<i>&#x3b2;</i>-phases of nickel hydroxide and cobalt hydroxide samples crystallize in cadmium iodide type structure. <i>&#x3b2;</i>-cobalt hydroxide on oxidation generates <i>&#x3b2;</i>-CoOOH which crystallized in 3R<sub>1</sub> polytype while the structure of <i>&#x3b2;</i>-phase of NiOOH polytype is less well understood. <i>&#x3b2;</i>- and <svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-3.42947pt" id="M1" height="12.7178pt" version="1.1" viewBox="-0.0498162 -9.28833 16.4389 12.7178" width="16.4389pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><path id="g113-224" d="M558 587C558 666 497 712 432 712C379 712 330 691 284 650C212 586 178 508 148 348L71 -65C49 -185 35 -229 23 -235L27 -261C49 -259 101 -251 124 -224C131 -216 138 -178 159 -24C171 66 197 200 227 356C264 550 295 668 393 668C443 668 479 632 479 575C479 516 446 458 383 418C361 404 344 398 318 397L296 350C395 338 460 281 460 192C460 110 411 40 300 40C258 40 215 55 192 69L181 51C191 18 222 -16 266 -16C308 -16 351 1 397 26C471 67 545 142 545 221C545 315 486 365 401 395C469 437 558 498 558 587Z"/></g><g transform="matrix(.0091,0,0,-0.0091,7.228,3.132)"><path id="g190-99" d="M152 404V712C115 698 54 683 7 677V654C71 648 73 642 73 579V24C128 -2 179 -12 220 -12C353 -12 471 92 471 238C471 357 381 449 274 449C262 449 249 446 233 439L152 404ZM152 374C170 384 202 393 230 393C313 393 382 326 382 213C382 97 330 26 246 26C194 26 165 62 158 81C154 91 152 101 152 116V374Z"/></g><g transform="matrix(.0091,0,0,-0.0091,11.933,3.132)"><path id="g190-100" d="M390 111C344 68 312 56 269 56C212 56 118 102 118 241C118 346 175 401 241 401C277 401 312 388 342 360C350 352 355 349 361 349C372 349 394 371 394 392C394 403 391 411 378 422C362 436 329 449 288 449H287C250 449 190 432 138 392C71 341 37 274 37 197C37 90 112 -12 238 -12C297 -12 363 32 407 90L390 111Z"/></g></svg>-phases of nickel hydroxide samples were prepared by using ammonium hydroxide and sodium hydroxide as precipitating agents. Powder X-ray diffraction data shows that <i>&#x3b2;</i>-phase of nickel hydroxide is perfectly crystalline in nature while <svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-3.42947pt" id="M2" height="12.7178pt" version="1.1" viewBox="-0.0498162 -9.28833 16.4389 12.7178" width="16.4389pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><use xlink:href="#g113-224"/></g><g transform="matrix(.0091,0,0,-0.0091,7.228,3.132)"><use xlink:href="#g190-99"/></g><g transform="matrix(.0091,0,0,-0.0091,11.933,3.132)"><use xlink:href="#g190-100"/></g></svg>-phase of nickel hydroxide is poorly ordered. <i>&#x3b2;</i>- and <svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-3.42947pt" id="M3" height="12.7178pt" version="1.1" viewBox="-0.0498162 -9.28833 16.4389 12.7178" width="16.4389pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><use xlink:href="#g113-224"/></g><g transform="matrix(.0091,0,0,-0.0091,7.228,3.132)"><use xlink:href="#g190-99"/></g><g transform="matrix(.0091,0,0,-0.0091,11.933,3.132)"><use xlink:href="#g190-100"/></g></svg>-phases of nickel hydroxide samples were subjected to chemical oxidation using sodium hypochlorite. The oxidized phases of <i>&#x3b2;</i>- and <svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-3.42947pt" id="M4" height="12.7178pt" version="1.1" viewBox="-0.0498162 -9.28833 16.4389 12.7178" width="16.4389pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><use xlink:href="#g113-224"/></g><g transform="matrix(.0091,0,0,-0.0091,7.228,3.132)"><use xlink:href="#g190-99"/></g><g transform="matrix(.0091,0,0,-0.0091,11.933,3.132)"><use xlink:href="#g190-100"/></g></svg>-phases of nickel oxyhydroxide are highly disordered and the broadening of reflections in the powder X-ray diffraction patterns is due to the presence of structural disorder, variations in the crystallite size, and strain. On reduction of <i>&#x3b2;</i>- and <svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-3.42947pt" id="M5" height="12.7178pt" version="1.1" viewBox="-0.0498162 -9.28833 16.4389 12.7178" width="16.4389pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><use xlink:href="#g113-224"/></g><g transform="matrix(.0091,0,0,-0.0091,7.228,3.132)"><use xlink:href="#g190-99"/></g><g transform="matrix(.0091,0,0,-0.0091,11.933,3.132)"><use xlink:href="#g190-100"/></g></svg>-phases of nickel oxyhydroxide, the powder X-ray diffraction patterns visually match the powder X-ray diffraction data of the pristine phases of <i>&#x3b2;</i>- and <svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-3.42947pt" id="M6" height="12.7178pt" version="1.1" viewBox="-0.0498162 -9.28833 16.4389 12.7178" width="16.4389pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><use xlink:href="#g113-224"/></g><g transform="matrix(.0091,0,0,-0.0091,7.228,3.132)"><use xlink:href="#g190-99"/></g><g transform="matrix(.0091,0,0,-0.0091,11.933,3.132)"><use xlink:href="#g190-100"/></g></svg>-phases of nickel hydroxide indicating that the <i>&#x3b2;</i>-phase of nickel hydroxide does not transform to <svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-3.42947pt" id="M7" height="12.7178pt" version="1.1" viewBox="-0.0498162 -9.28833 16.4389 12.7178" width="16.4389pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><use xlink:href="#g113-224"/></g><g transform="matrix(.0091,0,0,-0.0091,7.228,3.132)"><use xlink:href="#g190-99"/></g><g transform="matrix(.0091,0,0,-0.0091,11.933,3.132)"><use xlink:href="#g190-100"/></g></svg>-phase of nickel hydroxide, but the particle sizes are significantly affected.

Ramesh Thimmasandra Narayan

Effect of Crystallinity of <i>&#x3b2;</i>- and <i>&#x3b2;</i><sub>bc</sub>-Nickel Hydroxide Samples on Chemical Cycling

Tribological performance of Ni-P-TiO<sub>2</sub> composite coatings is improved by varying the tribological test parameters such as normal load, wear track diameter, and duration of test aiming at minimum wear and friction of the coating. Taguchi technique with grey relational analysis is employed for optimization of multiresponse problem using <svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-3.291101pt" id="M1" height="11.927pt" version="1.1" viewBox="-0.0498162 -8.6359 17.8195 11.927" width="17.8195pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><path id="g113-77" d="M541 160L512 170C485 116 462 88 439 67C411 41 376 35 318 35C272 35 238 37 224 48C207 61 205 85 212 121L290 533C305 611 308 615 391 622L397 650H139L133 622C217 615 221 612 206 533L126 118C111 41 103 34 23 26L17 0H474C489 31 528 124 541 160Z"/></g><g transform="matrix(.0091,0,0,-0.0091,8.294,3.132)"><path id="g50-51" d="M414 144C384 79 371 75 317 75H135L276 221C367 316 408 376 408 465C408 570 327 635 237 635C179 635 131 609 100 575L42 494L67 471C94 510 138 565 205 565C277 565 321 517 321 435C321 348 258 270 195 195C146 137 88 81 33 26V0H411C423 44 433 88 446 135L414 144Z"/></g><g transform="matrix(.0091,0,0,-0.0091,12.726,3.132)"><path id="g50-56" d="M453 623H65C60 580 56 530 46 472H80C103 538 110 548 175 548H389C310 380 195 168 90 0L98 -12L175 -2C273 206 366 408 462 610L453 623Z"/></g></svg> orthogonal array (OA). Analysis of variance (ANOVA) is used to find out the significant effect of test parameters and their interactions on friction and wear behavior of the coating. ANOVA results reveal that normal load and time (test duration) have the most significant effect in controlling wear and friction of the coating. Interaction between normal load and wear track diameter has some significant effect. Scanning electron microscopy of worn surface shows abrasive wear to be predominant. The surface morphology, composition, and phase structure analysis are done with the help of scanning electron microscopy (SEM), energy dispersive X-ray (EDX) analysis, and X-ray diffraction (XRD) analysis, respectively.

Prasanna Gadhari

Prasanta Sahoo

Improvement in Tribological Performance of Ni-P-TiO<sub>2</sub> Composite Coatings Using Taguchi Technique with Grey Relational Analysis

Lead bismuth titanate borosilicate glasses were prepared in the glass system 65[(<svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-3.40075pt" id="M1" height="12.6369pt" version="1.1" viewBox="-0.0498162 -9.23615 46.5602 12.6369" width="46.5602pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><path id="g121-78" d="M46 650V622C120 617 128 613 128 525V125C128 42 120 34 40 28V0H311V28C221 34 212 39 212 124V281L286 262C297 261 316 261 331 263C429 275 526 338 526 468C526 533 501 579 462 609C422 638 364 650 293 650H46ZM212 559C212 588 215 600 223 606C230 613 251 618 279 618C361 618 430 572 430 464C430 337 350 302 285 302C252 302 225 309 212 314V559Z"/></g><g transform="matrix(.013,0,0,-0.013,7.319,0)"><path id="g121-96" d="M152 404V712C115 698 54 683 7 677V654C71 648 73 642 73 579V24C128 -2 179 -12 220 -12C353 -12 471 92 471 238C471 357 381 449 274 449C262 449 249 446 233 439L152 404ZM152 374C170 384 202 393 230 393C313 393 382 326 382 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608C235 614 258 618 282 618C377 618 415 558 415 490C415 406 369 362 260 362H213ZM213 328H258C380 328 450 283 450 181C450 76 377 35 296 34C231 34 213 53 213 125V328Z"/></g><g transform="matrix(.013,0,0,-0.013,27.21,0)"><path id="g121-103" d="M135 536C164 536 186 560 186 587C186 617 164 639 136 639C109 639 85 617 85 587C85 560 109 536 135 536ZM252 0V26C188 32 181 38 181 106V451C138 433 90 420 39 412V388C99 379 102 374 102 312V106C102 38 95 32 32 26V0H252Z"/></g><g transform="matrix(.0091,0,0,-0.0091,30.736,3.132)"><path id="g58-47" d="M389 0V32C297 37 291 46 291 118V635C234 612 176 595 109 583V556L161 554C203 551 207 548 207 497V118C207 46 201 37 110 32V0H389Z"/></g><g transform="matrix(.0091,0,0,-0.0091,35.168,3.132)"><path id="g54-33" d="M556 236V289H56V236H556Z"/></g><g transform="matrix(.0091,0,0,-0.0091,40.728,3.132)"><use xlink:href="#g50-121"/></g></svg>)&#xB7;TiO<sub>3</sub>]-34[2SiO<sub>2</sub>&#xB7;B<sub>2</sub>O<sub>3</sub>]-1La<sub>2</sub>O<sub>3</sub> (<svg 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The amorphous nature of glass samples in this glass system is confirmed by using X-ray diffraction (XRD) study. Differential thermal analysis (DTA) has been employed to determine the glass transition temperature, <svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-5.52898pt" id="M4" height="14.4911pt" version="1.1" viewBox="-0.0498162 -8.96212 13.0802 14.4911" width="13.0802pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><path id="g113-85" d="M620 675H597C578 656 570 650 541 650H144C112 650 104 653 94 675H72C59 618 42 552 23 493L53 491C71 534 88 564 105 585C124 608 144 615 238 615H290L197 121C182 40 174 34 88 28L82 0H361L367 28C275 34 266 38 281 121L374 615H441C522 615 543 608 553 583C562 560 566 531 565 493L597 494C603 551 612 629 620 675Z"/></g><g transform="matrix(.0091,0,0,-0.0091,7.176,3.132)"><path id="g50-104" d="M554 433L549 437C539 437 513 441 503 443C481 447 456 451 436 451C354 451 268 415 216 368C150 308 99 205 99 106C99 24 136 -12 165 -12C196 -12 243 14 268 33C318 70 374 118 415 181H419L395 39C374 -84 332 -149 295 -175C269 -193 245 -197 212 -197C137 -197 93 -156 76 -102C71 -87 61 -87 51 -96C36 -110 24 -130 24 -147C24 -183 76 -257 171 -257C226 -257 285 -227 323 -200C387 -155 455 -76 480 94C499 225 538 391 554 433ZM460 386C457 361 438 287 426 254C408 218 373 176 332 133C294 93 246 61 217 61C198 61 186 80 186 122C186 167 206 250 231 294C262 349 288 375 317 387C334 394 358 400 381 400C413 400 439 393 460 386Z"/></g></svg>, as well as crystallization temperature, <svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-3.29108pt" id="M5" height="12.2532pt" version="1.1" viewBox="-0.0498162 -8.96212 11.5548 12.2532" width="11.5548pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><use xlink:href="#g113-85"/></g><g transform="matrix(.0091,0,0,-0.0091,7.176,3.132)"><path id="g50-100" d="M387 400C387 425 348 451 303 451C247 451 176 414 132 376C69 322 24 228 24 148C24 43 74 -12 147 -12C211 -12 301 33 363 103L346 128C319 99 249 51 193 51C148 51 112 84 112 165C112 230 130 287 154 330C170 359 199 400 243 400C277 400 304 383 326 354C333 345 343 343 354 348C378 360 387 382 387 400Z"/></g></svg>. DTA measurements were recorded in temperature range from 30 to 1200&#xb0;C. The prepared glasses were crystallized by regulated controlled heat treatment process on the basis of their DTA results. These samples are carried out for XRD measurements in the 2<svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-0.2063999pt" id="M6" height="9.49473pt" version="1.1" viewBox="-0.0498162 -9.28833 6.59789 9.49473" width="6.59789pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><path id="g113-230" d="M475 507C475 612 440 712 326 712C139 712 23 420 23 215C23 96 58 -12 180 -12C369 -12 475 293 475 507ZM391 522C391 486 387 448 379 394H126C155 538 222 677 310 677C386 677 391 571 391 522ZM373 346C344 193 283 22 189 22C126 22 106 114 106 196C106 243 111 293 118 346H373Z"/></g></svg> range from 20 to 80&#xb0; to study the crystallization behaviour and phase formation of the glass ceramic samples. The scanning electron microscopy (SEM) of these glass ceramic samples has been carried out to explore the morphology through nucleation and growth of the crystallites in the glassy matrix. The values of dielectric constant as well as dielectric loss were increased with increasing the temperature within the frequency range from 20&#x2009;Hz to 100&#x2009;Hz. The addition of 1&#x2009;mol&#x25; of <svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-3.272861pt" id="M7" height="12.0262pt" version="1.1" viewBox="-0.0498162 -8.75334 32.1636 12.0262" width="32.1636pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><use xlink:href="#g190-77"/></g><g transform="matrix(.013,0,0,-0.013,7.19,0)"><use xlink:href="#g190-98"/></g><g transform="matrix(.0091,0,0,-0.0091,12.944,3.132)"><use xlink:href="#g190-243"/></g><g transform="matrix(.013,0,0,-0.013,17.69,0)"><use xlink:href="#g190-80"/></g><g transform="matrix(.0091,0,0,-0.0091,27.437,3.132)"><use xlink:href="#g190-232"/></g></svg> to the lead bismuth titanate glasses enhances the crystallization and acts as donor dopant for this glass system.

C. R. Gautam

Abhishek Madheshiya

R. K. Dwivedi

Synthesis, Crystallization, and Dielectric Behaviour of Lead Bismuth Titanate Borosilicate Glasses with Addition of 1&#x25; La<sub>2</sub>O<sub>3</sub>

The problem of reflection and refraction of <i>SH</i>-waves at a plane interface between the homogeneous and inhomogeneous fibre-reinforced elastic half-spaces has been investigated. Amplitude and energy ratios corresponding to the reflected and refracted <i>SH</i>-waves are derived using appropriate boundary conditions. These ratios are computed numerically for a particular model and the results are depicted graphically.

C. Zorammuana

S. S. Singh

<i>SH</i>-Wave at a Plane Interface between Homogeneous and Inhomogeneous Fibre-Reinforced Elastic Half-Spaces

In the synthesis of nanostructure materials a specific emphasis has been focused on the control of shape and orientation of nanocrystals to obtain prerequisite properties of the materials.  Nanorice is a new hybrid nanoparticle prolate geometry of nanoshells with reduced symmetry having new exciting optical behavior. Rice-shaped <i>&#x3b2;</i>-FeOOH nanocrystals have been synthesized by a simple hydrolysis chemical method using ferric aqueous solution and urea as surfactant. The successive calcination of <i>&#x3b2;</i>-FeOOH nanocrystals at 650&#xb0;C results in the formation of the porous <i>&#x3b1;</i>-Fe<sub>2</sub>O<sub>3</sub> (hematite) microspheres. The as-synthesized yield of <i>&#x3b2;</i>-FeOOH nanocrystals was characterized by X-ray diffraction (XRD), scanning electron microscopy (SEM), energy dispersive X-ray analysis (EDAX), and optical spectroscopy. The successive transformation of rice-shaped <i>&#x3b2;</i>-FeOOH nanostructures into porous <i>&#x3b1;</i>-Fe<sub>2</sub>O<sub>3</sub> (hematite) microspheres through calcination process was confirmed by XRD, SEM, and EDAX studies. The water contact angle of as-prepared <i>&#x3b1;</i>-Fe<sub>2</sub>O<sub>3</sub> microspheres shows hydrophobic behavior of the material.

Beer Pal Singh

Nansy Sharma

Rakesh Kumar

Ashwani Kumar

Simple Hydrolysis Synthesis of Uniform Rice-Shaped <i>&#x3b2;</i>-FeOOH Nanocrystals and Their Transformation to <i>&#x3b1;</i>-Fe<sub>2</sub>O<sub>3</sub> Microspheres

Rheological characterization of polymers explains the flow behaviour and viscoelastic properties and tests fibre-forming ability. The current method investigates the viscoelastic properties and morphology of polymers and finds the rheological data and the right polymer viscosity, which is determining the best processing temperature. The right processing temperature saves the power, the material, and the time needed for production. After calculating polymers viscosity by using MFI tester, the method investigates rheological properties and surface shape at different temperatures and loads. The method could apply to other polymers to find the viscosity-temperature change and to set the best processing temperature.

Basel Younes

Simple Rheological Analysis Method of Spinnable-Polymer Flow Properties Using MFI Tester

Prepacked aggregate concrete (PAC) is a type of concrete that is placed in two stages where the coarse aggregates are first placed inside the formworks and then the grout is pumped from underneath through a manual pump. Grout properties including density, grout consistency, bleeding, and compressive strength are of great importance in PAC. Such properties could be improved by application of pozzolanic materials like palm oil fuel ash. This paper is aimed at finding the most optimum percentage of POFA replacement by weight of cement. It was concluded that 30&#x25; POFA replacement yielded the most optimum results.

Reza Hodjati

Hossein Aslani

Iman Faridmehr

A. S. M. Abdul Awal

Ziba Kazemi

Modification of Grout Properties in Prepacked Aggregate Concrete Incorporating Palm Oil Fuel Ash

Polymer films of PVA:Gd<sup>3+</sup> and PVA:Ho<sup>3+</sup> have been synthesized by a solution casting method in order to study their structural, optical, electrical, and magnetic properties. The semicrystalline nature of the polymer films has been confirmed from XRD analysis. The FTIR analysis confirms the complex formation of the polymer with the metal ions. Dielectric studies of these films have also been carried out at various set temperatures in the frequency from 100&#x2009;Hz to 1&#x2009;MHz for carrying out impedance spectroscopy analysis to evaluate the electrical conductivity which arises due to a single conduction mechanism and thus to have a single semicircle pattern from these polymer films. The DC electrical conductivity increases with an increase in the temperature and it could be due to high mobility of free charges (polarons and free ions) at higher temperatures. The conductivity trend follows the Arrhenius equation for PVA:Gd<sup>3+</sup> and for PVA:Ho<sup>3+</sup> polymer films. PVA:Gd<sup>3+</sup> polymer films show ferromagnetic nature, and PVA:Ho<sup>3+</sup> polymer films have revealed paramagnetic nature based on the trends noticed in the magnetic characteristic profiles.

M. Obula Reddy

B. Chandra Babu

Structural, Optical, Electrical, and Magnetic Properties of  PVA:Gd<sup>3+</sup> and PVA:Ho<sup>3+</sup> Polymer Films

This paper presents simulation of a Ni-based super-alloy during filling of a near-shaped turbine blade part to optimize its mechanical properties. Since geometrical shape of the airfoil is so complicated, a simple near-shaped part was made by plexiglass to water modeling. Condition and parameters of water modeling were obtained from the Procast software simulation. The flow pattern of the transparent systems, recorded by a high speed video camera, was analyzed. Air bubble amounts were quantitatively measured by an image analysis software. Quantified results were used to compare two systems in terms of ability to prevent bubble formation and entrainment. Both water modeling and computer simulating methods indicated that highest turbulences in bottom- and top-poured systems form in first initially pouring times. According to the water modeling results amount of bubble values was 40 and 18 percent for top-poured and bottom-poured systems, respectively. Then the Ni-base super-alloy IN939 is poured by investment casting in bottom- and top-poured systems and compared with each other. The results stated that bottom-poured system had higher mechanical properties compared to top-poured one. Ultimate tensile strength for the former was 820&#x2009;MPa while for the part which was cast by bottom-poured system it was 850&#x2009;MPa.

Mohammd Reza Alizadeh

Simulation of Ni-Based Super-Alloy and Optimizing of Its Mechanical Properties in a Near-Shaped Turbine Blade Part

Tensile and compressive behaviour of resorcinol-formaldehyde (RF) matrix and its composites reinforced with  fibers of <i>Luffa cylindrica</i> (LC) have been studied. LC fibers were subjected to chemical treatments such as alkali activation by NaOH followed by bleaching and acid hydrolysis in order to improve fiber-matrix adhesion. Both treated and untreated LC fibers are modified with calcium phosphate. The presence of hydroxy apatite, a polymorph of calcium phosphate and a major constituent of vertebrate bone and teeth, was confirmed from XRD peak of treated LC fiber. XRD analysis of the treated LC fiber has confirmed the crystalline nature of the chemically treated LC fiber by its crystallinity index. The effects of fiber loading of chemically treated and untreated LC fiber on ultimate stress, yield strength, breaking stress, and modulus of the composites were analyzed. The   tensile and compressive modulus of the composites were increased with incorporation of both treated and untreated LC fibers into the RF matrix. The modulus of composites with treated  LC fiber was enhanced compared to that of the untreated fiber composites. Furthermore the values of ultimate stress, yield stress, and breaking stress  were increased   with the incorporation of treated LC fiber in the composites.

Chhatrapati Parida

Sarat Kumar Dash

Sarat Chandra Das

Effect of Fiber Treatment and Fiber Loading on Mechanical Properties of <i>Luffa</i>-Resorcinol Composites

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Indian Journal of Materials Science