SeZnSb alloy and its nano tubes , graphene composites properties

Composite can alter the individual element physical property, could be useful to define the specific use of the material. Therefore, work demonstrates the synthesis of a new composition Se96-Zn2-Sb2 and its composites with 0.05% multi-walled carbon nano tubes and 0.05% bilayer graphene, in the glassy form. The diffused amorphous structure of the multi walled carbon nano tubes and bilayer gaphene in the Se96-Zn2-Sb2 alloy have been analyzed by using the Raman, X-ray photoluminescence spectroscopy, Furrier transmission infrared spectra, photoluminescence, UV/visible absorption spectroscopic measurements. The diffused prime Raman bands (G and D) have been appeared for the multi walled carbon nano tubes and graphene composites, while the X-ray photoluminescence core energy levels peak shifts have been observed for the composite materials. Subsequently the photoluminescence property at room temperature and a drastic enhancement (upto 80%) in infrared transmission percentage has been obtained for the bilayer gr...


I. INTRODUCTION
Although technology based on chalcogenide materials have delivered different unquestionable advantage; like infrared transmission and detection, threshold and memory switching, optical fibers, functional elements in integrated-optic circuits, non-linear optics, holographic and memory storage media, chemical and bio-sensors and infrared photovoltaics 1, 2 etc., but they have not free from a few questionable drawbacks (like, low edging, low electrical conductivity, stability etc), in comparison to counterpart technological materials (such as nano materials etc). 3To overcome the outlined drawbacks various compositions including metallic nano phase and rare earth composites [4][5][6] have been proposed by the investigators.Metal-chalcogenide alloys have attracted much attention in recent years, due to high thermal stability and structural complexity with the possibility to produce nano phase helicharical [7][8][9] structure.But improvements in working performances for these alloys could not achieve the upto desire demanding level.
Indeed, in the decade the nano materials; like, carbon nano tubes, nano rods, quantum dots etc, and recently investigated 10 graphene is boosted the nano scientific research.By the investigators have been made an effort, to understand and explore the changes in physical properties cause particle confinement at the nano scale or nano dimension.Attention has not been given only on the experimental investigations; also equally on the theoretical research for nano materials. 11Several models have been presented by the investigators 11 to describe the materials pure states and composites form. 12Composites are the multiphase of the materials, in which one phase is disperse in a second phase; as a result properties of the alloys in a combination of the individual component.Typically the filler element /-or alloy contain a large number inorganic building blocks in the nanosize regime a Tel: 91 -80 -22933279.Fax: +91 08023602602.Email: abhaysngh@rediffmail.com.and they distributed heterogeneously in the filler, in consequent reflect the physical properties in nonuniform form.Thus, composite simply reflects the intrinsic properties of the individual components of the alloys, which discrete in size, shape with a good structure property relationship 13 under the weak and strong interactions between the components.
Specifically two dimensional multi walled carbon nano tube (MWCNT), cylinder each carbon atom has precisely connects with three neighbours.The lattice of carbon nano tube (CNT) molecules mainly consists hexagons with a number of additional pentagons or heptagons within the structure. 13ncorporation of the MWCNT inside the inorganic matrix can modify properties of the special polymeric materials including structural, optical, electrical conductivity and mechanical enhancement.Such structural modification in the MWCNT, can be the consequence of reduction in interfacial energy between MWCNT side wall surface and complex alloy constitutes.While graphene (GF) has a large number molecules of the carbon atoms, which would strongly bound together in a flat configuration in a honeycomb lattice site structure.Out of the four outer electrons three electrons of each carbon atom has strongly bonded with three neighbouring atoms.In GF structure fourth electron 2p z orbital creates a p bond with the neighbouring carbon atom, while the s bonds provide the covalent backbone honeycomb lattice structure.The p and s bonds flexibility in the GF intrinsic structure provide a unique electronic state.Half filed p bond would allows to p orbital electrons tunnel from one atom site to another neighbouring site.Therefore, the GF internal structure has allows to electrons tunnel from site to site.This makes favourable circumstance to use it as a doping element in a complex chalcogenide alloy. 13,14 6][17][18] Further, these kind composite materials have also been struggling from lack of the comparative reports, cause difficulty to diffuse the nano tubes and graphene in the chalcogenide glassy matrix.Although theoretical descriptions on the MWCNT and bilayer GF have been predicted their low level doping possibility in chalcogenide alloys.In view of theoretical predictions and experimental evidences, herein made an effort has been made to resolve the problem, by successful synthesis of the chalcogenide-MWCNT and chalcogenide-bilayer GF composite materials with the Se-Zn-Sb (SZS) alloy.Subsequently, it has also investigated the impact on the chalcogenide alloy physical properties due to incorporation of small amounts of MWCNT and bilayer GF.

II. EXPERIMENTAL
Bulk materials had been prepared by employing the direct melt quenched technique.The high purity elements Se, Zn and Sb (99.999%Aldrich) and MWNCT tubes (length around 7-10 nm and dia 2 nm), bilayer GF had been taken in the appropriate compositional ratio: 96:2:2, 96:2:2+0.05%and 96:2:2+0.05%.Properly weighed materials were kept into clean (7 cm × 8 mm) quartz ampoules, whereas the ampoules was evacuated and sealed under at a vacuum of 10 −5 torr.Sealed ampoules were kept into a horizontal electric furnace and heated up to 1000 • C under a slow heating rate and maintained this furnace temperature for 15-16 hours.To ensure the homogeneity of molten materials ampoules were continuously rotating with the help of an electric motor, during uphold at a desired melting temperature.After achieving the desire melting time ampoules were frequently quenched in NaOH containing ice water, and prepared ingots of the materials were collected by breaking the ampoules.
Crystallographic structure of the prepared materials were confirmed from the X-ray Diffractometer (BRUKER D8 ADVANCE, Cu Kα , λ = 1.54 Å) and Differential Scanning Calorimetry (DSC).While surface morphologies were characterized by the ULTRA 55, Field Emission Scanning Electron Microscope (Karl Zeiss) equipment.Subsequently, Raman/(LabRAM HR) system was used for the spectroscopic characterization, with the 514.5 nm (2.41 eV) wave length Argon LASER in which charge coupled detector (CCD) in backscattering geometry, under the wave number range 30 to 3000 cm −1 , spectra were recorded with the resolution 0.5 cm −1 , where the operating power of laser was 2mV, while the Photoluminescence (PL) spectrums were recorded upto 1000 nm wave length range.The X-ray photoluminescence spectroscopy (XPS) core level and valence band spectra of the materials were obtained by the Multilab 2000 Thermo Scientific UK instrument.To perform the core and valance level spectra XPS measurement the Al Kα X-rays (1486.6 eV) was used under at a base vacuum of 3 × 10 −7 Pa, further, the powder samples were used for the furrier transmission infrared spectroscopy (FTIR) measurement.The fine powder of the materials and KBR chemical have taken in the ratio ∼5: 95 and made the 2.0 mm thickness pellets under at a 4 ton load.The measurements were performed in the wave number range 400 to 10000 cm −1 in transmission mode by using the Perkin Elmer Spectrum GX.The spectrums were collected at a resolution of 4 cm −1 in interval of 1 cm −1 .Moreover UV/Visible spectroscopic measurements were performed from the Sepctro S-600 equipment, for this fine bulk powder were kept in a sample holder carefully.Then spectra were recorded in UV/Visible absorption and reflectance modes, in the wave length range 200 to 1000 nm.

A. Materials Structures
Crystallographic structure of chalcogenide alloy SZS and its SZS-MWCNT and SZS-GF composites has exhibited in Fig. 1(a).The absence of sharp crystallization peak in the XRD patterns demonstrates materials have a random atomic arrangement in intrinsic complex structure.Alternatively to verify this outcome, composites whether have pure amorphous or amorphous glassy behaviour performed the DSC measurement (see Fig. 1(b)).DSC patterns of SZS, SZS-MWCNT and SZS-GF have exhibited the glass transition, crystallization and melting peaks, this revel materials have amorphous glassy structures and their onset crystallization and melting temperatures values would influenced from the addition of small amounts MWCNT and bilayer GF.Appearance of a slight deviation within the crystallization peak region in SZS-MWCNT has evident to the existence of two phases within the homogeneous amorphous structure.
This deviation in DSC pattern crystallization peak region has also verified from the outcome of the Field Effect Scanning Microscope measurement (see Fig. 2(a)-2(i)).Surface morphology of SZS alloy has shown a homogeneous structure at 100, 20 and 10 nm scales, while the composites morphologies have exhibited the presence of MWCNT and bilayer GF in diffuse agglomerated form within the amorphous structure at 100 and 20 nm scales, however at a smaller (10 nm) scale appears a homogeneous structure, cause, MWCNT and bilayer GF have a diffused structure but not a homogenous dispersion.Observation also demonstrates, the bilayer GF structure has a higher order diffusion and dispersion compatibility in SZS alloy, than the MWCNT.

B. Raman Interpretation
Raman spectra of amorphous (or disordered) materials are analogous to the crystalline materials only difference broadening in the relative peaks, the broadening in Raman spectra demonstrates to disorder structure of the alloy. 19Raman spectroscopic outcome (see Fig. 3(a)) of SZS alloy has shown a broad Raman active Se-Se peak in region between 220 to 270 cm −1 , with a sharp position at 252 cm −1 .Obtain Se-Se peak position in SZS composition is nearly consisting with pure Se-Sb alloy peak value 250 cm −1 , 20 which arises due to Se 8 ring structure. 21The Se-Sb Raman low phonon band peak in SZS alloy has appeared at 140 cm −1 , while the Zn-Sb sharp band edge has noticed at 107 cm −1 , which is also consist with past reports. 22The SZS-MWCNT composite is exhibited Se-Se, Se-Sb and Zn-Sb peaks at 236, 140 and 107 cm −1 with the mixed Raman G & D modes low energy phonon peak at ∼188 cm −1 , while the broad diffuse D and G bands active peaks, at 1344 & 1574 cm −1 and defect diffuse 2D band identify at 2699 cm −1 , this could be related to E 2 g Raman active mode.SZS-MWCNT composite is exhibited the strong (D, G and 2D) band peak shift toward lower wave number compare to well known pure MWCNT peak values 1353, 1582 and 2708 cm −1 .Moreover, in SZS-GF composite Se-Se, Se-Sb and Zn-Sb peaks are appeared at 246, 140 and 107 cm −1 with the low phonon G and D mixed Raman peak at 187 cm −1 , the doubly degenerate highly diffused (very low intensity) D and G band peaks have been appeared at 1382 and 1574 cm −1 ; in which 2D peak has been nearly disappeared.Dispersion in sp 2 carbon nanotubes and graphene phonon modes A, E 1 and E 2 symmetry 22,23 could be due to splitting of the doublydegenerate 2D peak into nondegenerate mode.Thus, the intrinsic structures of MWCNT and GF would have modified. 12,24

C. XPS Interpretation
In this subsequent, to confirm the stoichiometries chemical concentration in these materials XPS analysis was also performed.The quantized atoms core energy level XPS spectra of 3d 5/2 FIG. 3. (a) Raman spectra for SZS alloy and SZS-0.05%MWCNT& SZS-0.05%GF composites, in the wave number range upto 3000 cm −1 , (b) XPS core level spectra of the element Se for SZS alloy and SZS-0.05%MWCNT and SZS-0.05%GF composites, (c) XPS core level spectra of the element Sb and Zn (Zn core level is given in inset profile) for SZS alloy and SZS-0.05%MWCNT and SZS-0.05%GF composites, (d) XPS survey and C1 core level (C1 core level is given in inset) spectral peaks for SZS alloy and SZS-0.05%MWCNT& SZS-0.05%GF composites Se of SZS, SZS-MWCNT and SZS-GF is given in Fig. 3(b).The 3d 5/2 Se core level peaks of the SZS, SZS-MWCNT and SZS-GF have been appeared at 59, 55 and 55 eV bonding energies.A considerable 3d 5/2 Se core level peak shift towards to lower bonding energy has been observed for the SZS-MWCNT and SZS-GF composites.In which SZS-GF composite counts much higher than SZS-MWCNT and slightly superior to SZS alloy, it could be more electropositive MWCNT and GF inclusion relative to Se. [25][26][27][28][29] While the bonding energy core level spectra of 3d 5/2 Sb (see Fig. 3(c)) for these materials demonstrates, the peak position of Sb is unaffected from the incorporation of MWCNT and GF in SZS alloy.Except peak broadening and increase in the counts value for SZS-GF compare to SZS-MWCNT composite and parent alloy, with a significant difference SZS alloy has a little peak broadening [25][26][27][28][29] in the SeO at ∼ 544 eV while this peak is disappeared in the composites.Subsequently it is also evident the SZS-MWCNT composite counts value drastically reduced and became lower than parent alloy.Moreover, the diffuse core level bonding energy peaks of 2p 3/2 Zn has been observed, in well defined range 1021 to 1050 eV (see inset profile in Fig. 3(c)).The bonding energy core level survey spectra of these materials is exhibited [(Fig.3(d)) and C1 (285 eV) (in the inset)] in which peak shift toward lower bonding energy (at 977 eV) for the element Zn compare to its original peak position 1021 has been observed.This bonding peak shift might be the presence of greater amounts electronegative concentrations of Se and Sb in SZS alloy and carbon in composites.Along with survey spectrum is also exhibited the other oxygen impurity and mixed phase of the alloying elements smaller peaks at 603, 574, 369, 202, 179 and 143 eV bonding energy values.The peak bonding energy reduction has observed at 143-138 for the SZS-MWCNT composite in comparison to original SZS alloy.While in SZS-GF composite additional peaks has appeared at 255, 229, 161 eV with the reduced peak value at 200 and 138 eV.The appearance of additional small XPS peaks in SZS-GF composite is also providing the evidence regarding to mixing the graphite sub levels in the Se alloying chains. 29

D. UV/Visible and Reflection spectroscopy
][32] Thereby, UV/Visible absorption spectrums of SZS alloy and SZS-GF composite have shown (see Fig. 4(a)(i, ii, iii)) a large absorption tails with adjacent peaks in the range 400 to 850 nm, whereas a sharp absorption peak appears for the SZS-MWCNT composite.The amount of absorption percentage is recorded higher for SZS-MWCNT composite than SZS and SZS-GF.The optical energy band gaps for the SZS, SZS-GF and SZS-MWCNT, were evaluated in a common absorbance spectral range value 600 to 850 nm.By using plots (see Fig. 4(b)(i, ii, iii)), the optical energy band gaps for SZS alloy, SZS-GF and SZS-MWCNT composites have been obtained 1.37, 1.39 and 1.41 eV, respectively.These materials optical energy band gaps values are belonging to well described range (≥ 3 eV) for chalcogenide glasses.Subsequently, reflection spectrums of the materials (see Fig. 4(c)) have exhibited the reflectivity maximum and minimum; this is also consist with the absorption outcomes.

E. PL Interpretation
In amorphous semiconductors usually PL has not appears at room temperature, 38 but could be at low temperatures. 38PL event in such materials usually has interpreted as; an electron during the optical transition connected with the tunnelling and acquires an adjacent or a near region at the energy level, whereas, their excited state level just below the potential barriers. 38Therefore, the wave function can be localized practically in a specific micro region between the adjacent potential barriers.The coulombic interaction a bound state electron-hole pair creates, form a new energy level in the forbidden band.The newly formed energy level is known as a localised state.The potential strength of these localised states is depending on specific alloying elements, in which discrete levels and localised states are connected through a channel.Under the suitable circumstances an optically excited electron gradually gets back to the original region of the hole.This process is usually related to gradual tunnelling and diffusion, corresponding jumps connects to an interaction with phonon.2]39 Obtain PL spectrums for the described materials at the room temperature is exhibited in Fig. 5(a).As per predictions parent SZS alloy has not showing PL single, the SZS-MWCNT composite is also following the same trend, but contradictory SZS-GF composite has exhibited a broad PL single peak in the wave length range 635 to 790 nm.This PL single observation is consisting with well described behaviour in chalcogenide glasses; phonon energy decline after attending the maximum excitation.

F. FTIR Spectrum Interpretation
IR can provide valuable informations, 40 about the impurity atoms properties and their chemical bonding in the spectral ranges 0.5 -7, 0.8 -12 and 1.2 -16 μm.Specifically mid IR (3-25 μm wavelength, wavenumber: 3333 to 400 cm −1 ) transparency is important because it could be covered atmospheric windows of 3-5 and 8-12 μm wavelength regions along with molecular fingerprints. 41R optics utility of chalcogenide glasses depends on the restrictions on vibrational absorption bands by incorporation of the impurities.Therefore, it is important selection of the chemical composition to make a higher order IR transmitting glass. 42Under test materials FTIR transmission spectrums has exhibited in Fig. 5

(b). Diffusion of elemental covalent bonds of metalloid Sb and metallic
Zn in non-metal Se chains and rings has appeared in SZS alloy, by showing the non existence of sharp absorption peak in the spectrum.SZS-MWCNT composite has also showing transparency throughout the recorded spectral range with a relatively higher transmission percentage (∼18 to 48) than parent alloy.A drastic enhancement in IR transmission percentage (37 to 81) has been noticed for the SZS-GF composite in the entire recorded spectral range, in comparison to SZS alloy and SZS-MWCNT composite, nearly double at lower frequency, thrice and one half on higher frequency, while the highest IR transmission has been reported in such glasses around beyond the 20 μm. 43,44 is could be change in the intrinsic molecular structure of the material cause the induced effects on stretching and bending bond vibrations.[47]

IV. DISCUSSION
Physical property changes in these materials could be interpreted as: the amorphous Se structure is a mixture of two structural species, polymeric chains and Se 6 and Se 8 eight member ring molecules.The bonding within the structural units is covalent, whereas the inter-structural forces is of the weak Van der Waals type.The condensed form of Se has twofold nearest-neighbour coordination with distances d from 2.32 to 2.37.The bond angle is slightly above 100 0 , 4s 2 4p 4 valence electronic structure with a helical chain structure.Variation in dihedral angle can play important role in the structural chemistry of twofold coordinated cause the bond distance and bond-angle potential functions steeper than the dihedral angle potential, therefore, dihedral angle can be distorted more easily than other molecular parameter.Along with the coordination defects can also contribute substantially in properties modifications of amorphous Se. 48,49 Thereby, incorporation of foreign metallic hexagonal Zn (1021 eV) and metalloid Sb (530 eV) have affects the non-metallic Se (59 eV) host dihedral angle bonds with an induced structural inhomogeneity.It is expected during the thermal agitation the high energy bond of Zn 2e+ breaks the low energy Se 3e− chain and rings in the presence of second high energy Sb 3e− bond, whereas, Sb 3e do not contributed to transmit the Se chain length, but under an electronegative affinity interaction it can increase the concentrations of Se-Sb electronegative bonds. 50While other heteropolar bonds Zn-Sb, Se-Zn, Se-Sb and Se-Zn-Sb are present.However the presence of Zn cations can also substantially influence the electronegative Se-Se, Sb-Sb and Se-Sb bonds strength through a large number of cross linking Zn-Zn, Zn-Sb, Zn-Se and Se-Zn-Sb bond densities, 51,52 therefore the whole matrix is would transformed into a complex alloy; in which anion and cation exists.As a consequence, complex system is producing a large number of unsaturated hydrogen bonds accompanied Van der Waals like bonds; substantially, it can increase the structural and thermal stability of the SZS alloy.
Small amount incorporation MWCNT, GF, in parent SZS alloy affects the chemical equilibrium and localised density of the states.By making the additional homopolar heteropolar bonds C-Zn, C-Sb, C-C, C-Se, Zn-C-Sb-Se with other bonds.The incorporation of MWCNT and GF in SZS are increasing the electronegativity of the materials, this might increased the number of Van der Waals like bonds within the materials, as a consequence optoelectronics property is enhanced. 12,14 bsequently, it is possible to low dimension inorganic SZS alloy constituents can interact with two dimensional periodically structured organic MWCNT and bilayer GF armchair and zigzag bonds.During the melting process the MWCNT and bilayer GF could be functionalized through the inclusion of thermally excited SZS alloy constituents in MWCNT and bilayer GF configurations by the diffusion.Therefore, at high temperature under the long diffusion process (∼15 h) between the SZS and MWCNT & GF can broken the symmetry of the σ and π bonds, the sudden cooling of molten forms of the composite materials would provides the frozen solid solution.It has expected during the melting diffusion process.The week zigzag bonds (correspond to π bond) of MWCNT and bilayer GF would highly affected and diffuse in the SZS localised states.while the high energy armchair bonds (correspond to σ bond) loss their original periodicity, as a consequence homogenous crystallographic structure has appeared in XRD and DSC patterns for the composite materials.The inferior Tc value and agglomerated morphology in MWCNT composite is arises due to the nonquadratic thermal expansion, cause strong multi layers side wall properties.While, in bilayer GF a quadratic thermal expansion occurs, therefore diffusion order of σ and π bonds is higher, as a consequence corresponding Tc value is slightly higher with the diffuse agglomerated structure.
Subsequently presence of a metallic element Zn is also contributed sufficiently 14 in reduction to the thermal sustainability of the composite materials.
Dispersion in G, D and 2D Raman band peaks in the composite materials could be relates to change in charility, zigzag and armchair bonding cause to formation of new defect states in the host Se chains and rings in presence of elements Sb and Zn. 12 Specifically, in MWCNT and bilayer GF the Coulombic interaction depends on the metallicity / or geometry of the materials, therefore, it is possible SZS-MWCNT and SZS-GF composites can induce more electron-hole interactions with changing in the bond orientations, thereby, composites begin to transform toward lower dimensionality with a non periodic atomic arrangements.The appearance of considerable disperse G, D and 2D Raman bands in SZS-MWCNT reveals the composite tend toward one dimensional structural transformation due to suppression of carbon nano tube stacked layer under a disturbed symmetry, (might be in sp 3 hybrid structure, reason a little knowledge regarding the suppressed structure of carbon nano tubes), while in the SZS-GF composite complete dispersion of these bands peaks demonstrates the one dimensional sp3 hybridized (or graphene ribbon like structure) structural transformation.In which stacked layers drastically suppressed and induced a strong effect to make a mixed amorphous structure of the composite. 12,14,53 Frthermore, composites collective quantum localised states sp3 hybridition transformation has also affected the elemental core level spectra; which has been appeared in XPS outcomes.The 3d 5/2 Se core level peak shift toward the lower binding energies in SZS-MWCNT and SZS-GF can be related to reductions in metallicity of the composites compare to parent alloy.Lower strength of the 3d 5/2 Se core level peak of SZS-MWCNT compare to SZS-GF can relates to non-homogenous mixing of the composite configuration.The appearance of no change in 3d5/2 Sb peak compare to parent composition can be connected to non chain transmitting property of the element, while Zn core levels peak shifts toward lower the value side could be reduction in metallic nature.
Since hybridization of the orbitals in chalcogenide materials depends on the defects creation ability of the foreign elements. 38Therefore the impurity state π -electrons of SZS-MWCNT composite may play an important role in optical properties alternation.Cause, in MWCNT a π -plasmonic resonance occurs and spans within the entire visible spectral region with tail extending to nearinfrared wavelength range. 53The π -plasmon is a collective excitation depends on surface plasmons, therefore, the optical transitions can occur between π and π * energy bands at the same cutting line for the initial and final states.As a consequence, a strong absorption form between the top (π ) and bottom (π * ) bands and it vanishes at the wave vector k. 12 Thereby, constituents of SZS alloy expected to create numerous number of defect states between the side wall surfaces, whereas, optical absorption vanishes at the edge of the wave vector k.Therefore, SZS-MWCNT composite is exhibited the strong UV/Visible absorption property but its band tail could not expand longer due to the existence (or non-homogeneous dispersion of MWCNT) of strong defects armchair (correspond to σ bond) bonds, this trend is also appeared in the reflection spectra.On other hand GF has honeycomb structure and its optical wave vector limit not as sharp as carbon nano tubes.The quadratic thermal expansion and greater suppressed ability allows to a large change in charility, thereby, zigzag and armchair bonds spread actively.As a consequence optical absorption band tail and optical energy band gap larger and smaller than MWCNT composite, therefore, the corresponding reflection spectra profile has improved.Moreover the structural transformation of composite materials are also induced the other physioptical properties; such as PL property which reflects the transitions between the lone-pair states or inter band transitions.Thus SZS-GF composite material has exhibited the PL property at the room temperature due to a collective phononic emission under the cyclotronic resonance, cause, creation of huge number electron-hole dipoles by breaking the symmetry of the system.Subsequently, phonon spectra characteristic of the rings and chains could be derived; therefore, infra-red optical properties reflects a composite spectrum with contributions from both the ring and chain components under at most weak effects due to the inter-structural forces, in which incident photon energy matches the energy for allowed phonon creation, therefore photon can transfer energy directly to create an acoustic or optical phonon.Thus the vibration of an oscillating dipole moment of the ions can be described the material FT-IR property.Therefore a dramatic change is appeared in FT-IR transmission percentage spectra for the SZS-MWCNT and SZS-GF composites compare to parent SZS alloy.

V. CONCLUSIONS
In conclusive remarks the successful synthesis of new SZS chalcogenide glass and SZS-MWCNT & SZS-GF composites could be useful subject for it prospective technical investigations.Structural dispersion of MWCNT and bilayer GF in the glassy form from the direct melt quenched process can be considered a remarkable achievement.Unexpected PL single at room temperature, and huge enhancement in FT-IR transmission parentage (which earlier has not been noticed in chalcogenide glasses) for the SZS-GF system makes it useful for the various optoelectronics.Further this study left the unsolved problem; how to physical parameters would modify by incorporation of MWCNT and GF in different kind of chalcogenide system.