Microstructural behavior of magnetorheological elastomer undergoing durability evaluation by stress relaxation

The widespread use of magnetorheological elastomer (MRE) materials in various applications has yet to be limited due to the fact that there are substantial deficiencies in current experimental and theoretical research on its microstructural durability behavior. In this study, MRE composed of silicon rubber (SR) and 70 wt% of micron-sized carbonyl iron particles (CIP) was prepared and subjected to stress relaxation evaluation by torsional shear load. The microstructure and particle distribution of the obtained MRE was evaluated by a field emission scanning electron microscopy (FESEM). The influence of constant low strain at 0.01% is the continuing concern within the linear viscoelastic (LVE) region of MRE. Stress relaxation plays a significant role in the life cycle of MRE and revealed that storage modulus was reduced by 8.7%, normal force has weakened by 27%, and stress performance was reduced by 6.88% along approximately 84,000 s test duration time. This time scale was the longest ever reported being undertaken in the MRE stress relaxation study. Novel micro-mechanisms that responsible for the depleted performance of MRE was obtained by microstructurally observation using FESEM and in-phase mode of atomic force microscope (AFM). Attempts have been made to correlate strain localization produced by stress relaxation, with molecular deformation in MRE amorphous matrix. Exceptional attention was focused on the development of molecular slippage, disentanglement, microplasticity, microphase separation, and shear bands. The relation between these microstructural phenomena and the viscoelastic properties of MRE was diffusely defined and discussed. The presented MRE is homogeneous with uniform distribution of CIP. The most significant recent developments of systematic correlation between the effects of microstructural deformation and durability performance of MRE under stress relaxation has been observed and evaluated.

The interest in the development of magnetorheological elastomers is fast growing due to their ability to respond and behave relative to the external magnetic stimuli. This surpasses the potential of MRE beyond conventional materials and acknowledged scientifically as smart materials. Distinctively, magnetorheological elastomer (MRE) is composed of a soft elastomeric matrix that is embedded with magnetizable particles at the desired proportion. Possess a viscoelastic performance, MRE stiffness and damping behavior can be rapidly, continuously, and reversibly controlled by an external magnetic field [1][2][3] . These changeable properties bring MRE at the highest degree of hope to be used in prominent adaptive engineering applications as currently available for restrictedly small deformation and vibration control [4][5][6] . Existing research 7 recognizes the critical role played by MRE on a par with similar materials such as rubber and elastomer. MRE has increasingly reached into new engineering applications and bound with irrefutable scientific procedure evaluation, particularly on its long-term performance ostensibly durability.
Durability however has long been a question of great interest in a wide range of engineering material fields and plays a fundamental role in determining material resistance to any change in property levels due to the

Results and discussion
Stress relaxation. The performance of the MRE sample was first evaluated by its ability to store deformation energy elastically through storage modulus characterization. The plotted graph in Fig. 1 shows the comparability assessment of this behavior corresponds to the early stage durability in the range of 0-12,000 s, which indicates as 1st, 2nd and 3rd interval in the graph, and the final range from 72,000 to 84,000 s, at indication of 3rd last, 2nd last and final interval in the graph's legend. There were three set of 4000 s intervals for each range. As can be seen, the characteristic graph features distinctly show a storage modulus lowering trends with the increase in the test time at a constant 0.01% of strain. At the initial phase, storage modulus values were steadily decreased after the first 4000 s but with less diminution reaching to the third interval of test time. This behavior may be due to the MRE system that has microstructurally reversible aligns at still higher modulus of resilience. However, at instantaneous stress continuously applied to the system, the molecular chains were stretched, disentangled, and more expeditiously accumulated with the cross-linked of the MRE matrix. This continuous applied stress at similar constant strain has leisurely decreased the proportionality behavior of the MRE, and the covalent cross-linkages compromising the return-ability of the stretched chains. However, at a wider range of test duration up to 84,000 s, localized strain and microplasticity were suspected to be developed in the system. Furthermore, at a larger scale localization associated with the test time increase, the development of plasticity www.nature.com/scientificreports/ at the molecular level within the narrow regions of shear bands has imparted softening behavior to the MRE. As a result, the storage modulus was observed to decrease by 8.7% at the end of the test duration. Nevertheless, the storage modulus in the final phase interval performed slightly different from the beginning phase interval. Throughout the process of cumulatively decreased in storage modulus, the elastic response of MRE energystoring ability has reached a plateau, attributed to the stability of the molecular structure of the MRE. Throughout the test, the MRE sample notably suffered from the shear-contact force generated from the rheometer apparatus by a parallel rotary plate. This is associated with the shear property by the interaction between particles and the interactions between the particles and the matrix, which is similar to the mechanism associated with the normal force results 32 . Figure 2 shows the experimental results of normal force under oscillatory shear test. The sample was pre-compressed with the contact force to avoid slippage between the sample and the shear plate during the test. The pre-compression produced an initial 5.9 N normal force on the sample while the compressive strain was maintained constant. In this work, the interesting circumstances are the sheardeformation durability related to normal force throughout 4000 s. A steeper lessening trend was observed for the normal force at the beginning of 4000 s interval of the durability test, with some distortion and micro-changes while reaching the earliest 600 s of the shear oscillating time. The data accumulation at this point has just reached stability of the sample and this phenomenon was suspected to be associated with the random arrangement of the molecular chain structure, which suddenly slid between particles-matrix and the presence of micro-sized voids.
Continuous evaluation led the sample to be more stable and consistent in managing molecular restructuring and captivating with applied normal force and stress. However, the constant strain of 0.01% executed throughout the test thus resulting in the development of larger localized failure. The MRE sample was strained up to 84,000 s and the additional continuous stress applied to the sample was then distributed to the localized region of the molecular chain structure. As the sample held for constant deformation, the stress in the sample was reduced with time and this phenomenon is likely to be responsible for stress relaxation. The shear plasticity is assumed to occur through a series of this molecular local restructuring. Besides of fluctuated micro-stress at the molecular level as discussed earlier, the MRE sample was suffered from microplasticity, where the sample was all-encompassing in the elastic domain while some local areas were in the plastic domain. This permanent transformation has somehow reduced the elastic potentiality of the MRE system. Eventually, normal force was gradually reduced throughout the test associated with this micro-plasticity deformation by approximately 27%. Undisputable observation finds that normal force was solely reduced expeditiously during the initial phase and  www.nature.com/scientificreports/ lessen imperceptibly as reached to the final phase. Thus, an assumption can be made that with longer duration, the sample microscopically attains the stability and therefore, lesser effort for deformation would take place. Consequently, the incremental value of normal force applied on the sample while sheared, has been found to be indiscernible along the process. The long-term behavior prediction from time-dependent viscoelastic properties of MRE was investigated by stress relaxation. In the course of stress relaxation, stress deteriorated with time under conditions of constant deformation as shown in Fig. 3. In this study, the sample was tested up to 84,000 s and constant strain at 0.01%. At the beginning of the 4000 s time interval, the curve shows an initial instantaneous stress which increased with the increase in relaxation time. A slight increase in the stress relaxation rate, which then endured with balanced stress as indicates from the graph was agreed with the fact that the molecular chain of the matrix MRE was stretched, slide, and aligned according to the stress applied simultaneously along the process. At tremendously low strain levels, the sample took less time to achieve the balance stress. However, the interminable shear stress that has been applied and rapidly strained at a fixed deformation led to the structure relaxation mechanisms such as molecular relaxation, disentanglement of cross-links, and structural rearrangement. These mechanisms were contributed to the degradation of the sample stress relaxation's resistance property. As a result, by the end of durability evaluation, the stress relaxation behavior was decreased by approximately 6.9% with the increase of shear durability test time, particularly between the initial and the final phases of the test duration. This trend has particularly met the rubbery plateau characteristic of viscoelastic materials and agrees with literature 18 .
In this study, the durability was subjected to the stress relaxation, in which the sample was kept sheared with a constant strain throughout the entire test duration as an additional deformation beyond the assigned strain limit was impossible to have occurred. Therefore, stress relaxation can only occur on the molecular level. The relaxation mechanism that occurred in the sample was observed microscopically to prove that the decrease in the relaxation behavior was related to the disentanglement of cross-links and structural rearrangement of the molecular chains, which may occur from molecular rupturing. That behavior is common in the amorphous polymers, pertinently to the sample used in this study. Additionally, details of the microscopic investigation of this original durability evaluation method has led to interesting and novel findings related to this phenomenon.
Microstructure characterization. The theoretical concept of molecular chain structure and cross-linkages in sheared amorphous solid was ideally relevant to MRE evaluation due to its matrix amorphous molecular structure 18,23,41 . Inaugurate to the conceptualization for MRE, molecular chain structure and cross-linkages of cured MRE can be simplified into schematic details as in Fig. 4. Cross-linkages developed during the curing process of MRE is determining its elasticity and deformation limits. Such cross-linkages represent a critical structural factor that imparts high elastic properties and made the MRE system more rigid to prevent any viscous dominant response.
Stress relaxation happened on the molecular scale and involved changing the molecular chain arrangement. Besides, phenomena of stress relaxation occurred through a variety of mechanisms including disentanglement of cross-links, elastic stretching, inelastic deformation, structural change by phase transformation, structural rearrangement due to rupturing, microphase separation, microplasticity and shear bands formation by localized strain. The fundamental theoretical concept of molecular deformation of amorphous chain structure is illustrated in Fig. 5. As the MRE was imposed by the incessant shear stress at constant strain, the stress was distributed over the molecular structure and this would disentangle the chains to create the molecular slippage. As more slippages and losses of cross-links occur in the MRE, the molecular structure becomes inadequately able to be reconfigured and resulted in a permanent deformation, as shown in the schematic figure.
MRE sample with 70 wt% CIP and 30 wt% silicon matrix is cured without the magnetic field and homogeneous distribution of the particles was observed with some agglomeration of particles as shown in FESEM images in Fig. 6a,b. As can be seen from the image (a) and its magnified version, the protruding granulates are CIP and the background base material is the silicon rubber. Before the durability evaluation, CIP seems uniformly distributed over the silicone rubber and it varies in sizes conforming to the description given by the supplier as stated in the experimental details (3.8-5.3 μm). A schematic representation of the sample with randomly dispersed particles (isotropic) manifesting how rigid spheres laid in the un-deformed state is shown in Fig. 6c. Before the durability www.nature.com/scientificreports/ test, amorphous molecular structures of the matrix were un-stretched with initial cross-linkages position generated after cured with the curing agent. The CIP is represented by a rigid sphere of crystalline molecular structure arranged randomly within the matrix amorphous molecular structure.
Having an amorphous molecular structure, the sheared samples at this low strain experienced an interesting phenomenon, which is called strain localization in which the materials deformed plastically in very narrow regions referred to as shear bands 23 . Even though this phenomenon occurs typically at very low strain, the shear velocity gradient during the test has dominantly affected the development of the shear bands comprising their size and shapes. The velocity gradient develops across the sample during shear is higher at the most outer section and diminishes towards the center of the sample. In this study, the shear profile generated across the sample was found very much affected by the shear band development and its mechanism. Figure 7a shows the FESEM image of shear deformation closer to the center of the sample after durability evaluation (84,000 s). The FESEM image is generated from Piece 4 as shown in Fig. 15. As the sample was focused closer to the center region, the shear band was almost invisible, and apparent tiny stretched mark was uniformly developed as shown in the figure. Such tiny marks are due to the lesser stress experienced by the region, attributed to the different velocity gradient of shear stress across the sample. Besides, indiscernible marks around the particle and development of minuscule patterns on the matrix, it can be schematically represented as shown in Fig. 7b,c. Figure 7b demonstrates the bond stretching along the crystallographic plane and amorphous structure stretched with some non-permanent molecular slippage.
However, the stretched region was just below the localized elastic limits among the entangled amorphous molecular chains, and cross-linkages were then reversibly aligned. No permanent deformation occurred during the stretching at this stage, therefore no visible marks can be noticed. In contrast within the matrix domain, some cross-linkages of the molecular structure were uneasily reconfigured and less survived by breaking the cross-linkages from the stretching process. The disentanglement of the molecular structure has resulted in the slippage and breaking of the interconnected cross-linkages especially beyond the elastic limit of the localized phase. Steady shear stress that applied through the test has brought this phenomenon to the permanent deformation and forced it to remain localized in the confine shear band, as observed in Fig. 7c.   Fig. 8a. The FESEM images taken from Piece 1, 2 and 3, as in Fig. 15 produce comparable patterns of shear bands. Three samples to verify the phenomenon of the shear band offered adequate evidence for to summarize the characteristics of the mechanism throughout this discussion. More permanent molecular slippage occurred, and cross-linkages of amorphous chains were broken as a consequence of uneasily reconfiguration and this phenomenon has simultaneously softened the matrix chains. Splitting the soften chains and abided harder domains of the elastic matrix have produced microphase separation, between the elastic and microplasticity deformations.
Microphase is the representative of the micro-sized domain of the matrix whereas the shear band falls within this phase separation. At this stage, a microscopically shear band was identified having an average thickness of < 1 µm (0.5-0.8 µm). The stretched chain in this phenomenon was destroyed and diminished the covalent bond of the cross-linkages as illustrated in Fig. 8b. The continual shear load has repeatedly softened the chains causing their pending to be exceeding the elastic limit for this localized region. Subsequently, the plastic flow has likely taken place in the inner portion of the molecular chain, slightly beyond the localized limit. However, there must be an outer region belong to the elastic matrix domain, which is still elastically strained, because the stress in this domain is falling below the elastic limit 42 .
On the other hand, towards the edge of the sample, shear stress was completely contributed to the angular displacement of the sample. This region having a maximum shear velocity gradient and stress relaxation through molecular motion. The motion was produced from the stretched molecular chain of the amorphous matrix domain. As the stretching magnitude is kept constant, no macroscopic movement is possible. Therefore, stress relaxation of the molecular structure has been mainly subjected to the disentanglement of the amorphous molecular chains in the soft domain of the matrix, at the micro-level. Furthermore, fluctuating stress developed in the amorphous molecular chain is attributed to the deformation and the rupture of the chain together with the cross-linked at soft dominated domain 20 . The diversity of the soft domain chain structure was contributed by the homogenous distribution of CIP, which correlated to the reduction of the elastic matrix region.
As presented in Fig. 9a, the FESEM image shows the uniformed formation of shear bands visibly as stretched marks of microplasticity. In general, a clear formation of localized shear bands was achieved after the system is optimally sheared. The strain localization appears not to be persistent in this region and contributed to the uncertainty form of plastic strain. The plastic straining of the amorphous rubbery matrix at the molecular chain www.nature.com/scientificreports/ level has turned into stretched marks within the matrix, in which this phenomenon was not observed in the original sample before the test (Fig. 6).
As the shear velocity gradient is greater within this area, the shear bands become progressively thicker. The deformation mechanism moves through the shear direction and the deformations remain localized along the period of test duration. On average, the shear band deformation corresponded to the molecular chain disentanglement, breaking of cross-linkages, and the sequence of molecular slip events that contributed shear bands to  www.nature.com/scientificreports/ become homogenous. Figure 9b illustrates the schematic progression of the localized matrix amorphous structure towards stress fluctuation developed by continuous shearing. Due to stress relaxation, the remaining rigid region however acquired rather a uniform distribution of stresses, while large fluctuations remained within the shear bands 23 as demonstrated in Fig. 9c. At a longer period of test time, a range of elastic interaction, slip and rupturing of molecular chains, spatial distribution, and localization of strain have become apparent with the sighting of the shear bands and microplasticity marks, which obliquely aged the sample associated with the time elapsed. The condition of CIP and silicon matrix after durability evaluation, particularly after 84,000 s test duration can be closely observed in Fig. 10. At several locations, particles demonstrated more protruding out from the localized area surrounded by the shear bands deformation. This may denote a notable characteristic of the condition of long-term stress relaxation. This fascinating phenomenon may have led to the embracing of the dispersed CIP and some portion of the enclosed matrix between them, molecularly known as secondary interaction. Secondary interaction in this study is referred to as the limited restrained region between matrix amorphous and CIP crystalline molecular chain structure. Secondary interaction was developed by a crystallinity molecular structure embedded in the amorphous matrix and this interaction is much stronger than the amorphous structure itself due to the presence of CIP. In the amorphous matrix, the uniformed dispersal of particles has increased the diversity of soft localized regions and simultaneously promoted the microplasticity deformation of shear bands through the entire sample area. The potential of hard domain in this soft localized region decreased and the microphase separation between hard and soft domains imparted by shearing shoved away the particles to remain at a high entropy state.
In this investigation, the shear stress distributed uniformly to the region with less fluctuation in the primarily sheared region. As the fluctuated stress region was forced to remain localized in the shear band, a permanent www.nature.com/scientificreports/ microplasticity was developed. However, passing an obstructive particle, the soft domain of the shear band was forced to deviate alongside the hard domain molecular structure of the particle-matrix bond (i.e., secondary interaction). Besides, the dragged shear force after the deviation induced the microphase separation of shear bands, particularly between hard and soft domains. The shear force applied to the sample and passed through a particle at a localized soft domain is schematized in Fig. 11. Determination of micro-size particles distribution and formation of micro-sized of microplasticity shear bands was analyzed using AFM, which is an important technique for characterization of microphase separation of the shear bands 20 . In this study, the sheared MRE sample was analyzed using the AFM tapping mode technique to identify surface topography and reliable identification of the differences between the region with different phase variations. In-phase image over 100 µm scan area obtained by this taping method is shown in Fig. 12. AFM 3D-image processing has validated previous morphology investigation where particles are more protruded in the localized strained surface of sheared sample with shear bands deformation.
Measurement of the average diameters of the homogenously distributed particles was achieved from this scanned region. The topography measurement indicated points of 1 to 11 representing the position of pultruded CIP been measured. At more than 10 different identified pultruded CIP, it was found that the particle diameter values are considered in a good agreement with the FESEM observation in Fig. 13 and that they also comply with the standard dimension given by the manufacturer.
Morphological features of inter-domains and microphase separation of soft and hard localized domain regions can also be observed using this AFM taping method. This method systematically sets the phase offset of the harder domain with a lighter-color appearance whereas the softer domain appears darker 20,39 . These offsets concomitantly represent the modulus of the individual domain within a multi-domain of MRE resultant from stress relaxation durability shear test. Figure 14 clearly shows that a higher modulus domain of the matrix shown lighter color whereas, the lower modulus domain of shear bands appears darker. These observations agree with the expectation that shear bands were an amalgamation of micro-plastically stretched amorphous molecular chain structure. As the molecular chain stretched beyond the elastic limits of the localized strain region, crosslinkages suffered from rupturing, and without (little) cross-linkages, the chain uneasily reconfigured resulting in permanent transformation of plasticity. Micro-sized plasticity localized domain developed from this procedure originated shear bands 'scar' with softer domain as indicated by the darker color appearance in the AFM image.
A localized scan area of approximately 20 µm has permitted an advanced evaluation of the shear bands. Utilizing the topography measuring function of AFM analysis, the shear band of A is 0.53 µm in width, B is    43 and previous work on similar materials. Silicone rubber and iron particles were mixed in a beaker then mechanically stirred at a speed of 200 rpm and the mixture (NS625tds) was subsequently mixed with 0.1 wt% cross-linking agent (Nippon Steel Co., Japan). The agent was added for the curing process and followed the procedure provided by the Nippon Steel technical bulletin 44 . The whole mixture was then slowly poured on the mold base and spread evenly to ensure good surface finishing of the cured MRE. The curing process was carried out for 2 h at room temperature in a cylindrical closed-mold with a 50 mm diameter and 1.2 mm thickness of the circular sinking section inside the mold at off-state condition (no external magnetic stimuli). The degassing protocol was followed to eliminate the presence of air bubbles in the sample. Excessive  www.nature.com/scientificreports/ matrix bleed-out along the edges of the MRE disc sheet was removed using a trimming knife. Finally, MRE circular disc sample was cut out using 23 mm hollow hole punch tools for dynamic testing.

Measurement of durability by stress relaxation.
The shear stress relaxation behavior of the MRE samples were tested under torsional shear mode using an oscillation parallel plate rheometer (Physica MCR 302, Anton Paar Company, Graz, Austria). MRE circular samples with 23 mm diameter and 1.2 mm nominal thickness were used. The rheometer was priorly initialized to the desired test condition (temperature, force, gap) and the measuring tool was aligned and attached to the quick connector coupling. A rotary disc parallel plate (pp20 rod) with a 20 mm diameter and 1 mm thickness was used. The sample was centrally placed on the stationary base mount of the rheometer and preloaded before the oscillation using rotary disc and then subjected to an initial normal force of 5.9 N to avoid wall slip 45 . The study 46 suggested a technique used to have low initial normal force, but this technique was not commonly used by other researchers to investigate shear deformation under oscillatory rheometric and no available literature in the stress relaxation study was used the technique in their analysis. The measurement of significant shear stress relaxation parameters was conducted using the oscillatory test method which the measuring device oscillated around the axis during the test. The shear deformation was set at 0.01% constantly throughout the test and this was highlighted as the pristine attempt to stress relaxation test for MRE samples nearest to its state of rest to known as an equilibrium condition. The value was obtained by linear viscoelastic (LVE) determined on the basis of the visual technique and the procedure used in the literature 47 . Earlier, the amplitude sweep data for the LVE measurement was acquired from the rheological test of similar materials. The test frequencies were set at 1 Hz all the time to ideally simulate the real working condition in the application and consideration of the influenced by the shear velocity gradient during the test. The time interval of each test condition was set at every 4000 s and the total duration of the test reached up to 84,000 s to allow a wider range of behavior observation. Samples for microstructure observation were prepared before and after the durability test by cutting them using utility knife with an extremely sharp blade steadily set perpendicular to the cutting edge of the sample (around the edges area of the MRE) into 1 mm X 10 mm. The cut area was selected based on the understanding that the shear center point of the sample was not caused by any torsional deformation (imaginary point), compared to the shearing acted on the edge of the sample which contributed to the maximum angular displacement. One of the pieces was cut from the edge towards the center of the sample to verify the midpoint condition as shown in Fig. 15a. A total of four trimmed pieces (from one sample) were then stacked to each other to get a complete evaluation of each edge's cross-sectional area and the area closest to the center as shown in Fig. 15b. The correlation and feasible extent of data for each cross-sectioned are expected to represent the actual condition related to the randomly dispersed particles in the matrix. Both sample's surfaces were sputter-coated with 1 nm thick platinum using an auto fine coater device (JEC-3000FC, JEOL, Japan) operated at 20 mA for 25 s. Subsequently, samples were placed into holders and investigated with a field emission scanning electron microscope (FESEM, JSM-7800F Prime, JOEL, Japan) operated an accelerating voltage of 1 kV. We have carried out a preliminary and potential analysis on the other related sample. We've tried a few places on the sample and we've seen them under FESEM. No proof of shear band is found other than the position chosen as shown in Fig. 15.
Observation for morphological studies on the MRE sample was further investigated using tapping-mode AFM analysis. This open-loop mode operated on a NanoWizard 3, NanoOptics AFM (JPK Instruments, Germany) www.nature.com/scientificreports/ using a nanosensor tapping-mode monolithic-silicon AFM probe-type single-beam cantilever supplied by Budg-etSensors, USA. The cantilever had a nominal length of 125 µm and a nominal force constant 40 N/m, and a resonance frequency of 300 kHz. The non-coated tip of the cantilever having a rotated shape with a height of 17 µm and a radius of less than 10 nm. The initial scan area Details dimension design and full technical data of the AFM probes provided by manufacturer Budget Sensors (Innovative Solutions Bulgaria Ltd., Bulgaria).was set at 100 µm and details evaluation of the sheared sample with a particular failure mechanism was settled at approximately 20 µm scan area. Packaged analysis software was manipulated for the measurement and phase images.

Conclusions
Elastomer based magnetorheological material consisting of silicone rubber matrix was successfully fabricated with 70 wt% CIP and cured under natural conditions without an external magnetic field. Morphological evaluation by FESEM images revealed that CIP was uniformly disseminated and well bonded in the silicon matrix. The durability performance of MRE was comprehensively investigated by the stress relaxation assessment at a constant 0.01% strain within the LVE region for a total of 84,000 s test duration. At such low constant strain, and a relatively long test period, this study provides important contribution to understanding the MRE system towards stress relaxation behavior. In consequence, stress relaxation performance was reduced by 6.9% throughout the test period. Rheological evaluation by storage modulus subjected to stress relaxation was found to decrease by 8.7%. The accompanying shear-deformation durability that related to the normal force over the same test period was also investigated and found to gradually decrease by 27%. Concession to the MRE performance at storage modulus, normal force, and stress relaxation have motivated the extensive analysis of the possible phenomena at the microscopic level. The cross-sectioned surface condition of sheared samples was investigated via FESEM and exhibited a new finding of the failure mechanism in MRE. Stress relaxation has developed strain localization and produced microplasticity in very confined regions called shear bands. The amorphous molecular chain structure and cross-linkages of the matrix were suggested to be responsible for this permanent plasticity mechanism. Morphological analysis and measurement of the appeared shear bands and related deformations that have never been implemented in the investigation of MRE stress relaxation were then evaluated by AFM for the first time. Physical features of the shear bands have been successfully measured using the AFM topography measuring technique.