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Unlocking Gel-powers: Exploring Rheological Marvels of Acrylamide/Sodium Alginate Double-Network Hydrogels

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31 May 2023

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31 May 2023

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Abstract
Hydrogels, soft materials with 3D polymer networks in aqueous solution, have been developed for engineering and bio-related fields. However, these conventional hydrogels are weak and brittle due to lack of energy dissipation mechanisms. Recently, dual-network hydrogels have been proposed, combining rigid and flexible networks and exhibiting high strength, stretchability, and toughness. This paper explores the rheological properties of dual-network hydrogels based on acrylamide and sodium alginate under large deformations. This dual network is a combination of a covalently crosslinked polyacrylamide network and a supramolecular crosslinked sodium alginate network at the presence of divalent calcium cations. Small and large amplitude oscillatory shear methods with Fourier transform rheology, stress decomposition method, and Chebyshev polynomial analysis of large amplitude oscillatory shear (LAOS) data were employed to evaluate non-linearity limit, toughness, and network rigidity. The concentration of calcium ions affects (concentrations 0-80 mg/ml) the nonlinear transition and limit points, and all gel samples exhibit strain hardening, shear thickening, and shear densification.
Keywords: 
Acrylamide
;  
Sodium alginate
;  
Double network hydrogel
;  
Large amplitude oscillatory shear
;  
Fourier transform rheology
Subject: 
Chemistry and Materials Science  -   Polymers and Plastics

Introduction

Hydrogels are polymeric materials that can swell and retain large amounts of water in their three-dimensional cross-linked network structure, resulting in solid-like properties in the steady state [1]. Synthetic hydrogels have better mechanical properties than naturally occurring ones, and can be chemical or physical gels depending on their cross-linking method [2]. Chemical gels are formed through polymerization or cross-linking of monomers, while physical gels are formed through intermolecular interaction forces, while in most cases entanglements are not playing an important role, as the entanglement molar masses at the concentrations chosen are usually significantly higher than the molar mass between the crosslinks. This is easily visible from the fact that in most cases the precursor solutions of the polymers (for gels being made up of polymer chains and not polymerized directly from a monomer) are more or less Newtonian with viscosities like water or oil (i.e. between 1 mPas and 1 Pas at room temperature) [3,4,5,6,7,8,9,10,11,12,13,14,15,16,17,18,19,20,21,22,23,24,25]. However, chemical gels are typically fragile and are permanently damaged when subjected to high strain, resulting in poor mechanical strength [26,27].
In 2003, double-network (DN) hydrogels were introduced by Gong et al.[28] using a two-step sequential radical polymerization method. The unique entangled network structure of DN hydrogels presents the potential for improved mechanical properties. DN hydrogels consist of two networks, one rigidly cross-linked to form a rigid network and one ductile and loosely cross-linked, leading to a nonlinear effect between the networks that provides high strength [28]. The irregularities in the double network structure contribute to better mechanical properties [29,30].
There has been a recent surge in interest in DN hydrogels with controllable shape deformation and diverse network structures. Various modifications have been proposed to enhance their mechanical properties, electrical properties, and fatigue fracture resistance, resulting in wide applications in a wide array of fields, such as environmental and electrochemical engineering, biomedical devices, sensors, and tissue engineering [31,32,33,34].
There has been ambiguity in interpreting DN hydrogels, which has caused confusion with IPN/semi-IPN hydrogels. Gong et al.[28] clarified in 2003 that DN hydrogels are composed of two networks with different structures and properties, but their relationship is unclear [35]. In contrast, IPN hydrogels are at least partially interleaved at the molecular scale, and at least one of the polymer networks is chemically cross-linked and cannot be separated without breaking the chemical bonds [36]. DN hydrogels were later classified as a special type of IPN hydrogel. IPN hydrogels do not have significantly improved mechanical strength compared to their original networks due to their soft and rubbery consistency [37]. A published overview and classification of hydrogels based on physical or chemical cross-linking preparation route and physical properties exists [38].
Mechanical properties are crucial in the application of hydrogels and cannot be overlooked [39]. The comprehension of the rheological properties of hydrogels is vital in controlling their performance. The present focus of hydrogel research is on the correlation between network structure and hydrogel properties and the relationship between high strain and fracture [40]. The science of understanding the flow and deformation of materials is the study of rheology. Rheology can define the microstructure of soft materials [41], analyze changes in dynamic mechanical properties, and describe structural features. In polymer processing, rheology bridges the molecular structure and processing properties. The guidance of rheology is widely used in industrial polymer chemistry and processing technology [42].
Rheological characterization includes steady-state shear and dynamic mechanical tests (DMT) that measure viscosity, yield stress, zero shear viscosity, and thixotropy at varying shear rates. Dynamic oscillatory shear testing is commonly used to study complex fluids and soft materials, such as polymer melts and solutions, block copolymers, biopolymers, polyelectrolytes, surfactants, suspensions, and emulsions. DMT uses the storage (G') and loss (G") moduli to represent elastic and viscous behavior, respectively, under shear. High G' relative to G" indicates solid-like behavior, and low G' relative to G" indicates liquid-like behavior. The loss factor parameter (tan δ) is an indicator of the gel threshold [43,44,45,46]. DMT includes small amplitude oscillatory shear (SAOS) for linear viscoelastic response and large amplitude oscillatory shear (LAOS) for nonlinear material response observed at larger strain amplitudes (>0.1-30% depending on the sample) [7,47,48,49,50,51,52].
Linear viscoelasticity has limitations in understanding the rheological properties of complex fluids. In processing operations, large and fast deformations result in non-linear behavior. Non-linear viscoelasticity is essential for distinguishing complex fluids with similar micro or nano-structures. Matching non-linear parameters improves consistency between molecular theory, constitutive equations, and experiments [53,54,55,56,57]. Steady-state viscosity measurements are useful but limited, particularly for high deformation rates. LAOS testing is a useful alternative for a range of complex fluids and soft materials, allowing independent variation of strain amplitude and frequency, and easy generation and control [47,58,59,60,61,62].
LAOS and SAOS require appropriate selection of strain amplitude (γ0) and frequency (ω) for experimental input, but LAOS output analysis differs from that of SAOS due to material response becoming nonlinear under large enough strain amplitudes [55,58,59,61,63,64]. In biopolymer gel rheology, LAOS has been explored over the past two decades, allowing for deeper insights into microstructural changes under large deformation.[65] LAOS data analysis is crucial for interpreting complex rheological behavior, and various methods, such as Lissajous curves and Fourier transforms, have been used. LAOS characterization of biopolymers provides better understanding of rheological behavior and can simulate real polymer processing conditions [41,42,48,57,62,63,66,67,68,69,70].
A potential method for enhancing hydrogel properties is by constructing interpenetrating polymer network (IPN) structures [71]. Such a hydrogel is composed of two networks mutually permeating each other, one being a rigid polyelectrolyte with tight cross-linking and the other a flexible neutral polymer with loose cross-linking [72,73]. The polyacrylamide (PAAM)/sodium alginate (SA) composite hydrogel is a typical example, consisting of two interpenetrating polymer networks: a covalently cross-linked PAAM network and an alginate network formed by ionic interactions [74]. Linear polysaccharides extracted from brown algae cell walls include β-d-mannuronic acid (M) and α-l-guluronic acid (G), and are the alginate salts. In aqueous solution, G/blocks of alginate chains cross-link with bivalent cations (e.g., Ca2+) to form an alginate hydrogel, +), which can be explained by the formation mechanism of the "egg-box" structure [75]. Amongst other properties, swelling and mechanical properties of this hydrogel are pH-dependent [72]. PAAM is typically obtained by free-radical polymerization of acrylamide (AM) by the irreversible formation of covalent bonds [76]. For obtaining the DN hydrogel, at first, the neutral monomer AM is cross-linked to form the first network. Then, the polyelectrolyte SA is introduced to prepare the second network with rigid and strong properties, which can penetrate the first network [35]. Therefore, IPN hydrogels, combining the properties of natural and polyelectrolyte polymers, have improved mechanical properties compared to gels with a single network [77,78].
The IPN structure comprises a rigid polyelectrolyte network with tight cross-linking and a flexible neutral polymer network with loose cross-linking, mutually permeating each other. The PAAM network in the IPN structure is elastic, while the alginate network is brittle and fractures by breaking ionic bonds [74]. The fracture process in the alginate network dissipates energy through hysteresis [79]. Gong’s group conducted extensive research on PAAM single network hydrogels using mechanical and rheological characterization and proposed constitutive equations for their tensile and frictional behavior [80,81,82,83,84,85,86,87].
Wu et al.[88] investigated the structure and frictional behavior of PAAM/SA ion-covalent hybrid and sequential double network hydrogels on glass in water, NaCl, and CaCl2. They utilized a rotational rheometer to measure the friction between the samples and the glass substrate. The results indicated that the frictional stress of the PAAM/SA gel could be managed by the adsorptive elastic hydrodynamic friction of the covalently cross-linked PAAM network and the repulsive hydrodynamic friction of the minor SA ion network. They proposed a qualitative model to describe the effect of the ionic environment solution on the hybrid gel friction behavior. The findings demonstrated that the ionic environment solution had a significant impact on the ion cross-linking density, swelling degree, and charge shielding of the SA ion network at the gel-glass interface.
Stadler’s group[55,59] investigated the linear viscoelasticity, nonlinear rheology, and microstructure of composite hydrogels made of sodium alginate (SA) and poly (N-isopropylacrylamide-co-4-vinylphenylboronic acid) (NIBA) by varying the SA and NIBA content. They studied the interaction between NIBA and SA and the viscoelasticity of SA/NIBA blends as a function of NIBA concentration, using LAOS to obtain structural information. The mechanism of gelation and microstructure of SA/NIBA gels were elucidated. They found that SA and NIBA blends were in a sol state under alkaline and neutral conditions and formed hydrogen-bonded gels under acidic conditions. The addition of NIBA increased the hydrogel modulus and decreased the yield point, suggesting that small NIBA chains strengthened the SA chain network, but reduced the flexibility of the SA chains.
This paper shall examine PAAM/SA hydrogels and systematically explore the influence of pH variation, Ca2+ ion content, and SA concentration on both linear and nonlinear rheological properties and mechanical characteristics. A thorough state-of-the-art analysis and discussion on the structures shall offer a more profound understanding of the material property-rheology relationships.

Experimental Part

Materials

Preparation of PAAM/SA composite hydrogel: The composite hydrogel was prepared by a two-step method. Different ratios of AM (acrylamide, 99%, Aladdin, Shanghai, China) and SA (sodium alginate, AR, Aladdin, Shanghai, China) monomers were dissolved in deionized water, followed by the addition of N,N'-methylenebisacrylamide (MBAA,AR, McLean, Shanghai, China) as crosslinker and tetramethylethylenediamine (TEMED, 99% McLean, Shanghai, China) as accelerator, mixed into a homogeneous precursor solution by ultrasonic and magnetic stirring. The precursor solution contained 0.1 g/L of MBAA and 50 μL of 99% TEMED, and the concentrations of the different monomers added are shown in Table 1. Then, 40 μL of 0.05 wt% potassium persulfate (KPS, 99.9%, McLean, Shanghai, China) was added as initiator to the homogeneous precursor solution and poured into the mold (40.0 × 40.0 × 2.0 mm). The gel was cured at 60 °C for one hour, during which the AM monomers formed the first covalent 3-dimensional network. Aqueous calcium chloride solution (CaCl2, 99.9%, Aladdin, Shanghai, China) was used to displace the aqueous solution in the hydrogel during the course of 3 days. This solution exchange led to the formation of the second network SA, and the formation of PAAM/SA composite hydrogels was accomplished. For comparison, a PAAM gel was prepared in the same way as the composite hydrogel (except that no SA monomer was added). A pure SA gel was prepared by adding calcium chloride solution to the SA aqueous solution, followed by mixing and stabilizing for 24 h. All hydrogel samples discussed in this paper are listed in Table 1.

Characterization

SEM and FTIR

For SEM (scanning electron microscopy), the hydrogel was first immersed in liquid nitrogen for 10 min, followed by freeze-drying for two days. Then, the sample was broken to create a clean surface. Subsequently, the sample was mounted on an SEM stage with conductive carbon tape and a thin layer of gold was sputtered at 20 mA in vacuum for 50 s. The cross-sectional morphology of the hydrogel was observed using SEM. The prepared hydrogel was characterized using SEM (SU-70, Hitachi, Tokyo, Japan). The Fourier transform infrared (FTIR) spectra of DN hydrogel were collected using a Nicolet 6700 spectrometer (Thermo Fisher Scientific, Waltham, USA) on KBr pellets. The samples were prepared by grinding and dispersing the freeze-dried sample in KBr, pressing them into pellets, and then, performing infrared characterization. The spectral range was 400-4000 cm-1 with a resolution of 4 cm-1.

Rheology

Rheological characterization of two types of double-network hydrogels (S1 and S2) was performed using an Anton Paar MCR 302 rheometer (Graz, Austria). For hydrogel samples with soft solid properties, the parallel plate geometry with a 25 mm diameter plate (PP 25) was used at a test temperature of 25 °C and a 2 mm gap between the plates. Prior to testing, the samples were allowed to equilibrate for five minutes to ensure complete relaxation. For precursor solutions, cone-and-plate geometry with a 50 mm diameter plate and a 1° angle (CP 50) was used with a 0.102 mm gap between the plates to prevent non-uniform deformation and flow of the sample.
The steady-state viscosity of the samples was measured at shear rates γ ˙   of 0.01-1000 1/s after pre-shearing to eliminate the effects of air bubbles and non-uniform distribution [89]. The viscosity functions η( γ ˙ ) were used to determine the fluid type and rheological behavior of the samples at different pH values. Creep recovery experiments were conducted to determine the changes in strain and creep compliance over time [70]. A constant stress τ of 50 Pa (in the linear viscoelastic region (LVR)) was applied for 300 s followed by a creep recovery experiment for 600 s (stress τ = 0 Pa). While this setup does not completely ensure the stationarity of the deformation, it is a good indicator of the gels being viscoelastic liquids or solids. Frequency sweep tests were conducted at ω = 100-0.1 rad/s with a (strain γ 0 of 1% in the linear viscoelastic regime) to study the frequency dependence of the composite hydrogel's linear viscoelastic region and monitor the storage modulus (G’), loss modulus (G”), and loss factor (tanδ) as a function of frequency ω [90].
To characterize the linear and nonlinear viscoelastic regions of the gel samples, a dynamic strain sweep (DSS) was performed by increasing and decreasing the strain values logarithmically at a constant angular frequency ω = 1 rad/s. DSS was performed with five continuous cycles of increasing and decreasing strain amplitude γ 0 (Table 2).
While in the linear viscoelastic regime G’, G”, δ , … are clearly defined, the occurrence of overtones in the nonlinear regime makes a more detailed analysis necessary. For this purpose, the data were analyzed with MITLAOS [41,62], yielding the intensities of each (odd) overtone In as well as the corresponding phase angles δ n, from which the Chebichev coefficients en and vn as well as the higher order components of the moduli G’n and G”n were calculated.
In LAOS, the stress response is composed of odd higher harmonics, and the In /I1 ratio is the most commonly used indicator for quantifying and predicting nonlinear behavior. The signal-to-noise ratio (SNR), which is the ratio of the amplitude of the first harmonic peak to the standard deviation of the noise, is typically between 103 and 105. In addition to the higher harmonic ratio, the nonlinear parameter Q can also be used to characterize the degree of nonlinearity of the gel sample:[59]
Q = I 3 / I 1 γ 0 2
Which is used to determine Q0, the Q-parameter for γ 0 →0 [91,92]. Ewoldt et al.[41] introduced the minimum-strain modulus G’M, the large-strain modulus G’L, defined as:
G M ' = ∑ n = odd n G ' n ， G L ' = ∑ n = odd G ' n ( - 1 ) ( n - 1 ) / 2
As well as the minimum-rate dynamic viscosity η’M , large-rate dynamic viscosity η’L, defined as:
η L ' = 1 ω ∑ n = odd G " n ， η M ' = 1 ω ∑ n = odd G " n ( - 1 ) ( n - 1 ) / 2
From the minimum-strain modulus, the large-strain modulus, the minimum-rate dynamic viscosity, and large-rate dynamic viscosity the strain hardening (S) and shear-thickening (T) were determined. These properties can also be visually obtained from the Lissajous curves [66].
S ω , γ 0 = G L ' ω , γ 0 - G M ' ω , γ 0 G L ' ω , γ 0
T ω , γ 0 η L ' ω , γ 0 - η M ' ω , γ 0 η L ' ω , γ 0
When S < 0, the sample exhibits strain-softening behavior, while when S > 0, the sample exhibits strain-hardening behavior. When T < 0, the sample exhibits shear-thinning behavior, while when T > 0, the sample exhibits shear-thickening behavior.

Tensile Testing

Gel samples (25.0 × 20.0 × 2.0 mm) were tested for uniaxial stretching at a constant rate of 50 mm/min using a universal testing machine (CMT 5000, Sansi Testing, Shenzhen, China). The samples were cut into a dumbbell shape. The stress-strain curves were used to display the corresponding toughness [93], with nominal stress σ calculated as the ratio of tensile force σ to the cross-sectional area A of the deformed sample [94]. The mechanical properties of all samples were calculated as the average of at least three specimens. For cyclic tensile curves, samples were loaded to a predetermined strain ratio, immediately unloaded, and the hysteresis loop area estimated by the loading and unloading curves was used to calculate the sample's hysteresis energy density [95,96,97].

Results and Discussion

After preparation of the PAAM/SA DN hydrogels, they were characterized by scanning electron microscopy (SEM). The cross-sectional morphology of the pure AM and SA hydrogels are shown in Figure 1 (a&a’ and b&b’), while the PAAM/SA composite hydrogel (samples S1-30) is shown in Figure 1 (c&c’). The pure PAAM hydrogel has small pores (ca. 10 μm) and a disordered morphology, while pure SA hydrogel appears as a layered structure with layer sizes between 50 μm and 100 μm. In PAAM/SA hydrogel, SA forms a larger network structure with larger pores than the pure PAAM network, resulting in more uniform pores and an orderly network structure.
Figure 2(b) shows the FTIR spectra of AM, SA, and DN PAAM/SA hydrogel samples. For reference, Figure 2 (c&d) illustrates the molecular structure of AM and SA crosslinked by a crosslinking agent, while Figure 2 (a) shows the structure of the double network hydrogel. The FTIR spectrum of PAAM features characteristic absorption peaks at 1605 cm-1 and 1608 cm-1, denoting large amount of C=O and N-H moieties of PAAM hydrogels. Meanwhile, for the SA hydrogel, obvious characteristic absorption peaks at 3434 cm-1 and 1030 cm-1 are observed, indicating that the SA hydrogel contains a large amount of O-H and C-O groups. The characteristic absorption peaks of SA are observed in the PAAM/SA composite hydrogel. The characteristic absorption peaks near 3400 cm-1 and 1750 cm-1 were significantly enhanced, indicating that the PAAM/SA composite hydrogel system contains many O-H, N-H and C=O groups. Thus, the established system hydrogel comprises of a double network structure of SA and PAAM.

Rheological characterization

Figure 3 displays steady-state shear viscosity analysis of SA and PAAM/SA mixed aqueous solutions at different pH with the same concentration as the gels but without added crosslinker or Ca2+-ions. The concentration of SA used is consistent with the DN hydrogel. The macromolecule SA is composed of M (MMM), G (GGG), or alternating M and G structures, with high viscosity SA polymer chains being unstable and degradable [59]. Figure 3 reveals shear-thinning behavior (lowered viscosity at increased shear rate), stemming from dissociation of SA polymer chains at increased shear stress [98].
The data demonstrates that the sample exhibits gel-like behavior with a yield point at low pH, whereas at high pH, only a slight non-Newtonian behavior is observed for low SA concentrations (S1). For high SA concentrations (S2), the shear thinning is much more pronounced, which is easily explainable by the fact that AM is not polymerized and thus behaves more or less like a Newtonian liquid, while SA is a viscoelastic polymer in solution, which leads to shear thinning. While no Ca2+-ions were in the system that would lead to supramolecular crosslinking, the moieties of SA can have a whole host of other pH-dependent interactions, especially at low pH [55,59]. Owing to the pH-dependence of SA, also the pH has a much more significant influence for S2 than for S1. Obviously, increasing the SA-concentration increases the overall viscosity level strongly, suggesting that the crossover concentration for SA has been exceeded.
As all following characterizations were carried out at neutral pH, the data clearly show that no gel-like behavior is found for the precursor solutions.
Figure 4 shows the results of the creep and creep-recovery test for samples S1 (1.67 wt% SA) and S2 (2.67 wt% SA) [99]. All samples underwent instantaneous deformation (τ = 50 Pa), followed by a much smaller viscoelastic deformation for the remainder of the 300 s creep step, which – as expected – does not converge to a power law slope of 1, which would indicate a Newtonian creep behavior. This shows that the sample is crosslinked, i.e., has an infinite zero shear-rate viscosity [100,101,102]. The recovery step shows that almost the complete deformation is recovered, again indicating that only a very small tendency of permanent (i.e., viscous) deformation is found, which is what we would expect from a covalently crosslinked gel. The higher the CaCl2-content of the gels, the lower is the residual deformation. This is easily explained by SA being supramolecularly crosslinked by the Ca2+-ions. The more Ca2+-ions, the higher is the probability that the bonding sites on the SA-chain are bonding to a Ca2+-ion. However, one should remember that only a bond between one Ca2+-ion and 2 SA-bonding sites will lead to physical crosslinking between 2 chains (with both intermolecular intramolecular bonds, while only the intermolecular bonds will contribute to the network) [103,104,105,106]. As the bond between a Ca2+-ion and a SA- bonding site is easier to obtain than between Ca2+-ion and two SA-bonding sites, too many Ca2+-ions will weaken the gel once a significant excess of Ca2+-ions is in the system [107,108]. As compliance J and shear modulus G are approximately the inverse of each other, higher strain or compliance J correspond to a lower modulus [109].
In general, the higher the Ca2+-content the lower is J, i.e., the stiffer the gels, and the lower is the residual strain gets. The differences between the S1 and S2 series appear to be not so large, as the PAAM-network is a major contributor to network strength. At a CaCl2 concentrations of 0 mg/ml, the final strain values for the creep and recovery phase were significantly higher in S1-0 and S2-0 and the residual strain values significantly lower than in the other samples. This is because when there is no calcium ion in the sample, SA cannot form a second network, and therefore, only one PAAM network exists in the gel. Thus, the SA is still mostly a viscoelastic polymer solution, which could lead to shear bands and other weak points in the gel, which can be mended by adding Ca2+-ions.
Figure 5 and SI (Figure S1) show the frequency sweeps (FS) for gel sample series S1 and S2, respectively. The storage moduli G' for all samples except S1-0 and S2-0 is of constant and low slope, while S1-0 and S2-0 have a higher non-constant slope. The loss modulus for those samples is significantly lower and goes through a minimum around ω = 1 rad/s, which corresponds to loss factor tanδ values below 0.04. Considering that this means δ below 2°, the gels behave close to an ideal rubber [110,111]. Because the rheometer used is a single measurement head rheometer, it is likely that δ is even lower, as for highly elastic soft samples such rheometers tend to measure too high phase angles.
S1-0 and S2-0 show clearly different dynamic-mechanical data with significantly higher damping and lower overall modulus (especially S2-0). This can be explained by the fact that the PAAM-network is more or less unaffected by the content of Ca2+, while the SA-network does not exist, which leads to lots of dangling chains, thus increasing δ and lowering the overall network density, i.e., visible due to a lower G’.

Nonlinear rheological behavior of (PAAM/SA) hydrogels

Figure 6 shows the strain sweeps (γ0: 0.01 → 10 → 0.01 → 30 → 0.01 → 100 → 0.01 → 300 → 0.01 → 1000 → 0.01 (%)), whose G’ (Figure 6a) is very similar except for the last leg (γ0 = 1000 → 0.01 (%)), which indicates that at γ0 > 300% the sample is irreversibly damaged. Figure 6b shows that with each cycle, G” increases by several % (while G’ is approximately constant). A peak around γ0 ≈ 100% appears clearly after straining the sample with γ0 = 300%, which is much larger after γ0 = 1000%, which is assigned to damages in the network structure.
Figure 7 (a&d) show the influence of Ca2+-ions on the strain sweeps (γ0 =0.1→1000%) for the S1 and S2-series, respectively. The linear viscoelastic regime (G’ and G” independent of γ0) decreases significantly upon the addition of Ca2+-ions, while the overall linear viscoelastic values of G’ and G” as well as low damping are not affected very much by presence of Ca2+-ions (except S2-0).
Sim et al.[43] classified the large-amplitude oscillatory shear (LAOS) behavior of strain sweeps in 4 categories, according to which all samples behave according to Type III (weak strain overshoot, G' decreases while G'' increases and then decreases). With an increasing γ0 , the sample begins to enter the nonlinear region, thus the network structure of the gel samples begins to be distorted, resulting in the appearance of weak strain overshoot. The processes occurring here are ripping open the bonds between Ca2+ and the corresponding SA-moieties, which gradually turn the SA-gel network into a polymer solution with dangling ends. Furthermore, the PAAM-network is strained, creating similar effects, albeit without breaking ion-dipole bonds. As γ0 increases, the gel samples show a crossover point (G’ = G”). At higher deformations, G’ and G” decrease sharply, typically with power law slopes of -2 and -1, respectively [112].
In order to quantify these differences better, four characteristic quantities are defined. The linear viscoelastic G’, the modulus at the G’-G” crossover, the nonlinearity limit, defined by a 5% deviation from the viscoelastic G’, and the deformation at the G’-G” crossover. Figure 7(g&h) demonstrates that the influence of ion-content on the viscoelastic G’ and modulus at the G’-G” crossover is relatively small, and the characteristic deformations show a very significant dependence. The γ0 corresponding to the nonlinear limit decreased from 5.2% and 13.7% for S1-0 and S2-0, respectively, to 0.1% and 2.37% for S1-5 and S2-5, respectively, followed by a leveling off at concentrations above ca. 30 mg/ml at γ0 ≈ 1% [58,59]. Furthermore, the G” and deformation γ 0 at the G”-peak were assessed, which, however, yielded almost identical values to the G’-G”-crossover, as those coincide closely. It should be mentioned S1 has significantly lower nonlinearity limits than S2 at low Ca2+-concentrations, which we attribute to the lower SA-concentration, leading to a sparse network, which is not fully bis-complexed and thus easy to destruct. The crossover deformation shows a rather similar relationship, but without the deep minimum found for the nonlinearity limit.
Figure 7 (i) shows the relation between intrinsic nonlinearity Q0 and the calcium ion concentration, which exhibits a jump between 0 and 5 mg/ml Ca2+ by 2-3 orders of magnitude, followed by a broad minimum at intermediate concentrations. Knowing that SA has a certain number of bonding moieties and that each of those moieties needs to be complexed with another moiety via a Ca2+, it becomes clear that one Ca2+ should be in the sample for every 2 SA-moieties. From previous discussions and reports it is known that more dangling ends in the sample lead to a stronger nonlinearity[87]. Therefore, the closer the concentration of Ca2+ is to the optimum concentration of 0.5 equivalent (one Ca2+ for every two SA-moieties), the lower should be Q0. While the concentration of the SA-moieties is not known precisely, it is clear that their concentration for the S2-series is 60% higher. Taking the minimum position of the S1 and the S2-series, it is clear that the S2-series has a minimum at higher concentration than the S1 series and quantitatively also the factor 1.6 is justifiable.
The I3/I1 curves of all gel samples have similar shapes, as shown in Figure 7 (b&e). In the small strain amplitude region, the waveform of the stress response is consistent with the input strain waveform, thus I3/I1→0 [64]. The I3/I1 value of each sample increases with an increase in γ 0 until ca. 10-30% for the samples containing Ca2+-ions, followed by a slight decrease and finally, levelling off to the plateau value of S1-0 and S2-0 around I3/I1=0.1. When looking at this peak in detail it becomes apparent that the peak plateau is virtually reached at the crossover strain of the samples with Ca2+-ions, followed by ca. 1 order of magnitude before decreasing to the level of the Ca2+-free sample (S1-0&S2-0). This trend is better observed for the S1-series than for the S2-series as the former is “more fragile”, as discussed before.
To the best of our knowledge such a peak in I3/I1 has not been reported before, as no research article on double-network hydrogels with supramolecular bonds and LAOS is known to the authors. Apparently, the supramolecular bonds between Ca2+ and the corresponding moieties of SA lead to a higher nonlinearity (I3/I1) than the covalent PAAM-network. Thus, as long as the SA-network is halfway intact, the nonlinearity is higher than when it has broken down due to excessive shear. This could be explained by the supramolecular bonds of SA breaking and reforming twice within one cycle, which will lead to a stronger deviation from the sinusoidal curve shape. This fundamental difference in the response caused by Ca2+-ions is also clearly seen in the viscous Lissajous plots of S1 (Figure 8), other Lissajous plots can be found in SI (Figure S2-S4), where the curve shapes of γ 0 =0.1%, 300%, and 1000% are rather similar, while for the other deformations shown, S1-0 is clearly different from the other samples.
Figure 7 (c&f) show the Q-parameters, which just like I3/I1 are almost indistinguishable for γ0 > 300%, while for smaller deformations, the samples without Ca2+-ions show a significantly higher nonlinearity Q than S1-0&S2-0. From these data, the intrinsic nonlinearity parameter Q0 was determined.
The Chebyshev coefficients, strain hardening rate (S), and shear thickening rate (T), as defined in the experimental part, can be used to analyze the nonlinear rheological behavior of gel samples in LAOS experiments [113]. In LAOS testing, the third Chebyshev coefficients (e3 and v3) are mainly used to characterize the nonlinear response, and their physical interpretation is related to S and T: when e3/e1 > 0, the sample exhibits strain hardening properties similar to S > 0; when e3/e1 < 0, the sample exhibits strain softening properties similar to S < 0; when e3/e1 = 0, the gel sample is in the LVR region. When v3/v1 > 0, the sample exhibits shear thickening properties similar to T > 0; when v3/v1 < 0, the sample exhibits shear thinning properties similar to T < 0; when v3/v1 = 0, the gel sample is in the LVR region.
As shown in Figure 9(a, c, and e) and SI Figure S5 (a and b), as γ0 increases, samples S1 and S2 undergo a transition from the LVR region to the nonlinear viscoelastic region. During this transition, samples S1-(0, 20-80) / S2-(0, 20-80) exhibit strain softening before strain hardening, while sample S1-(10-15) / S2-(10-15) directly undergoes strain hardening without any strain softening. This indicates that the samples S1-(10-15)/S2-(10-15) have a faster feedback response to strain and stress and can immediately respond when subjected to γ0 beyond the maximum tolerance of the LVR region, which is also related to its higher strength and G'. The onset of strain hardening indicates that the gel samples have entered the nonlinear viscoelastic region. The reason for the strain hardening of gel samples is that when the gel sample is subjected to γ0, the network structure of the sample has the ability to resist deformation. However, when the γ0 exceeds a certain threshold, the network structure of the gel sample is destroyed, and the ability to resist deformation decreases significantly. This can also explain the phenomenon of S peaking, follow by decreasing at large deformations.
Furthermore, it should be pointed out that in comparison to I3/I1, the sensitivity to changes in structure is higher, as the deformation at which S, T, e3/e1, or v3/v1 deviates significantly from the linear values varies systematically stronger. E.g., when looking at the strain γ0, at which S = 0.5, a relation very similar to Figure 7 (i) would be obtained.

Mechanical properties

Figure 10 shows the mechanical properties characterization of all hydrogel samples. Figure 10(a) and (c) display nominal stress-strain curves. Hydrogel samples without calcium ions are relatively weak and brittle. However, when a strong SA network is formed by the addition of an appropriate amount of calcium ions, the fracture strength and strain of the hydrogel samples increase sharply, reaching a maximum of 0.33 MPa and 700%, respectively.
Figure 10 (b and d) show the relationship between the tensile strength and toughness of the samples and the concentration of calcium ions. The toughness of the gel samples is defined as the area under the stress-strain curve of the sample up to the point where it fractures. As shown in the Figure 9b and d, the tensile strength and toughness of sample series S1 and S2 initially increase and then decrease as the concentration of calcium ions increases. This is because calcium ions coordinate with the M and G blocks on the alginate during gelation, acting as connections between adjacent blocks (i.e., the egg-box model) [114]. The semi-rigid chains of G-block-containing alginate strongly electrostatically interact with calcium ions, thus the SA network structure adds a higher strength than AM chains possess alone. When the sample is stretched, the SA-Ca2+-SA bonds are the first to break, potentially followed by a new bond being established (sticky reptation) [115,116,117]. If there are too many or too few Ca2+-ions relative to the number of moieties on the SA, either un-complexed Ca2+-ions or mono-complexed Ca-SA-bonds exist, which both are not bonding. Stretching the sample and, thus, breaking SA-Ca2+-SA-bonds leads to a reformation of these bonds. However, as non-bonding mono-complexes are easier to form compared to bonding bis-complexes and an equilibrium between mono-and bis-complexes exits, it is logical that potentially un-complexed Ca2+-ions tend to form mono-complexes more likely than mono-complexes tend to form bis-complexes, if an excess of Ca2+-ions is present in the sample.
The optimum concentration of Ca2+-ions for the S1-series is 10 mg/ml, while for S2 a broader maximum with 20 and 30 mg/ml being approximately equal. The aforementioned factor 1.6 in SA-concentration becomes apparent here again. Overall, the increase of tensile strength and toughness of the best samples of S1 vs. S2-series (ca. 50%) is significantly higher than the increase of the total amount of polymer in the sample (S1: 16.67 wt% AM + 1.667 wt% SA vs. S2: 16.67 wt% AM + 2.667 wt% SA) by only 6%. This can be explained by the nature of double-network hydrogels, where one network stabilizes the other network. Clearly, a very low SA-concentration will lead to an improvement of the mechanical properties, but a higher concentration of S2 will lead to a stronger second network.

Conclusions

The rheological behavior of PAAM/SA composite hydrogels was studied under large strains using SAOS and LAOS rheological methods. Microstructure changes were analyzed through mechanical properties characterization, physical, and morphological analysis.
Both PAAM/SA gel precursor solutions and AM and SA aqueous solutions were in sol state under alkaline and natural conditions and in gel state under acidic conditions. Higher concentrations of SA in the solution caused more interaction between SA chains. After AM penetrated the SA chain, the SA chain needed more energy dissipation to be completely deconstructed.
From the linear rheological characterization, it was found that the addition of the SA rigid network structure significantly increased the G' and strength of the gel since the PAAM network was a tough network. In the nonlinear rheological characterization, all gel samples showed type III behavior, which means weak strain overshoot (G' decreases with increasing strain, and G" increases and then decreases). This weak strain overshoot indicates that the gel sample could resist deformation. The response of the single network PAAM hydrogel to strain was later and smaller in the nonlinear region. The response of the PAAM/SA composite hydrogel to strain was faster, with the nonlinear transition occurring more quickly and the nonlinear region being larger. From the nonlinear parameters, all gel samples initially exhibited strain hardening in the nonlinear region, followed by shear thickening at intermediate strains, and shear banding as the strain increased. The reason for the shear banding is that the network structure in the gel sample is destroyed. Finally, the gel sample exhibited the same response as the strain continued to increase.
The high-order harmonic to fundamental harmonic ratio (In/I1), nonlinear parameters (Q, e3/e1, v3/v1), and Chebyshev coefficients (S, T) are more sensitive to the interaction of polymers in hydrogels. The nonlinear viscoelasticity under dynamic oscillatory shear, particularly at high strain, is useful in studying the network structure and linear/nonlinear viscoelastic behavior of hydrogel systems, providing guidance for their design and processing.
The tensile strength and toughness of the PAAM/SA composite hydrogel both showed a trend of first increasing and then decreasing with an increase in the concentration of calcium ions. This indicates that there is a threshold for the concentration of calcium ions that enhances the strength of the gel sample, which is related to the concentration of SA in the sample. The amount of calcium ions required for physical cross-linking of SA chains in the gel sample is fixed. When the concentration of calcium ions exceeds this threshold, the strengthening of the gel sample by the Ca2+ ions will be limited.
This article focuses on the rheological characterization of hydrogels as soft matter, studying chain dynamics and nonlinear rheological effects under large strains, specifically in double-network hydrogels.
The results of this paper could contribute to further the understanding of the mechanics of double-network hydrogels and thus help design strong hydrogels for future soft matter applications.

Supplementary Materials

The following supporting information can be downloaded at the website of this paper posted on Preprints.org.

Author Contributions

Conceptualization, F.J.S.; Rheological experiments, S.C.W., F.J.S., L.L; blend and sample preparation, S.C.W., S.T.D.; Morphological characterization experiments, S.C.W., F.J.S., C.S.M.; data processing analysis, S.C.W., F.J.S.; writing—original draft preparation, S.C.W.; writing—review and editing, F.J.S, X.Z., S.H., S.H.-W., S.C.W.; supervision, F.J.S.; project administration, F.J.S.. All authors have read and agreed to the published version of the manuscript.

Funding

This research was funded by the National Science Foundation of China (5221101262) and the Shenzhen Project (JCYJ20210324093205013).

Data Availability Statement

The raw data can be extracted from the provided graphs in SI or is available from the authors upon request.

Acknowledgments

The authors would like to acknowledge funding from the National Science Foundation of China (5221101262) and from Shenzhen City (JCYJ20210324093205013). The authors thank the School of Materials Science and Engineering, Shenzhen University for the SEM and FTIR-characterization. This work was created based on the first author’s MSc-thesis using ChatGPT to translate the text from Chinese and polish the language.

Conflicts of Interest

The authors declare no conflict of interest.

Sample Availability

Samples of the compounds ... are available from the authors.

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Figure 1. SEM characterization of gel samples: (a&a’) pure acrylamide hydrogel, (b&b’) pure SA hydrogel, (c&c’) PAAM/SA composite hydrogel (samples S1-30).
Figure 1. SEM characterization of gel samples: (a&a’) pure acrylamide hydrogel, (b&b’) pure SA hydrogel, (c&c’) PAAM/SA composite hydrogel (samples S1-30).
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Figure 2. (a) Schematic diagram of sample preparation and internal network structure, (b) FTIR analysis of three gel samples, (c) SA chain segments supramolecularly "cross-linked" by calcium ions, (d) interactions between AM monomer and MBAA.
Figure 2. (a) Schematic diagram of sample preparation and internal network structure, (b) FTIR analysis of three gel samples, (c) SA chain segments supramolecularly "cross-linked" by calcium ions, (d) interactions between AM monomer and MBAA.
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Figure 3. (a) Viscosity characterization of sample S1 (1.67 wt% SA) and S2 (2.67 wt% SA) precursor solutions at different pH, (b) Viscosity characterization of SA aqueous solution at different pH.
Figure 3. (a) Viscosity characterization of sample S1 (1.67 wt% SA) and S2 (2.67 wt% SA) precursor solutions at different pH, (b) Viscosity characterization of SA aqueous solution at different pH.
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Figure 4. Creep recovery behavior of sample: (a) S1 (SA=1.667wt%), (b) S2 (SA=2.667wt%). (a and d) strain vs. time, (b,c,e and f) log. creep and creep recovery compliance vs. log time.
Figure 4. Creep recovery behavior of sample: (a) S1 (SA=1.667wt%), (b) S2 (SA=2.667wt%). (a and d) strain vs. time, (b,c,e and f) log. creep and creep recovery compliance vs. log time.
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Figure 5. (a and b) Frequency sweep curve of sample S1 showing the storage (a) and the loss modulus (b). (c) Relationship between loss coefficient and angular frequency, and (d) relationship between modulus of sample S1 and calcium ion concentration.
Figure 5. (a and b) Frequency sweep curve of sample S1 showing the storage (a) and the loss modulus (b). (c) Relationship between loss coefficient and angular frequency, and (d) relationship between modulus of sample S1 and calcium ion concentration.
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Figure 6. Strain sweeps of S1-0 with increasing and decreasing strain amplitude γ 0
Figure 6. Strain sweeps of S1-0 with increasing and decreasing strain amplitude γ 0
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Figure 7. Dynamic strain sweep curves and analysis of nonlinear parameters for gel samples with different calcium ion concentrations. DSS curves: (a) sample S1, (d) sample S2; analysis of nonlinear parameters I3/I1 and Q: (b&c) sample S1, (e&f) sample S2; (g&h) characteristic coefficients determined by nonlinear limits of S1 and S2; (i) relationship between intrinsic nonlinearity Q0 and calcium ion concentration.
Figure 7. Dynamic strain sweep curves and analysis of nonlinear parameters for gel samples with different calcium ion concentrations. DSS curves: (a) sample S1, (d) sample S2; analysis of nonlinear parameters I3/I1 and Q: (b&c) sample S1, (e&f) sample S2; (g&h) characteristic coefficients determined by nonlinear limits of S1 and S2; (i) relationship between intrinsic nonlinearity Q0 and calcium ion concentration.
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Figure 8. Viscous Lissajous curves of sample S1 at varying calcium ion concentrations with different γ0.
Figure 8. Viscous Lissajous curves of sample S1 at varying calcium ion concentrations with different γ0.
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Figure 9. (a) strain hardening ratio S, (b) shear thickening ratio T versus strain for sample S1. (c) strain hardening ratio S, (d) shear thickening ratio T versus strain for sample S2. (e and f) Chebyshev coefficient (e3/e1, and v3/v1) versus strain for sample S1.
Figure 9. (a) strain hardening ratio S, (b) shear thickening ratio T versus strain for sample S1. (c) strain hardening ratio S, (d) shear thickening ratio T versus strain for sample S2. (e and f) Chebyshev coefficient (e3/e1, and v3/v1) versus strain for sample S1.
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Figure 10. Tensile stress-strain curves of the S1- (a) and S2-series (c), corresponding tensile strengths and toughnesses (b and d) at different calcium ion concentrations.
Figure 10. Tensile stress-strain curves of the S1- (a) and S2-series (c), corresponding tensile strengths and toughnesses (b and d) at different calcium ion concentrations.
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Table 1. Names and monomer concentrations of all samples used in this study.
Table 1. Names and monomer concentrations of all samples used in this study.
Sample Name AM (wt%) SA (wt%) MBAA (wt%) TEMED, (wt%) KPS (wt%) X (mg/ml) = C(Ca2+)
S1-X 16.67 1.667 0.01 0.167 0.067 0，5，10，20，30，40，60，80
S2-X 16.67 2.667 0.01 0.167 0.067 0，5，10，20，30，40，60，80
Table 2. Dynamic strain sweep parameters.
Table 2. Dynamic strain sweep parameters.
Interval 1 Interval 2 Interval 3 Interval 4 Interval 5
γ 0 (%) 0.01 → 10
10 → 0.01		 0.01 → 30
30 → 0.01		 0.01 → 100
100 → 0.01		 0.01 → 300
300 → 0.01		 0.01 → 1000
1000 → 0.01
ω   (rad/s) 1 1 1 1 1
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