Controllable Construction of Temperature-Sensitive Supramolecular Hydrogel Based on Cellulose and Cyclodextrin

In temperature sensitive hydrogels, the swelling degree or light transmittance of the gel itself changes with variations in ambient temperature, prompting its wide application in controlled drug release, tissue engineering, and material separation. Considering the amphiphilic structure of β-cyclodextrin (β-CD), a cellulose-based supramolecular hydrogel with superior temperature sensitivity was synthesized based on a combination of cellulose and β-CD as well as the host–guest interaction between β-CD and polypropylene glycol (PPG). In the one-pot tandem reaction process, chemical grafting of β-CD on cellulose and the inclusion complexation of β-CD with PPG were performed simultaneously in a NaOH/urea/water system. The obtained supramolecular hydrogel had a lower critical solution temperature (LCST) of 34 °C. There existed covalent bonding between the cellulose and β-CD, host–guest complexation between the β-CD and PPG, and hydrogen bonding and hydrophobic interactions between the components in the network structure of the supramolecular hydrogel. The combination of various covalent and non-covalent bonds endowed the resulting supramolecular hydrogel with good internal network structure stability and thermal stability, as well as sensitive temperature responsiveness within a certain range—implying its potential as a smart material in the fields of medicine, biology, and textiles. This work is expected to bring new strategies for the fabrication of cellulose-based thermosensitive materials, benefitting the high-value utilization of cellulose.


Introduction
Thermosensitive hydrogels can change their swelling rate or light transmittance in response to changing ambient temperatures. Thermosensitive hydrogels are widely used in the fields of controlled drug release, tissue engineering, material separation, and biomedical materials precisely because of the nature of this phase transition with temperature changes [1][2][3][4]. Considering their differences in temperature responsiveness, thermosensitive hydrogels are divided into two types: positive thermosensitive hydrogel and negative thermosensitive hydrogel. Above the upper critical solution temperature (UCST), positive thermosensitive hydrogels exist in a transparent or swollen state, while they transition to be opaque or shrink below the UCST. On the contrary, negative thermosensitive hydrogels are opaque or contracted above the lower critical solution temperature (LCST) and exist in a transparent or swelling state below the LCST. At present, the synthesis of thermosensitive hydrogels is mainly based on polyethylene oxide, polyvinyl alcohol, polyacrylic acid, polyacrylamide, and other compounds [5][6][7]. Among these, poly (N-isopropyl acrylamide; PNIPAM) is the most widely studied due to its LCST being close to body temperature and its sensitive temperature responsiveness. Research focusing on thermosensitive copolymers aims at regulating the critical solution temperature and endowing temperature-sensitive gels with excellent properties such as dual temperature-sensitivity and self-healing [8,9].

Materials
Bleached eucalyptus kraft pulp (BEKP) was provided by Naping Paper Co., Ltd. (Fujian, China) and the α-cellulose content was greater than 94% according to the supplier. Sodium hydroxide, urea, epichlorohydrin, and polypropylene glycol (PPG, molecular mass of 1000) were purchased by the Shanghai Aladdin Biochemical Technology Co., Ltd., (Shanghai, China). All reagents were used as received.

Preparation of a Cellulose-Based Supramolecular Hydrogel
First, 7 g of sodium hydroxide and 12 g urea were dissolved in 81 g of deionized water, and the mixture was frozen at −23 °C for 12 h. When the frozen mixture was thawed to an ice-water mixed state, 4 g of BEKP was added to the mixture and stirred thoroughly to obtain a transparent cellulose solution. A certain amount of β-cyclodextrin (β-CD) and epichlorohydrin were added to the cellulose solution. After stirring at 30 °C for 4 h, the cellulose mixed solution was frozen at −23 °C for 24 h to form a hydrogel. The hydrogel was repeatedly washed with deionized water to remove the lye and unreacted epichlorohydrin, and to obtain a β-CD grafted cellulose hydrogel (CH-g-β-CD). After impregnation with PPG, the CH-g-β-CD hydrogel was frozen at −23 °C for 12 h and then thawed at room temperature for 3 h to obtain a cellulose-based supramolecular hydrogel (CH-g-β-CD/PPG).

Materials
Bleached eucalyptus kraft pulp (BEKP) was provided by Naping Paper Co., Ltd. (Fujian, China) and the α-cellulose content was greater than 94% according to the supplier. Sodium hydroxide, urea, epichlorohydrin, and polypropylene glycol (PPG, molecular mass of 1000) were purchased by the Shanghai Aladdin Biochemical Technology Co., Ltd., (Shanghai, China). All reagents were used as received.

Preparation of a Cellulose-Based Supramolecular Hydrogel
First, 7 g of sodium hydroxide and 12 g urea were dissolved in 81 g of deionized water, and the mixture was frozen at −23 • C for 12 h. When the frozen mixture was thawed to an ice-water mixed state, 4 g of BEKP was added to the mixture and stirred thoroughly to obtain a transparent cellulose solution. A certain amount of β-cyclodextrin (β-CD) and epichlorohydrin were added to the cellulose solution. After stirring at 30 • C for 4 h, the cellulose mixed solution was frozen at −23 • C for 24 h to form a hydrogel. The hydrogel was repeatedly washed with deionized water to remove the lye and unreacted epichlorohydrin, and to obtain a β-CD grafted cellulose hydrogel (CH-g-β-CD). After impregnation with PPG, the CH-g-β-CD hydrogel was frozen at −23 • C for 12 h and then thawed at room temperature for 3 h to obtain a cellulose-based supramolecular hydrogel (CH-g-β-CD/PPG).

Characterization
After freeze-drying, the hydrogel was ground into powder and characterized by Fourier transform infrared (FTIR) and 13 C Nuclear magnetic resonance ( 13 C NMR) spectroscopy. FTIR spectra were obtained with a Nicolet 380 FTIR spectrometer (Thermo electron Instruments Co., Ltd., Waltham, MA, USA) in wavenumbers ranging from 4000 cm −1 to 400 cm −1 and a resolution of 4 cm −1 . The 13 C NMR analyses were carried out with an Polymers 2022, 14, 3801 4 of 14 AVANCE III 400 13 C NMR (Bruker Corporation, Fällanden, Switzerland) at a magic angle spinning rate of 6 kHz and a proton resonance frequency of 75.5 MHz the surface and cross section morphology of the hydrogels were analyzed with a SU8010 FESEM (Hitachi, Ltd., Tokyo, Japan) at an accelerating voltage of 5 kV. The thermal stability was characterized by a thermogravimetric analyzer (NETZSCH STA 449 F3 Jupiter ® , Hamburg, Germany) under heating from 25 • C to 600 • C at 10 • C min −1 , with a flow of N 2 as the protecting gas.

Rheology
The rheology properties of the cellulose-based hydrogels were tested using a HAAKE MARS III rheometer (Thermo Fisher Scientific, Waltham, MA, USA) with a circular shape of 2.5 mm thickness and 60 mm diameter. The supramolecular hydrogels were first subjected to a strain scan to determine the range of the linear viscoelastic behavior of the samples. Then, the strain scan parameters were set at a frequency of 1 Hz, the strain ranged from 0.01% to 100%, and the temperature was set at 25 • C in a logarithmic point pattern. The storage modulus of the supramolecular hydrogel was determined by frequency scanning under the linear viscoelastic behavior of the sample. The frequency scan parameters were set to a scan range of 0.01-10 Hz at 25 • C in logarithmic point pattern. The temperature dependence of the supramolecular hydrogels was analyzed by temperature scanning under the linear viscoelastic behavior of the samples. The temperature scan parameters were set to 1 Hz, a temperature range of 23-80 • C, and a heating rate of 2 • C min −1 in a logarithmic point pattern.

Temperature Sensitivity
The swelling properties of cellulose-based supramolecular hydrogels at different temperatures were investigated by the gravimetric method. The mass of the dried supramolecular hydrogel was recorded as W f , and it was placed in deionized water at 20-40 • C for a certain period. The samples were weighed after wiping off the residual water on the surface of the gel with filter paper, at which point the gel reached its swelling equilibrium, and the mass was recorded as W e . The equilibrium swelling rate (SR e ) of the supramolecular hydrogels was calculated according to the following equation: where W f is the dry weight of the hydrogel; W e is the weight of the hydrogel at equilibrium. The phase transition behavior of the supramolecular hydrogels was reflected by the transmittance. The UV-Vis spectrophotometer was used to test the trend of the transmission of the supramolecular hydrogels at 480 nm with temperature changes in the range of 20-40 • C. Figure 2 shows the 13 C NMR spectra of the cellulose hydrogel, β-CD, and CH-g-β-CD hydrogel. The cellulose hydrogel displayed typical signals from cellulose at 105.4 ppm, 89.1 ppm, 75.3 ppm, and 65.4 ppm-assigned to the resonance absorption of C1, C4, C2,3,5, and C6, respectively [27,28]. The chemical shifts of C2 ,3 ,5 from the β-CD were the same as those from cellulose due to their identical glucose units, whereas the resonance absorptions at C1 (103.2 ppm), C4 (81.4 ppm), and C6 (63.8 ppm) were different from those of the cellulose due to the diversity in the number of glucose units and their molecular conformation [29]. In the spectrum of the CH-g-β-CD hydrogel, the resonance absorption peaks from the cellulose and β-CD appeared at 105.4 ppm, 103.2 ppm, 89.1 ppm, 81.4 ppm, 65.4 ppm, and 63.8 ppm, while resolution loss occurred at 89.1 ppm and 65.4 ppm. This indicated that the chemical grafting between the cellulose and β-CD was realized by covalent bonding, which weakened the movement of the carbon atoms in the glucose units. ppm. This indicated that the chemical grafting between the cellulose and β-CD was realized by covalent bonding, which weakened the movement of the carbon atoms in the glucose units.

FTIR
As illustrated in Figure 3, the FTIR spectra of the CH-g-β-CD hydrogel and CH-g-β-CD/PPG hydrogel were similar to that of the cellulose, indicating that the molecular structure of the cellulose was not fundamentally damaged after chemical grafting. The strong absorption peaks near 3435 cm −1 from the CH-g-β-CD hydrogel and CH-g-β-CD/PPG hydrogel were assigned to the O-H stretching vibration absorption of hydroxyl groups, which shifted to a higher wavenumber; the peak shape also became narrower compared to that of cellulose (3350 cm −1 ). These changes suggest that the grafting reaction results in a change in the hydrogen bonding structure of cellulose and a weakening in intermolecular hydrogen bonding [30]. The peaks at 2920, 1638, and 1432 cm −1 , respectively, were attributed to the vibrations of C-H, H-O-H, and C-H in the cellulose [31]. The characteristic peaks of C-O stretching vibrations (1033 cm −1 ) and β-glycosidic bonds (898 cm −1 ) were the result of the vibrational absorption of C1 from cellulose [32]. Three peaks were observed for cellulose at 1163, 1112, and 1060 cm −1 , respectively, corresponding to the stretching vibrations of a C-C skeleton, glucose ring, and C-O attached to a hydroxyl [33]. After grafting the β-CD, the peak intensity of these three peaks decreased significantly, with a broadening at 1033 cm −1 for the CH-g-β-CD hydrogel and CH-g-β-CD/PPG hydrogel-indicating the formation of a covalent bond between the cyclodextrin and cellulose [34]. Compared with the CH-g-β-CD hydrogel, the increase in the peak intensity of the CH-g-β-

FTIR
As illustrated in Figure 3, the FTIR spectra of the CH-g-β-CD hydrogel and CH-gβ-CD/PPG hydrogel were similar to that of the cellulose, indicating that the molecular structure of the cellulose was not fundamentally damaged after chemical grafting. The strong absorption peaks near 3435 cm −1 from the CH-g-β-CD hydrogel and CHg-β-CD/PPG hydrogel were assigned to the O-H stretching vibration absorption of hydroxyl groups, which shifted to a higher wavenumber; the peak shape also became narrower compared to that of cellulose (3350 cm −1 ). These changes suggest that the grafting reaction results in a change in the hydrogen bonding structure of cellulose and a weakening in intermolecular hydrogen bonding [30]. The peaks at 2920, 1638, and 1432 cm −1 , respectively, were attributed to the vibrations of C-H, H-O-H, and C-H in the cellulose [31]. The characteristic peaks of C-O stretching vibrations (1033 cm −1 ) and β-glycosidic bonds (898 cm −1 ) were the result of the vibrational absorption of C1 from cellulose [32]. Three peaks were observed for cellulose at 1163, 1112, and 1060 cm −1 , respectively, corresponding to the stretching vibrations of a C-C skeleton, glucose ring, and C-O attached to a hydroxyl [33]. After grafting the β-CD, the peak intensity of these three peaks decreased significantly, with a broadening at 1033 cm −1 for the CH-g-β-CD hydrogel and CH-g-β-CD/PPG hydrogel-indicating the formation of a covalent bond between the cyclodextrin and cellulose [34]. Compared with the CH-gβ-CD hydrogel, the increase in the peak intensity of the CH-g-β-CD/PPG hydrogel at 1033 and 898 cm −1 was mainly caused by C-O stretching vibrations from cyclodextrin- inclusive PPG chains, which confirmed the existence of the host-guest interaction between the β-CD and PPG in the supramolecular hydrogels [35].
Polymers 2022, 14, x FOR PEER REVIEW 6 of 14 CD/PPG hydrogel at 1033 and 898 cm −1 was mainly caused by C-O stretching vibrations from cyclodextrin-inclusive PPG chains, which confirmed the existence of the host-guest interaction between the β-CD and PPG in the supramolecular hydrogels [35].

Morphology
The cross-section morphology of the CH-g-β-CD hydrogel and CH-g-β-CD/PPG hydrogel were compared using the SEM images seen in Figure 4. It can be seen that both of them showed a developed pore structure and a connected network-like internal structure. After the inclusion of the PPG, the cellulose molecular chains and PPG chains in the network structure of the CH-g-β-CD/PPG hydrogel were tightly entangled together and formed relatively regular pore sizes (Figure 4c,d), which confirmed the orderly aggregation and good blending compatibility between cellulose and PPG. Cyclodextrin-inclusive PPG chains aggregated with each other and formed microcrystalline regions in the CH-gβ-CD/PPG hydrogel through hydrogen bonding between β-CD molecules. These microcrystalline regions served as physical cross-linking points to form a three-dimensional network structure with the uncoated PPG and cellulose molecular chains [36]. There existed hydrogen bonding and hydrophobic interactions among the β-CD, PPG, and cellulose in the network structure of the CH-g-β-CD/PPG hydrogel. These non-covalent interactions strengthened the compatibility of the components in the supramolecular hydrogel, resulting in a dense network structure.

Morphology
The cross-section morphology of the CH-g-β-CD hydrogel and CH-g-β-CD/PPG hydrogel were compared using the SEM images seen in Figure 4. It can be seen that both of them showed a developed pore structure and a connected network-like internal structure. After the inclusion of the PPG, the cellulose molecular chains and PPG chains in the network structure of the CH-g-β-CD/PPG hydrogel were tightly entangled together and formed relatively regular pore sizes (Figure 4c,d), which confirmed the orderly aggregation and good blending compatibility between cellulose and PPG. Cyclodextrin-inclusive PPG chains aggregated with each other and formed microcrystalline regions in the CH-g-β-CD/PPG hydrogel through hydrogen bonding between β-CD molecules. These microcrystalline regions served as physical cross-linking points to form a three-dimensional network structure with the uncoated PPG and cellulose molecular chains [36]. There existed hydrogen bonding and hydrophobic interactions among the β-CD, PPG, and cellulose in the network structure of the CH-g-β-CD/PPG hydrogel. These non-covalent interactions strengthened the compatibility of the components in the supramolecular hydrogel, resulting in a dense network structure. CD/PPG hydrogel at 1033 and 898 cm −1 was mainly caused by C-O stretching vibrations from cyclodextrin-inclusive PPG chains, which confirmed the existence of the host-guest interaction between the β-CD and PPG in the supramolecular hydrogels [35].

Morphology
The cross-section morphology of the CH-g-β-CD hydrogel and CH-g-β-CD/PPG hydrogel were compared using the SEM images seen in Figure 4. It can be seen that both of them showed a developed pore structure and a connected network-like internal structure. After the inclusion of the PPG, the cellulose molecular chains and PPG chains in the network structure of the CH-g-β-CD/PPG hydrogel were tightly entangled together and formed relatively regular pore sizes (Figure 4c,d), which confirmed the orderly aggregation and good blending compatibility between cellulose and PPG. Cyclodextrin-inclusive PPG chains aggregated with each other and formed microcrystalline regions in the CH-gβ-CD/PPG hydrogel through hydrogen bonding between β-CD molecules. These microcrystalline regions served as physical cross-linking points to form a three-dimensional network structure with the uncoated PPG and cellulose molecular chains [36]. There existed hydrogen bonding and hydrophobic interactions among the β-CD, PPG, and cellulose in the network structure of the CH-g-β-CD/PPG hydrogel. These non-covalent interactions strengthened the compatibility of the components in the supramolecular hydrogel, resulting in a dense network structure.

Rheological Analysis
When the strain amplitude was less than 1%, the storage modulus curves of the hydrogels with different β-CD contents remained horizontal (Figure 5a), which suggested that the G′ was independent of the strain and that the hydrogels exhibited linear behavior. When the strain amplitude was higher than 1%, the storage modulus gradually decreased as the strain amplitude increased, and the samples exhibited non-linear behavior. Therefore, the strain amplitude should be set at 1% during the frequency scan test. As shown in Figure 5b, the storage modulus curves of the hydrogels with different β-CD contents remained flat with increasing frequencies, indicating that the CH-g-β-CD hydrogel had a certain structural stability-maintained by the hydrogen bonding between the cellulose molecular chains and the mechanical forces caused by the intertwining of the molecular chains. As the levels of β-CD increased, the storage modulus declined from 1050 Pa to 650 Pa, because the addition of β-CD destroyed the hydrogen bonds and mechanical forces of the cellulose. Moreover, β-CD is difficult to form a gel with high strength with due to its cyclic oligosaccharide and cavity structure. Hence, the presence of β-CD weakened the stability of the three-dimensional network structure of the cellulose-based hydrogel, which demonstrated that cellulose played a supporting role in maintaining its mechanical strength as the backbone of the hydrogel. Figure 5c,d showed the loss modulus (G″) and the phase angle (tanδ) versus the scanning frequency for the CH-g-β-CD hydrogels with different β-CD contents. Independent of the β-CD content and frequency, the loss modulus was far less than the storage modulus (i.e., G′ > G″), and the tanδ was always below 1-suggesting that the elastic behavior of the hydrogel was maintained and that the internal network structure was not destroyed. The Tanδ increased gradually with increases in the β-CD content, which confirmed that the presence of β-CD resulted in the reduced stability of the hydrogel network.

Rheological Analysis
When the strain amplitude was less than 1%, the storage modulus curves of the hydrogels with different β-CD contents remained horizontal (Figure 5a), which suggested that the G was independent of the strain and that the hydrogels exhibited linear behavior. When the strain amplitude was higher than 1%, the storage modulus gradually decreased as the strain amplitude increased, and the samples exhibited non-linear behavior. Therefore, the strain amplitude should be set at 1% during the frequency scan test. As shown in Figure 5b, the storage modulus curves of the hydrogels with different β-CD contents remained flat with increasing frequencies, indicating that the CH-g-β-CD hydrogel had a certain structural stability-maintained by the hydrogen bonding between the cellulose molecular chains and the mechanical forces caused by the intertwining of the molecular chains. As the levels of β-CD increased, the storage modulus declined from 1050 Pa to 650 Pa, because the addition of β-CD destroyed the hydrogen bonds and mechanical forces of the cellulose. Moreover, β-CD is difficult to form a gel with high strength with due to its cyclic oligosaccharide and cavity structure. Hence, the presence of β-CD weakened the stability of the three-dimensional network structure of the cellulose-based hydrogel, which demonstrated that cellulose played a supporting role in maintaining its mechanical strength as the backbone of the hydrogel. Figure 5c,d showed the loss modulus (G") and the phase angle (tanδ) versus the scanning frequency for the CH-g-β-CD hydrogels with different β-CD contents. Independent of the β-CD content and frequency, the loss modulus was far less than the storage modulus (i.e., G > G"), and the tanδ was always below 1-suggesting that the elastic behavior of the hydrogel was maintained and that the internal network structure was not destroyed. The Tanδ increased gradually with increases in the β-CD content, which confirmed that the presence of β-CD resulted in the reduced stability of the hydrogel network.
The relationship between the storage modulus and strain amplitude of the CH-gβ-CD/PPG hydrogels with different PPG contents is shown in Figure 7a. All storage modulus curves in Figure 7a remained horizontal and showed strain-independent linear behavior when the strain amplitude was less than 1%, whereas non-linear behavior was exhibited with gradually decreases in G' as the strain increased further. Consequently, the strain amplitude should be set at 1% during the frequency and temperature scan tests. As illustrated in Figure 7b, the G of the CH-g-β-CD/PPG hydrogel was improved from 2500 Pa to 6000 Pa with increases in the PPG content. Compared with the cellulose hydrogel and CH-g-β-CD hydrogel (Figure 5), the G of the CH-g-β-CD/PPG hydrogel increased strikingly, which indicated that a more stable three-dimensional network structure was formed in the wake of the enhancement of hydrogen bonding and hydrophobic interactions formed by cyclodextrin-PPG inclusion complexes. The cavity of the β-CD was occupied by the water in the aqueous medium via weak polar-nonpolar interactions, while PPG was substituted into the cavity in the presence of PPG and formed a host-guest complexation. After the water molecules in the cavity were released, the β-CD recombined with the solvated water molecules around the PPG. Desolvation of the PPG and recombination of the solvent molecules contributed to the formation of cyclodextrin-PPG inclusion complexes. As the frequency increased, the storage modulus curves with different PPG contents remained flat-which revealed the good stability of the structure of the supramolecular hydrogel, owing to its intermolecular interactions and the support of the cellulose for the gel network. Like Figure 5b,c, the G" was far less than the G (Figure 7c) and the tanδ was always below 1 (Figure 7d), resulting in the elastic behavior of the CH-g-β-CD/PPG hydrogel. The increasing tanδ demonstrated that the increase in PPG content was conducive to strengthening the stability of the hydrogel network. mained flat with increasing frequencies, indicating that the CH-g-β-CD hydrogel had a certain structural stability-maintained by the hydrogen bonding between the cellulose molecular chains and the mechanical forces caused by the intertwining of the molecular chains. As the levels of β-CD increased, the storage modulus declined from 1050 Pa to 650 Pa, because the addition of β-CD destroyed the hydrogen bonds and mechanical forces of the cellulose. Moreover, β-CD is difficult to form a gel with high strength with due to its cyclic oligosaccharide and cavity structure. Hence, the presence of β-CD weakened the stability of the three-dimensional network structure of the cellulose-based hydrogel, which demonstrated that cellulose played a supporting role in maintaining its mechanical strength as the backbone of the hydrogel. Figure 5c,d showed the loss modulus (G″) and the phase angle (tanδ) versus the scanning frequency for the CH-g-β-CD hydrogels with different β-CD contents. Independent of the β-CD content and frequency, the loss modulus was far less than the storage modulus (i.e., G′ > G″), and the tanδ was always below 1-suggesting that the elastic behavior of the hydrogel was maintained and that the internal network structure was not destroyed. The Tanδ increased gradually with increases in the β-CD content, which confirmed that the presence of β-CD resulted in the reduced stability of the hydrogel network. The relationship between the storage modulus and strain amplitude of the CH-g-β-CD/PPG hydrogels with different PPG contents is shown in Figure 6a. All storage modulus curves in Figure 6a remained horizontal and showed strain-independent linear behavior when the strain amplitude was less than 1%, whereas non-linear behavior was exhibited with gradually decreases in G' as the strain increased further. Consequently, the strain amplitude should be set at 1% during the frequency and temperature scan tests. As illustrated in Figure 6b, the G′ of the CH-g-β-CD/PPG hydrogel was improved from 2500 Pa to 6000 Pa with increases in the PPG content. Compared with the cellulose hydrogel and CH-g-β-CD hydrogel (Figure 5), the G′ of the CH-g-β-CD/PPG hydrogel increased strikingly, which indicated that a more stable three-dimensional network structure was formed in the wake of the enhancement of hydrogen bonding and hydrophobic interactions formed by cyclodextrin-PPG inclusion complexes. The cavity of the β-CD was occupied by the water in the aqueous medium via weak polar-nonpolar interactions, while PPG was substituted into the cavity in the presence of PPG and formed a host-guest complexation. After the water molecules in the cavity were released, the β-CD recombined with the solvated water molecules around the PPG. Desolvation of the PPG and recombination of the solvent molecules contributed to the formation of cyclodextrin-PPG inclusion complexes. As the frequency increased, the storage modulus curves with different PPG contents remained flat-which revealed the good stability of the structure of the su- The relationship between the storage modulus and strain amplitude of the CH-g-β-CD/PPG hydrogels with different PPG contents is shown in Figure 6a. All storage modulus curves in Figure 6a remained horizontal and showed strain-independent linear behavior when the strain amplitude was less than 1%, whereas non-linear behavior was exhibited with gradually decreases in G' as the strain increased further. Consequently, the strain amplitude should be set at 1% during the frequency and temperature scan tests. As illustrated in Figure 6b, the G′ of the CH-g-β-CD/PPG hydrogel was improved from 2500 Pa to 6000 Pa with increases in the PPG content. Compared with the cellulose hydrogel and CH-g-β-CD hydrogel (Figure 5), the G′ of the CH-g-β-CD/PPG hydrogel increased strikingly, which indicated that a more stable three-dimensional network structure was formed in the wake of the enhancement of hydrogen bonding and hydrophobic interactions formed by cyclodextrin-PPG inclusion complexes. The cavity of the β-CD was occupied by the water in the aqueous medium via weak polar-nonpolar interactions, while PPG was substituted into the cavity in the presence of PPG and formed a host-guest complexation. After the water molecules in the cavity were released, the β-CD recombined with the solvated water molecules around the PPG. Desolvation of the PPG and recombination of the solvent molecules contributed to the formation of cyclodextrin-PPG inclusion complexes. As the frequency increased, the storage modulus curves with different PPG contents remained flat-which revealed the good stability of the structure of the supramolecular hydrogel, owing to its intermolecular interactions and the support of the cellulose for the gel network. Like Figure 5b,c, the G″ was far less than the G′ (Figure 6c) and the tanδ was always below 1 (Figure 6d), resulting in the elastic behavior of the CHg-β-CD/PPG hydrogel. The increasing tanδ demonstrated that the increase in PPG content was conducive to strengthening the stability of the hydrogel network. The influence of temperature on the G′, G″, and tanδ for the CH-g-β-CD/PPG hydrogels with different PPG contents is shown in Figure 7. The elastic behavior of the supramolecular hydrogel was manifested in that the G″ was far less than the G′ and the tanδ was below 1. As the temperature increased, the curves tended to be horizontal, and the structure of hydrogel network retained excellent stability without drastic changes. The reason for this phenomenon may be that the thermal motion exacerbated by increasing temperatures was restricted in the wake of the hydrogen bonding in the cyclodextrin-PPG inclusion complexes and mechanical forces in the intertwining cellulose.  The influence of temperature on the G , G", and tanδ for the CH-g-β-CD/PPG hydrogels with different PPG contents is shown in Figure 8. The elastic behavior of the supramolecular hydrogel was manifested in that the G" was far less than the G and the tanδ was below 1. As the temperature increased, the curves tended to be horizontal, and the structure of hydrogel network retained excellent stability without drastic changes. The reason for this phenomenon may be that the thermal motion exacerbated by increasing temperatures was restricted in the wake of the hydrogen bonding in the cyclodextrin-PPG inclusion complexes and mechanical forces in the intertwining cellulose. The influence of temperature on the G′, G″, and tanδ for the CH-g-β-CD/PPG hydrogels with different PPG contents is shown in Figure 7. The elastic behavior of the supramolecular hydrogel was manifested in that the G″ was far less than the G′ and the tanδ was below 1. As the temperature increased, the curves tended to be horizontal, and the structure of hydrogel network retained excellent stability without drastic changes. The reason for this phenomenon may be that the thermal motion exacerbated by increasing temperatures was restricted in the wake of the hydrogen bonding in the cyclodextrin-PPG inclusion complexes and mechanical forces in the intertwining cellulose.

TGA
It can be seen from Table 1 that the onset temperature of thermal decomposition and the temperature at the maximum weight loss rate (T max ) were 326 • C and 354.7 • C for the cellulose, respectively. Compared with the cellulose, the thermal stability of the CH-g-β-CD hydrogel receded, with a lower onset temperature and T max ; this can be attributed to the destruction of the crystalline region of the cellulose after grafting the β-CD and the weaker ether bonds formed between components other than the cellulose [37,38]. The T max of the CH-g-β-CD hydrogel was 328.4 • C, falling in between the cellulose (354.7 • C) and β-CD (316.5 • C). The fact that there was only one thermal decomposition peak for the CH-g-β-CD hydrogel (Figure 9b) is further evidence of covalent bonding between the cellulose and β-CD-as opposed to a physical mixture, where two peaks from the cellulose and β-CD occur simultaneously [39]. The DTG curves showed that β-CD had two thermal decomposition peaks and the peak at 86.5 • C was assigned to the dehydration of the β-CD, while the CH-g-β-CD hydrogel and CH-g-β-CD/PPG hydrogel had no obvious peaks below 200 • C, which revealed the diminished hydration of the β-CD after the grafting and inclusion. There was only one thermal decomposition peak for the CH-g-β-CD/PPG hydrogel, with a T max of 332.8 • C, falling in between the CH-g-β-CD hydrogel (328.4 • C) and PPG (375 • C)-which confirmed the host-guest interactions between the β-CD and PPG in the supramolecular hydrogel [40]. The thermal stability of the CH-g-β-CD/PPG hydrogel was stronger than that of the CH-g-β-CD hydrogel, mainly due to the hydrophobic interactions and hydrogen bonding between the β-CD and inclusive PPG and the aggregation of the PPG chains-resulting in a denser network structure in the supramolecular hydrogel.

TGA
It can be seen from Table 1 that the onset temperature of thermal decomposition and the temperature at the maximum weight loss rate (Tmax) were 326 °C and 354.7 °C for the cellulose, respectively. Compared with the cellulose, the thermal stability of the CH-g-β-CD hydrogel receded, with a lower onset temperature and Tmax; this can be attributed to the destruction of the crystalline region of the cellulose after grafting the β-CD and the weaker ether bonds formed between components other than the cellulose [37,38]. The Tmax of the CH-g-β-CD hydrogel was 328.4 °C, falling in between the cellulose (354.7 °C) and β-CD (316.5 °C). The fact that there was only one thermal decomposition peak for the CHg-β-CD hydrogel (Figure 8b) is further evidence of covalent bonding between the cellulose and β-CD-as opposed to a physical mixture, where two peaks from the cellulose and β-CD occur simultaneously [39]. The DTG curves showed that β-CD had two thermal decomposition peaks and the peak at 86.5 °C was assigned to the dehydration of the β-CD, while the CH-g-β-CD hydrogel and CH-g-β-CD/PPG hydrogel had no obvious peaks below 200 °C, which revealed the diminished hydration of the β-CD after the grafting and inclusion. There was only one thermal decomposition peak for the CH-g-β-CD/PPG hydrogel, with a Tmax of 332.8 °C, falling in between the CH-g-β-CD hydrogel (328.4 °C) and PPG (375 °C)-which confirmed the host-guest interactions between the β-CD and PPG in the supramolecular hydrogel [40]. The thermal stability of the CH-g-β-CD/PPG hydrogel was stronger than that of the CH-g-β-CD hydrogel, mainly due to the hydrophobic interactions and hydrogen bonding between the β-CD and inclusive PPG and the aggregation of the PPG chains-resulting in a denser network structure in the supramolecular hydrogel.  Figure 8. TG-curves (a) and DTG-curves (b) of the cellulose, β-CD, CH-g-β-CD, and CH-g-β-CD/PPG hydrogel. Figure 9. TG-curves (a) and DTG-curves (b) of the cellulose, β-CD, CH-g-β-CD, and CH-gβ-CD/PPG hydrogel.

Thermosensitivity
In Figure 10, the equilibrium swelling rate of the CH-g-β-CD/PPG hydrogel tended to decline as the temperature rose, indicating that the resulting supramolecular hydrogel was a negative thermosensitive hydrogel with an LCST of about 34 • C. During the swelling process, water molecules penetrated into the interior of the hydrogel network via intermolecular hydrogen bonds with hydroxyl, causing the interactions between different components to weaken and the hydrogel network to expand in volume. When the hydrogel network expanded and extended, the network structure was subjected to stress and elastic retraction, and the swelling rate of the hydrogel reached equilibrium when these two opposing forces formed a balance [41]. At temperatures below the LCST, the network structure of the supramolecular hydrogel became looser with a high-equilibrium swelling rate due to the penetration of water molecules [42]. On the other hand, when the temperature exceeded the LCST, the hydrogen bonds between the water molecules and the β-CD was broken, the hydrophobic interactions between the β-CD and PPG were further enhanced, and the aggregation of the PPG chains was aggravated. These changes led to the contraction of the hydrogel network and the sharp decline in the equilibrium swelling rate [43].

Thermosensitivity
In Figure 9, the equilibrium swelling rate of the CH-g-β-CD/PPG hy decline as the temperature rose, indicating that the resulting supramo was a negative thermosensitive hydrogel with an LCST of about 34 °C. D ing process, water molecules penetrated into the interior of the hydroge termolecular hydrogen bonds with hydroxyl, causing the interactions b components to weaken and the hydrogel network to expand in volume. gel network expanded and extended, the network structure was subjec elastic retraction, and the swelling rate of the hydrogel reached equilib two opposing forces formed a balance [41]. At temperatures below the LC structure of the supramolecular hydrogel became looser with a high-equ rate due to the penetration of water molecules [42]. On the other hand, w ature exceeded the LCST, the hydrogen bonds between the water molecu was broken, the hydrophobic interactions between the β-CD and PPG hanced, and the aggregation of the PPG chains was aggravated. These c contraction of the hydrogel network and the sharp decline in the equilibri [43].  Figure 10 illustrates that as the temperature increased, the transmit g-β-CD/PPG hydrogel decreased and a transparent opaque phase transiti an LCST of about 34 °C, which was consistent with the results shown in F in temperature affected the hydrophobic interactions and hydrogen bond molecular hydrogel network and the aggregation of the molecular chai volume and transmission of the hydrogel. At temperatures below the LC bonding between the water molecules and other components, as well as tization of the PPG, resulted in a loose network structure and high trans trast, when the temperature exceeded the LCST, the enhancement of th  Figure 11 illustrates that as the temperature increased, the transmittance of the CHg-β-CD/PPG hydrogel decreased and a transparent opaque phase transition occurred with an LCST of about 34 • C, which was consistent with the results shown in Figure 10. Changes in temperature affected the hydrophobic interactions and hydrogen bonding in the supramolecular hydrogel network and the aggregation of the molecular chains, as well as the volume and transmission of the hydrogel. At temperatures below the LCST, the hydrogen bonding between the water molecules and other components, as well as the good solventization of the PPG, resulted in a loose network structure and high transmittance. In contrast, when the temperature exceeded the LCST, the enhancement of the bonding forces between the various components in the supramolecular hydrogel led to the contraction of the gel, the denseness of the network structure, and a decrease in transmittance. rs 2022, 14, x FOR PEER REVIEW Figure 10. The optical transmittance of the CH-g-β-CD/PPG hydrogel ture.

Conclusions
The homogeneous grafting of the β-CD on the cellulose m clusion complexation of the β-CD with the PPG were conduc alkaline conditions. Based on the unique amphiphilic structur lose-based supramolecular hydrogel with thermosensitivity w guest complexation and hydrogen bonding. The resulting hyd mosensitive hydrogel with an LCST of 34 °C. When the tempe the equilibrium swelling rate and light transmittance of the sup creased sharply, implying a sensitive temperature responsive amphiphilic structure of the β-CD in the supramolecular hydro for its temperature sensitivity. A dense hydrogel network stru pores was formed by the interactions between cellulose, β-CD bonding and non-covalent bonding between the components c of its three-dimensional network structure and thermal stabilit ture of 294.2 °C. This CH-g-β-CD/PPG supramolecular hydrog ture sensitivity, good thermal stability, and structural stability, plication value in smart materials, drug delivery, tissue engine

Conclusions
The homogeneous grafting of the β-CD on the cellulose molecular chain and the inclusion complexation of the β-CD with the PPG were conducted synchronously under alkaline conditions. Based on the unique amphiphilic structure of cyclodextrin, a cellulosebased supramolecular hydrogel with thermosensitivity was constructed via host-guest complexation and hydrogen bonding. The resulting hydrogel was a negative thermosensitive hydrogel with an LCST of 34 • C. When the temperature exceeded the LCST, the equilibrium swelling rate and light transmittance of the supramolecular hydrogels decreased sharply, implying a sensitive temperature responsiveness. The presence of the amphiphilic structure of the β-CD in the supramolecular hydrogel was an essential reason for its temperature sensitivity. A dense hydrogel network structure with well-developed pores was formed by the interactions between cellulose, β-CD, and PPG. The covalent bonding and non-covalent bonding between the components contributed to the stability of its three-dimensional network structure and thermal stability, with an onset temperature of 294.2 • C. This CH-g-β-CD/PPG supramolecular hydrogel, with superior temperature sensitivity, good thermal stability, and structural stability, has a certain potential application value in smart materials, drug delivery, tissue engineering, and textiles.