The fact that the microstructure of steel depends on its composition and the heat treatment given to it has been heavily exploited in the design of steel for power plant applications. To obtain a steel that can function at the higher temperature where power plants operate without failure for extended life, heat treatment is needed to produce fine and highly stable dispersion of carbides, nitrides, and intermetallic compounds in the microstructure of the material. A significant contribution also comes from solid solution strengthening by substitutional solutes. We review here various types of phases, microstructures, functions, and interacting effects of the various alloying elements in the design of steel for modern power plant application.

V. C. Igwemezie

C. C. Ugwuegbu

U. Mark

Physical Metallurgy of Modern Creep-Resistant Steel for Steam Power Plants: Microstructure and Phase Transformations

This research work presents a machinability study between wrought grade titanium and selective laser melted (SLM) titanium Ti-6Al-4V in a face turning operation, machined at cutting speeds between 60 and 180&#x2009;m/min. Machinability characteristics such as tool wear, cutting forces, and machined surface quality were investigated. Coating delamination, adhesion, abrasion, attrition, and chipping wear mechanisms were dominant during machining of SLM Ti-6Al-4V. Maximum flank wear was found higher in machining SLM Ti-6Al-4V compared to wrought Ti-6Al-4V at all speeds. It was also found that high machining speeds lead to catastrophic failure of the cutting tool during machining of SLM Ti-6Al-4V. Cutting force was higher in machining SLM Ti-6Al-4V as compared to wrought Ti-6Al-4V for all cutting speeds due to its higher strength and hardness. Surface finish improved with the cutting speed despite the high tool wear observed at high machining speeds. Overall, machinability of SLM Ti-6Al-4V was found poor as compared to the wrought alloy.

Manikandakumar Shunmugavel

Ashwin Polishetty

Junior Nomani

Moshe Goldberg

Guy Littlefair

Metallurgical and Machinability Characteristics of Wrought and Selective Laser Melted Ti-6Al-4V

This study examined the through-thickness (<svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-0.29774pt" id="M1" height="6.44133pt" version="1.1" viewBox="-0.0498162 -6.14359 6.59789 6.44133" width="6.59789pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><path id="g113-123" d="M475 445L452 468C423 436 401 426 385 426S352 427 305 436C268 443 216 448 185 448C156 448 128 425 102 382C89 360 77 338 64 304L89 291C117 340 143 380 190 380C214 380 268 376 295 373C320 370 344 371 362 374L70 101C32 65 23 36 23 18C23 5 27 -3 31 -8C36 -8 39 -6 42 -1C52 15 67 31 80 40S110 49 143 33C195 8 257 -20 290 -20C339 -20 382 11 439 129L416 148C366 74 334 55 305 55C278 55 236 68 203 81C169 94 141 100 122 96C205 170 348 308 411 376L475 445Z"/></g></svg>-direction) compressive stress versus strain behavior of 99.76% commercially pure (grade II) titanium sheet with relatively small grain size. The current study complemented earlier compression studies by examining a very thin (1.60 mm) sheet and deforming the Ti by successive compression tests to relatively large strains. The low aspect ratio, of the compression specimens extracted from the sheet, led to frictional effects that can create high triaxial stresses complicating the uniaxial stress versus strain behavior analysis. Nonetheless, reasonable estimates were made of the through-thickness large-strain behavior of a commercially pure (grade II) thin Ti sheet to relatively large true strains of about 1.0.

K. K. Smith

M. E. Kassner

Through-Thickness Compression Testing of Commercially Pure (Grade II) Titanium Thin Sheet to Large Strains

Inferior surface quality is a significant problem faced by machinist. The purpose of this study is to present a surface texture analysis undertaken as part of machinability assessment of Super Austenitic Stainless Steel alloy-AL6XN. The surface texture analysis includes measuring the surface roughness and investigating the microstructural behaviour of the machined surfaces. Eight milling trials were conducted using combination of cutting parameters under wet machining. An optical profilometer (noncontact) was used to evaluate the surface texture at three positions. The surface texture was represented using the parameter, average surface roughness. Scanning Electron Microscope was utilised to inspect the machined surface microstructure and correlate the microstructure with the surface roughness. Results showed that maximum roughness values recorded at the three positions in the longitudinal direction (perpendicular to the machining grooves) were 1.21&#x2009;<i>&#x3bc;</i>m (trial 1), 1.63&#x2009;<i>&#x3bc;</i>m (trial 6), and 1.68&#x2009;<i>&#x3bc;</i>m (trial 7), respectively, whereas the roughness values were greatly reduced in the lateral direction. Also, results showed that the feed rate parameter significantly influences the roughness values compared to the other cutting parameters. The microstructure of the machined surfaces was distorted by the existence of cracks, deformed edges, and bands and wear deposition due to machining process.

Mohanad Alabdullah

A. Polishetty

G. Littlefair

Microstructural and Surface Texture Analysis due to Machining in Super Austenitic Stainless Steel

We developed a unique three-point bend testing apparatus to measure bulk mechanical properties of a model metallic glass alloy (SAM2X5 with nominal composition Fe<sub>49.7</sub>Cr<sub>17.1</sub>Mn<sub>1.9</sub>Mo<sub>7.4</sub>W<sub>1.6</sub>B<sub>15.2</sub>C<sub>3.8</sub>Si<sub>2.4</sub>) prepared by spark plasma sintering. The relatively large sample sizes in the present work allowed for the preparation of test specimens with a macroscale cross section (in the millimeter range) with well-controlled sample dimensions closer to standardized tests. Wire saw cutting allowed for a relatively sharp notch radius (3x smaller than previous studies) and minimal sample damage. We determined that Young’s modulus and notch fracture toughness measured by our three-point bending apparatus are 230 GPa and 4.9 MPa<svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-0.04981995pt" id="M1" height="4.18388pt" version="1.1" viewBox="-0.0498162 -4.13406 3.07474 4.18388" width="3.07474pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><path id="g113-46" d="M170 255C170 288 146 313 114 313S58 288 58 255C58 221 82 198 114 198S170 221 170 255Z"/></g></svg>m<sup>1/2</sup>. Also, Vickers indentation and flexure testing provided consistent results for Young’s modulus. Indentation fracture toughness measured by Vickers indentation produced values at least 50% lower than by flexure. The microscale mechanical properties testing technique presented in this work and subsequent analyses are applicable to specimens of other compositions or ones prepared by other methods.

Thien Q. Phan

James P. Kelly

Michael E. Kassner

Veronica Eliasson

Olivia A. Graeve

Andrea M. Hodge

Bulk Mechanical Properties Testing of Metallic Marginal Glass Formers

Nowadays near-net-shape casting technology is an important area of research in the iron and steel industry. Among different kinds of near-net-shape casting process, twin-roll casting process has received much attention among researchers. Twin-roll casting (TRC) has been the subject of extensive research, not only to develop the technology but also to achieve an understanding of microstructural evolution and to produce quality strips. The main issues concerning the design and operation of twin-roll casters are metal-mold heat transfer, metal delivery system, and their possible effects on the solid shell formation and characteristics of the strips. The present review gives an idea about the process aspect, modeling, and quality issues in vertical twin-roll strip casting process and helps to improve the design of twin-roll strip caster.

Seshadev Sahoo

Review on Vertical Twin-Roll Strip Casting: A Key Technology for Quality Strips

A systematic study on the structural and magnetic properties of <svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-3.4007pt" id="M1" height="12.1671pt" version="1.1" viewBox="-0.0498162 -8.7664 58.1449 12.1671" width="58.1449pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><path id="g121-68" d="M493 503C489 551 484 614 483 650H43V622C120 616 128 611 128 525V126C128 40 120 34 40 28V0H312V28C221 34 213 40 213 126V307H316C407 307 412 296 424 227H453V420H424C412 355 407 346 316 346H213V584C213 613 216 616 246 616H322C398 616 419 607 436 579C449 559 455 539 464 499L493 503Z"/></g><g transform="matrix(.013,0,0,-0.013,6.629,0)"><path id="g121-99" d="M380 106C343 72 306 56 265 56C195 56 116 112 115 248C235 252 361 262 377 265C396 269 400 277 400 297C400 374 333 449 250 449H249C198 449 144 421 103 376S37 269 37 201C37 88 109 -12 232 -12C263 -12 332 6 395 84L380 106ZM225 412C281 412 315 364 314 312C314 297 308 292 290 292C232 290 176 289 120 289C135 370 180 412 225 412Z"/></g><g transform="matrix(.0091,0,0,-0.0091,12.201,3.132)"><path id="g50-50" d="M389 0V32C297 38 291 46 291 118V635C234 613 175 595 109 583V556L161 554C203 552 207 547 207 497V118C207 46 201 38 110 32V0H389Z"/></g><g transform="matrix(.0091,0,0,-0.0091,16.632,3.132)"><path id="g50-49" d="M245 635C92 635 37 457 37 312C37 149 91 -12 244 -12C395 -12 449 166 449 312C449 469 395 635 245 635ZM243 598C332 598 358 454 358 312C358 173 334 26 245 26C158 26 128 174 128 313S152 598 243 598Z"/></g><g transform="matrix(.0091,0,0,-0.0091,21.064,3.132)"><use xlink:href="#g50-49"/></g><g transform="matrix(.0091,0,0,-0.0091,25.496,3.132)"><path id="g54-33" d="M556 236V289H56V236H556Z"/></g><g transform="matrix(.0091,0,0,-0.0091,31.056,3.132)"><path id="g50-121" d="M545 403C545 425 527 451 498 451C448 451 400 404 312 286L290 341C262 412 246 451 219 451C182 451 138 404 92 345L112 323C152 368 169 378 181 378C192 378 201 359 216 321L257 214C184 115 142 69 113 69C102 69 93 73 88 79S78 89 68 89C47 89 24 61 24 40C24 8 49 -12 75 -12C125 -12 175 31 271 175L312 64C330 15 357 -12 382 -12C421 -12 475 35 515 98L496 121C466 88 439 62 420 62C402 62 384 92 363 147L325 247C349 280 374 309 397 333C422 361 446 381 462 381C471 381 481 374 488 366C493 360 499 357 505 357C521 357 545 380 545 403Z"/></g><g transform="matrix(.013,0,0,-0.013,36.822,0)"><path id="g121-65" d="M614 175C564 76 510 21 408 21C256 21 146 149 146 336C146 488 235 629 402 629C510 629 570 586 597 480L626 488C620 541 614 582 606 638C578 643 510 665 429 665C206 665 44 527 44 316C44 157 153 -15 402 -15C474 -15 558 5 586 11C604 45 629 119 643 165L614 175Z"/></g><g transform="matrix(.013,0,0,-0.013,45.663,0)"><path id="g121-109" d="M257 449C165 449 37 374 37 209C37 98 119 -12 256 -12C355 -12 473 65 473 226C473 349 381 449 257 449ZM244 416C333 416 380 320 380 204C380 67 329 21 267 21C184 21 130 115 130 241C130 354 184 416 244 416Z"/></g><g transform="matrix(.0091,0,0,-0.0091,52.35,3.132)"><use xlink:href="#g50-121"/></g></svg> alloys (<svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-0.6370001pt" id="M2" height="8.98582pt" version="1.1" viewBox="-0.0498162 -8.34882 62.2941 8.98582" width="62.2941pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><path id="g113-50" d="M384 0V27C293 34 287 42 287 114V635C232 613 172 594 109 583V559L157 557C201 555 205 550 205 499V114C205 42 199 34 109 27V0H384Z"/></g><g transform="matrix(.013,0,0,-0.013,6.24,0)"><path id="g113-49" d="M241 635C89 635 35 457 35 312C35 153 89 -12 240 -12C390 -12 443 166 443 312C443 466 390 635 241 635ZM238 602C329 602 354 454 354 312C354 172 330 22 240 22C152 22 124 173 124 313S148 602 238 602Z"/></g><g transform="matrix(.013,0,0,-0.013,16.112,0)"><path id="g117-91" d="M512 -3V55L134 254V256L512 456V514L75 281V230L512 -3Z"/></g><g transform="matrix(.013,0,0,-0.013,27.375,0)"><path id="g113-121" d="M536 404C536 423 520 448 491 448C445 448 398 404 308 283L286 338C255 416 242 448 217 448C182 448 138 402 92 341L111 321C149 368 169 378 178 378C188 378 198 363 214 320L254 212C185 117 138 65 107 65C98 65 85 69 82 75C79 82 73 86 65 86C44 86 23 60 23 39C23 7 44 -12 71 -12C119 -12 168 33 265 177L306 61C321 17 347 -12 373 -12C413 -12 465 33 507 96L491 119C459 84 432 60 413 60C395 60 378 92 358 148L321 250C341 279 369 310 389 332C417 363 439 382 456 382C466 382 475 376 481 368C486 361 492 358 496 358C513 358 536 381 536 404Z"/></g><g transform="matrix(.013,0,0,-0.013,38.274,0)"><use xlink:href="#g117-91"/></g><g transform="matrix(.013,0,0,-0.013,49.537,0)"><path id="g113-58" d="M244 635C114 635 38 519 38 422C38 317 111 240 217 240C236 240 255 244 277 256L345 292C311 140 203 39 59 15L64 -15C89 -15 150 -5 204 17C339 72 440 202 440 386C440 521 368 635 244 635ZM228 602C326 602 352 479 352 390C352 370 351 347 348 324C327 308 293 296 258 296C174 296 124 369 124 458C124 517 152 602 228 602Z"/></g><g transform="matrix(.013,0,0,-0.013,55.778,0)"><use xlink:href="#g113-49"/></g></svg>, <svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-0.2064009pt" id="M3" height="8.8423pt" version="1.1" viewBox="-0.0498162 -8.6359 43.2082 8.8423" width="43.2082pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><path id="g113-133" d="M600 0V24L339 665L311 657L43 24V0H600ZM497 50H107L303 539L497 50Z"/></g><g transform="matrix(.013,0,0,-0.013,8.327,0)"><use xlink:href="#g113-121"/></g><g transform="matrix(.013,0,0,-0.013,19.226,0)"><path id="g117-34" d="M535 323V373H52V323H535ZM535 138V188H52V138H535Z"/></g><g transform="matrix(.013,0,0,-0.013,30.489,0)"><use xlink:href="#g113-50"/></g><g transform="matrix(.013,0,0,-0.013,36.729,0)"><use xlink:href="#g113-49"/></g></svg> in wt. percent) obtained by mechanical alloying is presented. Elemental powders of Fe and Co mixed in an adequate weight ratio were milled at room temperature in a shaker mixer mill using vials and balls of hardened steel as milling media with a ball : powder weight ratio of 12 : 1. The mixtures were milled for 3 h. The results show that, after milling, for almost all the composition (up to <svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-0.2063904pt" id="M4" height="8.55521pt" version="1.1" viewBox="-0.0498162 -8.34882 34.844 8.55521" width="34.844pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><use xlink:href="#g113-121"/></g><g transform="matrix(.013,0,0,-0.013,10.899,0)"><use xlink:href="#g117-34"/></g><g transform="matrix(.013,0,0,-0.013,22.162,0)"><path id="g113-55" d="M137 343C167 482 260 545 321 574C357 591 397 603 429 609L423 641C382 634 335 622 295 608C189 570 37 457 37 238C37 84 125 -12 242 -12C362 -12 447 89 447 209C447 311 374 393 267 393C247 393 226 386 204 376L137 343ZM227 337C318 337 361 256 361 173C361 105 336 22 258 22C176 22 126 120 126 240C126 266 127 291 132 310C155 323 189 337 227 337Z"/></g><g transform="matrix(.013,0,0,-0.013,28.402,0)"><use xlink:href="#g113-49"/></g></svg>), solid solutions based on bcc structures were obtained. For Co-rich alloys (<svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-1.11981pt" id="M5" height="9.46863pt" version="1.1" viewBox="-0.0498162 -8.34882 34.844 9.46863" width="34.844pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><use xlink:href="#g113-121"/></g><g transform="matrix(.013,0,0,-0.013,10.899,0)"><path id="g117-94" d="M531 285V335L57 550V494L473 310L57 127V71L531 285ZM531 -40V10H57V-40H531Z"/></g><g transform="matrix(.013,0,0,-0.013,22.162,0)"><path id="g113-56" d="M447 623H65C61 580 56 530 47 475H76C100 541 106 550 172 550H388C308 376 196 170 91 -1L98 -12L172 -2C268 204 360 408 455 611L447 623Z"/></g><g transform="matrix(.013,0,0,-0.013,28.404,0)"><use xlink:href="#g113-49"/></g></svg>), different phases were found, revealing the formation of a metastable intermetallic phase (FeCo, wairauite) together with fcc-Co and hcp-Co phases. The specific saturation magnetization increases by increasing Co content, reaching a maximum value of 225 emu/g for hcp-Fe<sub>70</sub>Co<sub>30</sub>, and then it shows a diminution up to 154 emu/g for bcc-Fe<sub>30</sub>Co<sub>70</sub>. All studied alloys (<svg xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg" style="vertical-align:-3.4007pt" id="M6" height="12.1671pt" version="1.1" viewBox="-0.0498162 -8.7664 58.1449 12.1671" width="58.1449pt"><g transform="matrix(.013,0,0,-0.013,0,0)"><use xlink:href="#g121-68"/></g><g transform="matrix(.013,0,0,-0.013,6.629,0)"><use xlink:href="#g121-99"/></g><g transform="matrix(.0091,0,0,-0.0091,12.201,3.132)"><use xlink:href="#g50-50"/></g><g transform="matrix(.0091,0,0,-0.0091,16.632,3.132)"><use xlink:href="#g50-49"/></g><g transform="matrix(.0091,0,0,-0.0091,21.064,3.132)"><use xlink:href="#g50-49"/></g><g transform="matrix(.0091,0,0,-0.0091,25.496,3.132)"><use xlink:href="#g54-33"/></g><g transform="matrix(.0091,0,0,-0.0091,31.056,3.132)"><use xlink:href="#g50-121"/></g><g transform="matrix(.013,0,0,-0.013,36.822,0)"><use xlink:href="#g121-65"/></g><g transform="matrix(.013,0,0,-0.013,45.663,0)"><use xlink:href="#g121-109"/></g><g transform="matrix(.0091,0,0,-0.0091,52.35,3.132)"><use xlink:href="#g50-121"/></g></svg>) present low coercivity, in the range from 0 to 65 Oe, which is lower than reported. The coercivity increases with the increment in Co, reaching a maximum of 64.1 Oe for Fe<sub>40</sub>Co<sub>60</sub>. After that, the coercivity falls up to 24.5 Oe for Co-rich alloys, which make them a very low coercive material.

F. S&#xe1;nchez-De Jes&#xfa;s

A. M. Bolar&#xed;n-Mir&#xf3;

C. A. Cort&#xe9;s Escobedo

G. Torres-Villase&#xf1;or

P. Vera-Serna

Structural Analysis and Magnetic Properties of FeCo Alloys Obtained by Mechanical Alloying

An anticorrosion activity of 8-quinoline sulphonyl chloride (8-QSC) on mild steel in 1&#x2009;M HCl solution was studied by weight loss (WL) method and electrochemical methods, namely, electrochemical impedance spectroscopy (EIS), Tafel polarization (TP), and linear polarization resistance (LPR). Results obtained from WL method, EIS, TP, and LPR, showed that 8-QSC is a good corrosion inhibitor for mild steel in 1&#x2009;M HCl solution. The results indicated that the inhibition efficiency and extent of surface coverage were increased with increase in inhibitor concentration and decrease in the corrosion rate. This is due to the formation of protective film on the surface of mild steel. Adsorption of 8-QSC on the mild steel surface was found to obey the Langmuir adsorption isotherm. A Tafel plot indicates that the used inhibitor behaves predominantly as cathodic type. The surface morphology of the mild steel was studied by Scanning Electron Microscopy (SEM) and Energy Dispersive X-Ray (EDX) Spectroscopy techniques. All the methods give the same order of inhibition efficiencies.

R. Ganapathi Sundaram

M. Sundaravadivelu

Anticorrosion Activity of 8-Quinoline Sulphonyl Chloride on Mild Steel in 1&#x2009;M HCl Solution

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Journal of Metallurgy