figure 4(b) indicated that the rapid gelation process and phase separation occurred during the initial stage. Moreover, the maximum storage modulus of the hydrogels increased with the increase of the MMT/xylan weight ratios from 0.00 to 0.11. It was further proved that the MMT played an important role in improving the strength of hydrogels. Meanwhile, Figure 4(c) shows the time dependence of the storage modulus of the hydrogels with different MBA contents. Cross-linking agent induced a stable network with the polymers by covalent bonds; thus, the increment of MBA content led to the regular increase of the maximum storage modulus of the hydrogels.


## 3.4. Effect of MMT Content on Swelling Capacity

The influence of MMT/xylan weight ratio on water absorbency of the superabsorbent hydrogels is shown in Figure5. It is obvious that MMT content is an important factor influencing water absorbency of the hydrogels. Increasing MMT/xylan weight ratios from 0.00 to 0.08 caused an increment in water absorbency. The maximum water absorbency (1423 g g−1) was obtained at weight ratio of MMT/xylan (0.08). This trend was attributed to the fact that the active –OH groups of MMT could react with the –OH, –SO3H, and –COOH groups of the polymeric chains, as indicated by FT-IR spectra (Figure 2). Hence, it can relieve the entanglement of graft polymeric chains and weaken the hydrogen-bonding interaction among hydrophilic groups, which decreases the physical cross-linking degree and improves polymeric network. As a result, the water absorbency can be enhanced by introducing moderate amount of MMT. However, a further increase of MMT caused a decrease in water absorbency. This phenomenon may be attributed to the fact that the MMT can act as an additional cross-linking point in the polymeric network to decrease the elasticity of polymers. Additionally, the excess of MMT would also decrease the hydrophilicity as well as the osmotic pressure difference, resulting in shrinkage of the composite [48].Figure 5
Effect of MMT contents on water absorbency of the hydrogels.


## 3.5. Effect of MBA Content on Swelling Capacity

The amount of cross-linking agent determines the cross-linking density of the hydrogel network, which is an important swelling-control element. The effect of cross-linker (MBA) to xylan weight ratio on the swelling capacity of the superabsorbent hydrogels was investigated. As shown in Figure6, the swelling ratio rose from 585 to 864 g g−1 when the MBA/xylan weight ratio increased from 0.05 to 0.2, while it decreased with a further increase in the weight ratio. The hydrophilic polymer chains would dissolve in an aqueous environment with just a few cross-linkers. Therefore, the network cannot be formed efficiently, and the water molecules cannot be held, which results in a decrease in the water absorbency. Contrarily, the excess cross-linking concentration causes the higher cross-linking density and decreases the space of polymer three-dimensional network, and consequently, it would not be beneficial to expand the structure and hold a large quantity of water.Figure 6
Effect of MBA contents on water absorbency of the hydrogels.


## 3.6. Effect of Monomer Ratio on the Swelling Capacity

The swelling capacity of hydrogels prepared with various weight ratios of AMPS/AA is shown in Figure7. As can be seen, increasing the AMPS concentration at monomer feed composition, the swelling capacity increased. Swelling and absorption properties are attributed to the presence of hydrophilic groups, such as –OH–, CONH–, –CONH2–, and –SO3H in the network. –S
O
3
- groups associated to AMPS present better affinity than –COO− group of AA. Moreover, the nonionic groups such as CONH– can improve their salt tolerance.Figure 7
Effect of monomer ratios on water absorbency of the hydrogels.


## 3.7. Equilibrium Swelling at Various pH Values

The xylan-g-poly(AA-AMPS)/MMT, containing carboxylate, carboxamide, and sulfonate groups, are the majority of anionic-type hydrogels. Ionic superabsorbent hydrogels exhibit swelling changes for a wide range of pHs. Since the swelling capacity of all “ionic” hydrogels is strongly influenced by ionic strength, no buffer solutions are used. Hence, stock NaOH (pH 13.0) and HCl (pH 1.0) solutions were diluted with distilled water to reach desired basic and acidic pH values, respectively. These results are illustrated in Figure 8. The swelling ratios of the superabsorbent hydrogels were finely preserved around 1000 g g−1 in a wide range of pH (6.0–10.0). However, swelling capacity was significantly decreased at pH lower than 6.0 and higher than 10.0, which reached to 108 g g−1 at pH 2.0 and 148 g g−1 at pH 12.0, respectively. In acidic media, the carboxylate and sulfonate anions were protonated. Moreover, the hydrogen-bonding interactions among carboxylate and sulfonate groups were strengthened, which generated the additional physical cross-linking. At higher pH (6.0–10.0), nearly all of the –COOH and –SO3H groups were converted to –COO− and –S
O
3
-. Consequently, the hydrogen-bonding interaction was eliminated and the electrostatic repulsion among the anionic groups increased. Therefore, the polymer network tended to swell more. At pHs greater than 10, the excess Na+ cations from NaOH shielded the –COO− and –S
O
3
- groups, which prevented effective anion-anion repulsion.Figure 8
Effect of external pH on the water absorbency of the hydrogels.


## 3.8. Swelling in Salt Solutions

The characteristics of external solution such as salt concentration and charge valency greatly influence the swelling behavior of the superabsorbent hydrogels. The swelling ratios of hydrogels in aqueous solution of LiCl, CaCl2, and FeCl3 with various concentrations are shown in Figure 9. Obviously, the swelling ratio decreased with increasing the concentration of external salt solutions. This well-known undesired swelling loss is often attributed to a “charge screening effect” of the additional cations causing a nonperfect anion-anion electrostatic repulsion [49]. Therefore, the osmotic pressure generating from the mobile ion concentration difference between the gel and aqueous phases decreased and resulted in shrinkage of the network. In addition, as shown in Figure 9, the swelling ratio in multivalent cationic saline (CaCl2 and FeCl3) solution was almost close to zero at the concentration above 0.1 mol L−1, while it reached 31 g g−1 (0.1 mol L−1) and 21 g g−1 (0.25 mol L−1) in monovalent cationic solution (LiCl), which are probably due to the complexation of the carboxylate and sulfonate groups with the multivalent cations inducing the formation of the additional cross-link points at the surface of particles. Hence, the network cross-link density was enhanced, resulting in the shrinkage of the network. As a result, the water absorbency was decreased considerably (LiCl > CaCl2 > FeCl3).Figure 9
Effect of different salt solution on the water absorbency of the hydrogels.


## 3.9. Effect of MMT Content on Water Retention

The water retention ability is an important parameter for hydrogels, especially used in dry and desert regions. The water retention abilities of the hydrogels with different MMT/xylan weight ratios are shown in Figure10. From this figure, the water retention of the hydrogels was rapidly decreased within 30 s, while small changes in the water retention occurred with prolonging the time. This behavior may be explained as follows: absorbed water in the network of hygrogels can exist in three states: bound, half bond, and free water. Free water is the easiest to remove, compared with bound and half-bond water. Additionally, the water retention of the hydrogels with various MMT/xylan weight ratios of 0.00, 0.03, 0.05, 0.08, and 0.11 was 65, 69, 74, 60, and 53%, respectively, centrifuged at 2000 rpm for 360 seconds. It can be concluded that the water retention can be enhanced with the moderate amount of MMT. This may be explained by the barrier effect of polymer/MMT hydrogels [50]. The nano-dispersed MMT in the composite, acted as an additional crosslinking point, impeded the diffusion of the water molecules, and made the diffuse path for water vapor longer. However, a further increase of MMT caused a decrease in water retention, which was probably due to that it was difficult to disperse MMT in the homogeneous network solution at higher MMT content, resulted in decreasing the water retention ability.Figure 10
Effect of MMT contents on water retention of the hydrogels.


## 4. Conclusions

The superabsorbent hydrogels were prepared by the graft copolymerization of AA and AMPS onto xylan in the presence of a cross-linking agent (MBA), MMT, and KPS as an initiator. The results of FT-IR showed that the superabsorbent hydrogel products comprised cross-linking structures of xylan and MMT with side chains carrying carboxylate, carboxamide, and sulfate. SEM studies showed that a sheet-like structure with significant interconnection formed a three-dimensional network, where MMT was finely dispersed to form a homogeneous composition. All the samples exhibited the high compressive modulus (E), about 35–55 KPa. The compressive modulus of the hydrogels increased with the increment of the MMT content in the hydrogels, in the order Gel 5> Gel 4> Gel 3> Gel 2> Gel 1. The maximum equilibrium swelling ratios of hydrogels in distilled water and 0.9 wt% sodium chloride solutions were up to 1423 g g−1 and 69 g g−1, respectively. The effect of various cationic salt solutions (LiCl, CaCl2, and FeCl3) on the swelling has the following order: Li+ > Ca2+ > Fe3+. As a result, these inorganic/organic hydrogels from xylan will have wide applications in the fields of agriculture, foods, tissue engineering, and drug delivery, due to their high swelling capacity and multistimulus response properties.



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*Source: 675035-2014-02-12.xml*