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ingot</title> <meta name="description" content="Search results for: ingot"> <meta name="keywords" content="ingot"> <meta name="viewport" content="width=device-width, initial-scale=1, minimum-scale=1, maximum-scale=1, user-scalable=no"> <meta charset="utf-8"> <link href="https://cdn.waset.org/favicon.ico" type="image/x-icon" rel="shortcut icon"> <link href="https://cdn.waset.org/static/plugins/bootstrap-4.2.1/css/bootstrap.min.css" rel="stylesheet"> <link href="https://cdn.waset.org/static/plugins/fontawesome/css/all.min.css" rel="stylesheet"> <link href="https://cdn.waset.org/static/css/site.css?v=150220211555" rel="stylesheet"> </head> <body> <header> <div class="container"> <nav class="navbar navbar-expand-lg navbar-light"> <a class="navbar-brand" href="https://waset.org"> <img src="https://cdn.waset.org/static/images/wasetc.png" alt="Open Science Research Excellence" title="Open Science Research Excellence" /> </a> <button class="d-block d-lg-none navbar-toggler ml-auto" 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class="input-group"> <i class="fas fa-search"></i> <input type="text" class="search-query" name="q" placeholder="Author, Title, Abstract, Keywords" value="ingot"> <input type="submit" class="btn_search" value="Search"> </div> </div> </form> </div> </div> <div class="row mt-3"> <div class="col-sm-3"> <div class="card"> <div class="card-body"><strong>Commenced</strong> in January 2007</div> </div> </div> <div class="col-sm-3"> <div class="card"> <div class="card-body"><strong>Frequency:</strong> Monthly</div> </div> </div> <div class="col-sm-3"> <div class="card"> <div class="card-body"><strong>Edition:</strong> International</div> </div> </div> <div class="col-sm-3"> <div class="card"> <div class="card-body"><strong>Paper Count:</strong> 16</div> </div> </div> </div> <h1 class="mt-3 mb-3 text-center" style="font-size:1.6rem;">Search results for: ingot</h1> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">16</span> Studies of Reduction Metal Impurity in Residual Melt by Czochralski Method </h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Jaemin%20Kim">Jaemin Kim</a>, <a href="https://publications.waset.org/abstracts/search?q=Ilsun%20Pang"> Ilsun Pang</a>, <a href="https://publications.waset.org/abstracts/search?q=Yongrae%20Cho"> Yongrae Cho</a>, <a href="https://publications.waset.org/abstracts/search?q=Kwanghun%20Kim"> Kwanghun Kim</a>, <a href="https://publications.waset.org/abstracts/search?q=Sungsun%20Baik"> Sungsun Baik </a> </p> <p class="card-text"><strong>Abstract:</strong></p> Manufacturing cost reduction is becoming more important due to excessive oversupply of Single crystalline ingot in recent solar market. Many companies are carrying out extensive research to grow more than one Single crystalline ingot in one batch to reduce manufacturing cost. However what most companies are finding difficult in this process is the effect on ingot due to increasing levels of impurities. Every ingot leaves a certain amount of melt after it is fully grown. This is the impurity that lowers the ingot quality. This impurity increase in the batch after second, third and more are grown subsequently in one batch. In order to solve this problem, the experiment to remove the residual melt in high temperature of hot zone was performed and succeeded. Theoretical average metal concentration of second ingot by new method was calculated and compared to it by conventional method. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=single%20crystal" title="single crystal">single crystal</a>, <a href="https://publications.waset.org/abstracts/search?q=solar%20cell" title=" solar cell"> solar cell</a>, <a href="https://publications.waset.org/abstracts/search?q=metal%20impurity" title=" metal impurity"> metal impurity</a>, <a href="https://publications.waset.org/abstracts/search?q=Ingot" title=" Ingot"> Ingot</a> </p> <a href="https://publications.waset.org/abstracts/24923/studies-of-reduction-metal-impurity-in-residual-melt-by-czochralski-method" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/24923.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">397</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">15</span> Development of 420 mm Diameter Silicon Crystal Growth Using Continuous Czochralski Process</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Ilsun%20Pang">Ilsun Pang</a>, <a href="https://publications.waset.org/abstracts/search?q=Kwanghun%20Kim"> Kwanghun Kim</a>, <a href="https://publications.waset.org/abstracts/search?q=Sungsun%20Baik"> Sungsun Baik </a> </p> <p class="card-text"><strong>Abstract:</strong></p> Large diameter Si wafer is used as semiconductor substrate. Large diameter Si crystal ingot should be needed in order to increase wafer size. To make convection of large silicon melt stable, magnetic field is normally applied, but magnetic field is expensive and it is not proper to stabilize the large Si melt. To solve the problem, we propose a continuous Czochralski process which can be applied to small melt without magnetic field. We used granule poly, which has size distribution of 1~3 mm and is easily supplied in double crucible during silicon ingot growth. As the result, we produced 420 mm diameter ingot. In this paper, we describe an experimental study on crystal growth of large diameter silicon by Continuous Czochralski process. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=Czochralski" title="Czochralski">Czochralski</a>, <a href="https://publications.waset.org/abstracts/search?q=ingot" title=" ingot"> ingot</a>, <a href="https://publications.waset.org/abstracts/search?q=silicon%20crystal" title=" silicon crystal"> silicon crystal</a>, <a href="https://publications.waset.org/abstracts/search?q=wafer" title=" wafer"> wafer</a> </p> <a href="https://publications.waset.org/abstracts/23956/development-of-420-mm-diameter-silicon-crystal-growth-using-continuous-czochralski-process" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/23956.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">450</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">14</span> Full-Scale 3D Simulation of the Electroslag Rapid Remelting Process </h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=E.%20Karimi-Sibaki">E. Karimi-Sibaki</a>, <a href="https://publications.waset.org/abstracts/search?q=A.%20Kharicha"> A. Kharicha</a>, <a href="https://publications.waset.org/abstracts/search?q=M.%20Wu"> M. Wu</a>, <a href="https://publications.waset.org/abstracts/search?q=A.%20Ludwig"> A. Ludwig</a> </p> <p class="card-text"><strong>Abstract:</strong></p> The standard electroslag remelting (ESR) process can ideally control the solidification of an ingot and produce homogeneous structure with minimum defects. However, the melt rate of electrode is rather low that makes the whole process uneconomical especially to produce small ingot sizes. In contrast, continuous casting is an economical process to produce small ingots such as billets at high casting speed. Unfortunately, deep liquid melt pool forms in the billet ingot of continuous casting that leads to center porosity and segregation. As such, continuous casting is not suitable to produce segregation prone alloys like tool steel or several super alloys. On the other hand, the electro slag rapid remelting (ESRR) process has advantages of both traditional ESR and continuous casting processes to produce billets. In the ESRR process, a T-shaped mold is used including a graphite ring that takes major amount of current through the mold. There are only a few reports available in the literature discussing about this topic. The research on the ESRR process is currently ongoing aiming to improve the design of the T-shaped mold, to decrease overall heat loss in the process, and to obtain a higher temperature at metal meniscus. In the present study, a 3D model is proposed to investigate the electromagnetic, thermal, and flow fields in the whole process as well as solidification of the billet ingot. We performed a fully coupled numerical simulation to explore the influence of the electromagnetically driven flow (MHD) on the thermal field in the slag and ingot. The main goal is to obtain some fundamental understanding of the formation of melt pool of the solidifying billet ingot in the ESRR process. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=billet%20ingot" title="billet ingot">billet ingot</a>, <a href="https://publications.waset.org/abstracts/search?q=magnetohydrodynamics%20%28mhd%29" title=" magnetohydrodynamics (mhd)"> magnetohydrodynamics (mhd)</a>, <a href="https://publications.waset.org/abstracts/search?q=numerical%20simulation" title=" numerical simulation"> numerical simulation</a>, <a href="https://publications.waset.org/abstracts/search?q=remelting" title=" remelting"> remelting</a>, <a href="https://publications.waset.org/abstracts/search?q=solidification" title=" solidification"> solidification</a>, <a href="https://publications.waset.org/abstracts/search?q=t-shaped%20mold." title=" t-shaped mold. "> t-shaped mold. </a> </p> <a href="https://publications.waset.org/abstracts/66855/full-scale-3d-simulation-of-the-electroslag-rapid-remelting-process" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/66855.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">294</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">13</span> Optimum Dispatching Rule in Solar Ingot-Wafer Manufacturing System</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Wheyming%20Song">Wheyming Song</a>, <a href="https://publications.waset.org/abstracts/search?q=Hung-Hsiang%20Lin"> Hung-Hsiang Lin</a>, <a href="https://publications.waset.org/abstracts/search?q=Scott%20Lian"> Scott Lian</a> </p> <p class="card-text"><strong>Abstract:</strong></p> In this research, we investigate the optimal dispatching rule for machines and manpower allocation in the solar ingot-wafer systems. The performance of the method is measured by the sales profit for each dollar paid to the operators in a one week at steady-state. The decision variables are identification-number of machines and operators when each job is required to be served in each process. We propose a rule which is a function of operator’s ability, corresponding salary, and standing location while in the factory. The rule is named ‘Multi-nominal distribution dispatch rule’. The proposed rule performs better than many traditional rules including generic algorithm and particle swarm optimization. Simulation results show that the proposed Multi-nominal distribution dispatch rule improvement on the sales profit dramatically. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=dispatching" title="dispatching">dispatching</a>, <a href="https://publications.waset.org/abstracts/search?q=solar%20ingot" title=" solar ingot"> solar ingot</a>, <a href="https://publications.waset.org/abstracts/search?q=simulation" title=" simulation"> simulation</a>, <a href="https://publications.waset.org/abstracts/search?q=flexsim" title=" flexsim"> flexsim</a> </p> <a href="https://publications.waset.org/abstracts/70569/optimum-dispatching-rule-in-solar-ingot-wafer-manufacturing-system" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/70569.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">300</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">12</span> Relationship between Extrusion Ratio and Mechanical Properties of Magnesium Alloy</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=C.%20H.%20Jeon">C. H. Jeon</a>, <a href="https://publications.waset.org/abstracts/search?q=Y.%20H.%20Kim"> Y. H. Kim</a>, <a href="https://publications.waset.org/abstracts/search?q=G.%20A.%20Lee"> G. A. Lee</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Reducing resource consumption and carbon dioxide emission are recognized as urgent issues. One way of resolving these issues is to reduce product weight. Magnesium alloys are considered promising candidates because of their lightness. Various studies have been conducted on using magnesium alloy instead of conventional iron or aluminum in mechanical parts, due to the light weight and superior specific strength of magnesium alloy. However, even stronger magnesium alloys are needed for mechanical parts. One common way to enhance the strength of magnesium alloy is by extruding the ingot. In order to enhance the mechanical properties, magnesium alloy ingot were extruded at various extrusion ratios. Relationship between extrusion ratio and mechanical properties was examined on extruded material of magnesium alloy. And Textures and microstructures of the extruded materials were investigated. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=extrusion" title="extrusion">extrusion</a>, <a href="https://publications.waset.org/abstracts/search?q=extrusion%20ratio" title=" extrusion ratio"> extrusion ratio</a>, <a href="https://publications.waset.org/abstracts/search?q=magnesium" title=" magnesium"> magnesium</a>, <a href="https://publications.waset.org/abstracts/search?q=mechanical%20property" title=" mechanical property"> mechanical property</a>, <a href="https://publications.waset.org/abstracts/search?q=lightweight%20material" title=" lightweight material"> lightweight material</a> </p> <a href="https://publications.waset.org/abstracts/30018/relationship-between-extrusion-ratio-and-mechanical-properties-of-magnesium-alloy" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/30018.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">500</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">11</span> An EBSD Investigation of Ti-6Al-4Nb Alloy Processed by Plan Strain Compression Test </h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Anna%20Jastrzebska">Anna Jastrzebska</a>, <a href="https://publications.waset.org/abstracts/search?q=K.%20S.%20Suresh"> K. S. Suresh</a>, <a href="https://publications.waset.org/abstracts/search?q=T.%20Kitashima"> T. Kitashima</a>, <a href="https://publications.waset.org/abstracts/search?q=Y.%20Yamabe-Mitarai"> Y. Yamabe-Mitarai</a>, <a href="https://publications.waset.org/abstracts/search?q=Z.%20Pakiela"> Z. Pakiela </a> </p> <p class="card-text"><strong>Abstract:</strong></p> Near α titanium alloys are important materials for aerospace applications, especially in high temperature applications such as jet engine. Mechanical properties of Ti alloys strongly depends on their processing route, then it is very important to understand micro-structure change by different processing. In our previous study, Nb was found to improve oxidation resistance of Ti alloys. In this study, micro-structure evolution of Ti-6Al-4Nb (wt %) alloy was investigated after plain strain compression test in hot working temperatures in the α and β phase region. High-resolution EBSD was successfully used for precise phase and texture characterization of this alloy. 1.1 kg of Ti-6Al-4Nb ingot was prepared using cold crucible levitation melting. The ingot was subsequently homogenized in 1050 deg.C for 1h followed by cooling in the air. Plate like specimens measuring 10×20×50 mm3 were cut from an ingot by electrical discharge machining (EDM). The plain strain compression test using an anvil with 10 x 35 mm in size was performed with 3 different strain rates: 0.1s-1, 1s-1and 10s-1 in 700 deg.C and 1050 deg.C to obtain 75% of deformation. The micro-structure was investigated by scanning electron microscopy (SEM) equipped with electron backscatter diffraction (EBSD) detector. The α/β phase ratio and phase morphology as well as the crystallographic texture, subgrain size, misorientation angles and misorientation gradients corresponding to each phase were determined over the middle and the edge of sample areas. The deformation mechanism in each working temperature was discussed. The evolution of texture changes with strain rate was investigated. The micro-structure obtained by plain strain compression test was heterogeneous with a wide range of grain sizes. This is because deformation and dynamic recrystallization occurred during deformation at temperature in the α and β phase. It was strongly influenced by strain rate. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=EBSD" title="EBSD">EBSD</a>, <a href="https://publications.waset.org/abstracts/search?q=plain%20strain%20compression%20test" title=" plain strain compression test"> plain strain compression test</a>, <a href="https://publications.waset.org/abstracts/search?q=Ti%20alloys" title=" Ti alloys"> Ti alloys</a> </p> <a href="https://publications.waset.org/abstracts/21431/an-ebsd-investigation-of-ti-6al-4nb-alloy-processed-by-plan-strain-compression-test" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/21431.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">380</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">10</span> Microstructure and High Temperature Deformation Behavior of Cast 310S Alloy</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Jung-Ho%20Moon">Jung-Ho Moon</a>, <a href="https://publications.waset.org/abstracts/search?q=Myung-Gon%20Yoon"> Myung-Gon Yoon</a>, <a href="https://publications.waset.org/abstracts/search?q=Tae%20Kwon%20Ha"> Tae Kwon Ha</a> </p> <p class="card-text"><strong>Abstract:</strong></p> High temperature deformation behavior of cast 310S stainless steel has been investigated in this study by performing tensile and compression tests at temperatures from 900 to 1200°C. Rectangular ingots of which the dimensions were 350×350×100 in millimeter were cast using vacuum induction melting. Phase equilibrium was calculated using the FactSage®, thermodynamic software and database. Thermal expansion coefficient was also measured on the ingot in the temperature range from room temperature to 1200°C. Tensile strength of cast 310S stainless steel was 9 MPa at 1200°C, which is a little higher than that of a wrought 310S. With temperature decreased, tensile strength increased rapidly and reached up to 72 MPa at 900°C. Elongation also increased with temperature decreased. Microstructure observation revealed that σ phase was precipitated along the grain boundary and within the matrix over 1200°C, which is detrimental to high temperature elongation. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=stainless%20steel" title="stainless steel">stainless steel</a>, <a href="https://publications.waset.org/abstracts/search?q=STS%20310S" title=" STS 310S"> STS 310S</a>, <a href="https://publications.waset.org/abstracts/search?q=high%20temperature%20deformation" title=" high temperature deformation"> high temperature deformation</a>, <a href="https://publications.waset.org/abstracts/search?q=microstructure" title=" microstructure"> microstructure</a>, <a href="https://publications.waset.org/abstracts/search?q=mechanical%20properties" title=" mechanical properties"> mechanical properties</a> </p> <a href="https://publications.waset.org/abstracts/11151/microstructure-and-high-temperature-deformation-behavior-of-cast-310s-alloy" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/11151.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">400</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">9</span> Improvement in Properties of Ni-Cr-Mo-V Steel through Process Control</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Arnab%20Majumdar">Arnab Majumdar</a>, <a href="https://publications.waset.org/abstracts/search?q=Sanjoy%20Sadhukhan"> Sanjoy Sadhukhan</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Although gun barrel steels are an important variety from defense view point, available literatures are very limited. In the present work, an IF grade Ni-Cr-Mo-V high strength low alloy steel is produced in Electric Earth Furnace-ESR Route. Ingot was hot forged to desired dimension with a reduction ratio of 70-75% followed by homogenization, hardening and tempering treatment. Sample chemistry, NMIR, macro and micro structural analyses were done. Mechanical properties which include tensile, impact, and fracture toughness were studied. Ultrasonic testing was done to identify internal flaws. The existing high strength low alloy Ni-Cr-Mo-V steel shows improved properties in modified processing route and heat treatment schedule in comparison to properties noted earlier for manufacturing of gun barrels. The improvement in properties seems to withstand higher explosive loads with the same amount of steel in gun barrel application. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=gun%20barrel%20steels" title="gun barrel steels">gun barrel steels</a>, <a href="https://publications.waset.org/abstracts/search?q=IF%20grade" title=" IF grade"> IF grade</a>, <a href="https://publications.waset.org/abstracts/search?q=chemistry" title=" chemistry"> chemistry</a>, <a href="https://publications.waset.org/abstracts/search?q=physical%20properties" title=" physical properties"> physical properties</a>, <a href="https://publications.waset.org/abstracts/search?q=thermal%20and%20mechanical%20processing" title=" thermal and mechanical processing"> thermal and mechanical processing</a>, <a href="https://publications.waset.org/abstracts/search?q=mechanical%20properties" title=" mechanical properties"> mechanical properties</a>, <a href="https://publications.waset.org/abstracts/search?q=ultrasonic%20testing" title=" ultrasonic testing"> ultrasonic testing</a> </p> <a href="https://publications.waset.org/abstracts/44634/improvement-in-properties-of-ni-cr-mo-v-steel-through-process-control" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/44634.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">377</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">8</span> Carbide Structure and Fracture Toughness of High Speed Tool Steels</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Jung-Ho%20Moon">Jung-Ho Moon</a>, <a href="https://publications.waset.org/abstracts/search?q=Tae%20Kwon%20Ha"> Tae Kwon Ha</a> </p> <p class="card-text"><strong>Abstract:</strong></p> M2 steels, the typical Co-free high speed steel (HSS) possessing hardness level of 63~65 HRc, are most widely used for cutting tools. On the other hand, Co-containing HSS’s, such as M35 and M42, show a higher hardness level of 65~67 HRc and used for high quality cutting tools. In the fabrication of HSS’s, it is very important to control cleanliness and eutectic carbide structure of the ingot and it is required to increase productivity at the same time. Production of HSS ingots includes a variety of processes such as casting, electro-slag remelting (ESR), forging, blooming, and wire rod rolling processes. In the present study, electro-slag rapid remelting (ESRR) process, an advanced ESR process combined by continuous casting, was successfully employed to fabricate HSS billets of M2, M35, and M42 steels. Distribution and structure of eutectic carbides of the billets were analysed and cleanliness, hardness, and composition profile of the billets were also evaluated. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=high%20speed%20tool%20steel" title="high speed tool steel">high speed tool steel</a>, <a href="https://publications.waset.org/abstracts/search?q=eutectic%20carbide" title=" eutectic carbide"> eutectic carbide</a>, <a href="https://publications.waset.org/abstracts/search?q=microstructure" title=" microstructure"> microstructure</a>, <a href="https://publications.waset.org/abstracts/search?q=hardness" title=" hardness"> hardness</a>, <a href="https://publications.waset.org/abstracts/search?q=fracture%20toughness" title=" fracture toughness"> fracture toughness</a> </p> <a href="https://publications.waset.org/abstracts/15803/carbide-structure-and-fracture-toughness-of-high-speed-tool-steels" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/15803.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">445</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">7</span> Calculation of Detection Efficiency of Horizontal Large Volume Source Using Exvol Code</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=M.%20Y.%20Kang">M. Y. Kang</a>, <a href="https://publications.waset.org/abstracts/search?q=Euntaek%20Yoon"> Euntaek Yoon</a>, <a href="https://publications.waset.org/abstracts/search?q=H.%20D.%20Choi"> H. D. Choi</a> </p> <p class="card-text"><strong>Abstract:</strong></p> To calculate the full energy (FE) absorption peak efficiency for arbitrary volume sample, we developed and verified the EXVol (Efficiency calculator for EXtended Voluminous source) code which is based on effective solid angle method. EXVol is possible to describe the source area as a non-uniform three-dimensional (x, y, z) source. And decompose and set it into several sets of volume units. Users can equally divide (x, y, z) coordinate system to calculate the detection efficiency at a specific position of a cylindrical volume source. By determining the detection efficiency for differential volume units, the total radiative absolute distribution and the correction factor of the detection efficiency can be obtained from the nondestructive measurement of the source. In order to check the performance of the EXVol code, Si ingot of 20 cm in diameter and 50 cm in height were used as a source. The detector was moved at the collimation geometry to calculate the detection efficiency at a specific position and compared with the experimental values. In this study, the performance of the EXVol code was extended to obtain the detection efficiency distribution at a specific position in a large volume source. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=attenuation" title="attenuation">attenuation</a>, <a href="https://publications.waset.org/abstracts/search?q=EXVol" title=" EXVol"> EXVol</a>, <a href="https://publications.waset.org/abstracts/search?q=detection%20efficiency" title=" detection efficiency"> detection efficiency</a>, <a href="https://publications.waset.org/abstracts/search?q=volume%20source" title=" volume source"> volume source</a> </p> <a href="https://publications.waset.org/abstracts/97158/calculation-of-detection-efficiency-of-horizontal-large-volume-source-using-exvol-code" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/97158.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">185</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">6</span> Preparation of Nb Silicide-Based Alloy Powder by Hydrogenation-Dehydrogenation (HDH) Reaction</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Gi-Beom%20Park">Gi-Beom Park</a>, <a href="https://publications.waset.org/abstracts/search?q=Hyong-Gi%20Park"> Hyong-Gi Park</a>, <a href="https://publications.waset.org/abstracts/search?q=Seong-Yong%20Lee"> Seong-Yong Lee</a>, <a href="https://publications.waset.org/abstracts/search?q=Jaeho%20Choi"> Jaeho Choi</a>, <a href="https://publications.waset.org/abstracts/search?q=Seok%20Hong%20Min"> Seok Hong Min</a>, <a href="https://publications.waset.org/abstracts/search?q=Tae%20Kwon%20Ha"> Tae Kwon Ha</a> </p> <p class="card-text"><strong>Abstract:</strong></p> The Nb silicide-based alloy has the excellent high-temperature strength and relatively lower density than the Ni-based superalloy; therefore, it has been receiving a lot of attention for the next generation high-temperature material. To enhance the high temperature creep property and oxidation resistance, Si was added to the Nb-based alloy, resulting in a multi-phase microstructure with metal solid solution and silicide phase. Since the silicide phase has a low machinability due to its brittle nature, it is necessary to fabricate components using the powder metallurgy. However, powder manufacturing techniques for the alloys have not yet been developed. In this study, we tried to fabricate Nb-based alloy powder by the hydrogenation-dehydrogenation reaction. The Nb-based alloy ingot was prepared by vacuum arc melting and it was annealed in the hydrogen atmosphere for the hydrogenation. After annealing, the hydrogen concentration was increased from 0.004wt% to 1.22wt% and Nb metal phase was transformed to Nb hydride phase. The alloy after hydrogenation could be easily pulverized into powder by ball milling due to its brittleness. For dehydrogenation, the alloy powders were annealed in the vacuum atmosphere. After vacuum annealing, the hydrogen concentration was decreased to 0.003wt% and Nb hydride phase was transformed back to Nb metal phase. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=Nb%20alloy" title="Nb alloy">Nb alloy</a>, <a href="https://publications.waset.org/abstracts/search?q=Nb%20metal%20and%20silicide%20composite" title=" Nb metal and silicide composite"> Nb metal and silicide composite</a>, <a href="https://publications.waset.org/abstracts/search?q=powder" title=" powder"> powder</a>, <a href="https://publications.waset.org/abstracts/search?q=hydrogenation-dehydrogenation%20reaction" title=" hydrogenation-dehydrogenation reaction"> hydrogenation-dehydrogenation reaction</a> </p> <a href="https://publications.waset.org/abstracts/96692/preparation-of-nb-silicide-based-alloy-powder-by-hydrogenation-dehydrogenation-hdh-reaction" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/96692.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">244</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">5</span> Recrystallization Behavior and Microstructural Evolution of Nickel Base Superalloy AD730 Billet during Hot Forging at Subsolvus Temperatures</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Marcos%20Perez">Marcos Perez</a>, <a href="https://publications.waset.org/abstracts/search?q=Christian%20Dumont"> Christian Dumont</a>, <a href="https://publications.waset.org/abstracts/search?q=Olivier%20Nodin"> Olivier Nodin</a>, <a href="https://publications.waset.org/abstracts/search?q=Sebastien%20Nouveau"> Sebastien Nouveau</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Nickel superalloys are used to manufacture high-temperature rotary engine parts such as high-pressure disks in gas turbine engines. High strength at high operating temperatures is required due to the levels of stress and heat the disk must withstand. Therefore it is necessary parts made from materials that can maintain mechanical strength at high temperatures whilst remain comparatively low in cost. A manufacturing process referred to as the triple melt process has made the production of cast and wrought (C&W) nickel superalloys possible. This means that the balance of cost and performance at high temperature may be optimized. AD730TM is a newly developed Ni-based superalloy for turbine disk applications, with reported superior service properties around 700°C when compared to Inconel 718 and several other alloys. The cast ingot is converted into billet during either cogging process or open die forging. The semi-finished billet is then further processed into its final geometry by forging, heat treating, and machining. Conventional ingot-to-billet conversion is an expensive and complex operation, requiring a significant amount of steps to break up the coarse as-cast structure and interdendritic regions. Due to the size of conventional ingots, it is difficult to achieve a uniformly high level of strain for recrystallization, resulting in non-recrystallized regions that retain large unrecrystallized grains. Non-uniform grain distributions will also affect the ultrasonic inspectability response, which is used to find defects in the final component. The main aim is to analyze the recrystallization behavior and microstructural evolution of AD730 at subsolvus temperatures from a semi-finished product (billet) under conditions representative of both cogging and hot forging operations. Special attention to the presence of large unrecrystallized grains was paid. Double truncated cones (DTCs) were hot forged at subsolvus temperatures in hydraulic press, followed by air cooling. SEM and EBSD analysis were conducted in the as-received (billet) and the as-forged conditions. AD730 from billet alloy presents a complex microstructure characterized by a mixture of several constituents. Large unrecrystallized grains present a substructure characterized by large misorientation gradients with the formation of medium to high angle boundaries in their interior, especially close to the grain boundaries, denoting inhomogeneous strain distribution. A fine distribution of intragranular precipitates was found in their interior, playing a key role on strain distribution and subsequent recrystallization behaviour during hot forging. Continuous dynamic recrystallization (CDRX) mechanism was found to be operating in the large unrecrystallized grains, promoting the formation intragranular DRX grains and the gradual recrystallization of these grains. Evidences that hetero-epitaxial recrystallization mechanism is operating in AD730 billet material were found. Coherent γ-shells around primary γ’ precipitates were found. However, no significant contribution to the overall recrystallization during hot forging was found. By contrast, strain presents the strongest effect on the microstructural evolution of AD730, increasing the recrystallization fraction and refining the structure. Regions with low level of deformation (ε ≤ 0.6) were translated into large fractions of unrecrystallized structures (strain accumulation). The presence of undissolved secondary γ’ precipitates (pinning effect), prior to hot forging operations, could explain these results. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=AD730%20alloy" title="AD730 alloy">AD730 alloy</a>, <a href="https://publications.waset.org/abstracts/search?q=continuous%20dynamic%20recrystallization" title=" continuous dynamic recrystallization"> continuous dynamic recrystallization</a>, <a href="https://publications.waset.org/abstracts/search?q=hot%20forging" title=" hot forging"> hot forging</a>, <a href="https://publications.waset.org/abstracts/search?q=%CE%B3%E2%80%99%20precipitates" title=" γ’ precipitates"> γ’ precipitates</a> </p> <a href="https://publications.waset.org/abstracts/98142/recrystallization-behavior-and-microstructural-evolution-of-nickel-base-superalloy-ad730-billet-during-hot-forging-at-subsolvus-temperatures" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/98142.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">199</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">4</span> Making of Alloy Steel by Direct Alloying with Mineral Oxides during Electro-Slag Remelting</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Vishwas%20Goel">Vishwas Goel</a>, <a href="https://publications.waset.org/abstracts/search?q=Kapil%20Surve"> Kapil Surve</a>, <a href="https://publications.waset.org/abstracts/search?q=Somnath%20Basu"> Somnath Basu</a> </p> <p class="card-text"><strong>Abstract:</strong></p> In-situ alloying in steel during the electro-slag remelting (ESR) process has already been achieved by the addition of necessary ferroalloys into the electro-slag remelting mold. However, the use of commercially available ferroalloys during ESR processing is often found to be financially less favorable, in comparison with the conventional alloying techniques. However, a process of alloying steel with elements like chromium and manganese using the electro-slag remelting route is under development without any ferrochrome addition. The process utilizes in-situ reduction of refined mineral chromite (Cr₂O₃) and resultant enrichment of chromium in the steel ingot produced. It was established in course of this work that this process can become more advantageous over conventional alloying techniques, both economically and environmentally, for applications which inherently demand the use of the electro-slag remelting process, such as manufacturing of superalloys. A key advantage is the lower overall CO₂ footprint of this process relative to the conventional route of production, storage, and the addition of ferrochrome. In addition to experimentally validating the feasibility of the envisaged reactions, a mathematical model to simulate the reduction of chromium (III) oxide and transfer to chromium to the molten steel droplets was also developed as part of the current work. The developed model helps to correlate the amount of chromite input and the magnitude of chromium alloying that can be achieved through this process. Experiments are in progress to validate the predictions made by this model and to fine-tune its parameters. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=alloying%20element" title="alloying element">alloying element</a>, <a href="https://publications.waset.org/abstracts/search?q=chromite" title=" chromite"> chromite</a>, <a href="https://publications.waset.org/abstracts/search?q=electro-slag%20remelting" title=" electro-slag remelting"> electro-slag remelting</a>, <a href="https://publications.waset.org/abstracts/search?q=ferrochrome" title=" ferrochrome"> ferrochrome</a> </p> <a href="https://publications.waset.org/abstracts/92699/making-of-alloy-steel-by-direct-alloying-with-mineral-oxides-during-electro-slag-remelting" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/92699.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">223</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">3</span> Switching Studies on Ge15In5Te56Ag24 Thin Films</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Diptoshi%20Roy">Diptoshi Roy</a>, <a href="https://publications.waset.org/abstracts/search?q=G.%20Sreevidya%20Varma"> G. Sreevidya Varma</a>, <a href="https://publications.waset.org/abstracts/search?q=S.%20Asokan"> S. Asokan</a>, <a href="https://publications.waset.org/abstracts/search?q=Chandasree%20Das"> Chandasree Das </a> </p> <p class="card-text"><strong>Abstract:</strong></p> Germanium Telluride based quaternary thin film switching devices with composition Ge<sub>15</sub>In<sub>5</sub>Te<sub>56</sub>Ag<sub>24,</sub> have been deposited in sandwich geometry on glass substrate with aluminum as top and bottom electrodes. The bulk glassy form of the said composition is prepared by melt quenching technique. In this technique, appropriate quantity of elements with high purity are taken in a quartz ampoule and sealed under a vacuum of 10<sup>-5 </sup>mbar. Then, it is allowed to rotate in a horizontal rotary furnace for 36 hours to ensure homogeneity of the melt. After that, the ampoule is quenched into a mixture of ice - water and NaOH to get the bulk ingot of the sample. The sample is then coated on a glass substrate using flash evaporation technique at a vacuum level of 10<sup>-6 </sup>mbar. The XRD report reveals the amorphous nature of the thin film sample and Energy - Dispersive X-ray Analysis (EDAX) confirms that the film retains the same chemical composition as that of the base sample. Electrical switching behavior of the device is studied with the help of Keithley (2410<sup>c</sup>) source-measure unit interfaced with Lab VIEW 7 (National Instruments). Switching studies, mainly SET (changing the state of the material from amorphous to crystalline) operation is conducted on the thin film form of the sample. This device is found to manifest memory switching as the device remains 'ON' even after the removal of the electric field. Also it is found that amorphous Ge<sub>15</sub>In<sub>5</sub>Te<sub>56</sub>Ag<sub>24 </sub>thin film unveils clean memory type of electrical switching behavior which can be justified by the absence of fluctuation in the I-V characteristics. The I-V characteristic also reveals that the switching is faster in this sample as no data points could be seen in the negative resistance region during the transition to on state and this leads to the conclusion of fast phase change during SET process. Scanning Electron Microscopy (SEM) studies are performed on the chosen sample to study the structural changes at the time of switching. SEM studies on the switched Ge<sub>15</sub>In<sub>5</sub>Te<sub>56</sub>Ag<sub>24</sub> sample has shown some morphological changes at the place of switching wherein it can be explained that a conducting crystalline channel is formed in the device when the device switches from high resistance to low resistance state. From these studies it can be concluded that the material may find its application in fast switching Non-Volatile Phase Change Memory (PCM) Devices. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=Chalcogenides" title="Chalcogenides">Chalcogenides</a>, <a href="https://publications.waset.org/abstracts/search?q=Vapor%20deposition" title=" Vapor deposition"> Vapor deposition</a>, <a href="https://publications.waset.org/abstracts/search?q=Electrical%20switching" title=" Electrical switching"> Electrical switching</a>, <a href="https://publications.waset.org/abstracts/search?q=PCM." title=" PCM."> PCM.</a> </p> <a href="https://publications.waset.org/abstracts/43850/switching-studies-on-ge15in5te56ag24-thin-films" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/43850.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">377</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">2</span> Critical Conditions for the Initiation of Dynamic Recrystallization Prediction: Analytical and Finite Element Modeling</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Pierre%20Tize%20Mha">Pierre Tize Mha</a>, <a href="https://publications.waset.org/abstracts/search?q=Mohammad%20Jahazi"> Mohammad Jahazi</a>, <a href="https://publications.waset.org/abstracts/search?q=Am%C3%A8vi%20Togne"> Amèvi Togne</a>, <a href="https://publications.waset.org/abstracts/search?q=Olivier%20Pantal%C3%A9"> Olivier Pantalé</a> </p> <p class="card-text"><strong>Abstract:</strong></p> Large-size forged blocks made of medium carbon high-strength steels are extensively used in the automotive industry as dies for the production of bumpers and dashboards through the plastic injection process. The manufacturing process of the large blocks starts with ingot casting, followed by open die forging and a quench and temper heat treatment process to achieve the desired mechanical properties and numerical simulation is widely used nowadays to predict these properties before the experiment. But the temperature gradient inside the specimen remains challenging in the sense that the temperature before loading inside the material is not the same, but during the simulation, constant temperature is used to simulate the experiment because it is assumed that temperature is homogenized after some holding time. Therefore to be close to the experiment, real distribution of the temperature through the specimen is needed before the mechanical loading. Thus, We present here a robust algorithm that allows the calculation of the temperature gradient within the specimen, thus representing a real temperature distribution within the specimen before deformation. Indeed, most numerical simulations consider a uniform temperature gradient which is not really the case because the surface and core temperatures of the specimen are not identical. Another feature that influences the mechanical properties of the specimen is recrystallization which strongly depends on the deformation conditions and the type of deformation like Upsetting, Cogging...etc. Indeed, Upsetting and Cogging are the stages where the greatest deformations are observed, and a lot of microstructural phenomena can be observed, like recrystallization, which requires in-depth characterization. Complete dynamic recrystallization plays an important role in the final grain size during the process and therefore helps to increase the mechanical properties of the final product. Thus, the identification of the conditions for the initiation of dynamic recrystallization is still relevant. Also, the temperature distribution within the sample and strain rate influence the recrystallization initiation. So the development of a technique allowing to predict the initiation of this recrystallization remains challenging. In this perspective, we propose here, in addition to the algorithm allowing to get the temperature distribution before the loading stage, an analytical model leading to determine the initiation of this recrystallization. These two techniques are implemented into the Abaqus finite element software via the UAMP and VUHARD subroutines for comparison with a simulation where an isothermal temperature is imposed. The Artificial Neural Network (ANN) model to describe the plastic behavior of the material is also implemented via the VUHARD subroutine. From the simulation, the temperature distribution inside the material and recrystallization initiation is properly predicted and compared to the literature models. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=dynamic%20recrystallization" title="dynamic recrystallization">dynamic recrystallization</a>, <a href="https://publications.waset.org/abstracts/search?q=finite%20element%20modeling" title=" finite element modeling"> finite element modeling</a>, <a href="https://publications.waset.org/abstracts/search?q=artificial%20neural%20network" title=" artificial neural network"> artificial neural network</a>, <a href="https://publications.waset.org/abstracts/search?q=numerical%20implementation" title=" numerical implementation"> numerical implementation</a> </p> <a href="https://publications.waset.org/abstracts/166612/critical-conditions-for-the-initiation-of-dynamic-recrystallization-prediction-analytical-and-finite-element-modeling" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/166612.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">80</span> </span> </div> </div> <div class="card paper-listing mb-3 mt-3"> <h5 class="card-header" style="font-size:.9rem"><span class="badge badge-info">1</span> Characterization of Alloyed Grey Cast Iron Quenched and Tempered for a Smooth Roll Application</h5> <div class="card-body"> <p class="card-text"><strong>Authors:</strong> <a href="https://publications.waset.org/abstracts/search?q=Mohamed%20Habireche">Mohamed Habireche</a>, <a href="https://publications.waset.org/abstracts/search?q=Nacer%20E.%20Bacha"> Nacer E. Bacha</a>, <a href="https://publications.waset.org/abstracts/search?q=Mohamed%20Djeghdjough"> Mohamed Djeghdjough</a> </p> <p class="card-text"><strong>Abstract:</strong></p> In the brick industry, smooth double roll crusher is used for medium and fine crushing of soft to medium hard material. Due to opposite inward rotation of the rolls, the feed material is nipped between the rolls and crushed by compression. They are subject to intense wear, known as three-body abrasion, due to the action of abrasive products. The production downtime affecting productivity stems from two sources: the bi-monthly rectification of the roll crushers and their replacement when they are completely worn out. Choosing the right material for the roll crushers should result in longer machine cycles, and reduced repair and maintenance costs. All roll crushers are imported from outside Algeria. This results in sometimes very long delivery times which handicap the brickyards, in particular in respecting delivery times and honored the orders made by customers. The aim of this work is to investigate the effect of alloying additions on microstructure and wear behavior of grey lamellar cast iron for smooth roll crushers in brick industry. The base gray iron was melted in an induction furnace with low frequency at a temperature of 1500 °C, in which return cast iron scrap, new cast iron ingot, and steel scrap were added to the melt to generate the desired composition. The chemical analysis of the bar samples was carried out using Emission Spectrometer Systems PV 8050 Series (Philips) except for the carbon, for which a carbon/sulphur analyser Elementrac CS-i was used. Unetched microstructure was used to evaluate the graphite flake morphology using the image comparison measurement method. At least five different fields were selected for quantitative estimation of phase constituents. The samples were observed under X100 magnification with a Zeiss Axiover T40 MAT optical microscope equipped with a digital camera. SEM microscope equipped with EDS was used to characterize the phases present in the microstructure. The hardness (750 kg load, 5mm diameter ball) was measured with a Brinell testing machine for both treated and as-solidified condition test pieces. The test bars were used for tensile strength and metallographic evaluations. Mechanical properties were evaluated using tensile specimens made as per ASTM E8 standards. Two specimens were tested for each alloy. From each rod, a test piece was made for the tensile test. The results showed that the quenched and tempered alloys had best wear resistance at 400 °C for alloyed grey cast iron (containing 0.62%Mn, 0.68%Cr, and 1.09% Cu) due to fine carbides in the tempered matrix. In quenched and tempered condition, increasing Cu content in cast irons improved its wear resistance moderately. Combined addition of Cu and Cr increases hardness and wear resistance for a quenched and tempered hypoeutectic grey cast iron. <p class="card-text"><strong>Keywords:</strong> <a href="https://publications.waset.org/abstracts/search?q=casting" title="casting">casting</a>, <a href="https://publications.waset.org/abstracts/search?q=cast%20iron" title=" cast iron"> cast iron</a>, <a href="https://publications.waset.org/abstracts/search?q=microstructure" title=" microstructure"> microstructure</a>, <a href="https://publications.waset.org/abstracts/search?q=heat%20treating" title=" heat treating"> heat treating</a> </p> <a href="https://publications.waset.org/abstracts/127992/characterization-of-alloyed-grey-cast-iron-quenched-and-tempered-for-a-smooth-roll-application" class="btn btn-primary btn-sm">Procedia</a> <a href="https://publications.waset.org/abstracts/127992.pdf" target="_blank" class="btn btn-primary btn-sm">PDF</a> <span class="bg-info text-light px-1 py-1 float-right rounded"> Downloads <span class="badge badge-light">105</span> </span> </div> </div> </div> </main> <footer> <div id="infolinks" class="pt-3 pb-2"> <div class="container"> <div style="background-color:#f5f5f5;" class="p-3"> <div class="row"> <div class="col-md-2"> <ul class="list-unstyled"> About <li><a href="https://waset.org/page/support">About Us</a></li> <li><a href="https://waset.org/page/support#legal-information">Legal</a></li> <li><a target="_blank" rel="nofollow" href="https://publications.waset.org/static/files/WASET-16th-foundational-anniversary.pdf">WASET celebrates its 16th foundational anniversary</a></li> </ul> </div> <div class="col-md-2"> <ul class="list-unstyled"> Account <li><a href="https://waset.org/profile">My Account</a></li> </ul> </div> <div class="col-md-2"> <ul class="list-unstyled"> Explore <li><a href="https://waset.org/disciplines">Disciplines</a></li> <li><a href="https://waset.org/conferences">Conferences</a></li> <li><a href="https://waset.org/conference-programs">Conference Program</a></li> <li><a href="https://waset.org/committees">Committees</a></li> <li><a href="https://publications.waset.org">Publications</a></li> </ul> </div> <div class="col-md-2"> <ul class="list-unstyled"> Research <li><a href="https://publications.waset.org/abstracts">Abstracts</a></li> <li><a href="https://publications.waset.org">Periodicals</a></li> <li><a href="https://publications.waset.org/archive">Archive</a></li> </ul> </div> <div class="col-md-2"> <ul class="list-unstyled"> Open Science <li><a target="_blank" rel="nofollow" href="https://publications.waset.org/static/files/Open-Science-Philosophy.pdf">Open Science Philosophy</a></li> <li><a target="_blank" rel="nofollow" href="https://publications.waset.org/static/files/Open-Science-Award.pdf">Open Science Award</a></li> <li><a target="_blank" rel="nofollow" href="https://publications.waset.org/static/files/Open-Society-Open-Science-and-Open-Innovation.pdf">Open Innovation</a></li> <li><a target="_blank" rel="nofollow" href="https://publications.waset.org/static/files/Postdoctoral-Fellowship-Award.pdf">Postdoctoral Fellowship Award</a></li> <li><a target="_blank" rel="nofollow" href="https://publications.waset.org/static/files/Scholarly-Research-Review.pdf">Scholarly Research Review</a></li> </ul> </div> <div class="col-md-2"> <ul class="list-unstyled"> Support <li><a href="https://waset.org/page/support">Support</a></li> <li><a href="https://waset.org/profile/messages/create">Contact Us</a></li> <li><a href="https://waset.org/profile/messages/create">Report Abuse</a></li> </ul> </div> </div> </div> </div> </div> <div class="container text-center"> <hr style="margin-top:0;margin-bottom:.3rem;"> <a href="https://creativecommons.org/licenses/by/4.0/" target="_blank" class="text-muted small">Creative Commons Attribution 4.0 International License</a> <div id="copy" class="mt-2">© 2024 World Academy of Science, Engineering and Technology</div> </div> </footer> <a href="javascript:" id="return-to-top"><i class="fas fa-arrow-up"></i></a> <div class="modal" id="modal-template"> <div class="modal-dialog"> <div class="modal-content"> <div class="row m-0 mt-1"> <div class="col-md-12"> <button type="button" class="close" data-dismiss="modal" aria-label="Close"><span aria-hidden="true">×</span></button> </div> </div> <div class="modal-body"></div> </div> </div> </div> <script src="https://cdn.waset.org/static/plugins/jquery-3.3.1.min.js"></script> <script src="https://cdn.waset.org/static/plugins/bootstrap-4.2.1/js/bootstrap.bundle.min.js"></script> <script src="https://cdn.waset.org/static/js/site.js?v=150220211556"></script> <script> jQuery(document).ready(function() { /*jQuery.get("https://publications.waset.org/xhr/user-menu", function (response) { jQuery('#mainNavMenu').append(response); });*/ jQuery.get({ url: "https://publications.waset.org/xhr/user-menu", cache: false }).then(function(response){ jQuery('#mainNavMenu').append(response); }); }); </script> </body> </html>