- freely available
Polymers 2012, 4(3), 1517-1534; doi:10.3390/polym4031517
Abstract: Different hydrogels were prepared starting from natural or semi-synthetic polysaccharides (carboxymethylcellulose, hyaluronic acid and chitosan) which were cross-linked by the addition of a cross-linking agent chosen according to the chemical groups present along the polymer chains. The cross-linking reaction allows for the formation of a three-dimensional network made of covalent bonds between the polymer chains, which is stable under physiological conditions. The presence of a substantial amount of water within the polysaccharide matrices makes such systems unique among hydrophilic gels. Water itself is responsible for some of their peculiar characteristics, one of which is their injectability which makes these hydrogels suitable for using as matrices for mini-invasive surgery and localized therapy.
The use of natural polymers, or biopolymers, as materials is not new. For instance, in nature, cellulose has always been used to provide structure for plants, chitin as the exoskeleton of crawfish and shrimps, collagen for mechanical support in connective tissues, and silk in spider’s webs. At present, these types of materials are the subject of much interest as materials for biomedical applications due to their high biocompatibility and low disposal costs [1,2]. Furthermore, the versatility of their chemical structures allows for the development of advanced functionalized materials that can meet a variety of requirements. In the biomedical field, the degradation of natural polymers into physiological metabolites makes them excellent candidates for a wide range of applications, such as drug delivery or regenerative medicine. Among the biopolymers, polysaccharides in particular have some excellent properties which make them the polymer group with the longest-standing and widest-ranging experience in terms of medical applications [3,4]: Non-toxicity (monomer residues are likewise not hazardous to health); water solubility or high capacity for swelling induced by simple chemical modifications and a wide variety of chemical structures [5,6,7]. Hyaluronic acid, carboxymethylcellose and chitosan were chosen as starting polysaccharides for the preparation of biocompatible hydrogels for biomediacal applications. Hyaluronan (Hyal) is a high molecular weight glycosaminoglycan composed of disaccharide repeating units of N-acetylglucosamine and glucuronic acid linked together through alternating beta-1,4 and beta-1,3 glycosidic bonds. In the human body, Hyal occurs in the salt form, hyaluronate, and is found in high concentrations in several soft connective tissues, including skin, umbilical cord, synovial fluid, and vitreous humor [8,9,10]. Sodium carboxymethylcellulose (CMC-Na) is synthesized by swelling cellulose with sodium hydroxide and alkali-catalyzed reaction of cellulose with chloroacetic acid. Over the years, CMC has been utilized as the sole material or in combination with drugs and co-excipients in wound dressing for the treatment of partial thickness wounds, deep diabetic foot ulcers, pressure sores, surgical wounds, toxic epidermal necrolysis, and as a dermal filler [11,12]. Chitosan, a cationic group-containing polysaccharide, is obtained by means of deacetylation of chitin extracted from the external skeleton (shell) of marine crustaceans. Coming from a natural, renewable, nontoxic and biodegradable source, it is justifiably viewed as an ‘ecologically-friendly’ product [13,14]. Its quality and properties depend on its purity, degree of deacetylation (ranging between 70% and 95%), molecular weight and crystallinity . Among its applications, mention should be made of chitosan’s use as a hypocholesteremic and bacteriostatic agent, as a drug carrier or as a scaffold for cell cultures [16,17].
Among hydrogels, injectable hydrogels have been attracting much interest in biomedical fields, especially for minimally-invasive surgery with the aim of avoiding the complications that may occur during traditional surgeries. There are several methods for obtaining in situ formation of a hydrogel starting from an injectable polymer solution, but all of these share the limitation of lack of control over the characteristics and stoichiometry of the hydrogels thus formed. Moreover, all the precursors added to the polymer solution remain in the injection site and may cause uncontrolled side reactions or local toxicity [18,19]. Our polysaccharide-based hydrogels can be considered “injectable hydrogels” thanks to their property to be squeezed through the needle of a syringe. Their injectability comes out from the fact that they show a thixotropic nature [20,21]. Hyal, CMC and CHT hydrogels, once pre-synthesized can be extensively purified in order to remove all impurities and fully characterized. They can be easily squeezed through a syringe needle, offering the advantage of opening up new perspectives in minimally-invasive surgery by using a pre-formed safe material with well known chemical and mechanical properties . Localized treatment with the hydrogel improved the healing of cartilage lesions without inducing inflammatory effects [22,23].
Water is the main component of these polysaccharide-based hydrogels (more than 90% of their weight when in their swollen state). Generally, water inside hydrogel matrices can be classified as one of three types: the water in the outermost layer is called free water, and can be easily removed under temperate conditions as it is physically entrapped within the polymer network. Free interstitial water does not take part in hydrogen bonds with polymer molecules. Its transition temperature, enthalpy and DSC curves are similar to those of pure water. The second type is bound water, which is directly bound to the polymer chain through hydrophilic groups or via hydrogen bonds. It is an integral part of the hydrogel structure and cannot easily separated from the hydrogel. The last type is semi-bound water, with intermediate properties between those of bound and free water . This paper deals with the physico-chemical characterization of the polysaccharide based hydrogels, focused to understand the role of water molecules in affecting the structure and the properties of the material in terms of swelling degree, rheological properties and infrared analysis either in the native state or after a mechanical stress.
2. Results and Discussion
2.1. Hydrogel Synthesis
Hydrogel synthesis follows the same chemical route that has been well-documented in carbodiimide chemistry [7,25]. Basically, the synthesis of CMC- and Hyal-based hydrogels exploits the formation of an amide bond between the carboxylate groups of the polymer chains and the primary amine groups of 1,3 diaminopropane (DAP), which is added to the polymer aqueous solution as the cross-linking agent of the polymer chain. 1-ethyl-3-[3-(dimethyl-amino)propyl] carbodiimide hydrochloride (EDC) works as the activating agent of the carboxylic groups, and N-hydroxysuccinimide (NHS) as the proton exchanger . The reaction schemes of CMC and Hyal hydrogel are shown in Figure 1a,b. The stoichiometry of the reaction can be tuned in order to form hydrogels with different degrees of cross-linking, taking into consideration the number of carboxylic groups in each polysaccharide, i.e., one carboxylic group per disaccharide unit in Hyal and two in CMC polymer. On the other hand, CHT synthesis (see Figure 1c) involves the formation of an amide bond between the amine groups of the polymer and the carboxylic groups of the cross-linking agent, i.e., adipic acid (AA) . The determination of the degree of cross-linking (defined as the number of polymer groups bound to the cross-linker) is obtained by pontentiometric titration of the free protonable groups remaining after hydrogel formation (carboxylate groups for CMC, Hyal or amine groups for CHT polymer), or by means of 13C nuclear magnetic resonance . Indeed, even if the molar ratio of polymer, EDC and DAP used for the synthesis of hydrogels, should allow the formation of a hydrogel cross-linked at 100%, the cross-linking degree of CMC, Hyal and CHT hydrogels was 79%, 45% and 44% respectively as determined by potentiometric titrations.
2.2. Rheological Characterization and Swelling Degree
In order to obtain information about the mechanical properties of the polymer network we subjected the hydrogel to a shear stress applied by a rheometer. The typical trend of G’ and G” vs. oscillation stress for these polysaccharide hydrogels is plotted in Figure 2. For low values of oscillation stress, the storage modulus (G’) is higher than the viscous one (G”) indicating the gel-like nature of the material. Above the cross-point (i.e., the oscillation stress at which G’ and G’’ assume the same value), the viscous modulus is higher than the storage modulus, which is characteristic of a liquid. This implies a sol-gel transition of the material . The behavior of G’ and G” was studied by increasing and decreasing the applied stress cyclically on the same hydrogel sample. When the oscillation stress is decreased (step 2 Figure 2), G’ and G’’ show always lower values than those found during the increase in oscillation stress (step 1 Figure 2). At the end of step 2, the G’ and G” values are lower than those of the native hydrogel at the first step. By repeating the same sequence of steps several times (that is, increasing and decreasing the oscillation stress on the same sample, step 3 and step 4 Figure 2), G’ and G” values follow the same trend and maintain the same values as those determined in step 2. This result indicates a sort of “recovery” effect of the G’ and G” values once the material is subjected to further cycles of stresses [7,26]. In the case of squeezed hydrogels (Figure 3(a–c)), both the storage modulus G’ and the loss modulus G’’ values are reduced due to the passage from the syringe with respect to those of the native hydrogels (Table 1). However, by repeating the same cycle of stress several times on the squeezed hydrogels, as done for the native ones (see Figure 2), G’ and G” values remain the same. This does not occur for a native hydrogel (see step 1 and step 2 Figure 2). The squeezing process induces the same effect on the hydrogel as the stress applied by the rheometer. The lower values of G’ and G” of a squeezed hydrogel with respect to its native sample indicate that the hydrogel network is softened by the application of a shear stress such as squeezing through a syringe or by the stress applied by a rheometer. However, the application of an additional stress does not lead to further alterations of the hydrogel’s mechanical properties. Hence, the squeezed hydrogels behave in the same manner as native hydrogels after the application of a stress applied by a rheometer.
|Hydrogel type||Status||G’ (Pa)||G” (Pa)|
|CMC||Native||550 ± 30||25 ± 1|
|Squeezed||240 ± 20||20 ± 2|
|HYAL||Native||970 ± 25||65 ± 10|
|Squeezed||340 ± 20||45 ± 5|
|CHT||Native||4350 ± 650||165 ± 45|
|Squeezed||3460 ± 150||230 ± 15|
Infrared spectra and nuclear magnetic resonance (N.M.R.) of the native hydrogel and that of the same hydrogel once stressed appear to be overlapped, indicating that the hydrogel’s chemistry is maintained. Therefore passing through a syringe or being subjected to a stress applied by a rheometer does not alter the chemical structure or affect the degree of cross-linking of the hydrogel . We can say that the application of a stress induces a change in the hydrogel’s matrix without affecting its chemistry. Therefore, the involvement of different factors such as the amount of water contained within the hydrogel and its arrangement as well as the polymer chains disposal have been considered.
The amount of water contained in the hydrogels was determined by measurements of swelling in NaCl 0.1 M solution at pH 7.4 (see Table 2). All the native hydrogels uptake the same amount of water at their maximum swelling degree within the experimental errors even if the structure of the starting polymers and the cross-linking of the hydrogels are different from each other. Concerning the swelling degree of squeezed hydrogels, the value of Hyal is slightly higher than that of CMC. CHT shows the lowest swelling degree (see Figure 4). This trend can be explained by considering the pKa of polysaccharides. The CHT hydrogel, which contains free amine groups, is partially charged at pH 7.4, as the pKa of CHT is between 6.5 and 7.5, depending on the degree of deacetylation . The NH3+ groups, which are highly hydrophilic, interact with the remaining free NH2, collapsing the polymeric chains and hindering the solvation of the hydrogel. In fact, the swelling degree of CHT is significantly higher (~1000) in NaCl 0.1 M at pH 4, when all the free –NH2 groups are protonated and able to repel each other. The CMC and Hyal hydrogels are both negatively charged at pH 7.4 because of the presence of free, completely unprotonated COO− (the pKa of both Hyal and CMC is ~4.0–4.5) . The presence of negatively charged groups increases the electrostatic repulsions between the polymer chains and thus the amount of water that can enter the hydrogel.
|Hydrogel type||Status||Swelling degree %|
|CMC||Native||640 ± 50|
|Squeezed||1235 ± 125|
|HYAL||Native||720 ± 25|
|Squeezed||1300 ± 150|
|CHT||Native||650 ± 80|
|Squeezed||830 ± 125|
The total amount of water within hydrogels in NaCl 0.1M is higher for the squeezed hydrogels than for the native ones (see Table 2). Under the application of a shear stress the polymer chains which are entangled during the cross-linking reaction unroll and align along the direction of the stress [30,31]. Hence, this necessarily induces a new disposal of water molecules within the hydrogel network. Bound water molecules move to a semi-bound state (see FT-IR analyses). This movement of water molecules determines a decrease of the mechanical properties of the hydrogel. The change in the arrangement of water molecules seems to be irreversible. In fact, by dipping a squeezed hydrogel in water for several days, it does not regain the original mechanical properties before being squeezed. The passage of water molecules from bound state to a semi bound state make the material also capable to uptake a higher amount of water because the higher mobility of water molecules allow them to form a higher number of bonds with other free water molecules.
2.3. FT-IR Analysis: The Role of Water
The role of water and water interactions inside the hydrogel were investigated by means of FT-IR analyses of the hydrogel in both swollen and dried forms. A typical IR spectrum of CMC hydrogel in dried state is shown in Figure 5, with main peak assignment listed in Table 3. In a first approximation the spectrum is composed of four regions [32,33]:
1. An intense band in the region between 950 and 1200 cm−1 corresponding to the –C–O, C–CH stretching and CO and C–O–C bending of the glycoside ring.
2. A region around 1300 and 1450 cm−1 where bands related to C–CH and O–CH stretching and –CO stretching are observed together with a peak at 1408 cm−1 beloning to the symmetric stretching of the free carboxylate groups of the polymer not involved in the hydrogel formations.
3. An intense group of bands that extends from 1500 to 1700 cm−1 corresponding to the amide I, amide II and free carboxylate groups of the CMC polymer.
4. A broad and intense band in the region between 2500 and 3600 cm−1 which is composed of several bands ascribed to the –OH stretching of the polymer glycoside ring, and the –OH stretching of water free and involved in hydrogel bonds.
|3264||water molecules –OH|
|1640||amide –C=O stretch|
|1582||carboxylate symm. stretch|
|1408||carboxylate asymm. stretch|
|1320||C–CH and O–CH stretch|
|1106||C–C C–O stretch|
Our attention was focused on the spectral region between 1500 and 1800 cm−1. In order to determine the components contributing to the band envelopes, we performed a curve-fitting analysis of the spectra of the swollen hydrogel in the region between 1500 and 1800 cm−1 (see Figure 6). The assignment of peak components for the CMC hydrogel in its native state and after squeezing is reported in Table 4. The main difference regards the position of the peak ascribed to the carboxylate asymmetric stretching, which shifts from 1578 cm−1 (spectrum of native hydrogel) to 1590 cm−1 (spectrum of squeezed hydrogel). The shift to higher wavenumbers is attributed to the loss of some hydrogen bonds involving the free carboxylate groups of the polymer chains . No significant shifts were observed in the position of amide I in the spectrum of native and squeezed CMC hydrogel in their swollen state. However, once the hydrogel is left to dry, the amide I peak shifts to higher wavenumbers compared with the position of the same peak for the hydrogel in the swollen state (from ~1631 cm−1 to ~1645 cm−1). This indicates that in the dried state, additional interactions between amide groups are involved [34,35].
|CMC hydrogelswollen state||Main peak wavenumber (cm−1)||Wavenumber (cm−1)||Assignment|
|native||1631||1675||water molecules –OH bend|
|1631||amide –C=O stretch.|
|1578||carboxylate asymmetry stretch.|
|1550||1550||amide –N–H bend|
|squeezed||1632||1675||water molecules -OH bend|
|1631||amide –C=O stretch.|
|1590||carboxylate asymm. stretch.|
|1552||1552||amide –N–H bend|
The same behavior was found for Hyal hydrogels. The typical IR spectrum of Hyal hydrogel in dried state is reported in Figure 7, with the main peak assignments listed in Table 5. As made for CMC hydrogel, a curve-fitting analysis of the swollen hydrogel spectra in the region between 1500 and 1800 cm−1 was carried out. The asymmetric stretching of free carboxylate groups shifted from 1608 cm−1 in the spectrum of native swollen hydrogel to 1616 cm−1 in the spectrum of squeezed hydrogel. The shift of the carboxylate groups is again attributed to the presence of hydrogen bonds involving the carboxylate groups. The higher amount of hydrogen bonds  in the native hydrogels could be responsible for the higher storage modulus (G’) and viscous modulus (G”) values of the native CMC and Hyal hydrogels in comparison with the same squeezed hydrogels.
|3310||water molecules –OH|
|1640||amide –C=O stretch|
|1610||carboxylate asymm. stretch|
|1560||amide N–H bend|
|1410||carboxylate symm. stretch|
|1375||C–CH and O–CH stretch|
|1146||C–C C–O stretch|
The spectrum of CHT hydrogel is shown in Figure 8 and the assignment of the main peaks is shown in Table 6. As discussed above for CMC hydrogel, the entire spectrum can be divided into four regions: An intense band in the region between 950 and 1200 cm−1 corresponding to –C–O, C–CH stretching and CO and C–O–C bending of the glycosidic ring; a region around 1300 and 1450 cm−1 where typical chitosan polymer bands related to C–CH and O–CH stretching and –CO stretching are found; and an intense group of bands that extends from 1500 to 1700 cm−1 corresponding to the amide I and amide II peaks ascribable to the two amide groups of CHT hydrogel, one belonging to chitin polymer and the other related to the one formed during the cross-linking reaction. The last region, which is composed of several bands ascribed to the –OH stretching of the polymer glycosidic ring, –OH stretching of water molecules (both free and involved in hydrogen bonds) and different types of amine group stretching, is between 2500 and 3600 cm−1 [37,38]. The spectrum of the swollen squeezed hydrogel was compared to that of the same hydrogel before squeezing in the region between 2600 and 3600 cm−1 (see Table 7) after application of the same curve-fitting procedure used for CMC and Hyal-based hydrogels. A shift of 12 cm−1 to lower wavenumbers was noted for the peaks at 3510 cm−1 and 3312 cm−1 ascribable to the stretching of free NH2 groups and the stretching of free NH3+ groups respectively, in the spectrum of the squeezed swollen CHT hydrogel with respect to that of native CHT hydrogel. In the case of the peak related to the amide N–H stretching, a shift of 8 cm−1 in position was found (3130 cm−1 for native hydrogels and 3138 cm−1 for squeezed hydrogels). Generally, the shift of the stretching of primary amine groups to lower wavenumbers is due to an interaction among such groups leading to the formation of NH2–NH3+ clusters . In the case of CHT hydrogels, such interactions seem to be stronger for the squeezed sample than for the native one (see Table 1). On the contrary, no significant difference of the positions of the amide I or amide II bands were observed in the spectrum of native and squeezed hydrogels in the swollen or dried state. Furthermore, in the case of the dried hydrogel, the peaks of NH2 groups, the stretching of free NH3+ groups and the stretching of NH groups are located at 3440, 3260 and 3100 cm−1 respectively, all at wavenumbers lower than those of the swollen hydrogel. This effect is again due to the existence of NH2–NH3+ interactions, which are more intense when the hydrogel is dried. In contrast, when the hydrogel is in the swollen state, the NH2–NH3+ interaction can be mediated by water molecules via hydrogen bonds between water and primary amine groups. A sort of competition between NH2-water, NH3+-water and NH2–NH3+ occurs, and it seems that the interactions between amine groups and water molecules are greater in the native swollen state than in the squeezed and dried state.
|3300||water molecules –OH|
|1640||amide –C=O stretch.|
|1545||amide N–H stretch|
|1314||C–CH and O–CH stretch.|
|1150||C–CH C–O stretch|
|CHT hydrogelswollen state||Main peak wavenumber (cm−1)||Wavenumber (cm−1)||Assignment|
|3510||free –NH2 stretch|
|3312||free –NH3+ stretch|
|3130||3130||amide –N–H stretch|
|3475||Free –NH2 stretch|
|3300||free –NH3+ stretch|
|3138||3138||amide –N–H stretch|
Upon application of a shear stress, such as the passage from a syringe needle, the strength of such physical interactions decreases, making the hydrogel softer. Basically, a different arrangement of water molecules from a bound state to a semi-bound state occurs, leading to a decrease in the mechanical properties of the hydrogels (see Figure 9). In summary, the presence of water molecules organized near the polymeric chains-so-called bound and semi-bound water-influences the mechanical properties of the hydrogels, making the materials tougher or softer. In the case of native-based hydrogel, polymer-water interactions occurring via hydrogen bonds which are quite strong are responsible for the higher values of G’ and G” as compared with the same squeezed hydrogel.
3. Experimental Section
Carboxy Methyl Cellulose with a degree of carboxymethylation of 95% (CMC) (MW 700 KDa) Chitosan (MW 210 KDa), with a degree of deacetylation of 75% (CHT) and Hyaluronan (Hyal) (MW 200 KDa) were purchased from Sigma-Aldrich (Switzerland). Hyaluronic acid in the sodium salt form (Hyal) (MW 150–200 KDa) was purchased from Biophyl S.p.A. (Milan, Italy). The cross-linking agents, i.e., 1-3-diaminopropane (DAP) and adipic acid (AA), the activating agents 1-ethyl-3-[3-(dimethyl-amino)propyl)carbodiimide hydrochloride (EDC), N-hydroxysuccinimide (NHS) and all other chemicals and solvents were purchased from Sigma-Aldrich and used with no further purification.
3.2. Hydrogel Synthesis
All the hydrogels were synthesized by cross-linking each polysaccharide using an appropriate cross-linking agent chosen according to the chemical moieties present along the polysaccharide chains. The Hyal and CMC hydrogels were synthesized following the same chemical route, i.e., by exploiting the EDC chemistry: basically, an amide bond between the carboxylic groups of the polysaccharides and the primary amine of 1,3-diaminopropane (DAP)—the cross-linking agent-was formed thanks to the presence of EDC. The cross-linking agent, DAP was added to the mixture at a molar ratio of 0.5 with respect to the moles of carboxylic acid of the polymers and to EDC and NHS moles. The molar ratio of EDC and NHS mole is 1 to 1 . The pH of the mixture was adjusted to 4.75 and the reaction was allowed to continue under stirring overnight at room temperature. The synthesis of CHT followed the same route with the use of adipic acid (AA) instead of DAP as the cross-linking agent by using the same molar ratio of EDC, NHS and cross-linker of the synthesis of Hyal and CMC hydrogels. These molar ratios have been used for the synthesis of hydrogels with a theoretical cross-linking of 100%. Once formed, the hydrogel was purified by means of alternate washings in absolute ethanol and water for 4–5 days until no traces of free EDC or NHS were revealed by UV spectrophotometry.
3.3. Mechanical Properties
Rheological measurements were performed on native hydrogels at their maximum swollen state and the same hydrogels once being squeezed from a syringe with a needle of 18 gauge. A strain-controlled AR2000 Rheometer (TA-Instruments, Leatherhead, United Kingdom) in the parallel plate configuration at a controlled temperature of 25 ± 1 °C was used. The native hydrogels were directly squeezed between the parallel plates of the rheometer. During a stress sweep test, the sample is subjected to an increasing or decreasing stress, while frequency and temperature are maintained constant. A frequency of 1 Hz was used. The test gives the values of the storage modulus (G’) and the loss modulus (G”). The G’ values provide information about the energy stored in the material during deformation stress while G” describes its viscous character. In order to verify how the hydrogels respond to the variation of an applied stress, a four-step dynamic stress sweep test was performed. The measurement is carried out by increasing (step 1) and decreasing (step 2) the oscillation twice, through the addition of a further increasing step (step 3) and decreasing step (step 4) [7,25]. The sample is subjected cyclically to the same applied stress (increasing and decreasing steps). Moreover, rheological measurements were performed on hydrogels once squeezed by waiting for different time from the squeezing. No variation of G’ and G” values by waiting for longer time form the squeezing were observed (by keeping the sample once squeezed in a moist chamber).
3.4. Water Uptake
Swelling measurements were performed on both native and squeezed hydrogels (at least three samples for each type of hydrogel) by estimating the variation in the height of each hydrogel from the dried state (freeze dried hydrogel containing about 10% of water) to the swollen state. The native and squeezed hydrogels were freeze-dried and then a same amount of dried hydrogel placed inside small cylindrical containers (diameter 12 mm, height 35 mm) and pressed down to the bottom. The initial height of each sample was 1.0 mm. Each hydrogel was immersed in 1 mL of NaCl 0.1 M solution at pH 7.4 and the height of the swollen material was measured using a digital caliber (experimental error ±0.02) until the value remained unchanged.
The swelling degree (SD) of each hydrogel was calculated according to the equation:
where hs is the height of the swollen hydrogel and h0 is the initial height of the hydrogel in dried state (freeze-dried) .
3.5. FT-IR Analysis
Infrared analyses were performed on native hydrogels and on the same hydrogels immediately after being squeezed. Infrared spectra were recorded using an FTIR spectrometer (Biorad FTS 6000) working in attenuated total reflection mode equipped with a 45° Ge ATR crystal and a mercury cadmium telluride detector. The spectra were an average of 512 scans at a resolution of 2 cm−1. The spectra were corrected for the baseline and smoothed. The spectrum of water was subtracted for each reordered spectrum of hydrogels in both hydrated and dried state using the same parameters. In order to find all the components of each peak, curve fitting was performed using special software (XPSPEAK). Spectra were fitted by using a mixture of Lorentzian (20%) and Gaussian (80%) line shapes by minimization the error sum. The spectra fitted well with four components of the main peak.
Polysaccharide-based hydrogels starting from polymers of varying chemistry were synthesized. All hydrogels contain huge amounts of water, which affects their rheological properties. Their most advantageous properties have to do with their injectability, which makes them promising biomaterials for minimally-invasive surgery and localized therapy. The arrangement of water molecules inside hydrogel structures can be considered a critical point in understanding their rheological behavior. From data reported in this paper, we deduce that under the application of a shear stress (such as passage through a syringe needle or the stress applied by a rheometer), a different arrangement of water molecules from a bound state to a semi-bound state occurs, leading to a decrease in the mechanical properties of the hydrogels and an increase of the swelling degree.
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