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Article

Butyl Rubber-Based Composite: Thermal Degradation and Prediction of Service Lifetime

by
Phuong Nguyen-Tri
1,*,
Ennouri Triki
2 and
Tuan Anh Nguyen
3
1
Department of Chemistry, University of Montreal, Montreal, QC H3T 1J4, Canada
2
Department of Mechanical Engineering, McGill University, Montreal, QC H3T 1E2, Canada
3
Institute for Tropical Technology, Vietnam Academy of Science and Technology (VAST), Hanoi 122100, Vietnam
*
Author to whom correspondence should be addressed.
J. Compos. Sci. 2019, 3(2), 48; https://doi.org/10.3390/jcs3020048
Submission received: 11 April 2019 / Revised: 25 April 2019 / Accepted: 26 April 2019 / Published: 5 May 2019
(This article belongs to the Special Issue Durability of Composites Under Severe Environmental Conditions)
Browse Figures
Versions Notes

Abstract

:
Butyl rubber-based composite (BRC) is one of the most popular materials for the fabrication of protective gloves against chemical and mechanical risks. However, in many workplaces, such as metal manufacturing or automotive mechanical services, its mechanical hazards usually appear together with metalworking fluids (MWFs). The presence of these contaminants, particularly at high temperatures, could modify its properties due to the scission, the plasticization and the crosslinking of the polymer network and thus lead to severe modification of the mechanical and physicochemical properties of material. This work aims to determine the effect of temperature and a metalworking fluid on the mechanical behavior of butyl rubber composite, dealing with crosslinking density, cohesion forces and the elastic constant of BRC, based on Mooney–Rivlin’s theory. The effect of temperature with and without MWFs on the thermo-dynamical properties and morphology of butyl membranes was also investigated. The prediction of service lifetime was then evaluated from the extrapolation of the Arrhenius plot at different temperatures.

1. Introduction

Rubber is one of the most important materials for various industries, especially in petroleum, construction [1] and protection material sectors [2,3]. Protective gloves are often covered by an elastomeric coating to protect against chemical and mechanical damages due to its good resistance against abrasion, oils and chemicals, and its excellent damping properties [4,5,6,7,8,9,10,11,12]. However, the swelling phenomena involving the degradation of the mechanical properties of these materials have often been observed [13]. Butyl rubber-based composite (BRC) is one of the most effective materials against chemical risks [4,13]. However, this material is sensitive to nonpolar solvents or metalworking fluid. These non-polar compounds can easily penetrate into the polymer and lead to a dramatic change of material properties. These problems represent a large risk for users and thus require a better understanding of the problem [13,14]. Like other polymers, butyl rubber-based composites can be affected by oxidation, and this effect becomes more intensive at a high temperature.
The swelling characteristics of rubbers are related to the deterioration of mechanical properties and may affect their failure mechanics. Currently, there are no models to predict the failure mechanisms in the presence of industrial contaminants. Several investigations have been reported on the effect of industrial contaminants on the morphology, mechanical properties and structure of glove material. In previous works [15,16,17,18,19,20,21,22,23,24], we reported that polymers and composites [16,17,18,19,20,22,23,25,26,27,28,29,30,31,32,33,34,35,36,37,38,39,40,41] can be degraded by several aging agents such as heat, water, humidity, oxygen, ozone and various other environments factors [16,17,18,19,20,21,22,23,24]. The scission, crosslinking and plasticization of polymer networks may occur and led to severe deterioration of the mechanical and physicochemical properties of the material [42], which are quite important with regard their applications in various fields of mechanical engineering.
Many researchers have attempted to understand the relationship between morphological and property changes within the microstructure of rubber material [43], especially with a failure mechanism of elastomer, by using several traditional test methods, including the tensile test, strain-stress relation and compression measurements [44,45,46]. Mooney–Rivlin’s equation is usually used to evaluate the property-structure relationship of material by analyzing the tensile stress-strain curves of materials. In this model, Rivlin [47,48] proposed an extension of the Mooney’s model by describing W as a polynomial series in (I1 − 3) and (I2 − 3):
W = ∑i,j=0 Cij.(I1-3)i(I2-3)j with C∞ = 0
During a simple tensile test, we define:
I1 = λ2 + 2/λ; I2 = 1/λ2; I3 = 1
The stress σn is given by the equation:
σn = 2(λ − 1/λ2)(dW/dI1 + dW/λ.dI2)
According to the behavior law, we can still write:
σn = λ.dW/dλ + dW/λ.dλ2
From which:
σn = 2 (C1+C2/λ) (λ − 1/λ2)
where W is the density of deformation energy, λ is the elongation of material and C1 and C2 are two elastic constants associated with network structure and the flexibility of the network, respectively. According to Equation (5), the plot of σn/2 (λ − 1/λ2) as a function of λ−1 should be linear and the C1 constant is directly calculated by extrapolating the linear portion of the curve up to λ−1 = 0, and the C2 constant is the curve slope. In the molecular aspect, this constant C1 of Mooney–Rivlin’s model is characterized by the density of crosslinking between elastomer chains [49,50]. It can be used to evaluate the physical manifestation of the degree of crosslinking N [51,52].
N = 2C1/kT
The constant C2 is associated with the cohesion forces (intramolecular bonds and interchain) and reinforcement-matrix interactions [52]. This constant also reflects the flexibility of the structure of the material [53]. It depends on the degree of vulcanization, which increases with the increasing of the crosslink density [53]. The values of the two constants C1 and C2 that can be determined during the tensile tests allow for studying the influence of the crosslinking degree and network structure on the stiffness of the material. Gordon [52] determined the Young’s modulus according to C1 and C2:
E = 6(C1 + C2)
It reported that the constant C1 usually remains constant with the variation of the swelling degree of the polymer material, while the constant C2 decreases with the increase of the swelling degree [54,55,56]. It lacks a systematic ability to research the effect of temperature and metalworking on the morphology, properties and structure of elastomer materials.
In this study, a butyl rubber membrane, representing a common material used in protective gloves, was used to determinate the swelling characteristics to metalworking fluid at various temperatures ranging from 80 °C to 120 °C. The elastic behaviors dealing with elastic constants, crosslinking density and modulus were continuously followed during the contamination procedure to evaluate the dominant parameter on polymer deterioration. The modification of morphology, tensile properties and physicochemical properties were also investigated.

2. Materials and Methods

2.1. Materials

The butyl rubber-based composite (BRC) membranes used in this work were made from butyl rubber with carbon black fillers. These commercial products (thickness of ~1.6 mm) were kindly supplied by MCMaster-Carr Inc. (Montreal, QC, Canada). An industrial metalworking fluid (MWF) used in this work, namely Milform 64 SST, was directly purchased from a company in the metalworking sector in Quebec, Canada. The chemical composition can be found in our previous publications [57,58]. The carbon black filler content in composite membranes was estimated to be about 52 wt% (by thermal gravimetric analysis (TGA) measurement).

2.2. Contamination Procedure

The elastomer membranes having the mass (m0) were immersed into MWF for different periods of time for the measuring of the swelling index changes according to the American Society for Testing and Materials (ASTM) D471-12 standard. They were then delicately wiped by thick wiping papers to remove the excess oil on the sample surface and reweighed (mt). The process was repeated until a saturated state was reached. The swelling index (M) was calculated according to the following equation:
M ( % ) = m t − m 0 m 0 × 100
where m0 and mt are the weight of the samples before and after their immersion in contaminant, respectively.

2.3. Scanning Electron Microscopy (SEM)

The scanning electron microscopy model Hitachi S570 was used to investigate the morphology and the fractography changes of samples before and after the contamination process. These observations served to examine the failure modes of morphology changes of the elastomer materials.

2.4. Tensile Tests

Tensile properties of elastomer membranes were measured with the dog bone rectangular samples. Measurements were performed with an Alliance 2000 (MTS) universal testing machine equipped with a 1000 N load cell and operated at a cross-head speed of 500 mm/min according to the ASTM D412-06 standard test method. For each condition, three replicates were measured, and the results were averaged. Figure S1 shows an example of train-stress curves of an original BRC. The samples were then placed into an oven to control the aging temperature. The samples were removed for each period to perform the analysis.

2.5. Thermal Gravimetric Analysis (TGA)

TGA was carried out with original and aged composite samples to evaluate the percentage of filler content and the effect of the aging process on the sample weight loss as a function of time. TGA was carried out in a nitrogen atmosphere at a heating rate of 20 °C/min using a Parkin Elmer TGA model 4000. Thermograms were recorded from 0 to 800 °C.

2.6. Dynamic Mechanical Thermal Analysis (DMTA)

The dynamic mechanical thermal property of the non-aged and aged BRC samples was measured by Instruments (DMTA, Q 800) at a testing temperature ranging from −100 °C to 0 °C with a heating rate of 5 °C/min.

3. Results and Discussion

3.1. Effect of Temperature on Mechanical Properties

The influence of temperature on the viscoelastic properties of BRC was investigated at three different temperatures ranging from 80 to 120 °C. Figure 1a shows the relationship between the constant C1 and the exposure time. It demonstrates that the highest value of constant C1 was observed at a temperature around 120 °C. At the beginning of the exposure (t ˂ 4 h), C1 underwent a significant increase, and then rapidly decreased before achieving a constant value. At a lower exposure temperature (80 °C and 100 °C), the variation of the constant C1 was not significant, represented by a slight decrease of C1 at the first hours of exposure then appeared to be converged to the similar value observed at 120 °C. These results allow the confirmation that the stiffness of butyl is optionally increased with temperature, as reported in the case of a neoprene membrane which was exposed to a high temperature [59]. Figure 1b shows the variation of C2 as a function of exposure time at different temperatures. The variation of the constant C2 at 80 °C appeared to be similar to that at 100 °C, with a parabolic shape curve. An increase in C2 at the first hours of exposition (t ˂ 4 h) was observed, and then it slightly decreased with time. It can be attributed to the increase of cohesive force at the first hours of exposition time, followed by a decrease [54]. This physical phenomenon was completely different to that observed at a higher exposure temperature (120 °C). The constant C2 decreased significantly from the first steps of exposure and went down to zero. These results are not surprising, and are in good agreement with the study published by Marck [54].
The synergy between the variation of C1 and C2 was also investigated, and the results are shown in Table 1. This synergy is determined by calculating the theoretical Young’s modulus by using Equation (7) and the experimental Young’s modulus from the first linear region of the force-displacement curves (Figure 1d). The obtained results show that the rigidity of the butyl remains almost unchanged at 80 °C. However, a significant increase of Young’s modulus with exposure time was recorded at 120 °C. This can be attributed generally to the increasing of crosslinking density (N) that may have occurred at a high temperature due to the vulcanization or reticulation of polymer chains. After 24 h exposure in MWF, the Young’s modulus seemed to increase at 100 and 120 °C (Figure 1c). Figure 1d demonstrates the tensile force of BRC as a function of exposure time, and it can be seen that the rupture properties remained constant during all exposure times regardless of the exposure temperature. The variation of tensile strength at the break with exposure time was not significant. This implies that the BRC has a relatively high resistance to temperature for a short time and the latter does not affect the mechanical failure behavior.

3.2. Effect of Simultaneous Temperature and Metalworking Fluid on Properties, Structure and Morphology

In the working condition, glove materials are often in contact with hot MWFs, generated by friction of machine devices. This factor could directly affect the protective performance of the glove materials. The effect of simultaneous temperature and MWFs on the properties of butyl membranes was investigated. Figure 2a shows the variation of the constant C1 as a function of expose temperature in the presence of a metalworking fluid (Milform 64 SST). As shown in Figure 2a, the changes of the constant C1 with an exposure time at 80 °C were substantially similar to that at 100 °C, thus these two curves are approximately superposed. However, at 120 °C, the curve tendency is different when compared with that at lower exposure temperatures, where C1 values dramatically dropped in the first hours of exposure and then tended to archive at a plateau region. Figure 2b shows the effect of temperature and MWFs on the constant C2. It demonstrates that the constant C2 rapidly decreased with the exposure time and approached to zero after 24 h of exposition. Therefore, the cohesive strength of the inter-chain eventually became weak [54] and the viscoelastic behavior may have also been affected. The results are in good agreement with that observed by Gumbrell et al. [60] and Allen et al. [61] in studying the aging process of natural rubber to different solvents.
The calculation of the Young’s modulus, in particular at 80 °C and 100 °C, highlights the effect of simultaneous temperature and contaminants on the rigidity of the material. A significant decrease of the Young’s modulus as a function of exposure time was observed (Table 2). This could be attributed to the reduction of the cohesive strength of inter-chains. The rigidity of butyl at 120 °C was unstable. The Young’s modulus first increased, then decreased before achieving a plateau region. This variation was possibly related to the changes in the cross-linking density (N) as shown in Figure 2c. This variation was due to the correlation between the constants C1 and C2. Similar behavior was also discussed by Nohilé et al. [4], demonstrating that the swelling of BRC by solvents led to an increase of the material rigidity due to the loss of fillers. The latter leads to a reduction of the tensile strength of BRC as shown in Figure 2d. It can be seen from these figures that the mechanical properties of the material were decreased regardless of what exposure temperatures were applied. It was observed that the longer the exposure time, the higher the loss of the mechanical properties.

3.3. Effect of Temperature and Metalworking Fuid (MWF) on Dynamical Thermo-Mechanical Properties

Dynamical thermo-mechanical analysis (DMTA) provides access to the elastic modulus and tangent values of materials. Figure 3a shows the example of Young’s modulus of the BRC membrane before and after aging at 100 °C during 24 h in MWF (Milform 64SST). The curves are recorded from the temperatures −120 °C to 70 °C. It shows that thermal degradation of the membrane in metalworking fluid significantly reduced its Young’s modulus. It is clearly seen that the Young’s modulus decreased from 1.45 × 107 to 4 × 106 MPa at −120 °C after aging at 100 °C for 24 h of exposure.
For an elastomer material, the glass transition temperature (Tg) is an important factor that directly involves the final properties of materials. This parameter is directly determined by DMTA curves, corresponding to the maximum peak of tan (δ). Figure 3b shows the example of the variation of tan (δ) of aged and un-aged samples at 100 °C with different aging times. It can be seen that the curve has a transition located around at −55 °C due to the glass transition temperature of butyl rubber. Another peak at a higher temperature of −8 °C was also observed. This may be associated with the movement of the local molecular relaxation side [62,63]. These local molecular movements not only affect the viscoelastic response, but also the mechanical properties (elastic modulus, plastic deformation) and also the diffusion of solvents in the polymer matrix.
After aging at 100 °C in a metalworking fluid (Milform 64SST) for 24 h, a significant decrease of the glass transition temperature value from −45 °C to −63 °C was observed. This result is in good agreement with the literature in showing that there was a decrease of Tg of BRC during thermal aging in silicone oil [64]. The intensity of tan peak (δ) of the aged sample was observed to be lower than that of the un-aged sample. The disappearance of the peak corresponding to the secondary transition temperature associated with the local molecular movement was observed in the aged sample. It can be attributed to the presence of MWF in the elastomer matrix and lead to a better “molecular lubrication”, or it may have simply been a plasticizing effect of MWF [65]. Regarding the reduction of Tg, the glass transition temperature varied linearly with the molar mass and the molecular loss led to a shift of the Tg to lower temperature areas [66]. The decrease of Tg observed in this present study may be due to the thermal and chemical degradation of material by chains scissions that led to a reduction of the molecular mass, which can explain the deterioration of the mechanical properties of the material as shown in the previous section.

3.4. Effect of Temperature and MWF on Morphology, Thermal Properties and Service Lifetime of Butyl Composites

The scanning electron microscope was used to study the changes of the BRC membrane morphology during the aging process. Figure 4a shows the SEM images of a non-aged BRC sample and a sample of butyl after aging at 100 °C, not in MWF (Figure 4b) and after exposure in MWF at 100 °C at different magnifications (Figure 4c,d). These figures show that in the case of an unexposed sample, a large distribution of fillers in the elastomer matrix was observed (Figure 4a). However, these reinforcements were missing at the surface of the exposed sample. The appearance of holes on the surface of the aged sample was also observed, and this can be attributed to the removal of fillers that was replaced by the metalworking fluid (Figure 4b). In other studies, the same damage was observed with bromobutyl rubber when they underwent a thermal aging process [67]. During the presence of MWF at an elevated temperature, various micro cracks on the exposed sample (Figure 4c) were found due to the loss of reinforcements at the sample surface, generated by thermo-oxidation aging and the plasticization effect. This observation was clearer at a higher magnification (Figure 4d) and in good agreement with the literature [67]. The appearance of micro-cracks on rubber materials is believed to be due to the dissolving of low molecular weight molecules in the butyl composites [68]. The loss of fillers was confirmed by thermogravimetric analysis (TGA) under an argon atmosphere at the temperature range from 30 to 800 °C (Figure 5). The TGA curves show that the decomposition of BRC evolved in the same way for both aged and un-aged samples. It found that the onset decomposition temperature of an original sample was about 205 °C with a residue of 52% at 460 °C, while the onset decomposition temperature for the aged sample was about 201 °C with a residue of 42% at 460 °C. In other words, the aging process led to a reduction of carbon black filler from 52% for original rubber to about 42% for the aged sample.
Changes in tensile force were observed at all studied temperatures (Figure 6). Indeed, after 24 h of exposure, the tensile force dropped by about 23% at 80 °C, whereas it decreased by about 41% at 120 °C. The results of the tensile tests of BRC at different temperatures helped to give a prediction of the service life by applying the Arrhenius model to the time-temperature data (Equation (9)). In fact, the variation of the rate of the overall aging processes can be calculated from the aforementioned equation (Equation (9)), where E is activation energy, R is the universal constant (8.314 J/mol.K), T is absolute temperature and A is the pre-exponential factor. The curves describing the relationship between ln(t) vs. 1/T should be linear, and thus the activation energy and service life time can be calculated from this curve.
K = A exp (−E/RT)
The definition of the end-used service lifetime of the material is still a subject in question in the literature. However, the assumption proposed by Rachid et al. [69] in which the material is considered run out when there is a reduction of about 50% of tensile force seems to be acceptable. Here, were calculated the service lifetime for each aging temperature using an empirical regression method proposed by El Aidani et al. [16,69]. These lifetime values were exploited from the Arrhenius curve, as shown in Figure 7, by plotting the logarithm of the lifetimes as a function of the inverse of the exposed temperatures. Figure 7 shows a good agreement with the Arrhenius model, with a high linear correlation coefficient (R2 = 0.95). This indicates that the effect of the thermal treatment between 80 and 120 °C on the tensile force of BRC can be satisfactorily described by the Arrhenius model, which can therefore be used to predict the lifetime in this range of temperatures. The results of the service lifetime of BRC can be found in Figure 6. An activation energy value of 157 kJ.mol−1 was obtained from the Arrhenius curve. This means that at 80 °C the mechanical properties of BRC remained acceptable until 344 days, while it dropped to about 2 days at 120 °C.

4. Conclusions

The effect of temperature with and without MWFs on the evolution of mechanical and physico-chemical descriptors as well as the structure of BRC was investigated. The Mooney–Rivlin’s theory was used to determine the changes of physical and chemical bonds and the viscoelastic behavior of BRCs when they were in contact with MWFs at high temperatures via the determination of the elastic constant C1 and C2 at different temperatures ranging from 80 °C to 120 °C. The results show that temperature and MWFs led to the decrease of elastic constant C2, suggesting a decrease of the force of cohesion of the polymer network. When BRC membranes were in contact with MWFs at high temperatures, the irreversible behavior related to the intrinsic property of elastomers was missing, and significant changes in mechanical properties of material were observed.
The temperature was found to accelerate the degradation process and the loss of mechanical properties of material was more pronounced at a high temperature. The decrease of elasticity and reduction of the glass transition temperature of BRC was also observed, implying that BRC is not appropriate to use in oily working conditions, particularly at a high temperature. In this case, gloves made from BRC must be changed more frequently to ensure an adequate protection level against mechanical and chemical risks. This work also provides useful information for rubber manufacturers to better understand the physicochemical degradation phenomena of their products under oily working conditions and thus improve the quality of their products.

Supplementary Materials

The following are available online at https://www.mdpi.com/2504-477X/3/2/48/s1, Figure S1: Example of Stress-Strain curves of an original BRC.

Author Contributions

P.N.-T. planned, supervised the work and wrote the manuscript. E.T. realized the experiments and participated to explain the results. T.A.N. participated in editing the manuscript.

Funding

This research was funded by the Institut de Recherche Robert-Sauvé en Santé et en Sécurité du Travail, QC, Canada (Project R-983).

Acknowledgments

Thanks also to Jaime Lara (University of Montreal) for his constant support during this project.

Conflicts of Interest

The authors declare no conflict of interest.

References

  1. Youssf, O.; Hassanli, R.; Mills, J.E.; Ma, X.; Zhuge, Y. Cyclic Performance of Steel–Concrete–Steel Sandwich Beams with Rubcrete and LECA Concrete Core. J. Compos. Sci. 2019, 3, 5. [Google Scholar] [CrossRef]
  2. Youssf, O.; Hassanli, R.; Mills, J.E.; Skinner, W.; Ma, X.; Zhuge, Y.; Roychand, R.; Gravina, R. Influence of Mixing Procedures, Rubber Treatment, and Fibre Additives on Rubcrete Performance. J. Compos. Sci. 2019, 3, 41. [Google Scholar] [CrossRef]
  3. Aguilar-Bolados, H.; Contreras-Cid, A.; Neira-Carrillo, A.; Lopez-Manchado, M.; Yazdani-Pedram, M. Removal of Surfactant from Nanocomposites Films Based on Thermally Reduced Graphene Oxide and Natural Rubber. J. Compos. Sci. 2019, 3, 31. [Google Scholar] [CrossRef]
  4. Nohilé, C.; Dolez, P.I.; Vu-Khanh, T. Mechanical and Chemical Effects of Solvent Swelling on Butyl Rubber; Wiley: Hoboken, NJ, USA, 2007. [Google Scholar] [CrossRef]
  5. Ebnesajjad, S. 8—Characteristics of Adhesive Materials. In Handbook of Adhesives and Surface Preparation; Ebnesajjad, S., Ed.; William Andrew Publishing: Oxford, UK, 2011; pp. 137–183. [Google Scholar]
  6. Pape, P.G. 15—Adhesion Promoters. In Handbook of Adhesives and Surface Preparation; Ebnesajjad, S., Ed.; William Andrew Publishing: Oxford, UK, 2011; pp. 369–386. [Google Scholar]
  7. Rabilloud, G. 12—Adhesives for Electronics. In Handbook of Adhesives and Surface Preparation; Ebnesajjad, S., Ed.; William Andrew Publishing: Oxford, UK, 2011; pp. 259–299. [Google Scholar]
  8. Rabilloud, G. 9—Heat-Resistant Adhesives. In Handbook of Adhesives and Surface Preparation; Ebnesajjad, S., Ed.; William Andrew Publishing: Oxford, UK, 2011; pp. 85–220. [Google Scholar]
  9. Fabris, H.J.; Knauss, W.G. Synthetic Polymer Adhesives; Elsevier: Amsterdam, Netherlands, 1989; pp. 131–177. [Google Scholar]
  10. Haworth, J.P.; Baldwin, F.P. Butyl Rubber Properties and Compounding. Ind. Eng. Chem. 1942, 34, 1301–1308. [Google Scholar] [CrossRef]
  11. Ford, F.P.; Gessler, A.M. Some Properties of Butyl Rubber-Carbon Black Systems. Ind. Eng. Chem. 1952, 44, 819–824. [Google Scholar] [CrossRef]
  12. Yu, B.-C.; Jung, J.-W.; Park, K.; Goodenough, J.B. A new approach for recycling waste rubber products in Li–S batteries. Energy Environ. Sci. 2017, 10, 86–90. [Google Scholar] [CrossRef]
  13. Xu, W.; Que Hee, S.S. Permeation of a Metalworking Fluid through a Latex Glove Under Field Use Conditions. Bull. Environ. Contam. Toxicol. 2009, 84, 5. [Google Scholar] [CrossRef]
  14. Xu, W.; Que Hee, S.S. Swelling of four glove materials challenged by six metalworking fluids. Arch. Environ. Contam. Toxicol. 2008, 54, 1–8. [Google Scholar] [CrossRef]
  15. Nguyen-Tri, P.; Prud’homme, R.E. Nanoscale Lamellar Assembly and Segregation Mechanism of Poly (3-hydroxybutyrate)/Poly (ethylene glycol) Blends. Macromolecules 2018, 51, 181–188. [Google Scholar]
  16. Nguyen-Tri, P.; Malajati, Y.; Lara, J.; Vu-Khanh, T. Photochemical aging of an e-PTFE/NOMEX® membrane used in firefighter protective clothing. Polym. Degrad. Stab. 2013, 98, 1300–1310. [Google Scholar]
  17. Nguyen-Tri, P.; El Aidani, R.; Leborgne, É.; Pham, T.; Vu-Khanh, T. Chemical ageingaging of a polyester nonwoven membrane used in aerosol and drainage filter. Polym. Degrad. Stab. 2014, 101, 71–80. [Google Scholar] [CrossRef]
  18. Nguyen, T.V.; Nguyen Tri, P.; Nguyen, T.D.; El Aidani, R.; Trinh, V.T.; Decker, C. Accelerated degradation of water borne acrylic nanocomposites used in outdoor protective coatings. Polym. Degrad. Stab. 2016, 128, 65–76. [Google Scholar] [CrossRef]
  19. Nguyen Tri, P.; Rtimi, S.; Nguyen, T.A.; Vu, M.T. Chapter 5: Physics, Electrochemistry, Photochemistry, and Photoelectrochemistry of Hybrid Nanoparticles. In Noble Metal-Metal Oxide Hydrid Nanoparticles: Fundamentals and Applications; Elsevier: Amsterdam, The Netherlands, 2019; pp. 95–123. [Google Scholar] [CrossRef]
  20. Nguyen, T.V.; Le, X.H.; Dao, P.H.; Decker, C.; Nguyen-Tri, P. Stability of acrylic polyurethane coatings under accelerated aging tests and natural outdoor exposure: The critical role of the used photo-stabilizers. Prog. Org. Coat. 2018, 124, 137–146. [Google Scholar] [CrossRef]
  21. Nguyen-Tri, P.; Nguyen, T.A.; Carriere, P.; Ngo, X.C. Nanocomposite Coatings: Preparation, Characterization, Properties, and Applications. Int. J. Corros. 2018, 2018, 1–19. [Google Scholar] [CrossRef] [Green Version]
  22. Nguyen-Tri, P.; Prud’homme, R.E. Nanoscale analysis of the photodegradation of polyester fibers by AFM-IR. J. Photochem. Photobiol. A Chem. 2019, 371, 196–204. [Google Scholar] [CrossRef]
  23. Nguyen-Tri, P.; Tran, H.N.; Plamondon, C.O.; Tuduri, L.; Vo, D.-V.N.; Nanda, S.; Mishra, A.; Chao, H.-P.; Bajpai, A.K. Recent progress in the preparation, properties and applications of superhydrophobic nano-based coatings and surfaces: A review. Prog. Org. Coat. 2019, 132, 235–256. [Google Scholar] [CrossRef]
  24. Nguyen-Tri, P.; Rtimi, S.; Ouellet Plamondon, C. Nanomaterials-Based Coatings: Fundamentals and Applications; Elsevier: Amsterdam, The Netherlands, 2019; Volume 1, 474p, ISBN 9780128158845. [Google Scholar]
  25. Tri Phuong, N.; Gilbert, V.; Chuong, B. Preparation of Recycled Polypropylene/ Organophilic Modified Layered Silicates Nanocomposites Part I: The Recycling Process of Polypropylene and the Mechanical Properties of Recycled Polypropylene/Organoclay Nanocomposites. J. Reinf. Plast. Compos. 2008, 27, 1983–2000. [Google Scholar] [CrossRef]
  26. Nguyen Tri, P.; Gilbert, V. Non-isothermal Crystallization Kinetics of Short Bamboo Fiber-reinforced Recycled Polypropylene Composites. J. Reinf. Plast. Compos. 2010, 29, 2576–2591. [Google Scholar] [CrossRef]
  27. Nguyen Tri, P.; Sollogoub, C.; Guinault, A. Relationship between fiber chemical treatment and properties of recycled pp/bamboo fiber composites. J. Reinf. Plast. Compos. 2010, 29, 3244–3256. [Google Scholar] [CrossRef]
  28. Boukehili, H.; Nguyen-Tri, P. Helium gas barrier and water absorption behavior of bamboo fiber reinforced recycled polypropylene. J. Reinf. Plast. Compos. 2012, 31, 1638–1651. [Google Scholar] [CrossRef]
  29. Nguyen Tri, P.; Guinault, A.; Sollogoub, C. Élaboration et propriétés des composites polypropylène recyclé/fibres de bambou. Matériaux Tech. 2012, 100, 413–423. [Google Scholar] [CrossRef] [Green Version]
  30. Triki, E.; Nguyen-Tri, P.; Boukehili, H.; Vu-Khanh, T. Investigation of tearing mechanisms of woven textile. Polym. Compos. 2012, 33, 1578–1585. [Google Scholar] [CrossRef]
  31. Triki, E.; Vu-Khanh, T.; Nguyen-Tri, P.; Boukehili, H. Mechanics and mechanisms of tear resistance of woven fabrics. Theor. App. Fract. Mech. 2012, 61, 33–39. [Google Scholar] [CrossRef]
  32. Tri, P.N.; Domenek, S.; Guinault, A.; Sollogoub, C. Crystallization behavior of poly(lactide)/poly(β-hydroxybutyrate)/talc composites. J. Appl. Polym. Sci. 2013, 129, 3355–3365. [Google Scholar] [CrossRef] [Green Version]
  33. Triki, E.; Nguyen-Tri, P.; Gauvin, C.; Azaiez, M.; Vu-Khanh, T. Combined puncture/cutting of elastomer membranes by pointed blades: Characterization of mechanisms. J. Appl. Polym. Sci. 2015, 132, 42150. [Google Scholar] [CrossRef]
  34. Azizi, S.; David, E.; Fréchette, M.F.; Nguyen-Tri, P.; Ouellet-Plamondon, C.M. Electrical and thermal phenomena in low-density polyethylene/carbon black composites near the percolation threshold. J. Appl. Polym. Sci. 2019, 136, 47043. [Google Scholar] [CrossRef]
  35. Azizi, S.; David, E.; Fréchette, M.F.; Nguyen-Tri, P.; Ouellet-Plamondon, C.M. Electrical and thermal conductivity of ethylene vinyl acetate composite with graphene and carbon black filler. Polym. Test. 2018, 72, 24–31. [Google Scholar] [CrossRef]
  36. Nguyen-Tri, P.; Prud’homme, R.E. Crystallization and Segregation Behavior at the Submicrometer Scale of PCL/PEG Blends. Macromolecules 2018, 51, 7266–7273. [Google Scholar] [CrossRef]
  37. Satyabrata, M.; Anh Nguyen, T.; Nguyen-Tri, P. Noble Metal-Metal Oxide Hybrid Nanoparticles; Fundamentals and Application; Elsevier: Amsterdam, The Netherlands, 2018; Volume 1, 675p, ISBN 978-0-12-814134-2. [Google Scholar]
  38. Duc Chinh, V.; Speranza, G.; Migliaresi, C.; Van Chuc, N.; Minh Tan, V.; Phuong, N.-T. Synthesis of Gold Nanoparticles Decorated with Multiwalled Carbon Nanotubes (Au-MWCNTs) via Cysteaminium Chloride Functionalization. Sci. Rep. 2019, 9, 5667. [Google Scholar] [CrossRef]
  39. Nguyen Tri, P.; Nguyen, T.A.; Nguyen, T.H.; Carriere, P. Chapter 7: Antibacterial Behavior of Hybrid Nanoparticles. In Noble Metal-Metal Oxide Hydrid Nanoparticles: Fundamentals and Applications; Elsevier: Amsterdam, The Netherlands, 2019; pp. 141–155. [Google Scholar]
  40. Nguyen Tri, P.; Ouellet-Plamondon, C.; Rtimi, S.; Assadi, A.A.; Nguyen, T.A. Chapter 3 Methods for Synthesis of Hybrid Nanoparticles. In Noble Metal-Metal Oxide Hydrid Nanoparticles: Fundamentals and Applications; Elsevier: Amsterdam, The Netherlands, 2019; pp. 51–63. [Google Scholar] [CrossRef]
  41. Nguyen-Tri, P.; Nguyen, V.; Nguyen, T. Biological Activity and Nanostructuration of Fe3O4-Ag/High Density Polyethylene Nanocomposites. J. Compos. Sci. 2019, 3, 34. [Google Scholar] [CrossRef]
  42. Ben Hassine, M.; Naït-Abdelaziz, M.; Zaïri, F.; Colin, X.; Tourcher, C.; Marque, G. Time to failure prediction in rubber components subjected to thermal ageing: A combined approach based upon the intrinsic defect concept and the fracture mechanics. Mech. Mater. 2014, 79, 15–24. [Google Scholar] [CrossRef] [Green Version]
  43. Syed, I.H.; Vouagner, P.; Fleck, F.; Lacayo-Pineda, J. Nonlinearity in the Mechanical Response of Rubber as Investigated by High-Frequency DMA. Polymers 2019, 11, 581. [Google Scholar] [CrossRef] [PubMed]
  44. Xiang, K.; Huang, G.; Zheng, J.; Wang, X.; Huang, J. Investigation on the thermal oxidative aging mechanism and lifetime prediction of butyl rubber. Macromol. Res. 2013, 21, 10–16. [Google Scholar] [CrossRef]
  45. Haghtalab, A.; Rahimi, S. Study of viscoelastic properties of nanocomposites of SiO2-acrylonitrile-butadiene-styrene. J. Appl. Polym. Sci. 2013, 127, 4318–4327. [Google Scholar] [CrossRef]
  46. Lewicki, J.P.; Liggat, J.J.; Hayward, D.; Pethrick, R.A.; Patel, M. Degradative Thermal Analysis and Dielectric Spectroscopy Studies of Aging in Polysiloxane Nanocomposites. ACS Symp. Ser. 2009, 1004, 239–254. [Google Scholar]
  47. Rivlin, R.S. Large Elastic Deformations of Isotropic Materials. IV. Further Developments of the General Theory. Philos. Trans. R. Soc. A Math. Phys. Eng. Sci. 1948, 241, 379–397. [Google Scholar] [CrossRef]
  48. Rivlin, R.S. Large Elastic Deformations of Isotropic Materials. I. Fundamental Concepts. Philos. Trans. R. Soc. A Math. Phys. Eng. Sci. 1948, 240, 459–490. [Google Scholar] [CrossRef]
  49. Arimoto, H. α–γ Transition of nylon 6. J. Polym. Sci. Part A Gen. Pap. 1964, 2, 2283–2295. [Google Scholar] [CrossRef]
  50. Slichter, W.P. Molecular motion in polyamides. J. Polym. Sci. 1959, 35, 77–92. [Google Scholar] [CrossRef]
  51. Hagen, R.; Salmén, L.; Stenberg, B. Effects of the type of crosslink on viscoelastic properties of natural rubber. J. Polym. Sci. Part B Polym. Phys. 1996, 34, 1997–2006. [Google Scholar] [CrossRef]
  52. Gordon, M. The Physics of Rubber Elasticity (Third Edition). L. R. G.; Treloar, Clarendon Press, Oxford. 1975 pp. xii + 370. Price: £14.00. Br. Polym. J. 1976, 8, 39. [Google Scholar] [CrossRef]
  53. Sombatsompop, N. Investigation of Swelling Behavior of NR Vulcanisates. Polym.-Plast. Technol. Eng. 1998, 37, 19–39. [Google Scholar] [CrossRef]
  54. Mark, J.E. Experimental Determinations of Crosslink Densities. Rubber Chem. Technol. 1982, 55, 762–768. [Google Scholar] [CrossRef]
  55. Priss, L.S. Molecular origin of constants in the theory of rubber-like elasticity considering network chains steric interaction. Pure Appl. Chem. 1981, 53, 1581–1596. [Google Scholar] [CrossRef]
  56. Mark, J.E. The Constants 2C1and 2C2 in Phenomeno-Logical Elasticity Theory and Their Dependence on Experimental Variables. Rubber Chem. Technol. 1975, 48, 495–512. [Google Scholar] [CrossRef]
  57. Nguyen-Tri, P.; Tuduri, L.; Triti, E.; Gauvin, C.; Vu-Khanh, T. Swelling behavior of polymeric membranes to metalworking fluids. J. Appl. Polym. Sci. 2018, 135, 45717. [Google Scholar] [CrossRef]
  58. Nguyen-Tri, P.; Triki, E.; Tuduri, L.; Gauvin, C.; Vu-Khanh, T. Effet des fluides de coupe sur la résistance à la coupure et à la perforation des gants de protection; Bibliothèque et Archives nationales du Québec ed, IRSST: Montréal, QC, Canada, 2016. [Google Scholar]
  59. Ha-Anh, T.; Vu-Khanh, T. Prediction of mechanical properties of polychloroprene during thermo-oxidative aging. Polym. Test. 2005, 24, 775–780. [Google Scholar] [CrossRef] [Green Version]
  60. Gumbrell, S.M.; Mullins, L.; Rivlin, R.S. Departures of the elastic behaviour of rubbers in simple extension from the kinetic theory. Trans. Faraday Soc. 1953, 49, 1495–1505. [Google Scholar] [CrossRef]
  61. Allen, G.; Kirkham, M.J.; Padget, J.; Price, C. Thermodynamics of rubber elasticity at constant volume. Trans. Faraday Soc. 1971, 67, 1278–1292. [Google Scholar] [CrossRef]
  62. Dutta, N.K.; Khastgir, D.; Tripathy, D.K. The effect of carbon black concentration on the dynamic mechanical properties of bromobutyl rubber. J. Mater. Sci. 1991, 26, 177–188. [Google Scholar] [CrossRef]
  63. García, M.; Garmendia, I.; García, J. Influence of natural fiber type in eco-composites. J. Appl. Polym. Sci. 2008, 107, 2994–3004. [Google Scholar] [CrossRef]
  64. Ali, S.; Ramzan, S.; Raza, R.; Ahmed, F.; Ullah, S.; Hussain, R.; Ali, S. Thermal and Thermo-Mechanical Behavior of Butyl based Rubber Exposed to Silicon Oil at Elevated Temperature. J. Chem. Soc. Pakistan 2013, 35, 1437–1444. [Google Scholar]
  65. Barrere, C.; Dal Maso, F. Résines époxy réticulées par des polyamines: Structure et propriétés. Revue de l’Institut Français du Pétrole 2006, 52, 317–335. [Google Scholar] [CrossRef]
  66. Fox, T.G.; Flory, P.J. Second-Order Transition Temperatures and Related Properties of Polystyrene. I. Influence of Molecular Weight. J. Appl. Phys. 1950, 21, 581–591. [Google Scholar] [CrossRef]
  67. Kannan, G.K.; Gaikewad, L.V.; Nirmala, L.; Kumar, N.S. Thermal ageing studies of bromo-butyl rubber used in NBCpersonal protective equipment. J. Sci. Ind. Res. 2010, 69, 841–849. [Google Scholar]
  68. Grandcoin, J.; Boukamel, A.; Lejeunes, S. A micro-mechanically based continuum damage model for fatigue life prediction of filled rubbers. Int. J. Solids Struct. 2014, 51, 1274–1286. [Google Scholar] [CrossRef] [Green Version]
  69. El Aidani, R.; Dolez, P.I.; Vu-Khanh, T. Effect of thermal aging on the mechanical and barrier properties of an e-PTFE/Nomex® moisture membrane used in firefighters’ protective suits. J. Appl. Polym. Sci. 2011, 121, 3101–3110. [Google Scholar] [CrossRef]
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Figure 1. Effect of temperature on the mechanical properties of butyl rubber-based composite (BRC) as a function of metalworking fluid (MWF) exposure time (a) constant C1; (b) constant C2; (c) crosslinking density (N); (d) tensile force.
Figure 1. Effect of temperature on the mechanical properties of butyl rubber-based composite (BRC) as a function of metalworking fluid (MWF) exposure time (a) constant C1; (b) constant C2; (c) crosslinking density (N); (d) tensile force.
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Figure 2. Effect of temperature and a MWF on the mechanical properties of BRC as function of MWF exposure time (a) constant C1; (b) constant C2; (c) crosslinking density (N); (d) tensile force.
Figure 2. Effect of temperature and a MWF on the mechanical properties of BRC as function of MWF exposure time (a) constant C1; (b) constant C2; (c) crosslinking density (N); (d) tensile force.
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Figure 3. Evolution of storage modulus (a) and tangent delta values (b) of butyl rubber composite membrane before and after exposure in metalworking fluid (Milform 64 SST) at 100 °C for 24 h.
Figure 3. Evolution of storage modulus (a) and tangent delta values (b) of butyl rubber composite membrane before and after exposure in metalworking fluid (Milform 64 SST) at 100 °C for 24 h.
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Figure 4. Scanning electron microscopy (SEM) images of butyl rubber composite membranes: (a) non-aged sample; (b) aged at 100 °C, not in MWF; (c) aged at 100 °C with the presence of a metalworking fluid (Milform 64 SST) for 24 h; (d) higher magnification of Figure 4c, showing the rugosity of the sample surface.
Figure 4. Scanning electron microscopy (SEM) images of butyl rubber composite membranes: (a) non-aged sample; (b) aged at 100 °C, not in MWF; (c) aged at 100 °C with the presence of a metalworking fluid (Milform 64 SST) for 24 h; (d) higher magnification of Figure 4c, showing the rugosity of the sample surface.
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Figure 5. Thermogravimetric curves of butyl rubber composite before (green line) and after aging (red line) in Milform 64 SST at 80 °C during a week.
Figure 5. Thermogravimetric curves of butyl rubber composite before (green line) and after aging (red line) in Milform 64 SST at 80 °C during a week.
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Figure 6. Variation of tensile force of BRC at different temperatures as a function of exposure time.
Figure 6. Variation of tensile force of BRC at different temperatures as a function of exposure time.
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Figure 7. Extrapolation of the Arrhenius plot of the BRC membrane based on tensile force. Insert: predicted values of service lifetime, calculated from the Arrhenius plot based on tensile force at different temperatures.
Figure 7. Extrapolation of the Arrhenius plot of the BRC membrane based on tensile force. Insert: predicted values of service lifetime, calculated from the Arrhenius plot based on tensile force at different temperatures.
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Table
Table 1. Young’s modulus values of a butyl membrane exposed to various temperatures.
Table 1. Young’s modulus values of a butyl membrane exposed to various temperatures.
Exposure Time (h)Exposure Temperature
80 °C100 °C120 °C
EtheoEexpEtheoEexpEtheoEexp
04.08 (0.42)3.40 (0.04)3.78 (0.06)3.00 (0.05)4.80 (0.30)4.11 (0.16)
13.90 (0.36)2.89 (0.2)3.93 (0.48)3.15 (0.25)6.57 (0.12)6.10 (1.10)
23.99 (0.30)3.01 (0.09)3.90 (0.10)3.20 (0.13)8.12 0.24)7.43 (0.18)
43.78 (0.24)2.99 (0.03)3.66 (0.36)2.88 (0.18)6.65 (0.66)5.45 (0.85)
63.78 (0.42)2.98 (0.10)3.72 (0.04)3.01 (0.02)5.44 (0.18)4.57 (0.02)
143.84 (0.24)2.98 (0.09)4.14 (0.09)3.27 (0.01)6.35 (0.36)5.08 (0.14)
243.90 (0.36)2.96 (0.02)4.08 (0.09)3.30 (0.09)6.08 (0.16)4.80 (0.12)
Note: between parentheses: standard deviation (SD). Etheo: theoretical modulus. Eexp: experimental modulus.
Table
Table 2. Young’s modulus values of the BRC membrane exposed at different temperatures in the presence of metalworking fluid.
Table 2. Young’s modulus values of the BRC membrane exposed at different temperatures in the presence of metalworking fluid.
t (h)Exposure Temperatures
80 °C100 °C120 °C
EtheoEexpEtheoEexpEtheoEexp
03.72 (0.36)2.87 (0.20)3.36 (0.36)2.70 (0.22)4.74 (0.15)4.26 (0.28)
13.36 (0.36)2.64 (0.16)3.03 (0.12)2.51 (0.09)6.76 (0.54)6.28 (0.17)
23.12 (0.30)2.43 (0.08)3.03 (0.20)2.52 (0.01)6.78 (0.09)6.46 (0.01)
43.00 (0.24)2.41 (0.05)2.82 (0.30)2.33 (0.11)3.804 (0.36)3.26 (0.18)
62.70 (0.42)2.30 (0.03)2.52 (0.12)2.18 (0.03)3.72 (0.36)3.41 (0.03)
142.46 (0.24)2.31 (0.05)2.40 (0.48)2.01 (0.05)3.66 (0.18)3.15 (0.04)
242.22 (0.36)1.98 (0.02)2.16 (0.42)1.92 (0.06)3.64 (0.04)3.06 (0.05)
Note: between parentheses: standard deviation (SD), Etheo: theoretical modulus. Eexp: experimental modulus.

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Nguyen-Tri, P.; Triki, E.; Nguyen, T.A. Butyl Rubber-Based Composite: Thermal Degradation and Prediction of Service Lifetime. J. Compos. Sci. 2019, 3, 48. https://doi.org/10.3390/jcs3020048

AMA Style

Nguyen-Tri P, Triki E, Nguyen TA. Butyl Rubber-Based Composite: Thermal Degradation and Prediction of Service Lifetime. Journal of Composites Science. 2019; 3(2):48. https://doi.org/10.3390/jcs3020048

Chicago/Turabian Style

Nguyen-Tri, Phuong, Ennouri Triki, and Tuan Anh Nguyen. 2019. "Butyl Rubber-Based Composite: Thermal Degradation and Prediction of Service Lifetime" Journal of Composites Science 3, no. 2: 48. https://doi.org/10.3390/jcs3020048

APA Style

Nguyen-Tri, P., Triki, E., & Nguyen, T. A. (2019). Butyl Rubber-Based Composite: Thermal Degradation and Prediction of Service Lifetime. Journal of Composites Science, 3(2), 48. https://doi.org/10.3390/jcs3020048

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