Port Said University Facutly of Science

Chemistry Department

New Polymer Composite Materials

Under The Supervision

of

AssocProfAyman S. Al-Hussaini

Prepared by

Aliaa IsmailDesoky Fourth level student

Industrial and AppliedChemistry Department

(2015-2016)

Aknowledgement

Firstely, I thank my God for providing me with everything that I require in

completing this project .

I would like to express my deepest thanks to my supervisor " Dr. Ayman S. Al-

Hussaini" for his patient guidance , constant supervision and his continuous support,

I consider myself lucky for being able to work with a very professional lecture like

him .

Also I'd like to thank "Dr. Ibrahim Mohey" head chemistry department port

said university for his contribution .

I'd like to express my special gratitude to all doctorsanddemonstrstors who

taught me during the four years.

My deepest thanks and appreciation to my parent, family and friends for

their cooperation, encouragement which helped me In the completion of this project .

Aliaa Ismail Desoky

Content……………………………………………………………………………………………….Page . No

Introduction to Polymer Composites ………………………………………………………………1

Definitions and Classification……………………………………………………………………..2-3

Thermosetting Polymer and NanoClay based Natural Fiber Bio-Composites……………………..4

Analysis of Mechanical Behavior of Glass Fibre/ Al2O3- SiCReinforced Polymer composites ……………………………………………………………………………………………………….5

Effect of different hybrid method on properties of carbonnanotubes/dolomite hybrid filled phenolic composites……………………………………………………………………………..…5-6

Preparation of composite particles with magnetic silica coreand fluorescent polymer shell………………………………………………………………………………………………...7-8

Anaerobic Biodegradation of Polymer Composites Filledwith Natural Fibers………………...…8-9

Polyvinyl alcohol–sulphanilic acid water soluble composite as corrosion inhibitor for mild steel in hydrochloric acid medium …………………………………………………………………….…10-9

Cross-linked gel polymer electrolyte containing multi-wall carbon nanotubes forapplication in dye-sensitized solar cells……………………………………………………………………………..11-13

Development of Natural Rubber-Fibrous NanoClayAttapulgite Composites: The Effect of Chemical Treatment of Filler on Mechanical and DynamicMechanical Properties of Composites………………………………………………………………………………………….14

Bioactivity of a Bio-composite Fabricated from CoCrMo/Bioactive Glass by Powder Metallurgy Method for Biomedical Application………………………………………………………...………15

The effect of nanosilica on the mechanical properties of polymer-cementcomposites (PCC)……………………………………………………………………………………………….16 Synthesis and ion conduction mechanism onhot-pressed sodium ion conducting nano composite polymerelectrolytes……………………………………………………………………………17-18 Flammability, Biodegradability and Mechanical Properties of Bio-Composites Waste Polypropylene /KenafFiber Containing Nano CaCO3 with Diammonium Phosphate…………………………………………………………………………………..….18-19

Characterization of Carbon Fiber Reinforced Epoxy Composites Modified with Nanoclay and Carbon Nanotubes……………………………………………………………………….………20-21 Thermal behavior of BST//PVDF ceramic–polymer composites…………………..………….. 21-22 Hybrid composites prepared from Industrialwaste: Mechanical and swelling behavior………………………………………………………………………………………….22-23 Development of a Safe Solid-State Microorganism/Biodegradable Polymer Composite for Decomposition of Formaldehyde………………………………………………………………….23 Fracture mechanisms in epoxy composites reinforced with carbonnanotubes…………………24-25 Enhanced mechanical properties of polyvinyl alcoholcomposite films containing copper oxide nanoparticlesas filler……………………………………………………………….…………...25-27 Effect of PET functionalization in composites ofrubber–PET–HDPE type………..………….28-29 Effect of types of wood on the thermal conductivities of wood sawdust particle reinforced composites…………………………………………………………………………….………..29-30 Looking for Oil-free Building Materials Clay Pipes to ReplacePolymer Pipes……………….30-31 Reinforcement of bacterial cellulose aerogels with biocompatiblepolymers…………………31-32 Electrodeposition, characterization, and antibacterial activity ofzinc/silver particle composite coatings……………………………………………………………………………………….…32-33 Effect of silicon carbide and pulping processes on physical andmechanical properties of pulp plastic composites (PPCs)………………………………………………………………………………34-35 The Effect of Pressure on Moisture Diffusion in Polymer Matrix Composites…………..…….35-36 Effect of epoxy modifiers (Al2O3/SiO2/TiO2) on mechanicalperformance of epoxy/glass fiber hybrid composites………………………………………………………………….……………37-38 Composite gels based on Poly (vinyl alcohol) for biomedicaluses……………………………38-39 Enhancing Fracture Toughness of Glass/Epoxy Compositesfor Wind Blades Using Silica Nanoparticles and RubberParticles……………………………………………………………..39-40 Polymer composites containing non-covalently functionalizedCarbon nanotubes: a study of their dispersion characteristicsand response to AC electric fields…………………………….……..40-41 Mechanical Behaviour of Polypropylene Reinforced PalmFibers Composites……………….41-42 Glass Fiber Reinforced Polymer-Clay Nanocomposites:Processing, Structure and Hygrothermal Effects onMechanical Properties……………………………………………………….……….42-44 Mechanical properties of HDPE/textile fibers composites…………………………………..….44-45

Mechanical and flame-retardant properties of epoxy/Mg–Al LDH composites………………..…45 Poly (vinyl alcohol – aniline) water soluble compositeas corrosion inhibitor for mild steel in 1 M HCl ………………………………………………………………………………………..……46-47 Effects of bone particle on the properties and microstructure ofpolypropylene/bone ash particulate composites………………………………………………………………………………….……47-49 References………………………………………………………………………………..……..50-52

Introduction to Polymer Composites Man has discovered long ago that clay bricks can be made stronger and moredurable by reinforcing

the clay with straw and sticks. There are also many naturally occurring composites, such as wood

and bones. Wood consists of strongcellulose fibers held togetherby a lignin matrix. Bones consist of

short and softcollagen fibers embedded in a mineral matrix. Both wood and bones demonstratethe

outstanding adaptability and capabilities of composite materials in supportingloads under diverse

conditions. Composite materials, thus far can be definedas materials consisting of two or more

constituents (phases) that are combined atthe macroscopic level and are not soluble in each other.

Modern synthetic composites using reinforcement fibers (one phase) and matrices (another phase)

ofvarious types have been introduced as replacement materials to metals in civilian,military, and

aerospace applications. The marking point in the composites revolution has been associated with the

development of carbon and boron fibers in the 1960s.These new fibers, which have higher stiffness

than glass fibers, gave a significant increase in the stiffness of composites structures. The ability to

tailor these materials to the specific needs and their superior properties are the drivingforce behind

this increased utilization. The high strength, high stiffness-to-weightratio of carbon-fiber-reinforced

polymers made them more suitable for aerospaceand high-performance sporting equipment. The

superior resistance of glass fibersto environmental attack made glass-fiber-reinforced polymers

more attractive formarine products and in the chemical and food industries.While the advantages of

composites over conventional materials are obvious,one must not overlook their limitations. Being

relatively new materials, there isan apparent lack in knowledge and experience that limits their fast

incorporationinto existing and new designs. The high cost of materials and complexities in

theirmanufacturing is perhaps the most serious problem that designers with compositeshave to deal

with. Components fabricated from composite materials are endeavored to be made net shape. This

in part is made possible because of the fact that many components are built layer by layer out of

contoured two-dimensional plies that closely capture the final shape of the product.

Definitions and Classification

Composite materials are composed of mixtures of two or more distinct constituentsor phases

separated by a distinct interface. For a material to be called a “compositematerial” within the

context of the technical discussion in this book it must satisfythe following conditions :

1. It is manufactured (naturally occurring composites such as wood and bones areexcluded).

2. It is composed of two or more physically and/or chemically distinct and suitablyarranged

constituents. This arrangement of constituents is imparted into thecomposite during early

manufacturing stages. Metal alloys that produce secondphase or intermetallic precipitates during

solidification or during subsequent heattreatment are not considered as composites.

3. The constituents are present in reasonable proportions.

4. It has characteristics that are not depicted by any of the constituents alone.Thus, a metal alloy that

develops second phase particles subsequent to heat treatment(e.g., precipitation hardening) is not a

composite. On the other hand, tungstencarbide powder that is mixed with a binder metal,

compacted, and sintered forms acemented carbide composite.The constituent that is continuous and

most of the time is present in the greaterquantity is called the matrix. The normal view is that it is

the matrix propertiesthat are improved on incorporating another constituent to produce a composite.

Themain purpose of the matrix is to enclose and bind the reinforcement, thus effectivelydistributing

applied load to it, and to protect it from outside and hostile environment.The majority of current

applications of composites utilize polymeric matrices, butmetal and ceramic matrices are also found

in specific high-temperature, high-wearapplications.The second constituent in a composite is the

reinforcement phase, which isin most cases made of a stronger and stiffer material than the matrix.

The reinforcementis the primary load-bearing constituent in the composite and its shape,volume,

and arrangement adversely affect the properties of the composite material.Reinforcements can be in

the form of long fibers, short fibers, particles, orwhiskers.

Composites are classified according to the type of matrix material into metalmatrix, ceramic matrix,

or polymer matrix composites. It is further classified accordingto the reinforcement form and

arrangement into particulate reinforced (random,preferred orientation) and fiber reinforced

(continuous, discontinuous, aligned, random). Hybrid composites are multilayer composites witha

mix of fibers in each (or some) of the layers. Advanced composites are thosecomposite materials

traditionally used in aerospace applications and are characterizedby high specific stiffness and

strength. Commonly, composite materials show marked anisotropy (properties are dependenton

direction) because of the distinctive properties of the constituents and the inhomogeneousor

textured distribution of the reinforcement. The composite materialsapproach isotropic state as the

reinforcement phase becomes smaller in size andrandomly oriented.[i]

Figure 1:Classification of composites[ii]

Thermosetting Polymer and Nano Clay based Natural Fiber Bio-Composites Biocomposite materials based on natural fibres are of great interest, often due to their low cost

origin. Natural fibrereinforcedbiocomposites are emerging as a possible substitute to glass

fibrereinforced composites. Owing to the advantage of low cost, lowdensity, reduced energy

consumption, natural fibres offer an opportunity to developing countries to use their own

naturalresources for producing composite materials.Although glass and other synthetic fibre-

reinforced plastics possess high specificstrength, their fields of application are very limited because

of the inherent higher cost of production. In the present workexperiments have been conducted to

study the influence of nanoclay in polyester resin based composites reinforced with

coirfibres.Themechanical properties of the composite are evaluated. The addition of nanoclay to the

coirfibre reinforced compositesexhibited considerable enhancement in the mechanical propertiesat

lower cost and therefore can be used as a substitute to glassfibres.[iii]

Figure2:Images of specimen preparation and testing.

Analysis of Mechanical Behavior of Glass Fibre/ Al2O3- SiCReinforced Polymer composites

Nowadays, polymer matrix composite plays a vital role in industries namely automotive, aerospace

and marine. This paper involves thefabrication of epoxy and polyester resin composites using

aluminiumoxide, silicon carbide with different proportion of Al2O3 andSiCalongwith GFRP. A

mixing unit has been fabricated for making reinforcement mixtures. Mechanical testing like tensile,

impact hardness shear biaxial are conducted in order to know the properties of fabricated

composites. The result shows that composites with epoxy resin shows higherstrength as compared

to composites with polyester resin.[iv]

Figure3:Biaxial stress Vs. Test samples

Effect of different hybrid method on properties of carbonnanotubes/dolomite hybrid filled phenolic composites Hybridization of multi wall carbon nanotubes (MWCNTs) with other filler in polymer matrix

composites (PMC) is one of thetechniques for combining different properties of fillers for making

more unique composites. In this work, the hybrid filler(CNTs–dolomite) are prepared via chemical

vapour deposition (CVD hybrid) and the milling method (physically hybrid).

Theeffect of different hybrid method on properties of multi wall carbon nanotubes/dolomite hybrid

filled phenolic composites werestudied. Phenolic/CVD hybrid composites and phenolic/physically

hybrid composites with different filler loadings were preparedusing hot mounting press. The

prepared samples were characterized for their thermal conductivity and hardness. The

thermalconductivity was measured using the Transient Plane Source (TPS) method, using a Hot-

DiskTM Thermal Constant Analyzerand the hardness was measured using Rockwell micro-

hardness.

The results showed that at 5% filler loading, the phenolic/CVDhybrid composites were capable of

increasing the thermal conductivity and micro-hardness up to 7.22% and 101.6%

respectivelycompared to pure phenolic.[v]

Figure4: Thermal conductivity of phenolic, phenolic/CVD hybrid and phenolic/physically hybrid composites as a function of filler loading

Figure5: Hardness of phenolic, phenolic/CVD hybrid and phenolic/physically hybrid composites as a function of filler loading

Preparation of composite particles with magnetic silica coreand fluorescent polymer shell Dual functions of magnetic and fluorescent propertieswere created in composite particles that

incorporatedmagnetite (Fe3O4) nanoparticles in particle cores of silica andfluorescent pyrene in

particle shells of polystyrene. TheFe3O4 nanoparticles were prepared with a

conventionalhomogeneous precipitation method and surface modifiedwith a coupling agent of

carboxyethylsilanetriol. The silicaparticles incorporating Fe3O4 nanoparticles were synthesizedwith

a modified Stöber method in which the Fe3O4 nanoparticles were added to a System

oftetraethylorthosilicate(TEOS)/ammonia/water/ethanol. Then, theMagnetite/silicacomposite

particles were coated with the pyrene/polystyreneshell in a soap-free emulsion polymerization,

which wasconducted in the presence of pyrene in a mixed solvent ofwater/ethanol. The composite

particles prepared in the mixedsolvent had both magnetic and fluorescent properties. Thefluorescent

spectrum of the particles with Fe3O4 was verysimilar to that without Fe3O4, indicating that the

magneticcomponent within the core particles scarcely interfered withthe fluorescent emission from

the polymer shell.[vi]

Figure6: TEM image of magnetic silica particles prepared at [TEOS]=0.2 M, [H2O]=5 M, [NH3]=1 M, and 30 °C. The Fe3O4 nanoparticles were added at 2 min after the initiation of TEOS hydrolysis

Figure7: TEM image of silica particles prepared without the addition of Fe3O4 nanoparticles at [TEOS]=0.2 M, [H2O]=11 M, [NH3]=1 Mand 35 °C

Anaerobic Biodegradation of Polymer Composites Filledwith Natural Fibers

Polymer composites with natural fibers preparedby melt blending were investigated. Synthetic

andnatural macromolecules were used, including poly(lacticacid), polyhydroxybutyrate-co-

polyhydroxyvalerateandlow density polyethylene. These polymers were filled withflax fibers.

Mechanical properties of the composites, biogasproduction and mass loss under anaerobic digestion

havebeen presented. It has been shown that the mechanicalproperties sustain after 28 days of

biodegradation. Suchmaterials can be found in applications as packaging, aswell as in medicine as

polymeric scaffolds, and drugdelivery systems etc.[vii]

Figure8: Total biogas production from anaerobic digestion tests ofPHB/PHV and PHB/PHV F1 composite. There have been lack of changes in the value for other materials observed

Figure9: Picture of PE, PE+F1, PHB/PHV, PHB/PHV+F1, PLA and PLA+F1 samples after immersion for 28 and 42 days (respectively)

Polyvinyl alcohol–sulphanilic acid water solublecomposite as corrosion inhibitor for mild steelin hydrochloric acid medium

The inhibitive action of synthesized polyvinyl alcohol–sulphanilic acid (PVASA) compositeon the

corrosion of commercial mild steel in 1 M HCl medium has been investigated byweight loss,

potentiodynamic polarization, and electrochemical impedance spectroscopic (EIS)methods.

Characterization of PVASA composite has been carried out using Fourier transforminfrared

spectroscopy (FTIR).

Experimental results reveal that PVASA composite acts as an inhibitorin the acid environment. The

inhibition efficiency increases with an increase in the concentrationof the inhibitor. Maximum

inhibition efficiency of PVASA composite was found to be 84% at6000 ppm. Thermodynamic and

kinetic parameters have been obtained from temperature studies.Electrochemical measurement

reveals that PVASA composite acts as a mixed inhibitor and the

adsorption follows Langmuir adsorption isotherm.[viii]

Figure10: Variation of inhibition efficiency with temperature at various inhibitor concentrations.

Figure11:Potentiodynamic polarization curves for mild steel in 1 M HCl in absence and presence of different concentration of PVASA composite.

Cross-linked gel polymer electrolyte containing multi-wall carbon nanotubes forapplication in dye-sensitized solar cells

A cross-linked gel polymer electrolyte composed of poly (ethylene oxide-co-2-(2-methoxyethoxy)

ethylglycidylether-co-allylglycidyl ether, _-butyrolactone, LiI and I2, mixed with functionalized

multi-wallcarbon nanotubes (MWCNT), was applied in dye-sensitized solar cells (DSSC).

The electrolyte was characterizedby differential scanning calorimetry, conductivity measurements

and Raman spectroscopy. Dueto its nature, the terpolymer was chemically cross-linked during

DSSC assembly to give rise to quasi-solidstate solar cells. The gel polymer electrolyte containing 1

wt% of MWCNT exhibited conductivity valueshigher than 10−3 Scm−1. An increase in MWCNT

content provided a smaller concentration of polyiodidespecies, as confirmed by Raman

spectroscopy. The highest photocurrent (8.74mAcm−2) was achievedby DSSC based on the cross-

linked gel polymer electrolyte containing 1 wt% of MWCNT compared toDSSC based on non-

cross-linked gel polymer electrolytes (7.93mAcm−2). The incorporation of 3 wt%of MWCNT into

the gel polymer electrolyte promoted a decrease in both Jsc and Voc, probably due topoorer light

transmittance of the electrolyte in the visible range and higher charge recombination

losses,respectively. Thus, the highest efficiency in this work was achieved by using electrolyte

containing 1 wt%of MWCNT. After the cross-linking process, the dimensional stability of the gel

composite electrolyte wasimproved and the conversion efficiency of DSSC was only slightly

affected, changing from 3.37% (beforecross-linking) to 3.35%.[ix]

Figure12: (a) Scanning electron microscopy (FESEM) and (b) high-resolution transmission electron microscopy (HRTEM) images of MWCNT after oxidation and (c) Raman spectra of MWCNT before and after functionalization (laser excitation set at 632.8 nm).

Figure13: DSC curves of composite gel polymer electrolyte prepared with different MWCNT concentrations: (a) before and (b) after cross-linking.

DevelopmentofNaturalRubber-Fibro NanoClayAttapulgiteComposites: The Effect of ChemicalTreatment of Filler on Mechanical and DynamicMechanical Properties of Composites Common nanoclay fillers have layered structure. Some nanoclays like Attapulgite (AT), Sepiolite

have rodlikefibrous structure. Compared to layered structured clay fibrous clay AT can undergo

better dispersion in polymermatrix leading to better improvement in composite properties. Chemical

modifications of AT are done through aminetreatment as well as by amine+silane treatment to get

chemically modified fillers AAT and SAT respectively. In thepresent investigation, nano

composites are prepared using natural rubber (NR) filled with AT, AAT and SAT.

Threedifferent loadings of each filler are used namely 2.5, 5, and 10 phr (parts per hundred of

rubber). Mechanicalproperties like tensile strength, elongation at break increase with the increase in

filler loading up to 5 phr there afterthese properties marginally fall when loading is increased to 10

phr due to problem of filler dispersion at higherloading. However, modulus at 300% elongation and

tear strength increases with the increase in filler loading up to 10phr. Very similar trend can also be

observed for composites with chemically modified fillers, AAT and SAT. But thedegree of

reinforcement is higher in the case of AAT and SAT compared to that of unmodified filler AT for

the samefiller loading. This difference is mainly due to better polymer-filler interaction and filler

dispersion in the case ofchemically modified clays AAT and SAT compared to unmodified AT.

Tear strength of composites increasesremarkably with the addition of AT and which is further

enhanced when chemically modified clays AAT and SATare added. Dynamic-mechanical analyses

of different clay composites give idea about the difference in the degree ofpolymer–filler interaction

due to chemical treatment of filler.[x]

Figure14: FTIR of different clays

Bioactivity of a Bio-composite Fabricated from CoCrMo/Bioactive Glass by Powder Metallurgy Method for Biomedical Application In present times, researchers are attracted towards studies on biocomposite as a potential

biodegradable bone implant materials.Bioactivity of the composite in a simulated body fluid (SBF)

was investigated. A porous Co-Cr-Mo based composite materialwith bio-glass 45S5 was produce

by using powder metallurgy method (PM) technology. Prepared composite powders were

coldpressed and sintered at 1000°C for 2 h.

X-ray diffraction (XRD), scanning electron microscopy were used for phase analysis andalso for

evaluation of particle distribution of composites. Bioactivity behavior of the prepared

nanocomposites was evaluated insimulated body fluid (SBF) for 1 up to 18 days. The results

showed that the apatite layer were formed on the surface of samplewith addition of bioactive glass.

It was concluded that bioinert Co-Cr-Mo alloy could be successfully converted into

bioactivecomposite by adding 6 wt% of BG particles.[xi]

Figure15: SEM micrographs for samples (a) with no BG and (b) with 6 wt. % BG

The effect of nanosilica on the mechanical properties of polymer-cementcomposites (PCC) In the last decade nanomaterials due to their unique physical and chemical properties, have attracted

the interest of researchersto fabricate new building materials with novel functions. One of the most

referred to and used cementitiousnanosizedmaterialsisnanosilica (nSiO2). Although the number of

publications devoted to the influence of nanosilica on the properties ofcementitious composites has

increased over the course of the last decade, the field of polymer-cement composites (PCC)

hasremained under-studied.

Therefore, this paper will deal with the potential application and the influence of nanosilica (nSiO2)

onthe mechanical properties of PCC.In this study the influence of diameter (100 nm and 250 nm)

and quantity (1%, 3%, 5% by weight of cement) of nSiO2 on theconsistency and mechanical

properties of polymer-cement mortars (PCC) have been examined.

Moreover, the hydration ofcement compounds was followed by X-ray diffraction (XRD).Studies

have shown that the addition of nanosilica has great potential to accelerate the pozzolanic reaction,

thus reacting morewith the CH and increasing conversion of C-S-H, and having the potential to

improve mechanical properties of PCC. Theobstacle overcome is the high water demand of

nanosilica particles, leading to significant deterioration of consistency. Finerparticles of nSiO2

seem to be more effective and cause fewer problems with the consistency of fresh mortars.[xii]

Figure16: XRD pattern of target mortars: (a) CH peaks, and (b) C-S-H peaks.

Synthesis and ion conduction mechanism onhot-pressed sodium ion conducting nano-composite polymerelectrolytes

Synthesis and ion conduction studies on SiO2 dispersed hot-pressed sodium ion conductingnano-

composite polymer electrolytes (100 _ x)[70PEO:30NaHCO3] + xSiO2, where x is inwt.%, are

reported. The nano-composite polymer electrolytes (NCPEs) are cast by the dispersionofnano-filler

SiO2 using a hot-press method in place of the traditional solution-cast technique.The effect of nano-

filler SiO2 is characterized with the help of some basic ion transport parametersviz. ionic

conductivity, ionic mobility, mobile ion concentration and activation energy measurements.

The material characterization and polymer–salt/SiO2 complexation are reported with thehelp of

XRD, FTIR, SEM, DSC and TGA studies. Based on SPE host and NCPE OCC, a solidstate

polymeric battery fabrication and cell-potential discharge characteristics are also reportedat

different load conditions.[xiii]

Figure17: Schematic presentation of two kinds of cross-linking in NCPEs: (a) polymer segments via cation-cation interaction and (b) polymer segments via cation–anion interaction.

Figure18: XRD patterns: (a) NaHCO3, (b) pure PEO, (c) SPEhost: (70PEO:30NaHCO3), (d) purenano-sized SiO2 and (e) NCPE OCC: [95 (70PEO:30NaHCO3)+5SiO2].

Flammability, Biodegradability and Mechanical Propertiesof Bio-Composites Waste Polypropylene/KenafFiberContainingNano CaCO3 with Diammonium Phosphate

Bio-composites base on waste polypropylene (rPP) and kenaffibre (KF) using coupling agent

acrylic acid (AA), andcrosslinkerdivinylbenzene (DVB) containingnano CaCO3 (nCC) with and

without DAP as a mixture fire retardant(FR) was successfully processed in melt. Flammability of

bio-composite was horizontally burning tested, accordingto ASTM D635. To study the nature of its

biodegradability, the bio-composites were technically buried in garbagedump land. The tensile

strength properties of bio-composites were measured according to ASTM D638 type V. Effectof

20% total weight flame-retardant [nCC+DAP] ratio 7:13 can effectively reduce the burning rate

(BR) up to 54%compared to bio-composites without any fire retardant.

Biodegradability of bio-composite rPP/DVB/AA/KF/[nCC+DAP] was examined by burying the

bio-composite specimens in the garbage soil during four months. Thebiodegradability of bio-

composite was measured by the losing weight (LW) of bio-composite specimensafterburying in the

soil for four months, it was found up to 11.82%. However, the present of [nCC+DAP] in the

biocompositescan marginally decreasing the tensile strength (TS), compared to that of without

FR.[xiv]

Figure19: Results of flammability test of bio-composites: (a) time to ignition, (b) burning rate, and

(c) heat release

Figure20: Results of biodegradability test of bio-composites: (a) water absorption and (b) lost of weight

Figure21: Results of Mechanical Properties of Bio-composites: (a) MFI, (b) TS, and (c) Impact

Characterization of Carbon Fiber Reinforced Epoxy CompositesModified with Nanoclay and Carbon Nanotubes Fiber reinforced polymer composites show significantly superior performance over many traditional

metallic materials becauseof their superior strength to weight ratio and higher stiffness.

Enhancement of properties of FRP composites can be possible bythe modification of matrix

properties. Significant development in the use of nanoparticles for modification of epoxy matrix

hasled to improved mechanical properties of the FRP composites.

In this study, carbon fiber reinforced epoxy composites weremodified with 2

wt.%Montmorillonitenanoclay and 0.3 wt.% multi-walled carbon nanotubes (MWCNTs). 3 point

bending test,Dynamic Mechanical Analysis (DMA) and low velocity impact test (LVI) were

conducted for characterizing modified samples.

Results obtained from these experiments were compared with unmodified carbon/epoxy

composites. Reinforcement withnanoparticles was found to significantly improve the mechanical

and thermo-mechanical properties of carbon fiber reinforcedpolymer (CFRP) composites.[xv]

Figure22: Dispersion of nanoparticles and fabrication of laminates

Figure23: Thermoscopic images of control and modified carbon/epoxy composites.

Thermal behavior of BST//PVDF ceramic–polymer composites

In this paper, we report the results of a studyof microstructure and thermal behavior of ceramic–

polymercomposites composed of barium strontium titanateBa0.6Sr0.4TiO3 (BST60/40) and

polyvinylidenefluoride(PVDF). The Ba0.6Sr0.4TiO3 ceramic powder was preparedby the sol–gel

method.

Thermal evolution of the dried gelas well as ceramic powder was studied by simultaneousthermal

analysis. The composite BST60/40//PVDF wasobtained by hot pressing method for volume fraction

ofBST60/40 ceramic powder cv= 50 %. The morphology ofBST60/40//PVDF composite powder

was observed bytransmission electron microscopy and the morphology ofBST60/40//PVDF

composite sample was observed byscanning electron microscopy. Temperature dependence

ofdielectric constant and dielectric loss factor of BST60/40//PVDF composites was measured in the

frequency range off = (10 9 103–1 9 106) Hz. Dynamic mechanical propertiesof BST60/40//PVDF

composites were measured bydynamic mechanical thermal analysis DMTA.[xvi]

Figure24: The steps of preparing of BST60/40 ceramic powder: a sol, b gel, c gelating, d dry gel, e before calcinations, fafter calcinations

Figure25: The basic steps for fabrication of BST60/40//PVDF composite by hot pressing

technique

Hybrid composites prepared from Industrialwaste: Mechanical and swelling behavior

In this assessment, hybrid composites were prepared from the combination of industrial waste,as

marble waste powder (MWP) with conventional fillers, carbon black (CB) as well as silica

asreinforcing material, incorporated with natural rubber (NR). The properties studied were

curing,mechanical and swelling behavior.

Assimilation of CB as well as silica into MWP containingNR compound responded in decreasing

the scorch time and cure time besides increasing inthe torque. Additionally, increasing the CB and

silica in their respective NR hybrid compositeincreases the tensile, tear, modulus, hardness, and

cross-link density, but decreases the elongationand swelling coefficient. The degradation property

e.g., thermal aging of the hybrid compositewas also estimated. The overall behavior at 70 _C aging

temperature signified that thereplacement of MS by CB and silica improved the aging

performance.[xvii]

Development of a Safe Solid-StatMicroorganism/BiodegradablePolymer Composite for Decomposition of Formaldehyde

A very safe and environmentally friendly solidstatematerial for bioremediation was prepared using

acombination of Aspergillusoryzaeandpoly(e-caprolactone)(PCL), a porous biodegradable polymer.

The novelmaterial was capable of decomposing 200 ppm formaldehydesolutions to 0 ppm within 7

days.

Degradation abilitywas prolonged by addition of yeast extract-peptone-dextrosemedium into the

composite; 200 ppm formaldehydewas decomposed to 0 ppm over eight additional

decompositioncycles and 100 days. A unique mechanism isproposed where, during PCL

degradation, the solid-statecomposite provides nutrients to A. oryzae.[xviii]

Figure26: Sustainability of A. oryzae/nutrient/PCL composite (filled circle) or A. oryzae (filled triangle) formaldehyde degradation Fracture mechanisms in epoxy composites reinforced withcarbonnanotubes Recent advances in nanotechnology and nanostructured materials offer the possibility to improve

the mechanical properties ofcomposite structures in terms of toughness and stiffness. In particular,

in aerospace applications research efforts are focused onthe design of advanced composite materials

reinforced with carbon nanotubes (CNTs) that combine weight saving withmultifunctional

properties, including thermal, mechanical and electromagnetic ones. It is well known that carbon

nanoparticlesenhance the fracture strength, the modulus, and the yield strength of a polymer matrix

through different mechanisms. However,despite the large amount of investigations on CNT-based

composites and their relevant properties, there is a lack ofunderstanding of the mechanisms leading

to the failure of these materials under impact or static loads, which limits their use

inpracticalapplications.

In this work, we present an experimental investigation of the fracture mechanisms of aerospace

gradeepoxy composites reinforced with multi-walled CNTs bridging the mechanical

characterization with non-destructive methods,such as optical spectroscopy and electron

microscopy.

Our results show that it is possible to link the failure mechanisms of thenanostructured composite at

the interface between the CNT and the epoxy matrix, namely cracking, pull-out and

telescopicfailure, with the molecular fingerprint of the carbon structure at the fracture surface after

mechanical testing.[xix]

Figure27: HR-SEM images of the fracture surface of nanocomposite with 1 wt% loading of MWCNTs. Samples were coated with sputtered gold toimprovethe contrast, therefore the nanotube dimension appears bigger than the original size. Enhanced mechanical properties of polyvinylalcoholcomposite films containing copper oxide nanoparticlesas filler This study has been conducted to investigate the effect of incorporatingCuO nanoparticles inside

PVA matrix with the aim of enhancing the mechanicalproperties of PVA for reinforcement

purposes. Films were prepared by solutionintercalation technique with 0.5, 1.0, 1.5 and 2.0 wt%

CuOnanofiller content takingneat PVA as the reference for the study.

Structural characterisations of the preparednanocomposite films were carried out by FTIR, SEM

and XRD techniques. Variousmechanical parameters such as tensile strength, elastic modulus,

flexuralstrengthand toughness were investigated and significant enhancement in the properties

ofpolyvinyl alcohol films containing CuOnanofillers was observed. Elastic modulusand toughness

showed a linear relation with respect to nanofiller concentration atlowwt%, whereas at higher wt%

of CuO, the nature was observed to be non-linear.PVA-2.0 wt% CuOnanocomposite showed the

highest values of flexural strength,toughness and tensile strength among all the fabricated

nanocomposite films.[xx]

Figure28: SEM images of a neat PVA, b PVA-0.5 wt% CuO, c PVA-1.0 wt% CuO, d PVA- 1.5 wt% CuOand e PVA-2.0 wt% CuO Effect of PET functionalization in composites ofrubber–PET–HDPE type The functionalization of polyethylene terephthalate (PET) from tire rubber–PET–highdensity

polyethylene (HDPE) composites represents a key strategy for improving the compositeproperties.

This is a practical and effective method to improve the interface between matrix (wastetire rubber)

and fillers (waste PET and HDPE). By PET functionalization, adherence and surfaceproperties of

composite materials can be controlled. PET functionalization was performed withpolyethylene

glycol (PEG 400, 1%) and sodium dodecylsulphate (SDS 1%). The characterizationof the

components and composite are discussed in terms of surface energy values (evaluated fromwater

contact angle measurements) and surface morphology by using scanning electron

microscopy(SEM).

The structural and conformational changes were investigated by Fourier Transform Infrared(FTIR)

Spectroscopy while the crystalline structure was studied by X-ray diffraction (XRD).The improved

interfacial adhesion, thermal stability and mechanical properties (stress–strain, compressionand

impact resistance) of the composites are correlated with the PET functionalization,with non-ionic

(PEG) and an anionic surfactant (SDS).

The results proved that the interface propertiesare improved by functionalization of PET. The best

mechanical properties were recorded at30 min moulding. The samples with 45% PET–SDS showed

the best combination of mechanicalproperties: tensile strength (1.56 N/mm2), impact strength

(43.72 kJ/m2) and compression(158.78 N/mm2).[xxi]

Figure29: Formation of SDS micelles on PET chain.

Figure30 :SEM images of the fracture surface after tensile failure (1a-CS). Effect of types of wood on the thermal conductivities of wood sawdust particle reinforced composites Wood dust reinforcing polymer matrix composites has been one of the epoch-making and

pioneering study both from scientificand economical eye over the last decades, due to the eco-

friendliness and aesthetical properties. Wood dust is suitable andbeguiling filler for thermoset

polymers due to its cost effectiveness, low density and high specific properties. It is

biodegradableand nonabrasive during processing.

The research was proceeded with the objective of evaluating the effect of different types ofwood

saw dust on the properties of composite materials. In this experiment, thermal behaviours of

composites reinforced withwood dust particles of various woods (three types of woods) were

investigated. Size was a viable parameter to control theproperties of developed composites. As a

result two different particle sizes as medium and coarse sized wood particles were usedto develop

the composites and characterize their thermal conductivities.

The results of the experiment thus observed were quiteinteresting. Pure polyester has been found to

have lower thermal conductivity compared to that of any wood reinforced polyesterand that wood

strength or true density has been found to influence the thermal conductivity of the as-received

polymer. Withincrease in the dust particle content, thermal conductivities of all composites have

been found to increase.[xxii]

Figure31: Rectangular blocks made from three different woods (a) Kerosene, (b) Gamari and (c) Garjan.

Figure32: Photographs showing the (a) casting mould , (b) as cast sample and (c) final ASTM standard tensile test sample after machining . Looking for Oil-free Building Materials Clay Pipes to ReplacePolymer Pipes After centuries of environmental pollution, many studies have illustrated the impact of oil and its

products over the surroundingenvironment. Therefore, as a step toward sustainable neighbourhoods,

it may an idea to search for alternative oil-free buildingmaterials. On the other hand, plastic is

considered the main building material that derived from oil and used in a wide-range as(water

system pipes, insulation material, plastic fibre for reinforcement concrete, etc.).However, it is

enough for these materials to be derived from oil to be polluting materials, but they are also strange

materials tonature that they take thousands of years to decompose. Moreover, some materials like

polystyrene it is not even accepted yet tobe recycled because of the economic point of view.

All above has urged us to search for alternative eco-friendly materials, thus the natural materials

that come from the earth likeclay may be that one. So these papers are going to present the

possibility of replacing plastic pipes with clay ones by test andanalyze some specimens following

the standards.[xxiii]

Figure33: (a) the nature of clay; (b) crushed sieved clay “powdery clay; (c) type of sand used

Figure34: The Final pipes Reinforcement of bacterial cellulose aerogels with biocompatiblepolymers Bacterial cellulose (BC) aerogels, which are fragile, ultra-lightweight, open-porous and

transversallyisotropic materials, have been reinforced with the biocompatible polymers polylactic

acid (PLA), poly-caprolactone (PCL), cellulose acetate (CA), and poly(methyl methacrylate)

(PMMA), respectively, atvarying BC/polymer ratios. Supercritical carbon dioxide anti-solvent

precipitation and simultaneousextraction of the anti-solvent using scCO2have been used as core

techniques for incorporating thesecondary polymer into the BC matrix and to convert the formed

composite organogels into aerogels.

Uniaxial compression tests revealed a considerable enhancement of the mechanical properties as

com-pared to BC aerogels. Nitrogen sorption experiments at 77 K and scanning electron

micrographs confirmedthe preservation (or even enhancement) of the surface-area-to-volume ratio

for most of the samples.The formation of an open-porous, interpenetrating network of the second

polymer has been demon-strated by treatment of BC/PMMA hybrid aerogels with EMIM acetate,

which exclusively extractedcellulose, leaving behind self-supporting organogels.[xxiv]

Figure35: BC/PMMA80 organogel during extraction of BC with an ionic liquid, containing regions of varying amounts of residual BC (opaque). SEM pictures: morphology of aBC/PMMA80 aerogel (A) and of an aerogel as obtained from (A) after extraction of BC by EMIM acetate. Electrodeposition, characterization, and antibacterial activity ofzinc/silver particle composite coatings

Composite coatings consisting of zinc and silver particles (Zn/AgPs) with antibacterial activity were

pre-pared using an electrodeposition technique. The morphology, composition, and structure of the

Zn/AgPscomposite coatings were analyzed using scanning electron microscopy (SEM) coupled

with energy-dispersive spectroscopy (EDS), inductively coupled plasma (ICP) spectrometry, and X-

ray diffraction(XRD).

The antibacterial properties of the coatings against the microorganisms Escherichia coli as a

modelGram-negative bacterium and Staphylococcus aureus as a model Gram-positive bacterium

were studiedquantitatively and qualitatively. The results revealed that the dispersant

cetyltrimethylammonium bro-mide (CTAB) assisted in the formation of a stable suspension of Ag

particles in the electrolytic bath for24 h. Likewise, a high concentration of CTAB in the electrolytic

bath promoted an increase in the numberof Ag particles occluded in the Zn/AgPs coatings.

The Zn/AgPs coatings that were obtained were compact,smooth, and shiny materials. Antimicrobial

tests performed on the Zn/AgPs coatings revealed that theinhibition of bacterial growth after 30

minof contact time was between 91% and 98% when the AgPscontent ranged from 4.3 to 14.0 mg

cm−3. [xxv]

Figure36:Schematic model of the absorption of CTAB on charged electrode surfaces.

Figure37: Tests of the antibacterial activity of Zn/AgP coatings with 4.3 mg cm−3AgPs against pathogens: (a) E. coli and (b) S. aureus.

Effect of silicon carbide and pulping processes on physical andmechanical properties of pulp plastic composites (PPCs) This study evaluated the effect of different pulping processes and SiC particles on physical and

mechanicalproperties of pulp plastic composites (PPCs). Polypropylene (PP), SODA and NSSC

pulp fibers (max. 40 and50 wt.%), silicon carbide particles (0, 5, 10, 15 wt.%), and 5 wt.% maleic

anhydride polypropylene (MAPP)as coupling agent were used to produce pulp plastic composites

(PPCs) by injection molding. The physical and mechanical properties of samples were characterized

according to ASTM standards. SODA pulpcomposites illustrated higher values in all properties

except contact angle and showed approximatelysame abrasion resistance compared to NSSC pulp

composites.

The addition of SiC particles improved thenegative effect of pulp fibers in water absorption, and

increased both contact angle and abrasion resistance of PPCs. By contrast, tensile, flexural, and

impact properties of pulp plastic composites decreased byincreasingSiC particles. In general, 50

wt.% SODA/SiC composite containing 10 wt.% SiC particles showedthe highest efficiency among

composites .[xxvi]

Figure38: (a) Flexural strength and (b) flexural modulus as function of SODA and NSSC pulps and SiC content. The Effect of Pressure on Moisture Diffusion in Polymer Matrix Composites Temperature and humidity play a significant role in themechanicalbehaviorand long-term durability

of polymer matrix composites (PMCs). Several standardtest methods including some accelerated

test methods involving higher temperaturesand pressures are available for environmental

qualification of these PMCs. While theeffect of temperature on humidity diffusion has been studied

extensively, the effectof pressure has received less attention.

This study seeks to interrogate the effect ofpressure on diffusion. This effect was observed by

building test chambers designedto maintain a constant relative humidity of 80 % at 60 ◦C at three

different pressures(0.1014 MPa, 0.5171 MPa, and 1.0342 MPa). A liquid water immersion test

chamber at 60 ◦C was also considered. It was observed that the time to saturation and thesaturation

moisture content increased with increasing chamber pressure. Immersionin liquid water provided

the upper bound for the maximum moisture saturation and alower bound for the time to

saturation.[xxvii]

Figure39: Schematic of the accelerated experimental test setup Effect of epoxy modifiers (Al2O3/SiO2/TiO2 ) on mechanicalperformance of epox/glass fiber hybrid composites

Fiber reinforced polymer composite is an important material for structural application. The

diversified application of FRPcomposite has taken centre of attraction for interdisciplinary research.

However, improvements on mechanical properties of thisclass of materials are still under research

for different applications.

In this paper we have modified the epoxy matrix by Al2O3,SiO2 and TiO2 micro particles in glass

fiber/epoxy composite to improve the mechanical properties. The composites arefabricated by hand

lay-up method. It is observed that mechanical properties like flexural strength, flexural modulus and

ILSS aremore in case of SiO2 modified epoxy composite compare to other micro modifiers. This

may be because of smaller particle sizeof silica compare to others. Alumina modified epoxy

composite increases the hardness and impact energy compare to othermodifiers.

Agglomeration of Al2O3 micro particles in the matrix is observed in SEM. This may be because of

bigger particle sizeof Alumina. SEM analysis clearly indicates the mode of failure is the

combination of crack in matrix, matrix/fiber debondingandfiber pull out for all types of

composites.[xxviii]

Figure40: SEM micrograph for TiO2 particle modified epoxy composite Composite gels based on Poly (vinyl alcohol) for biomedicaluses Nowadays, poly (vinyl alcohol) (PVA) hydrogels are being studied for several biomedical

applications such as jointreplacement, wound dressings and controlled drug-releasing devices,

among others. Reinforced PVA hydrogels showgood mechanical properties and are a suitable

option to replace cartilages. Furthermore, these materials can prevent loss ofbody fluids, be a barrier

against bacteria and also permeable to oxygen, for these all interesting properties, they are usedlike

wound dressings. For drug delivery systems a material that can control the dose and release at the

site of action isdesirable, this can be accomplished using hydrogels, which are loaded with a drug,

and then they can release it when anexternal stimulus (light, temperature, magnetic field, etc.) takes

place.

The aim of this work was to obtain compositehydrogels for the previously mentioned biomedical

applications. Hydroxyapatite (HA) reinforced PVA gels were preparedfor potential uses as cartilage

replacement, HA improves the mechanical, tribological and fixing properties of the

polymer,reaching values similar to that of the cartilages.

For wound dressings, the hydrogel was reinforced with bentonite (clay) inorder to increase the

dimensional stability and antimicrobial properties. Gels with controlled drug release capability

undermagnetic stimulation (ferrogels) were also synthesized and characterized here.[xxix]

Figure41: a, b and c show the micrographs for the composites where it can be observed the HA particles,bentonite and magnetite within the matrix of PVA. a) b) Enhancing Fracture Toughness of Glass/Epoxy Compositesfor Wind Blades Using Silica Nanoparticles and RubberParticles The research aims to investigate the interlaminar fracture toughness of glass fiber/epoxy

composites, which consistofthe silica nanoparticles and the rubber particles. Two kinds of rubber

particles, one is the reactive liquid rubber(CTBN) and the other is the core-shell rubber (CSR), were

employed to modify the fracture toughness of epoxy resin.

In general, the disadvantage of adding rubber particles into polymeric resin is the dramatic

reduction of stiffnessalthough the toughness could be modified accordingly. In order to enhance the

fracture toughness of the fibercomposites without sacrificing their stiffness, the silica nanoparticles

in conjunction with the rubber particles wereintroduced concurrently into the epoxy matrix to form

a hybrid nanocomposite.

Experimental results obtained fromtensile tests on bulk epoxy confirm the presumption that the

reduction of the epoxy stiffness because of the presenceof rubber particles can be effectively

compensated by the silica nanoparticles. Furthermore, the fracture testsconducted on the DCB

specimens revealed that the inclusion of silica nanoparticles together with the CSR particlecan

appreciably increase the fracture toughness of the glass/epoxy composites up to 82%. On the other

hand, whenthe epoxy matrices were modified with CTBN rubber particles and silica nanoparticles,

the improvement of theinterlaminar fracture toughness was around 48%.[xxx]

Polymer composites containing non-covalently functionalizedCarbon nanotubes: a study of their dispersion characteristicsand response to AC electric fields Multi-wall carbon nanotubes (MWCNT) functionalized with a hyperbranched polyethylene (HBPE)

and subsequentlymelt compounded with an ethylene-octene copolymer (EOC8100) matrix are

examined in terms of their dispersioncharacteristics and electric field response.

It was found that, when compared with their non-functionalizedcounterparts, HBPE-functionalized

MWCNT produce substantially more uniform composites. On the other hand,MWCNT

functionalization results in a higher electrical percolation threshold. Electrification of the composite

meltsshowed that longer insulator-to-conductor transition times should be expected as a

consequence of the improveddispersion quality. The functionalization, however, did not prevent

MWCNT from forming highly electricallyconducting networks in the melt, or exhibiting electric

field-induced percolation thresholds of less than 1wt% filler.[xxxi]

Figure42: Schematics of the: (a) Electrode cell; (b) Test circuit used for electrification of the composites

Figure43: Effect of MWCNT surface functionalization on its distribution inside a polymer matrix under an electric field. Mechanical Behaviour of Polypropylene Reinforced PalmFibers Composites Nowadays, a great attention has been dedicated to natural fibers as reinforcement for polymers.

Natural fibers,compared to glass fibers, exhibit better mechanical properties, such as stiffness,

impact strength, flexibility andmodulus. However certain drawbacks, such as the incompatibility

between fibers and polymer matrices, the tendencyto form aggregates during processing and the

poor resistance to moisture, reduce the use of these natural fibers asreinforcements in polymers.

Several treatments and modifications are being used to improve fibers/matrixcompatibility, such as

bleaching, acetylation and use coupling agent.

In this work, the effect of coupling agent in thepalm fibers/ PP composites was evaluated on

mechanical behavior .Palm fibers were mixed with the polymericmatrix (PP) in a thermokinetic

mixer, with speed rate maintained at 5250 rpm, in which fibers were responsible for 5wt% in the

composition. When the coupling agent was used, the proportion of PP was 95 wt% and the coupling

agentwas 5 phr. After the mixture, composites were dried, ground in mill and placed in an injector

camera according toASTM D-790 specification.

Results showed that, the addition of coupling agent in the composites improvedsignificantly the

flexible strength and modulus when compared to the pure polymer.[xxxii]

Figure44: SEM of palm fibers cross section (A) and (B) and longitudinal (C) and (D).

Glass Fiber Reinforced Polymer-Clay Nanocomposites:Processing, Structure and Hygrothermal Effects onMechanical Properties Polymer composites have been the mainstay of high-performance structural materials, but these

materials areinherently sensitive to environmental factors such as temperature, exposure to liquids,

gases, electrical fieldsandradiation, which significantly affects their useful life. Addition of layered

silicate nanofillers in the polymer matrixhas led to improvements in the elastic moduli, strength,

heat resistance, decreased gas permeability and flammability. In the present work epoxy modified

with Cloisite 30 B®nanoclay (at 1, 3 and 5 wt% of resin) and E-glassunidirectional fibers are used

to prepare fiber reinforced nanocomposites using hand lay-up method.

Thenanocomposites have been characterized by X-ray diffraction (XRD) and scanning electron

microscopy (SEM).XRD results show that the interlayer spacing between the clay platelets

increased significantly indicating that thepolymer is able to intercalate between the clay layers. The

mechanical properties are measured by carrying outtensile, hardness and flexural tests and values

are compared with those found for fiber reinforced neat epoxycomposites.

The tests show that an addition of nano-clay up to 3 wt% increases tensile strength and micro-

hardnessand there is a decrease in values with further clay addition up to 5 wt%. The flexural

strength increased significantlywith clay loading and the highest value is observed for specimens

with 5 wt% of clay. Further, durability studies onnanocomposites have been performed in water and

NaOH baths under accelerated hygrothermal conditions. Duringthe exposure it is observed that the

degradation in NaOH environment is more severe than in water.[xxxiii]

Figure45: (a) Flexural Strength degradation; and (b) percent decrease in strength in water bath .itshows the effect of immersion of specimen in water on flexural strength of specimen. It can beseen from Figures a and b that 3 wt% nanoclay specimen outperformed in terms that the degradation in flexural strength in water bath was less in comparison to other specimens.

Figure46:(a) Flexural Strength degradation; and (b) percent decrease in strength in NaOHbath, as can be seen from Figures a and b, the strength degradation wasapproximately same for 3 wt% and 5 wt% specimens. The neat epoxy – fiber composite suffered a steep drop in strength in both water and NaOH bath. Mechanical properties of HDPE/textile fibers composites

The use of natural fibers as reinforcement for thermoplastics has generated much interest due to the

low cost, lowdensity, high specific properties characteristics. In this work the mechanical properties

of high density polyethylene/textile fibers residues composites were studied. Effect of pretreatment

with sulfuric acid on textile fibers to preparecomposites was made to provide an improvement in

mechanical properties of these materials.

This treatment onfibers was evaluated by X-ray diffraction technique. Composites were produced in

a thermokinetic mixer in thefollowing composition: 5 and 10 wt% fibers. After mixing the samples

were injection molding according to ASTMD-638 specification.

Specimens were tested in tensile mode and composite fractures surface were analyzed in

ascanningelectron microscopy. Also was studied moisture absorption. Results showed that HDPE/

textile fibersresidue presents good mechanical performance compared with high-density

polyethylene.[xxxiv]

Figure47: SEM of fractures composites: (a) HDPE/ FT 5%; (b) HDPE/ FT 10%.

Mechanical and flame-retardant properties of epoxy/Mg–Al LDH composites Layered double hydroxides (LDH) are a class of chemical compounds that can be used to modify or

incorporatecharacteristics into a variety of thermoplastics or thermosets polymer matrices. The

focus of thepresent work is to synthesize organomodified-LDH MgAl intercalated with glycinate, to

use them to formulateepoxy composites with distinct LDH content, and to evaluate their

mechanical, thermal andflame-retardant (horizontal and vertical burning) properties. The solvents

used to aid LDH dispersion intothe resin were acetone, chloroform and dimethylformamide.

All samples containing 1%, 3% and 5% (w/w)of LDH showed self-extinguishing behavior in the

vertical test and all samples containing LDH showedbetter performance in terms of burning rate

than pristine epoxy. The mechanical properties of the compositesvaried based on the solvent used

and the lowest concentration of LDH (1%) yielded the best performance,as expected for this kind of

filler .[xxxv]

Poly (vinyl alcohol – aniline) water soluble compositeas corrosion inhibitor for mild steel in 1 M HCl

Poly (vinyl alcohol – aniline) PVAA composite was tested for its performance in protectingmild

steel MS against corrosion in 1 MHCl. The inhibitive parameters were evaluated by meansof weight

loss, electrochemical polarization and impedance methods.

Results indicated that theaddition of PVAA to the acid reduces the corrosion of the metal. Inhibition

efficiency increases withincrease in inhibitor concentration. The results further revealed that PVAA

at a concentration of2000 ppm furnishes a maximum of 92% inhibition efficiency. Thermodynamic

parameters suchas free energy of adsorption, heat of adsorption, etc., had been evaluated from

temperature studies.The adsorption of PVAA followed Langmuir and Temkin adsorption isotherms.

Polarizationcurves revealed that PVAA is a mixed inhibitor.[xxxvi]

Figure48: Langmuir’s adsorption plots of PVAA composite in1.0 M HCl.

Figure49: Temkin’s adsorption plots of PVAA composite in 1.0 M HCl.

Figure50: Potenziodynamic polarization curves of mild steel in 1.0 M HCl. Effects of bone particle on the properties and microstructure ofpolypropylene/bone ash particulate composites

The effects of uncarbonized (fresh) and carbonized bone particles on the microstructure and

properties ofpolypropylene composites have been studied. The addition of the bone particles ranges

from 5 to 25 wt%inuncarbonized and carbonized forms in the polypropylene matrix. The physical

and mechanical propertieswere used as criteria for the evaluation of the composites. Microstructures

of the composites wereassessed with scanning electron microscopy (SEM/EDS).

The results revealed that the addition of carbonizedbone particles reinforcement has superior

properties than uncarbonized bone particles compositebased materials with an increase in the

compressive strength, hardness values, tensile strength and flexuralstrength by 53%, 45% and 35%

respectively, and a decrease in the % elongation and impact energy by75% and 32%, respectively at

25 wt% carbonized bone, with 28% increase in tensile strength at 15 wt% carbonizedbone addition.

The increase in strength and hardness values was attributed to the distribution ofhard phases of bone

particles in the ductile polypropylene matrix.[xxxvii]

Figure51: Schematic diagram of the flow sheet for the development of polypropylene/bone reinforced composite.

Figure52: Micrograph of (a) carbonized bone powder (CB) (b) fresh bone powder (FB) (c) polypropylene (d) pressed PP/bonecomposite.

Figure53: Variation of flexural strength with wt% bone.

References

1 - Jamal Y. Sheikh-Ahmad - Machining of Polymer Composites (2009).

ii - Bunsell, A.R. and Harris, B. Composites, 5, 157(1974).

iii - K Deepaka, N SrinivasaReddya, T V SeshaiahNaidua -Procedia Materials Science 10, 626 -

631( 2015).

iv- S. Rajesh a*, B. VijayaRamnathb, C.Elanchezhianb, N.Aravindc, V.VijaiRahuld, S. Sathishd -

Procedia Engineering 97, 598 - 606( 2014 )

v - SitiShuhadah Md. Saleh a, b, Hazizan Md. Akil a, c* , Muhammad HelmiAbdulKudusa,

KhairelRafeziAhmadb and NurSurayaAnis Ahmad Bakhtiara - Procedia Chemistry 19, 45-49( 2016

)

6-Daisuke Nagao &Mikio Yokoyama & Shu Saeki & Yoshio Kobayashi &Mikio Konno - Colloid

PolymSci 286, 959-964(2008)

vii - Andrzej Iwan´czuk • Marek Kozłowski •Marcin Łukaszewicz • SławomirJabłon´ ski - J Polym

Environ 23,277–282(2015)

viii - M. Srimathi *, R. Rajalakshmi, S. Subhashini - Arabian Journal of Chemistry 7, 647–

656(2014)

ix - João E. Benedetti, Aline A. Corrêa, MayaraCarmello, Luiz C.P. Almeida, Agnaldo S. Gonc¸

alves, Ana F. Nogueira∗ - Journal of Power Sources 208, 263–270(2012)

x - J.P. Ratha, T.K. Chakia, D. Khastgira, - Procedia Chemistry 4, 131–137( 2012 )

xi - RohayaAbdullaha, NurMaizatulShimaAdzalib, ZuraidawaniCheDaudc - Procedia Chemistry

19, 566 – 570( 2016)

xii - PawełSikoraa,*, PawełŁukowskia, Krzysztof Cendrowskib,

ElżbietaHorszczarukb,EwaMijowskab - Procedia Engineering 108, 139– 145 ( 2015 )

xiii - Angesh Chandra a,*, Archana Chandra a,b, K. Thakur c - Arabian Journal of Chemistry

(2013)

xiv - N.S. Suhartya,, I.P. Almanarb, Sudirmanc, K. Dihardjod, N. Astasaria - Procedia Chemistry 4,

282 – 287( 2012 )

xv - MdEkramul Islam, Tanjheel H. Mahdi, Mahesh V. Hosur*, ShaikJeelani - Procedia

Engineering 105, 821 – 828( 2015 )

xvi - KatarzynaOsin´ska • DionizyCzekaj - J Therm Anal Calorim 113,69–76(2013)

xvii - Khalil Ahmed * - Journal of Advanced Research 6, 225–232(2015)

xviii - Ikuhiro Tanida • AsamiSakaue • Satoshi Osawa - J Polym Environ 22,329–335(2014)

xix- S. Laurenzia*, S. Bottib, A. Rufolonic, M. G. Santonicolad - Procedia Engineering 88, 157 –

164( 2014 )

xx- JammulaKoteshwara Rao1• Abhishek Raizada1 •Debargha Ganguly1 • Madri Manish Mankad1

•S. V. Satyanarayana2 • G. M. Madhu1 - Polym. Bull. 72,2033–2047 (2015)

xxi - Cristina Cazan *, MihaelaCosnita, Anca Duta - Arabian Journal of Chemistry (2015)

xxii - M.Faruk Hossain, ShoumyaNandyShuvo*, M.A.Islam - Procedia Engineering 90, 46 – 51(

2014 )

xxiii - Riyadh Salhaa, Florin V.Tosaa - Procedia Technology 22, 343 – 350( 2016 )

xxiv - N. Pirchera, S. Veigelb, N. Aignera,1, J.M. Nedelecc,d, T. Rosenaua, F. Liebnera,∗ -

Carbohydrate Polymers 111 , 505–513 (2014)

xxv - Y. Reyes-Vidala,1, R. Suarez-Rojasa, C. Ruiza, J. Torresa, StefanT¸˘aluc,AliaMéndezb, G.

Trejoa,∗ - Applied Surface Science 342 , 34–41(2015)

xxvi - AlirezaSukhtesaraie, S. Behnam Hosseini∗ - Journal of Asian Ceramic Societies 4 ,112–

119(2016)

xxvii - S. P. Pilli · L. V. Smith - Int J Thermophys 33,1715–1725(2012)

xxviii - Ramesh K. Nayak a*, Alina Dasha and B.C.Ray b - Procedia Materials Science 6 ,1359 –

1364( 2014 )

xxix - J.S. Gonzaleza*, A.S. Maioloa, C.E. Hoppeb and V.A. Alvareza - Procedia Materials

Science 1 , 483 – 490( 2012 )

xxx - J.L. TSAIa1, B.H. HUANG1, and Y.L. CHENG1 - Procedia Engineering 14 ,1982–

1987(2011)

xxxi - O. Osazuwaa, M. Kontopouloua, P. Xiangb, Z. Yeb, A. Docoslisa a* - Procedia Engineering

42 ,1414 – 1424( 2012 )

xxxii- Goulart, S.A.S.a; Oliveira, T.A.a; Teixeira, A.a; Miléo, P.C.b; Mulinari, D.R.a - Procedia

Engineering 10 ,2034–2039(2011)

xxxiii - B. Sharmaa, , S. Mahajana, R. Chhibbera, R. Mehtab - Procedia Chemistry 4 , 39 – 46(

2012 )

xxxiv - P. S. Souzaa*, E. F. Rodriguesa, J. M. C Pretaa, S. A. S. Goularta, D. R. Mulinaria -

Procedia Engineering 10 ,2040–2045(2011)

xxxv - Cristiane M. Becker a,⇑, Aline D. Gabbardo a, Fernando Wypych b, Sandro C. Amico a -

Composites: Part A 42 ,196–202(2011)

xxxvi - R. Karthikaiselvi a,*, S. Subhashini b, R. Rajalakshmi b - Arabian Journal of Chemistry 5,

517–522(2012)

xxxvii - F. Asuke a, V.S. Aigbodion b,⇑, M. Abdulwahaba,c, O.S.I. Fayomi c, A.P.I. Popoola c,

C.I. Nwoyi d, B. Garba a - Results in Physics 2 ,135–141 (2012)