Ternary Ni-P-Al alloy coating was fabricated by magnetron sputtering technique with a Ni-P/Al composite target source. The effects of thermal treatments, including deposition process heating and postannealing, on phase transformation phenomenon and related mechanical properties were investigated. The as-deposited coatings produced under process temperature below <svg style="vertical-align:-0.1575pt;width:34.537498px;" id="M1" height="10.075" version="1.1" viewBox="0 0 34.537498 10.075" width="34.537498"  xmlns="http://www.w3.org/2000/svg"    >
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</svg> showed an amorphous/nanocrystalline microstructure. Significant crystallization of Ni matrix and precipitation of <svg style="vertical-align:-4.25362pt;width:33.4375px;" id="M2" height="14.9875" version="1.1" viewBox="0 0 33.4375 14.9875" width="33.4375"  xmlns="http://www.w3.org/2000/svg"    >
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</svg> and <svg style="vertical-align:-4.25362pt;width:39.075001px;" id="M3" height="14.9875" version="1.1" viewBox="0 0 39.075001 14.9875" width="39.075001"  xmlns="http://www.w3.org/2000/svg"    >
	<g transform="matrix(1.25,0,0,-1.25,0,14.9875)">
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</svg> compounds were observed for the coatings manufactured under high sputtering temperatures above <svg style="vertical-align:-0.1575pt;width:34.537498px;" id="M4" height="10.075" version="1.1" viewBox="0 0 34.537498 10.075" width="34.537498"  xmlns="http://www.w3.org/2000/svg"    >
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</svg>. The amorphous Ni-P-Al coatings were postannealed from 500 to <svg style="vertical-align:-0.1575pt;width:34.537498px;" id="M5" height="10.025" version="1.1" viewBox="0 0 34.537498 10.025" width="34.537498"  xmlns="http://www.w3.org/2000/svg"    >
	<g transform="matrix(1.25,0,0,-1.25,0,10.025)">
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</svg> in vacuum environment for comparison. The amorphous feature of the Ni-P-Al coating remained unchanged under a high annealing temperature of <svg style="vertical-align:-0.1575pt;width:34.537498px;" id="M6" height="10.075" version="1.1" viewBox="0 0 34.537498 10.075" width="34.537498"  xmlns="http://www.w3.org/2000/svg"    >
	<g transform="matrix(1.25,0,0,-1.25,0,10.075)">
		<g transform="translate(72,-63.94)">
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				<tspan style="font-size: 11.21px; " x="0" y="0">5</tspan>
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				<tspan style="font-size: 11.21px; " x="11.208" y="0">0</tspan>
			</text>

			<text transform="matrix(1,0,0,-1,-55.14,68.91)">
				<tspan style="font-size: 7.85px; " x="0" y="0">∘</tspan>
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</svg>, showing a superior thermal stability as compared to those fabricated under high process temperatures. Superior hardness was obtained for the post-annealed Ni-P-Al coatings due to volumetric constraint of crystallization and precipitation. On the other hand, the overaging phenomenon and subsequent degradation in hardness were found for the Ni-P-Al coatings fabricated under high-temperature deposition processes. The phase transformation mechanisms of the coatings through different thermal treatments were intensively discussed.

Yu-Ming Su

Chia-Che Wu

Fan-Bean Wu

Process Heating and Postannealing Effects on Microstructure and Hardness of the Sputtered Ni-P-Al Coatings

Tracer diffusion in amorphous solid is studied by mean of <svg style="vertical-align:-3.27605pt;width:16.625px;" id="M1" height="11.825" version="1.1" viewBox="0 0 16.625 11.825" width="16.625" xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg"><g transform="matrix(.017,-0,0,-.017,.062,7.675)"><path id="x1D45B" d="M495 86q-46 -47 -87 -72.5t-63 -25.5q-43 0 -16 107l49 210q7 34 8 50.5t-3 21t-13 4.5q-35 0 -109.5 -72.5t-115.5 -140.5q-21 -75 -38 -159q-50 -10 -76 -21l-6 8l84 340q8 35 -4 35q-17 0 -67 -46l-15 26q44 44 85.5 70.5t64.5 26.5q35 0 10 -103l-24 -98h2&#xA;q42 56 97 103.5t96 71.5q46 26 74 26q9 0 16 -2.5t14 -11.5t9.5 -24.5t-1 -44t-13.5 -68.5q-30 -117 -47 -200q-4 -19 -3.5 -25t6.5 -6q21 0 70 48z" /></g><g transform="matrix(.012,-0,0,-.012,8.6,11.762)"><path id="x1D435" d="M594 511q0 -122 -171 -157l1 -2q158 -33 158 -159q0 -52 -34.5 -95t-90.5 -65q-76 -33 -217 -33h-223l8 28q63 5 79.5 19t26.5 72l83 426q9 48 -2.5 60t-77.5 17l6 28h259q195 0 195 -139zM499 509q0 59 -37 83t-91 24q-36 0 -51 -9q-17 -9 -22 -44l-35 -195h62&#xA;q82 0 128 37t46 104zM481 199q0 71 -48 102.5t-121 31.5h-56l-37 -201q-11 -58 7.5 -77t80.5 -19q76 0 125 44.5t49 118.5z" /></g></svg>-bubble statistic. The <svg style="vertical-align:-3.27605pt;width:16.625px;" id="M2" height="11.825" version="1.1" viewBox="0 0 16.625 11.825" width="16.625" xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg"><g transform="matrix(.017,-0,0,-.017,.062,7.675)"><use xlink:href="#x1D45B" /></g><g transform="matrix(.012,-0,0,-.012,8.6,11.762)"><use xlink:href="#x1D435" /></g></svg>-bubble is defined as a group of atoms around a spherical void and large bubble that represents a structural defect which could be eliminated under thermal annealing. 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603q-42 0 -67.5 -31t-25.5 -72q0 -50 32.5 -79.5&#xA;t98.5 -62.5q61 48 61 124q0 59 -29.5 90t-69.5 31zM248 20q46 0 76.5 33.5t30.5 89.5q0 50 -39 85.5t-110 71.5q-81 -54 -81 -137q0 -67 35.5 -105t87.5 -38z" /></g><g transform="matrix(.012,-0,0,-.012,21.661,15.187)"><use xlink:href="#x30" /></g><g transform="matrix(.017,-0,0,-.017,28,11.112)"><path id="x50" d="M46 650h247q112 0 169 -41q64 -49 64 -141q0 -91 -56.5 -143t-138.5 -62q-23 -3 -45 -1l-74 19v-157q0 -63 15.5 -77t83.5 -19v-28h-271v28q60 5 74 20t14 77v400q0 65 -12.5 79t-69.5 18v28zM212 559v-245q31 -12 73 -12q59 0 102 38t43 124q0 77 -42.5 115.5&#xA;t-108.5 38.5q-44 0 -56 -12q-11 -8 -11 -47z" /></g><g transform="matrix(.012,-0,0,-.012,37.575,15.187)"><path id="x32" d="M412 140l28 -9q0 -2 -35 -131h-373v23q112 112 161 170q59 70 92 127t33 115q0 63 -31 98t-86 35q-75 0 -137 -93l-22 20l57 81q55 59 135 59q69 0 118.5 -46.5t49.5 -122.5q0 -62 -29.5 -114t-102.5 -130l-141 -149h186q42 0 58.5 10.5t38.5 56.5z" /></g><g transform="matrix(.012,-0,0,-.012,43.286,15.187)"><use xlink:href="#x30" /></g></svg> suffer from a large number of vacancy bubbles which function like diffusion vehicle. The concentration of vacancy bubble weakly depends on temperature, but essentially on the relaxation degree of considered sample. The diffusion coefficient estimated for proposed mechanism via vacancy bubbles is in a reasonable agreement with experiment for actual amorphous alloys. The relaxation effect for tracer diffusion in amorphous alloys is interpreted by the elimination of vacancy bubbles under thermal annealing.

P. K. Hung

P. H. Kien

H. V. Hue

Tracer Diffusion Mechanism in Amorphous Solids

To verify the effect of composition on the bulk glass forming ability (BGFA) of Cu-based alloys, properties have been collected from the literature (<i  >&#x7e;</i>100 papers, more than 200 alloys). Surveying the BGFA criteria published so far, it has been found that the atomic mismatch condition of Egami-Waseda is fulfilled for all the Cu-based BGFAs, the <svg style="vertical-align:-0.18pt" id="M1" height="9.7124996" version="1.1" viewBox="0 0 7.6999998 9.7124996" width="7.6999998"  xmlns="http://www.w3.org/2000/svg"    >
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</svg> value being above 0,3. The Zhang Bangwei criterion could be applied for the binary Cu-based alloys. The Miracle and Senkov criteria do not necessarily apply for Cu based bulk amorphous alloys. The critical thickness versus <svg style="vertical-align:-4.28511pt" id="M2" height="14.9375" version="1.1" viewBox="0 0 92.574997 14.9375" width="92.574997"  xmlns="http://www.w3.org/2000/svg"    >
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			<text transform="matrix(1,0,0,-1,-71.95,64.28)">
				<tspan style="font-size: 11.21px; " x="0" y="0">𝛾</tspan>
				<tspan style="font-size: 11.21px; " x="8.7982798" y="0">=</tspan>
				<tspan style="font-size: 11.21px; " x="19.591583" y="0">0</tspan>
				<tspan style="font-size: 11.21px; " x="25.195583" y="0">.</tspan>
				<tspan style="font-size: 11.21px; " x="27.997583" y="0">3</tspan>
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</svg>, somewhat higher than the 0.33 value found in other BGFA alloys. The Park and Kim parameter correlates rather poorly with the critical thickness for Cu based alloys. The Cheney and Vecchino parameter is a good indicator to find the best glass former if it is possible to calculate the exact liquids projection. In 2009 Xiu-lin and Pan defined a new parameter which correlates a bit better with the critical thickness. Based on this survey it is still very difficult to find one parameter in order to characterize the real GFA without an unrealized mechanism of crystallization.

D. Janovszky

K. Tomolya

M. Sveda

A. Roosz

Survey of BGFA Criteria for the Cu-Based Bulk Amorphous Alloys

A dislocation model, accurately describing the uniaxial plastic stress-strain behavior of dual phase (DP) steels, is proposed and the impact of martensite content and ferrite grain size in four commercially produced DP steels is analyzed. It is assumed that the plastic deformation process is localized to the ferrite. This is taken into account by introducing a nonhomogeneity parameter, <svg style="vertical-align:-3.56265pt;width:29.775px;" id="M1" height="16.6625" version="1.1" viewBox="0 0 29.775 16.6625" width="29.775" xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg"><g transform="matrix(.017,-0,0,-.017,.062,12.162)"><path id="x1D453" d="M619 670q0 -13 -9 -26t-18 -19q-13 -10 -25 2q-36 38 -66 38q-31 0 -54.5 -50t-45.5 -185h120l-20 -31l-107 -12q-23 -138 -57 -293q-27 -122 -55 -184.5t-75 -109.5q-60 -61 -114 -61q-25 0 -47.5 15t-22.5 31q0 17 31 44q11 8 20 -1q10 -11 31 -19t35 -8q26 0 47 19&#xA;q34 34 71 253l54 315h-90l-3 12l31 30h70q28 138 90 204q35 37 75 57.5t70 20.5q26 0 45 -14t19 -28z" /></g><g transform="matrix(.017,-0,0,-.017,10.976,12.162)"><path id="x28" d="M300 -147l-18 -23q-106 71 -159 185.5t-53 254.5v1q0 139 53 252.5t159 186.5l18 -24q-74 -62 -115.5 -173.5t-41.5 -242.5q0 -130 41.5 -242.5t115.5 -174.5z" /></g><g transform="matrix(.017,-0,0,-.017,16.857,12.162)"><path id="x1D700" d="M387 375q0 -16 -17 -31t-29 -15q-9 0 -12 13q-13 74 -80 74q-36 0 -61 -24.5t-25 -56.5t24 -51.5t68 -19.5q33 0 47 2l2 -7l-32 -42q-20 2 -54 2q-45 0 -74 -21.5t-29 -60.5q0 -41 28 -65.5t73 -24.5q78 0 145 67l17 -23q-33 -47 -84.5 -75t-111.5 -28q-70 0 -114.5 35.5&#xA;t-44.5 92.5q0 46 38 78t95 45v2q-35 10 -54.5 33t-19.5 52q0 55 53 88.5t122 33.5q67 0 98.5 -23.5t31.5 -49.5z" /></g><g transform="matrix(.017,-0,0,-.017,23.827,12.162)"><path id="x29" d="M275 270q0 -296 -211 -440l-19 23q75 62 116.5 174t41.5 243t-42 243t-116 173l19 24q211 -144 211 -440z" /></g></svg>, that specifies the volume fraction of ferrite taking active part in the plastic deformation process. It is found that the larger the martensite content the smaller the initial volume fraction of active ferrite which yields a higher initial deformation hardening rate. This explains the high energy absorbing capacity of DP steels with high volume fractions of martensite.  Further, the effect of ferrite grain size strengthening in DP steels is important. The flow stress grain size sensitivity for DP steels is observed to be 7 times larger than that for single phase ferrite.

Yngve Bergstr&#xf6;m

Ylva Granbom

Dirk Sterkenburg

A Dislocation-Based Theory for the Deformation Hardening Behavior of DP Steels: Impact of Martensite Content and Ferrite Grain Size

Powder consolidation assisted by pulsed current and uniaxial pressure, namely, Spark Plasma Sintering (SPS), is increasingly popular. One limitation however lies in the difficulty of controlling the sample temperature during compaction. The aim of this work is to present a computational method for the assembly temperature based on the finite elements method (FEM). Computed temperatures have been compared with experimental data for three different dies filled with three materials with different electrical conductivities (TiAl, SiC, <svg style="vertical-align:-3.25793pt;width:39.224998px;" id="M1" height="14.8625" version="1.1" viewBox="0 0 39.224998 14.8625" width="39.224998"  xmlns="http://www.w3.org/2000/svg">
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				<tspan style="font-size: 12.50px; " x="0" y="0">A</tspan>
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			<text transform="matrix(1,0,0,-1,-59.45,60.28)">
				<tspan style="font-size: 8.75px; " x="0" y="0">2</tspan>
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			<text transform="matrix(1,0,0,-1,-54.57,63.41)">
				<tspan style="font-size: 12.50px; " x="0" y="0">O</tspan>
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</svg>). The results obtained are encouraging: the difference between computed and experimental values is less than 5&#x25;. This allows thinking about this FEM approach as a predictive tool for selecting the right control temperatures in the SPS machine.

G. Mol&#233;nat

L. Durand

J. Galy

A. Couret

Temperature Control in Spark Plasma Sintering: An FEM Approach

Protection of global environment and sustainable sources of clean water are a necessity for human survival. The wide use of heavy metals by modern industries has generated heavy metals containing wastes and by-products. Specifically, large quantities of arsenic compounds are being discharged into the environment. The full potential of Electrocoagulation (EC) with air injection as an alternative wastewater treatment technique to remove arsenic from water showed more than 99 percent of removal without adding any chemicals. This study has been carried out to determine the feasibility of arsenic adsorption on iron species by EC process using the Langmuir's Isotherm. Thermodynamic parameters such as <svg style="vertical-align:-0.0pt;width:30.9625px;" id="M1" height="12.9375" version="1.1" viewBox="0 0 30.9625 12.9375" width="30.9625" xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg"><g transform="matrix(.017,-0,0,-.017,.062,12.875)"><path id="x394" d="M600 0h-557v24l268 633l28 8l261 -641v-24zM497 50l-194 489l-196 -489h390z" /></g><g transform="matrix(.017,-0,0,-.017,10.959,12.875)"><path id="x1D43B" d="M865 650q-1 -4 -4 -14t-4 -14q-62 -5 -77 -19.5t-29 -82.5l-74 -394q-12 -61 -0.5 -77t75.5 -21l-6 -28h-273l8 28q64 5 82 21t29 76l36 198h-380l-37 -197q-11 -64 0.5 -78.5t79.5 -19.5l-6 -28h-268l6 28q60 6 75.5 21.5t26.5 76.5l75 394q13 66 2 81.5t-77 20.5l8 28&#xA;h263l-6 -28q-58 -5 -75.5 -21t-30.5 -81l-26 -153h377l29 153q12 67 2 81t-74 21l5 28h268z" /></g><g transform="matrix(.012,-0,0,-.012,25.862,4.712)"><path id="x2218" d="M326 255q0 -56 -41 -96t-99 -40t-99 40t-41 96t41 96t99 40t99 -40t41 -96zM274 255q0 38 -25.5 65t-62.5 27t-62.5 -27t-25.5 -65t25.5 -65t62.5 -27t62.5 27t25.5 65z" /></g></svg>, <svg style="vertical-align:-0.23206pt;width:24.2125px;" id="M2" height="13.225" version="1.1" viewBox="0 0 24.2125 13.225" width="24.2125" xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg"><g transform="matrix(.017,-0,0,-.017,.062,12.875)"><use xlink:href="#x394" /></g><g transform="matrix(.017,-0,0,-.017,10.959,12.875)"><path id="x1D446" d="M457 488l-30 -3q-17 148 -131 148q-53 0 -84.5 -34.5t-31.5 -82.5q0 -42 25.5 -72t74.5 -62l33 -22q63 -42 95 -85t32 -102q0 -84 -67 -137t-163 -53q-58 0 -113 22t-70 43l-4 152l27 4q4 -32 15 -62.5t31 -59.5t53.5 -47t76.5 -18q56 0 92 35t36 96q0 39 -25 70t-78 68&#xA;l-31 22q-32 23 -53.5 41.5t-45 57t-23.5 77.5q0 82 58 132.5t156 50.5q46 0 101 -17l18.5 -6t17 -6t8.5 -3q-4 -55 0 -147z" /></g><g transform="matrix(.012,-0,0,-.012,19.112,4.712)"><use xlink:href="#x2218" /></g></svg>, and <svg style="vertical-align:-0.23206pt;width:28.362499px;" id="M3" height="13.225" version="1.1" viewBox="0 0 28.362499 13.225" width="28.362499" xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg"><g transform="matrix(.017,-0,0,-.017,.062,12.875)"><use xlink:href="#x394" /></g><g transform="matrix(.017,-0,0,-.017,10.959,12.875)"><path id="x1D43A" d="M713 296l-5 -25q-47 -7 -59 -20t-23 -72l-15 -79q-9 -48 -3 -74q-15 -3 -55 -13t-63 -15t-59.5 -10t-70.5 -5q-149 0 -243 80t-94 220q0 169 127.5 276.5t336.5 107.5q91 0 206 -36l-10 -165l-29 -1q1 85 -47.5 126t-146.5 41q-153 0 -243.5 -97t-90.5 -242&#xA;q0 -122 68.5 -198.5t188.5 -76.5q121 0 139 75l20 86q13 58 -1.5 70.5t-99.5 20.5l5 26h267z" /></g><g transform="matrix(.012,-0,0,-.012,23.262,4.712)"><use xlink:href="#x2218" /></g></svg> were calculated. It was found that the adsorption process is exothermic and spontaneous. Some experiments were conducted to determine the optimum operating conditions such as current density, pH, and residence time. Also in this study, X-Ray Diffraction, Scanning Electron Microscopy, Mössbauer Spectroscopy, and Fourier Transform infrared spectroscopy were used to characterize the EC solid products that revealed the expected crystalline iron oxides (lepidocrocite, magnetite, gohetite, and iron oxide).

J. R. Parga

V. Vazquez

H. Moreno

Thermodynamic Studies of the Arsenic Adsorption on Iron Species Generated by Electrocoagulation

An experimental investigation into the oxidation kinetics of molten sulfide has been conducted at laboratory scale to provide information concerning the influence of the gas feed (flow and oxygen pressure) and melt temperature on the desulfurization rate. Data showed that the reaction rate was strongly dependent on the gas flow rate and significantly from oxygen pressure, whereas the influence of temperature was negligible. The variation of the sulfur conversion with the operation time was similar to that found in industrial trials when &#8220;white metal&#8221; was blown to blister copper in a Peirce-Smith converter. A unique equation for both scales could be established. This correlation made it possible to calculate the operation time in the converter at different gas flow rates and oxygen enrichments.

A. Rosell&#243;

J. Mart&#237;nez

F. Carrillo

A Kinetic Comparison between Laboratory and Industrial Scales in the Copper Blowing Process

In order to improve the surface quality and formability of 3003 aluminum alloy sheet, laser-textured rolls are used in cold rolling. The influences of the cold rolling procedures with conventional and laser-textured rolls on the evolution of microstructure and texture were studied by the means of microstructural observations and X-ray texture analysis. Experimental results show that the microstructures are similar besides the samples rolled with laser-textured rolls containing a relatively larger amount of shear bands. The sheets deformed with conventional rolls have developed the typical rolling textures of FCC metals, which consist of Bs, Cu, and S components. However, the rolling textures of the sheets rolled with laser-textured rolls are comparatively weak, and the shear texture <svg     style="vertical-align:-2.30685pt;width:74.925003px;" id="M1" height="15.05" version="1.1" viewBox="0 0 74.925003 15.05" width="74.925003"  xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg">
	
		
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</svg> is developed on the surface layer, but not observed in the intermediate layer of the sheet. The intensity of the rotated cube orientation increases with the increase of rolling reduction and then decreases after 90&#x25; rolling reduction.

Chunbo Cai

Zesheng Ji

Huajun Zhang

Guojun Wang

Study on the Microstructure and Texture of 3003 Aluminum Sheets Rolled by Laser-Textured Roll

Advanced Cu-40mass&#x25;Zn alloys with a high tensile strength and excellent machinability have been developed via a powder metallurgy (P/M) process. They are environmentally benign because fine graphite particles are included instead of lead (Pb) to improve their machinability. The effect of the content and particle size of the graphite on the mechanical properties and machinability are investigated in this paper. When applying a conventional P/M process consisting of the cold compaction and hot extrusion to consolidate elementally premixed mixture of Cu-40mass&#x25;Zn and graphite powder, the addition of 1 mass&#x25; graphite particles with <svg style="vertical-align:-0.17555pt;width:42.962502px;" id="M2" height="11.1" version="1.1" viewBox="0 0 42.962502 11.1" width="42.962502"  xmlns="http://www.w3.org/2000/svg">
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				<tspan style="font-size: 12.50px; " x="21.75522" y="0">1</tspan>
				<tspan style="font-size: 12.50px; " x="28.00672" y="0">0</tspan>
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</svg>&#x2009;<svg style="vertical-align:-2.29482pt;width:9.6374998px;" id="M3" height="9.6750002" version="1.1" viewBox="0 0 9.6374998 9.6750002" width="9.6374998"  xmlns="http://www.w3.org/2000/svg">
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</svg>m in diameter is suitable to obtain a high tensile strength and good machinability at the same time.

Katsuyoshi Kondoh

Hisashi Imai

Yoshiharu Kosaka

Akimichi Kojima

Junko Umeda

Machinable Cu-40<svg style="vertical-align:-0.43678pt" height="11.75" version="1.1" viewBox="0 0 12.975 11.75" width="12.975" xmlns:xlink="http://www.w3.org/1999/xlink" xmlns="http://www.w3.org/2000/svg"><g transform="matrix(.017,-0,0,-.017,.062,11.15)"><path id="x25" d="M594 629l-404 -661l-31 23l402 661zM194 635q70 0 107 -56t37 -125t-37.5 -125.5t-107.5 -56.5t-107 56.5t-37 124.5q0 70 37.5 126t107.5 56zM193 605q-28 0 -45 -29t-21.5 -59.5t-4.5 -62.5t4.5 -63t22 -60t45.5 -29q22 0 37.5 16t22 42t9 48t2.5 45q0 152 -72 152z&#xA;M567 351q69 0 106 -56t37 -125t-37 -125.5t-107 -56.5t-107.5 56.5t-37.5 124.5q0 43 14.5 83t49 69.5t82.5 29.5zM566 322q-28 0 -45 -28.5t-22 -59.5t-5 -64q0 -23 3 -46t10.5 -48.5t23 -41.5t36.5 -16q28 0 45 29.5t21 59.5t4 62q0 24 -2.5 46.5t-9.5 48.5t-22 42t-37 16&#xA;z" /></g></svg> Zn Composites Containing Graphite Particles by Powder Metallurgy Process

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