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Braz. J. Chem. Eng. vol.26 no.1 São Paulo Jan./Mar. 2009
D. A. BaetaI; J. A. ZatteraII; M. G. OliveiraIII; P. J. OliveiraI,*
IDepartamento de Engenharia Química, Universidade Federal Rural do Rio de Janeiro, Seropédica, Fax: + (55) (21) 3787-3750, 23890-000, Rio de Janeiro - RJ, Brazil. E-mail: email@example.com
IIUniversidade de Caxias do Sul, Centro de Ciências Exatas e Tecnologia, Departamento de Engenharia Químicas, Fax: + (55) (54) 3218-2160, 9500-1970, Caxias do Sul - RS, Brazil. E-mail: firstname.lastname@example.org
IIIInstituto Nacional de Tecnologia, Fax: + (55) (21) 2123-1064, Avenida Venezuela 82, Saúde, 20081-312, Rio de Janeiro - RJ, Brazil. E-mail: email@example.com
Styrene-butadiene rubber (SBR) has large applications in the shoe industry, especially as expanded sheets used to produce insoles and inner soles. According to TG analysis, the rubber content in SBR residues (SBR-r) was found to be around 26-wt%. Based on that data, a cost-effective technique for the reuse of SBR-r in Nitrile rubber (NBR) was developed. Later, the effect of SBR-r on the cure behavior, mechanical performance, swelling, and crosslink density of reused rubber was investigated, with more emphasis placed on the effect of both particle size and loading of waste filler. Cure characteristics such as optimum cure time and scorch time were then reduced by the increasing amount of SBR-r filler. Owing to the reinforced nature of the largest particle size SBR-r, the best results for the mechanical properties of NBR were those in which SBR-r was added at the end of the cure process. The study has thus shown that SBR residue (SBR-r) can be used as an economical alternative filler in NBR.
Keywords: Vulcanization; Adhesion; Elastomer; Cure.
The perfection of industrial processes and the development of new formulations for rubber have contributed to the significant increase in residue amount and type. The main source of waste rubber is discarded rubber products, such as discarded tires, rubber pipes, rubber belts, rubber shoes, edge scraps, waste products that are produced in rubber processes and others (Fang and et al 2001). Thus, the disposal of rubber waste is a serious economic and ecological problem.
In recent years, the polymer industry has developed an interest in the improvement of cost-effective techniques to convert waste and used rubber into a processable form (Harshaft, 1972; Lee and Millem, 1977; Braton and Koutsky, 1974, Phadke et al 1983). Researchers have used various techniques such as chemical, thermo-mechanical, and cryomechanical processes (Ratcliffe, 1977 and Biddulph, 1977.) The earlier approach to this problem was to reclaim or remove the crosslinks in rubber rejects and then use the latter as new rubber. However, the use of reclaimed rubber was limited owing to three main reasons:
(i) In the case of waste tires, easy reclamation was not possible due to the presence of steel belts or plies (Rajalingam, 1983.)
(ii) The properties of reclaimed rubber are inferior due to degradation of the chains of polymer during processing (Mathew, 2001.)
(iii) After the process of reclamation, components of the mixture responsible for certain properties are inefficient (Acetta, 1981.)
Many reviews regarding the disposal problem of rubber rejects and possible solutions are available in the literature (Phadke, 1984; Phadke, 1985; Claramma, 1986; Azzir, 1990). Zhan et al (2001) discuss the significance of recycling rubber waste to protect the environment and to conserve energy. The use of cryoground rejects as filler in rubbers and polyolefins is well known (Oliphant, 1993). Recently, several new methods for the devulcanization of rubber waste have become available, but the most important one among these is the devulcanization process using ultrasonic irradiation. Studies in this field (Tukachinsky, 1996; Levin, 1996; Isayev et al., 1995 and Isayev et al., 1996) have found that, in the presence of heat and temperature, ultrasonic waves were able to break up the three-dimensional network in cross-linked rubbers. The resulting devulcanised rubber could then be reprocessed, shaped, and revulcanised just like virgin rubber. Chemical, mechanical, plasma, corona and electron-beam radiation were reported to be useful in improving matrix-filler adhesion (Fujimoto, 1979; Creasey and Wager, 1968; Fujimoto et al., 1981, Yasuda et al., 1977; Zimmermann et al., 199 and Yu et al., 1992).
The adoption of new materials and modern processes of footwear manufacture have increased the production and efficiency of the sector. However, it has also resulted in augmented production of residues. It is estimated that 3 million tons of residues are produced annually in the processing stage alone. However, residue amounts have grown on the same scale.
Styrene Butadiene Rubber residues (SBR-r) present a great potential for use as load in elastomeric formulations. In its formulation, this residue contains expanding agent and curatives, besides inorganic loads (Sombatsompop, 1999; Sakai, 1991 and Tatiböuet et al., 2004). When properties such as tensile strength and tearing and abrasion resistance are compared with the same rubber compositions without load (Saxena et al., 1999), they reflect reinforcement in the elastomer proceeding from fillers.
In this article, we report on a cost-effective method to reuse SBR residues as fillers in nitrile rubber (NBR), as well as the influence of load on the cure characteristics. Emphasis has been given to the effect of particle size, addition order and the effect of the amount of SBR-r on mechanical properties. Swelling studies have also been carried through to understand the interaction of SBR waste filler and NBR matrix.
NBR (NBR615-B) (33 wt % of acrylonitrile; Mooney viscosity = 47) was kindly supplied by NITRIFLEX S.A., Rio de Janeiro, Brazil. Styrene Butadiene Rubber residues (SBR-r) (density = 0.9006 g/cm3; gel amount = 93.04%) was kindly supplied by a footwear industry from Caxias do Sul- RS, Brazil. Rubber additives were as follows: zinc oxide, stearic acid, sulfur, tetra methyl thiuram disulphide (TMTD) and mercapto benzothiazyl disulphide (MBTS) (all commercial grades).
Styrene Butadiene Rubber (SBR 1507) (23.3% of styrene; Mooney viscosity = 39) was kindly supplied by PETROFLEX S.A, Rio de Janeiro, Brazil.
Styrene Butadiene Rubber residue (SBR-r) (23.3% of styrene) was kindly supplied by CIAFLEX BORRACHAS LTDA, Rio Grande do Sul, Brazil.
Processing and Characterization of SBR Residue
The SBR-r residue was triturated in a knives mill. It was then sieved into three different particle sizes, ranging from 44 to 63 µm (mesh 170 or AB1 or AE1), 64 to 88 µm (mesh 250 or AB2 or AE2), and 28 to 841 µm (all or AB3 or AE3), where AB and AE are addition at the beginning and at the end stage, respectively.
The SBR residues were evaluated by infrared spectroscopy with Fourier transform (FTIR and FTIR-ATR) and thermo gravimetric analysis (TG). The TG measurements were carried out under nitrogen atmosphere by using a Shimadzu TGA-50 at a heating rate of 10ºC/min. SiO2, CaCO3 and SiO/CaCO3 (80/20 wt%) were also evaluated by infrared spectroscopy with Fourier transform (FTIR).
Mixing of NBR and filler was carried out using a laboratory two roll mill with a friction ratio of 1:1.5. The basic formulation used is given in Table 1. For the study of the addition order, the mix composition to which the residue was added in the end is described as AE2 and AE3.
Sample Preparation and Testing
The cure characteristics of rubber compositions were determined by using a Rubber Process Analyzer (RPA 2000) at 160ºC, frequency of 1.667 Hz and arc degree of 0.5º, and by measuring optimum cure time, scorch time, minimum torque and maximum torque.
The compounds were compression-molded at 160ºC by using an electrically- heated hydraulic press for their respective optimum cure times (t90). Dumbell-shaped tensile and angular tear specimens were punched out from compression-molded sheets along the mill grain direction.
The tensile properties of the compounds were measured by means of an EMIC model DL 2000, at a crosshead speed of 50 mm/min based on ASTM D412-87, and the tear resistances of the compounds were measured at a crosshead speed of 500 mm/min based on ASTM D624-86. Hardness was tested based on ASTM D 2240 using a Shore A durometer.
Determination of Vr and Crosslink Density
In order to estimate the extent of cross-linking, the fraction of rubber volume in the swollen network (Vr) of the rubber in toluene-swollen specimens was determined after a 7-day period through the following equation (1):
where D is the weight after drying out, f the fraction of insoluble components, T the weight of sample, A0 the weight of the absorbed solvent, ρr the density of the rubber and ρs the density of the density of the solvent (George, 2000)
Crosslink density for vulcanized compositions was determined by using the swelling method. The crosslink density was calculated through the Flory-Rehner equation as shown in equation 2 (Mark 1987).
Where Vr is the volume fraction of rubber in swollen vulcanization, V0 is the molar volume of solvent used (toluene = 106.2 cm3/mol), χ the polymer-solvent interaction parameter (NBR-toluene = 0.472), and ρ is the polymer density.
RESULTS AND DISCUSSION
Characterization of SBR Residues
The basic components of SBR residue were identified with the help of FTIR analysis. The SBR rubber was determined by ATR absorbance peaks at 2920 and 2850 cm-1 attributed to the CH stretching of aromatic rings. The absorption at 1600 cm-1 was due to the stretching vibration of the CH2 and CH3. The absorption at 966 and 699 cm-1 was attributed to aromatic C-C stretching. Others peaks at 912 and 757 cm-1 were attributed to trans 1,4 structure and γCH of the single substituted benzene ring and the CH out of plane deformation, respectively.
Figure 1 shows the FTIR-ATR spectrum. As it can be visualized, the presence of calcium carbonate was assigned by bands at 1422 and 874 cm-1 (CO3-2 stretching and CO3-2out of plane deformation, respectively). Finally, silica was detected due to bands at 3450 and at 1120 cm-1, the characteristic absorption band attributed to the SiO stretching.
Other chemical expanding agents, curatives, etc. could not be identified by FTIR-ATR analysis because of their reaction and decomposition during processing.
The SBR residue was also submitted to thermogravimetric analysis (TG) in order to determine the amount of rubber and inorganic material present therein. The decomposition of the residue occurred in two steps, as shown in Figure 2. The first step started at around 450ºC, corresponding to 26%wt and was attributed to SBR decomposition. The second step started at around 680ºC to 750ºC, and was attributed to inorganic filler decomposition, in this case corresponding to CaCO3 decomposition. The SBR (23.3% styrene) curve is shown for comparative analysis with SBR-r samples.
Filler incorporation during rubber processing can be done in several ways, according to its nature. Therefore, this work studied two different orders of SBR-r addition. The first method adopted was the addition of SBR-r after ten minutes of processing NBR pure gum in the roll mill, and the second one was its addition at the final stage of composition processing, i.e., after the incorporation of all curatives in NBR gum.
The efficiency of these methods was evaluated regarding their mechanical properties. For this study, the compositions AB2, AB3, AE2 and AE3 were used. Table 2 presents the results obtained. As can be seen, the values of tensile strength and elongation at break were better for the two samples in which SBR residues were added at the final stage: AE2 and AE3.
The SBR-r contains some additives such as vulcanizing agents and inorganic fillers from formulation. Theses compounds can migrate to NBR phases due to differences in solubility parameters between rubbers. The presence of these components can affect the crosslinking of NBR and the mechanical properties of the mixes. When the vulcanizers (sulphur and accelerators) are added before the SBR-r, their distribution in NBR phases is favoured. Subsequently, when the residue is added at the final stage, the transfer of cure agents of SBR-r phases is reduced by the presence of a cure system in the NBR matrix.
This kind of behavior can also be explained by the reduction of competition for curatives between NBR and SBR-r when the residue was added at the end stage, resulting in a better crosslinked rubber matrix.
Size and Filler Loading
The best results for mechanical properties were obtained when SBR-r was added at the end stage. For the study of filler loading and particle size on rheometric and mechanical properties, the above method of addition was adopted. Figure 3 and 4 show the effect of SBR-r loading on the optimum cure time (t90) and scorch time (ts1) of NBR compositions with three different particle sizes (AE1, AE2, and AE3); the values were presented in Table 3.
All series of compositions showed a decreasing trend when filler loading increased. In fact, as the loading of SBR-r residues increased, both the transference and the availability of the unreacted accelerator for NBR phases increased, which led to an increasing rate of vulcanizing reaction. Then, reductions in curing characteristics such as optimum cure time and scorch time were observed.
Other researchers observed a similar trend in other rubber residue containing composites and related this to residual curatives in the waste rubber sample, such as sulphur and accelerators used in the original formulations (Hong, 2002).
In relation to the effect of the particle size, the decrease in optimum cure time and scorch time were observed for the AE3 blend, Table 3. The size of particles composing the AE3 mix was in the 28 to 841 µm range, whereas the particle size range of the AE2 sample was 64 to 88 µm and of the AE1 sample was 44 to 63 µm. The AE3 sample had both large (841 µm) and small particles (28 µm), and it was the presence of these small particles that may have increased interaction between energy charges (SBRR) and the matrix (NBR), owing to an increase in the superficial contact area between the phases.
Thus, as particle size decreased, there was an increase in surface area, which favored the curative diffusion from residue to virgin rubber.
Table 3 compares the torque values for NBR rubber as functions of the SBR-r content and size. The minimum (ML) and maximum torque (MH) increased with the addition of SBR-r, which was related to the increase in system viscosity because of the presence of cross-linked material in the SBR-r. The increase of MH may also have been related to the increase in crosslink degree promoted by residual curatives in the SBR-r.
Table 4 also shows the variation of rheometric characteristics of filler loading of NBR loaded with size-3 filler (AE3). The minimum torque (ML) was affected by an increase in the SBR-r loading rate. This indicates that it is more difficult to process compounds that contain SBR-r compared to compounds without SBR-r. The apparent reason for minimum torque increase is that cross-linked SBR-r does not easily flow to the matrix and this results in higher viscosity of the blends. A significant increase in the maximum torque was dependent on the SBR-r content, suggesting an increase in crosslink density.
The increase in crosslink degree was confirmed by swelling experiments in toluene. The rubber volume in the swelling network (Vr) rose in accordance with the SBR-r amount due to swelling restrictions imposed by the crosslinked network of the NBR matrix. Indeed, crosslink density values of NBR compositions continually increased with SBR-r amount. This trend also confirmed the values of maximum torque (MH), known to be a function of the crosslinking degree and filler loading.
The addition of SBR-r resulted in an increase of the ultimate tensile strength up to the limit of 70 phr. Beyond this amount, the formation of filler agglomerates may occur. It has been extensively reported in the literature that poor stress transfer at the filler-polymer interphase discontinuity creates particulate-filled composites, which in their turn generate a weaker structure. Agglomeration of the filler particles and dowelling of the polymer at the interphase aggravate the situation by creating stress concentration points, which account for the weakness in the composite.
Figure 5: Effect of the filler size and loading on the tensile strength of NBR compounds.
Elongation at break (Eb) showed a slight increase of up to 30 phr. Further addition of SBR-r resulted in lower values of Eb. The decrease in elongation at break of vulcanizates containing SBR-r indicated hindrance by SBR-r of deformability of the NBR matrix. It should be remarked that SBR-r was vulcanizated and contained inorganic fillers such as silica and calcium carbonate.
The hardness values also joined the same trend exhibited by maximum torque (MH), being a function of crosslink degree and filler loading in rubber composition. Table 5 shows the variation of hardness on filler loading and size. The three particle sizes employed resulted in compositions with higher hardness as SBR-r amount increased. Again, this trend confirms the values of MH and crosslink density.
Tear strength of NBR compositions was also studied. There was a little increase upon SBR-r addition, suggesting a good adhesion between filler and NBR matrix, Table 5. However, the addition of a compatibilizer was clearly necessary to improve this adhesion. Moreover, by comparing the three particle sizes, the largest particle size SBR-r were seen to promote better mechanical properties, as they were more reinforcing. This tendency opposes the conventional rules for filler-polymer interaction with respect to particle size. Nevertheless, the filler studied in the article was not an inorganic one, thus involving other questions besides particle size. As discussed earlier, curative diffusion phenomena also play an important role in polymer fillers. As particle size decreases, the surface area increases, accelerating the migration of curatives and consequently weakening the matrix. Owing to these particle sizes, AE3 showed better mechanical properties over other compositions.
Figure 6 shows the rubber volume in the swollen network vulcanization of NBR compounds with various SBR-r residue (AE3) contents in toluene. The Vr values increased with SBR-r concentration. The increase in Vr values seemed to vary depending on the extent of crosslinking, as the restriction to swelling increased with network formation. From the above results, it is clear that crosslink density increases with SBR-r content.
Figure 7 presents the variations of crosslink density for NBR compounds loaded with size 3 filler (AE3). It can be observed that the crosslink density increased significantly with an increase in SBR-r loading. Higher crosslink density leads to improved mechanical properties, which also explains the increase in maximum torque.
The use of SBR-r residues as potential fillers in NBR rubber is very appealing because of the simplicity of the technique. Studies of addition order showed that the values of tensile strength and elongation at break were better for the samples in which SBR-r residues were added in the end stage. The morphology of particle size and size distribution were analyzed and, by increasing filler loading, a reduction in optimum cure and scorch time was observed. Up to 70 phr filler loading, the tensile strength showed good improvement. Size 3 filler exhibits superior tensile strength over others. Hardness values and tear strength values were found to increase with increasing filler content. This observation was supported by higher crosslink density.
The authors thank CNPq, FAPERJ, Nitriflex S.A Ind. & Com. and Instituto Nacional de Tecnologia (INT).
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(Submitted: November 13, 2007 ; Revised: May 8, 2008 ; Accepted: May 14, 2008)
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