Thermal Transformation of End-of-Life Latex to Valuable Materials

: Recent studies have demonstrated that carbon nanomaterials have huge potential in composite applications, but there is a continuous quest for identifying the most viable technique for producing this material. In this study, the possibility of using an innovative approach for the synthesis of value-added carbon nanomaterials and green gases from end-of-life soft mattress materials (latex) was investigated. Thermogravimetric analysis (TGA) was used to determine the thermal degradation of latex. Quantitative gas analysis at three di ﬀ erent temperatures by infrared spectroscopy (IR) suggested that small gas molecules, especially CH 4 , could be produced at a higher temperature. The carbon residues produced after gas analysis were characterised by XRD, SEM, TEM, XPS, and Raman spectroscopy, suggesting the possibility of direct synthesis of carbon nanomaterials from waste latex. These carbon materials have Na, Zn, Si, and K in their structure, and further study is needed for understanding the e ﬀ ect of these elements on composite properties. Our study demonstrated that heat treatment of waste latex at 1000 ◦ C for 15 min produced carbon materials, which contained 7–16% S and 1.2–2% N, and gases, such as CH 4 , could be synthesised.


Introduction
Several studies have shown that carbon nanomaterials with heteroatoms (nitrogen, boron, sulphur and phosphorous) as fillers are a promising way to further improve the properties of composite materials [1]. Carbon nanomaterials play an important role in different applications of composite materials. Carbon nanomaterials containing nitrogen have been proved to promote the interaction of sulphur atoms with the carbon matrix [2]. Sulphur can also enhance the affinity of polysulfides to the carbons with better cycling behaviour, which can be used in applications, such as electrodes [3,4]. Zhou et al. [5] presented a Li/polysulphide battery with a high-energy density and long-cyclic life using three-dimensional nitrogen/sulphur co-doped graphene sponge electrodes.
In addition, the presence of heteroatoms in carbon materials enhances the performance of carbon nanomaterials in electrochemistry applications [6]. Among those, nitrogen (N) is reckoned as a peerless addition. Upon the introduction of more electronegative N atoms into sp2 hybridized C frameworks, the electric property and chemical activity can be modified [7][8][9][10]. Wang et al. demonstrated that the (typically~5-20 mg sample weight) in an inert atmosphere with simultaneous recording of the loss in weight of the sample as the temperature is raised at a uniform rate. Thermogravimetric analysis of waste materials has been widely investigated by many reporters in the literature [47][48][49][50][51][52]. In addition, FTIR, connected with TGA, precisely demonstrates the breaking of the chemical structure with evolved gases of low molecular weight to high molecular weight, depending on the degradation temperatures of the heat transformation process. For example, Zhu et al. investigated the pyrolysis of medical waste by using coupled TGA-Fourier transform infrared spectrometry (TGA-FTIR) [24]. Similar techniques were followed by Yang et al. [53] and Guintoli et al. [54] to investigate palm oil waste and agricultural waste, respectively. Furthermore, Ischia et al. conducted a thermogravimetric analysis coupled to a mass spectrometer to examine the pyrolysis of sewage sludge [55].
In this work, the possibility of using a selective thermal transformation technique for transforming waste latex to value-added material was studied. The evolved gases were characterised by using coupled TGA-Fourier transform infrared spectrometry. In addition, the final products after high-temperature transformation were also characterised to understand the future possibility of using this material.

Materials and Methods
Latex from waste mattress was collected from Resource Recovery Australia. To examine the chemical composition of collected latex, X-ray photoelectron spectroscopy (XPS, ESCALAB250Xi, Thermo scientific, London, UK; X-ray source: mono-chromated Al K alpha, Power: 164W (10.8 mA and 15.2 kV); binding energy reference: C1s = 285.0 eV for adventitious hydrocarbon) was used.
Then thermal degradation and gas identification were conducted using TGA-FTIR (Thermogravimetric-analyser model Perkin Elmer Pyris 1) from a low temperature (30 • C) to a high temperature (1200 • C) at a heating rate of 20 • C/min with the initial sample weight of 5.469 mg.
Selective thermal transformation of latex was investigated using a preheated high temperature furnace (Model: HTF 7060, Ceramic Engineering, Mortdale, Australia) and quantitative gas analysis was conducted by an Infrared (IR) gas analyser (Uras 26, ABB Automation GmbH, Frankfurt, Germany). For thermal transformation, 0.3 g of latex was put in a high purity alumina crucible and placed on graphite sample holder. This assembly pushed into the cold zone (150~200 • C) of a high-temperature horizontal tube furnace with the help of a graphite rod. It was kept in the cold zone for 12 min to avoid thermal shock, and then it was pushed into the hot zone (three different temperatures were studied: 600 • C, 800 • C, and 1000 • C) under argon gas flow at a rate of 1 L/min during heat treatment. The gas outlet was connected to an infrared (IR) analyser for the continuous monitoring of CO, CO 2 , and CH 4 gases produced during heat treatment. The heat treatment was carried out for 15 min, then samples were pulled back into the cold zone and kept there for 20 min to avoid thermal shock and re-oxidation of the final residual product after gas production.
The residual products were collected in a glass vial, and furthermore the structures of these products were examined by XPS (XPS, ESCALAB250Xi, Thermo scientific, London, UK) and Raman Spectroscopy (InVia, Renishaw using an Ar+ ion 70 laser at λ = 514.5 nm). The microstructure of the latex before and after selective thermal transformation was also investigated by an Oxford system attached with a Carl Zeiss AURIGA ® CrossBeam ® field emission gun scanning electron microscopy (FEG SEM) workstation and TEM equipped with a field emission gun (Philips CM 200, Amsterdam, The Netherlands).

Results and Discussion
To examine the morphological structure of latex, we used a scanning electron microscope (SEM), as shown in Figure 1. The low resolution microscope image shows the foam like homogeneous porous structure. Some other nano particles were observed from a high resolution SEM image. To understand the chemical structure of latex, XPS analysis was conducted. To understand the chemical components present in the surface of latex material, XPS analyses were conducted. From the total XPS spectra (Figure 2), it was noted that latex is mainly composed of C (73.22%) and O (12.46%), and also some other elements like Si (11.42%), Zn (2.11%) as well as N (0.79%). The deconvoluted C1s spectra demonstrates the surface functionalities with carbon atom. The high-resolution C1s spectrum of the latex reveal that there are three main components arising at 284.76, 286.35, and 288.75 eV for C = C (aromatic rings), C-O (alkoxy and epoxy), and C = O (carboxyl) groups respectively [56]. To understand the chemical components present in the surface of latex material, XPS analyses were conducted. From the total XPS spectra (Figure 2), it was noted that latex is mainly composed of C (73.22%) and O (12.46%), and also some other elements like Si (11.42%), Zn (2.11%) as well as N (0.79%). The deconvoluted C1s spectra demonstrates the surface functionalities with carbon atom. The high-resolution C1s spectrum of the latex reveal that there are three main components arising at 284.76, 286.35, and 288.75 eV for C = C (aromatic rings), C-O (alkoxy and epoxy), and C = O (carboxyl) groups respectively [56]. To understand the chemical components present in the surface of latex material, XPS analyses were conducted. From the total XPS spectra (Figure 2), it was noted that latex is mainly composed of C (73.22%) and O (12.46%), and also some other elements like Si (11.42%), Zn (2.11%) as well as N (0.79%). The deconvoluted C1s spectra demonstrates the surface functionalities with carbon atom. The high-resolution C1s spectrum of the latex reveal that there are three main components arising at 284.76, 286.35, and 288.75 eV for C = C (aromatic rings), C-O (alkoxy and epoxy), and C = O (carboxyl) groups respectively [56]. Thermogravimetric analysis (TGA) was also carried out to determine polymer degradation during continuous heating from 30 • C to 1000 • C at a heating rate of 20 • C/min. The TGA and derivative thermogravimetric (DTG) results are shown in Figure 3. The TGA (Figure 3) shows the heat transformation of latex which degrades in four stages of weight loss. The DTG curve shows that significant transformation of latex took place in two temperatures: a main step, which is the origin of the DTG peak at about 387 • C, and a small secondary step seen as a shoulder at somewhat higher temperature (about 438 • C).
J. Compos. Sci. 2020, 4, x 5 of 16 significant transformation of latex took place in two temperatures: a main step, which is the origin of the DTG peak at about 387 °C, and a small secondary step seen as a shoulder at somewhat higher temperature (about 438 °C). The thermal decomposition of waste latex began at the first step from 169 °C to 200 °C, with 3.6% weight loss for volatile compounds. Significant loss of mass occurred in Step 2 and Step 3. The maximum weight loss (67.8%) was found to occur in Step 2 from 289-330 °C which corresponds to the structural decomposition of latex polymer; and Step 3 corresponds to the second height weight loss (14.4%) from 423-488 °C which was also for the second phase decomposition of polymer of latex. The mass loss slowed down significantly at higher temperatures (Step 4) and was 4.9 wt% between 500-1000 °C. Finally, 9.3%, which is the final residue, was carbon black like material.
FTIR is widely used to characterised volatile species evolving during pyrolysis, and Figure 4 demonstrates the gaseous molecule during thermal transformation of latex. At a lower temperature of 50 °C (Figure 4a), there was no significant gas evolved. At the maximum decomposition of latex at 387 °C (TGA Figure 3), the gas species were detected at the FTIR spectrum peak with 1293 cm −1 -2000 cm −1 , and 3450-4000 cm −1 is the characteristic peak of water (moisture in source material) that appears due to the O-H stretching, which also found in biomass and refuse-derived fuel (RDF) waste reported by other researchers. The peak appeared ranging from 2255-2395 cm −1 due to the C = O stretching for CO2 species. At 387 °C, the small peak appeared at 2180 cm −1 , ranging from 2168 cm −1 -2210 cm −1 due to the C-O stretching for the CO molecule. The peak at absorption wavelength from 869-927 cm −1 was due to disubstituted alkane gas (CH3=CH3), and the peak appeared at 1025 cm −1 in the region 984-1084 cm −1 for alkene (CH2=CH2) [57,58]. At a higher temperature (1000 °C) the detection peak for ethane (CH3-CH3) and CO disappeared, a low amount CH4 was detected, and only a significant amount CO2 gas was produced [59][60][61].
The quantitative measurement of three gases (CO, CO2, and CH4) generated during the thermal transformation (600 °C-1000 °C) of latex in the horizontal tube furnace was also recorded continuously using an IR gas analyser under inert environment. The results of the gas analysis have been summarised in Table 1. Volumes of gases released at three representative temperatures are shown in Figure 5. At 600 °C, the volume of released CH4 gas was 5.5 and 7.5 times higher than that of CO2 and CO respectively. In addition, CH4 produced at 800 °C was also found higher by 13.1 and 31.3 than CO2 and CO respectively. Furthermore, latex was introduced at 1000 °C, and interestingly, green gas (CH4) production was detected 21.1 and 51.6 times higher than that of CO2 and CO respectively. The comparative result (Figure 5d) illustrates that negligible amounts of CO and CO2

%
Step 2 Step 1 Derivative Weight (% / min) Weight (%) The thermal decomposition of waste latex began at the first step from 169 • C to 200 • C, with 3.6% weight loss for volatile compounds. Significant loss of mass occurred in Step 2 and Step 3. The maximum weight loss (67.8%) was found to occur in Step 2 from 289-330 • C which corresponds to the structural decomposition of latex polymer; and Step 3 corresponds to the second height weight loss (14.4%) from 423-488 • C which was also for the second phase decomposition of polymer of latex. The mass loss slowed down significantly at higher temperatures (Step 4) and was 4.9 wt% between 500-1000 • C. Finally, 9.3%, which is the final residue, was carbon black like material.
FTIR is widely used to characterised volatile species evolving during pyrolysis, and Figure 4 demonstrates the gaseous molecule during thermal transformation of latex. At a lower temperature of 50 • C (Figure 4a), there was no significant gas evolved. At the maximum decomposition of latex at 387 • C (TGA Figure 3), the gas species were detected at the FTIR spectrum peak with 1293 cm −1 -2000 cm −1 , and 3450-4000 cm −1 is the characteristic peak of water (moisture in source material) that appears due to the O-H stretching, which also found in biomass and refuse-derived fuel (RDF) waste reported by other researchers. The peak appeared ranging from 2255-2395 cm −1 due to the C = O stretching for CO 2 species. At 387 • C, the small peak appeared at 2180 cm −1 , ranging from 2168 cm −1 -2210 cm −1 due to the C-O stretching for the CO molecule. The peak at absorption wavelength from 869-927 cm −1 was due to disubstituted alkane gas (CH 3 =CH 3 ), and the peak appeared at 1025 cm −1 in the region 984-1084 cm −1 for alkene (CH 2 =CH 2 ) [57,58]. At a higher temperature (1000 • C) the detection peak for ethane (CH 3 -CH 3 ) and CO disappeared, a low amount CH 4 was detected, and only a significant amount CO 2 gas was produced [59][60][61].
The quantitative measurement of three gases (CO, CO 2, and CH 4 ) generated during the thermal transformation (600 • C-1000 • C) of latex in the horizontal tube furnace was also recorded continuously using an IR gas analyser under inert environment. The results of the gas analysis have been summarised in Table 1. Volumes of gases released at three representative temperatures are shown in Figure 5. At 600 • C, the volume of released CH 4 gas was 5.5 and 7.5 times higher than that of CO 2 and CO respectively. In addition, CH 4 produced at 800 • C was also found higher by 13.1 and 31.3 than CO 2 and CO respectively. Furthermore, latex was introduced at 1000 • C, and interestingly, green gas (CH 4 ) production was detected 21.1 and 51.6 times higher than that of CO 2 and CO respectively. The comparative result (Figure 5d) illustrates that negligible amounts of CO and CO 2 were produced compared to CH 4 , and the rapid release of CH 4 gas was produced at higher temperatures (1000 • C) which is 3.1 and 49.0 times higher than CH 4 produced at 800 • C and 600 • C respectively. These results illustrate that bonding of latex degrades into small molecule gases at higher temperatures, which leads to gases like CH 4 and H 2 being produced at higher temperatures. were produced compared to CH4, and the rapid release of CH4 gas was produced at higher temperatures (1000 °C) which is 3.1 and 49.0 times higher than CH4 produced at 800 °C and 600 °C respectively. These results illustrate that bonding of latex degrades into small molecule gases at higher temperatures, which leads to gases like CH4 and H2 being produced at higher temperatures. After quantitative gas analysis (15 min heat treatment in a horizontal tube furnace) the residual black carbon like materials were characterised by XPS, Raman spectroscopy, SEM, and TEM.   After quantitative gas analysis (15 min heat treatment in a horizontal tube furnace) the residual black carbon like materials were characterised by XPS, Raman spectroscopy, SEM, and TEM.
XPS analysis (Figure 6) was performed to understand the main components in the materials which illustrated that all products after selective thermal transformation at different temperatures (C-600, C-800, C−1000) contain carbon and other elements. In detail, C, Na, Zn, O, N, K, S, Si were found at binding energy 284.  Table 2 shows the chemical composition of prepared materials and illustrates that all samples contained carbon as well as the same type of other elements. In addition, carbon percentage increased significantly at higher temperatures, while the percentage of S dramatically dropped at 1000 • C.  Table 2 shows the chemical composition of prepared materials and illustrates that all samples contained carbon as well as the same type of other elements. In addition, carbon percentage increased significantly at higher temperatures, while the percentage of S dramatically dropped at 1000 °C. Table 2. Chemical composition of carbon residue after heat treatment of latex in a horizontal tube furnace for 15 min at three different temperatures.

Materials
Chemical Composition by XPS Analysis  The microstructures of the heat-treated samples were investigated by transmission electron microscopy (TEM). The results (Figure 7) clearly indicate that the nanomaterials phase constituent after heat treatment at different temperatures and the structure of nano particles became more ordered by increasing the temperature. The phase separation was not significantly observed at lower temperatures, but at a higher temperature (1000 • C) discrete lights within the selected area electron diffraction (SAED) ring pattern reveals the phase separation of carbon and metals which complements the XRD results.  To determine the structure of the carbon phase, residual carbons were also analysed by Raman spectroscopy, where the scattering process includes contributions from various phonon vibration modes of materials. The spectrum from latex carbon residues after excitation with 514 nm laser light is shown in Figure 8. The spectrums peak at position 1359, 1346, and 1354 cm −1 for C-600, C-800, and C−1000 respectively, known as D (defect) band which feature representing disorder in graphitic structures; and the peak at 1599, 1584, and 1552 cm −1 for C-600, C-800, and C−1000 respectively, known as G (graphite) band, represents highly ordered graphitic structure [11,66,67]. The relative intensity ratio of IG/ID bands was determined from peak intensity, which can be used to determine the extent of disorder/or the degree of graphitisation in the carbon structure [66]. These were determined to be 1.33, 1.12, and 1.20 for C-600, C-800, and C−1000 C respectively; this result indicates extensive disorder and poor graphitisation in the carbon structure. Both Raman and X-ray diffraction results are in good agreement and indicate these materials to be disordered carbons.
Heteroatom carbon materials (N, B, P, S) are highly demanded materials for different application in composites [62][63][64][65][66]. There were various types of materials used for making carbon nanomaterials incorporated with different elements. For example, N-doped carbon materials were prepared by direct thermal treatment of carbons with N-containing precursors activated carbon [11,67], carbon To determine the structure of the carbon phase, residual carbons were also analysed by Raman spectroscopy, where the scattering process includes contributions from various phonon vibration modes of materials. The spectrum from latex carbon residues after excitation with 514 nm laser light is shown in Figure 8. The spectrums peak at position 1359, 1346, and 1354 cm −1 for C-600, C-800, and C−1000 respectively, known as D (defect) band which feature representing disorder in graphitic structures; and the peak at 1599, 1584, and 1552 cm −1 for C-600, C-800, and C−1000 respectively, known as G (graphite) band, represents highly ordered graphitic structure [11,66,67]. The relative intensity ratio of I G /I D bands was determined from peak intensity, which can be used to determine the extent of disorder/or the degree of graphitisation in the carbon structure [66]. These were determined to be 1.33, 1.12, and 1.20 for C-600, C-800, and C−1000 C respectively; this result indicates extensive disorder and poor graphitisation in the carbon structure. Both Raman and X-ray diffraction results are in good agreement and indicate these materials to be disordered carbons. A comparison study of our results and previous literature reported results based on carbon nanomaterials with different elements is shown in Table 3. Wu et al. [21] reported a two step synthesis method using the precursors 5-amino−1,3,4-thiadiazole-2-thiol and graphene oxide, with the final product doped graphene which composed of 0.48-1.8% N and 0.58-1.1% S. In this process (hydrothermal and pyrolysis) synthesise time required 22 h to get to the final product. Similarly, doped graphene (1.85% N and 0.99% S) was synthesised from cysteine precursor in three step process for a total reaction time of 29 h [23]. In addition, doped graphene (1.3-1.5% S) and doped (2.4-4.6% N and 1.2-1.7% S) graphene were prepared in a single step process (thermal treatment for 1h) from the precursors benzyl disulphide (+graphene oxide) and NH3-H2S gas (+graphene-silica) respectively [24,25]. However, urea and thiourea (GO + CNT) resulted in doped (2.4-4.6% N and 0.67-0.71% S) graphene/carbon nanotube via hydrothermal process at 180 °C for 12 h [26]. Table 3 shows that our synthesised carbon materials are much better than reported doped graphene material in terms of Sdoping (6.65-15.49%), reaction time (only 15 min), and remarkable N-doping (1.29% to 2.04%). Figure  9 compares these rations for different materials. Heteroatom carbon materials (N, B, P, S) are highly demanded materials for different application in composites [62][63][64][65][66]. There were various types of materials used for making carbon nanomaterials incorporated with different elements. For example, N-doped carbon materials were prepared by direct thermal treatment of carbons with N-containing precursors activated carbon [11,67], carbon nanotubes (CNTs) [68], graphene oxide (GO), and reduced graphene oxide (RGO) [11]. The nitrogen-containing precursors can be ammonia [68,69], urea [70], melamine [71], cyanamide [72], dicyandiamide [73], polyaniline (PANI) and polypyrrole (PPy) [74], and metal-organic frameworks (MOFs) [75]. On the other hand, S-doped carbon synthesised by using many precursors, mainly: thiophenemethanol [76], tetra(thiophene-2-ylmethoxy)silane [77], microporous poly(1,3,5-tris(thienyl)benzene) network (PTTB) [78], thiophene [78], H2S/graphene oxide [67], benzyl disulphide (BDS) [79], K 2 SO 4 or Na 2 S 2 O 3 /glucose [80], sulphur/graphite [81], etc. These S and N-doped carbons can be used as electrodes for supercapacitors [82], batteries [62], and fuel cells [79]. Synthesis of co-doped carbon materials from waste materials have not yet been reported.
A comparison study of our results and previous literature reported results based on carbon nanomaterials with different elements is shown in Table 3. Wu et al. [21] reported a two step synthesis method using the precursors 5-amino−1,3,4-thiadiazole-2-thiol and graphene oxide, with the final product doped graphene which composed of 0.48-1.8% N and 0.58-1.1% S. In this process (hydrothermal and pyrolysis) synthesise time required 22 h to get to the final product. Similarly, doped graphene (1.85% N and 0.99% S) was synthesised from cysteine precursor in three step process for a total reaction time of 29 h [23]. In addition, doped graphene (1.3-1.5% S) and doped (2.4-4.6% N and 1.2-1.7% S) graphene were prepared in a single step process (thermal treatment for 1h) from the precursors benzyl disulphide (+graphene oxide) and NH 3 -H 2 S gas (+graphene-silica) respectively [24,25]. However, urea and thiourea (GO + CNT) resulted in doped (2.4-4.6% N and 0.67-0.71% S) graphene/carbon nanotube via hydrothermal process at 180 • C for 12 h [26]. Table 3 shows that our synthesised carbon materials are much better than reported doped graphene material in terms of S-doping (6.65-15.49%), reaction time (only 15 min), and remarkable N-doping (1.29% to 2.04%). Figure 9 compares these rations for different materials. for a total reaction time of 29 h [23]. In addition, doped graphene (1.3-1.5% S) and doped (2.4-4.6% N and 1.2-1.7% S) graphene were prepared in a single step process (thermal treatment for 1h) from the precursors benzyl disulphide (+graphene oxide) and NH3-H2S gas (+graphene-silica) respectively [24,25]. However, urea and thiourea (GO + CNT) resulted in doped (2.4-4.6% N and 0.67-0.71% S) graphene/carbon nanotube via hydrothermal process at 180 °C for 12 h [26]. Table 3 shows that our synthesised carbon materials are much better than reported doped graphene material in terms of Sdoping (6.65-15.49%), reaction time (only 15 min), and remarkable N-doping (1.29% to 2.04%). Figure  9 compares these rations for different materials.  Moreover, N/S-codoped carbon spheres (0.95% S and 2.85% N) were synthesised by Kang and co-worker, via these precursors (D-glucose, L-cystenine, KOH, S-powder) in a three step process (total reaction time = 37 h) towards its application in Li-S battery [27]. A similar application (Li-S battery) for S/N-doped carbon fibre synthesised via a three step process for 63 h, was reported by Lan et al. [29]. However, catalytic oxidation activity of S/N-codoped porous carbon (2% N and 0.8% S) to make small organic molecules was synthesised in a single step (pyrolysis of cysteine for 2h at 800 • C) reported by Yao et al. [28]. Besides, S/N-doped porous carbon prepared by a two step process with a total reaction time of 171 h (used PPy precursors, KOH, S powder), performed well as electrode material for supercapacitors and fuel cells [30]. All these results illustrate that there is a great potential for using waste as input for producing doped carbon.
On the other hand, carbon nanotube (0.18% N and 3.02-4.29% N) from toluenethiol and sulphur precursors via a two-step process (hydrothermal at 180 • C and thermal treatment at 900 • C) for 9.5 h, towards its application for fuel cells. S/N-doped carbon nanotube (1-3% N and 0.6-1.5% S) prepared in a single step via pyrolysis of urea, thiourea and CNT at 800 • C for 1 h could be used in a similar application [10]. These results emphasize that this new approach for synthesised carbon materials can be considered as an alternative approach for producing high-value-added materials from waste. Produced carbon and other additives can be used as the filler in polymeric composite because of its exceptional fire resistance properties. Also produced methane can be used for producing green hydrogen or it can be used as a source of energy on its own. More study on the properties of produced product is needed to identify the best process for producing these materials and the best application for them.

Conclusions
The possibility of selective thermal transformation of waste latex to directly transform waste mattress component (latex) to value-added gas as well as carbon nanomaterials has been investigated. The waste latex can be suggested as a remarkable material to produce green gases, especially methane. The quantitative gas analysis suggested that temperature had significant effect on the production of CH 4 gas. A magnificent amount of CH 4 gas (18,5760 ppm/Kg) was produced at the higher temperature of 1000 • C, which is much greater than that produced at 800 • C and 600 • C, by factor 3 and 49 respectively. The resultant carbon residue was characterised by XPS, TEM, XRD, and Raman, suggesting the synthesis of value-added carbon materials with 7-15% S and 1-2% N. According to the literature review, our synthesis method can be considered as an alternative approach for synthesis of carbon after further investigation of the produced material. These results suggest the following possibilities for nanomaterials and should be further researched: (1) waste soft mattress materials (latex) can be recycled to produce green gas (CH 4 ) production; (2) carbon materials synthesis by direct carbonisation of latex; and (3) produced carbon can be used as a valuable material for other applications after full characterisation and investigation of the produced materials.