Journal of Mining and Metallurgy, Section B: Metallurgy
Journal of Mining and Metallurgy, Section B: Metallurgy -an international medium for the publication of contributions on the theory and practice of metallurgy
University of Belgrade, Technical Faculty in Bor
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Investigating the Al-Cr-La ternary system: Al-rich corner phase equilibria at 600 °C
The phase equilibria of the ternary Al-Cr-La system were investigated in the Al-rich corner at 600 °C, with a minimum Al content of 98.77 at.%. The formed phases, transformation temperatures (specifically liquidus and solidus), and microstructure evolution were experimentally determined by isothermal annealing at 600 °C for 600 hours and by Differential Scanning Calorimetry (DSC) analysis. A Scanning Electron Microscope (SEM) equipped with Energy-Dispersive X-ray Spectroscopy (EDXS) was used to fully characterize the samples. The equilibrium microstructure consists of (Al), the binary phase Al45Cr7, and the ternary phase LaCr2Al20 in samples with increased Cr content (from 0.03 up to 1.12 at.%), while it consists of (Al), the mixture (Al) + Al11La3, and the ternary LaCr2Al20 phase in samples with increased La content (from 0.03 up to 0.45 at.%). It was observed that even a small amount of alloying elements leads to the formation of the ternary phase.
Copyright (c) 2026 Journal of Mining and Metallurgy, Section B: Metallurgy
Influence of growth velocity v and temperature gradient G on the interlamellar spacing λ of FeC unidirectionally crystallized eutectic
The paper presents the results of investigations concerning the influence of growth velocity (v) and temperature gradient (G) on the interlamellar spacing (λ) in an irregular iron-carbon (Fe-C) eutectic unidirectionally crystallized. The aim of this study was to verify the growth model of D.J. Fisher and W. Kurz and to determine the relationship λ = f(v, G) based on experimental and numerical analysis. The crystallization process was carried out using the Bridgman-Stockbarger method with liquid metal cooling (LMC), and the structure was studied using optical microscopy and scanning electron microscopy. In parallel, numerical simulations were performed in ProCAST to determine the temperature gradient in the liquid at the crystallization front. The results showed that increasing the growth velocity at constant G leads to a decrease in interlamellar spacing λ, while at constant velocity a decrease in G results in an increase in λ. The experimental data obtained showed good agreement with the results of mathematical modelling, confirming the suitability of the W. Kurz and D.J. Fisher model in describing the crystallization of irregular Fe-C eutectic alloys.
Extraction and recovery of zinc, potassium, and sodium from blast furnace dust by ultrasonic-assisted ammonia leaching
To efficiently recover valuable elements (Zn, K, Na) from blast furnace dust (BFD) and address issues such as alkali metal enrichment and disrupted furnace operation caused by its direct reuse, ammonia leaching experiments were conducted in this study using an NH3·H2O–NH4HCO3 system combined with ultrasound and ammonium persulfate. Single-factor experiments were performed to investigate the effects of variables such as [NH3]T and solid-to-liquid ratio on the leaching efficiencies of Zn, K, and Na under ultrasonic conditions. Under the conditions of [NH3]T = 6 mol·L−1, a solid-to-liquid ratio of 1:6, [NH3]/[NH4+] = 1:1, 40 °C, and 90 W ultrasound power, the leaching efficiencies of Zn, K, and Na reached 90.73%, 91.45%, and 91.56%, respectively. Based on these results, the effect of ultrasound combined with 1 mol·L−1 ammonium persulfate on zinc leaching was further evaluated, and the Zn leaching efficiency increased to 95.16%, while the leaching efficiencies of K and Na slightly increased to 92.35% and 92.50%, respectively. The enhanced Zn leaching is reasonably attributed to the synergistic effects of ultrasonic intensification and persulfate oxidation, in which ultrasound promotes particle fragmentation and mass transfer, while activated ammonium persulfate generates SO4•⁻ radicals that facilitate the oxidation of refractory ZnS. Kinetic analysis indicated that Zn leaching was mainly controlled by the surface chemical reaction, and ultrasound reduced the apparent activation energy from 62.37 to 44.15 kJ·mol−1. This synergistic leaching process, with high selectivity and low cost, provides theoretical and technical references for BFD resource recovery.
A comparative study of mechanical behaviour of heat-treated 3D printed In-718 and ASTM F75 alloys across multiple length scales
The hardness and strength of many alloys often differ when measured at the nano, micro, and macroscopic scales. Therefore, it is essential to study the mechanical behavior of important alloys across a wide range of length scales. In this work, we present a scenario in which two industrially significant alloys, In-718 and ASTM F75, exhibit different behaviors at the micro and macroscopic levels. Both alloys are promising candidates for similar applications in the aerospace and petroleum industries. The alloys were first 3D printed using selective laser melting (SLM) and then heat-treated in a vacuum. The average yield strength and percentage elongation (along the build direction) of the In-718 alloy were 29% and 19% higher, respectively, than those observed for the ASTM F75 alloy. The difference between the ultimate tensile strength (UTS) and Vickers hardness (at a load of 98 N) was almost negligible, i.e., less than 5%. In contrast to the Vickers hardness values of 3.9 GPa and 3.8 GPa, the average nanohardness of the In-718 and ASTM F75 alloys was 5.7 GPa and 7.6 GPa, respectively, which was substantially higher than their Vickers hardness. Furthermore, the ASTM F75 alloy demonstrated much better wear resistance in ScanningWear tests performed using a nanoindenter. The explanation for these differences and the similarities between macro- and nanomechanical behavior are presented in this work.
Structure, mechanical properties, and corrosion resistance of low-nickel nitrogen-alloyed austenite stainless steel
This study investigates the structure, mechanical properties, and corrosion resistance of low-nickel nitrogen-alloyed austenitic stainless steels (Cr17Mn9Ni3N, 05Cr18Mn10Ni3N) as cost-effective alternatives to conventional AISI 304L and AISI 321 grades. The alloys were produced by vacuum induction melting with nitrogen introduced via nitrided ferrochrome. Microstructural analysis confirmed fully austenitic structures with finer grain sizes (ASTM No. 4.5–6.0) compared to conventional steels (ASTM No. 3.5–4.0). Mechanical testing revealed superior yield strength (~414 MPa) and tensile strength (~730–748 MPa) in nitrogen-alloyed steels, attributed to solid-solution strengthening by nitrogen. However, the impact toughness at cryogenic temperatures (-196°C) was reduced, and brittle facets were found on the fracture surface. Potentiodynamic polarization tests showed that AISI 304L steel exhibited a higher pitting potential. The pitting potentials of Cr17Mn9Ni3N and 05Cr18Mn10Ni3N steels were lower than that of AISI 304L but higher than that of AISI 321 steel. Economic analysis highlighted significant cost savings potential through nickel substitution with nitrogen. The results validate nitrogen-alloyed steels as viable alternatives for applications requiring high strength and corrosion resistance, though cryogenic applications require careful nickel content optimization.
Aluminium thermal reduction process for preparing ferrosilicon and alumina from fly ash
There has been a focus on environmental protection and the recycling of solid waste resources, particularly fly ash and aluminum dross. Efforts to utilize fly ash efficiently have increased. In this paper, a process is introduced for producing alumina-rich slag and ferrosilicon alloy through aluminothermic reduction of fly ash with aluminium dross. Scanning electron microscopy (SEM) and energy dispersive spectroscopy (EDS) confirm the formation of spherical ferrosilicon alloy encased in a loose, porous alumina matrix during the aluminothermic reduction process. Thermodynamic calculations indicated that the reduction temperature of SiO2 and mullite decreases in the presence of Fe2O3. Under conditions of 1673 K, a specific aluminium dross to fly ash ratio (A/F), and a reduction time of 20 minutes, the magnetic fraction contains 85.89% ferrosilicon, while the non-magnetic fraction has an alumina content of 79.42%. This process offers a solution with potential environmental and economic benefits for the application of fly ash and aluminum ash.
Effects of scanning speed on mechanical, wear property, and corrosion behavior of CP-Ti fabricated by the selective laser melting technique
In this study, CP-Ti was prepared using the selective laser melting (SLM) technique to systematically investigate the effect of scanning speed on microstructure, mechanical properties, wear properties, and corrosion behavior. The optimum relative density of 99.87±0.12% was achieved at a scanning speed of 800 mm/s, with corresponding tensile strength, yield strength, elongation, and hardness values of 543±17 MPa, 453±7 MPa, 14±1%, and 294±4 HV, respectively. Additionally, SLM-processed CP-Ti with optimum relative density exhibited the lowest wear rate (2.72×10-7 mm2/N) and excellent corrosion resistance. These results indicate that CP-Ti with high relative density, strength, and hardness, low wear rate, and excellent corrosion resistance can be fabricated by controlling the scanning speed, making it well-suited for biomedical implant applications.
Optimization of smelting process of magnesium based on machine learning
The traditional magnesium reduction process consumes a significant amount of energy, which contradicts China’s green and low-carbon development goals. Therefore, exploring more energy-efficient methods is crucial for environmental protection. The magnesium reduction rate is influenced by several factors, including gas flow rate, briquetting pressure, ferrosilicon content, reduction temperature, and reduction time. In this study, data analysis utilizing a machine learning algorithm: support vector machine (SVM)—was employed to predict the magnesium reduction rate. Given that energy-saving processes are a primary objective for enterprises, the processing was optimized using the particle swarm optimization (PSO) algorithm based on the SVM model, while maintaining a constant magnesium reduction rate. This optimization aims to reduce energy and gas consumption during the magnesium smelting process. Experimental verification of the magnesium reduction rate under the optimized processing conditions demonstrated that the application of machine learning algorithms can lead to resource savings in the magnesium reduction process. To further evaluate the environmental benefits of the optimized process, a Life Cycle Assessment (LCA) focusing on energy consumption and carbon dioxide (CO2) emissions was conducted. The LCA results indicate that the optimized process significantly reduces life cycle energy consumption (reduced by 5.33%) and CO2 emissions (reduced by 3.63%) compared with the initial process, providing precise environmental performance data for the promotion and application of magnesium alloys in lightweight structures.
Phase and roughness analysis of nanocrystalline coatings based on 310S steel with aluminum additions
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Name="List Table 7 Colorful Accent 6"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Mention"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Smart Hyperlink"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Hashtag"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Unresolved Mention"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Smart Link"/> </w:LatentStyles> </xml><![endif]--><!-- [if gte mso 10]> <![endif]--> Aluminum alloying is commonly used to improve high-temperature oxidation resistance. In this study, Al was incorporated into nanocrystalline coatings produced by magnetron sputtering of 310S chromium–nickel steel. The effect of this addition on the phase composition and morphology of the coatings, which influence the formation of protective oxide layers under high-temperature conditions, was investigated. The coatings were analyzed using scanning electron microscopy (SEM) and atomic force microscopy (AFM), with emphasis on surface roughness, as well as X-ray diffractometry (XRD) to determine crystallite size and phase composition. The results showed that the addition of aluminum affects phase stability in the coatings. At Al contents of 1–2 at.%, there is a twofold reduction in the fraction of the fcc phase in the coating (and its disappearance at 5 at.%), along with a similar decrease in surface roughness. At the same time, crystallite size increases while the nanocrystalline structure is retained, creating favorable conditions for the formation of dense Al₂O₃ oxide layers on the coatings.
Influence of holding time during rapid tempering after rapid austenitization on the microstructure and mechanical properties of low carbon steel
The rising demand for high-quality steel in construction, automotive, and other industrial sectors presents significant challenges, particularly regarding energy consumption and CO₂ emissions from large-scale production. This study explores the use of rapid tempering as a heat treatment strategy to enhance the mechanical properties of low carbon steel while potentially reducing the environmental footprint of steel manufacturing. Rapid tempering was performed following rapid austenitization at 1000 °C for 90 seconds using a 7-kW induction furnace, followed by quenching in ice water. Soaking times of 5, 15, and 20 seconds were applied during tempering, and results were compared with conventional heat treatment. The rapid tempering process resulted in a microstructure consisting of tempered martensite, with only slight morphological changes in the martensitic phase compared to conventional tempering, and the formation of markedly finer cementite precipitates. Mechanical testing demonstrated superior performance in rapid tempering, with the 5-second condition achieving the highest hardness (422.667 HV), tensile strength (1308.9 MPa), and yield strength (1270 MPa), while the 20-second condition yielded the highest toughness (139.336 J/cm²) and elongation (33.833%). Based on the balance among tensile strength, hardness, and toughness, the RA-RT 5- second specimen exhibited the most optimal mechanical performance.
Evolution of microstructure under different homogenization conditions and its effect on recrystallization processes during hot rolling of AA5182 alloy
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SemiHidden="true" UnhideWhenUsed="true" Name="toc 6"/> <w:LsdException Locked="false" Priority="39" SemiHidden="true" UnhideWhenUsed="true" Name="toc 7"/> <w:LsdException Locked="false" Priority="39" SemiHidden="true" UnhideWhenUsed="true" Name="toc 8"/> <w:LsdException Locked="false" Priority="39" SemiHidden="true" UnhideWhenUsed="true" Name="toc 9"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Normal Indent"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="footnote text"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="annotation text"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="header"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="footer"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="index heading"/> <w:LsdException Locked="false" Priority="35" SemiHidden="true" UnhideWhenUsed="true" QFormat="true" Name="caption"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="table of figures"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="envelope address"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="envelope return"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="footnote reference"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="annotation reference"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="line number"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="page number"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="endnote reference"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="endnote text"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="table of authorities"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="macro"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="toa heading"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List Bullet"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List Number"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List 2"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List 3"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List 4"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List 5"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List Bullet 2"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List Bullet 3"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List Bullet 4"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List Bullet 5"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List Number 2"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List Number 3"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List Number 4"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List Number 5"/> <w:LsdException Locked="false" Priority="10" QFormat="true" Name="Title"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Closing"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Signature"/> <w:LsdException Locked="false" Priority="1" SemiHidden="true" UnhideWhenUsed="true" Name="Default Paragraph Font"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Body Text"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Body Text Indent"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List Continue"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List Continue 2"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List Continue 3"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List Continue 4"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="List Continue 5"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Message Header"/> <w:LsdException Locked="false" Priority="11" QFormat="true" Name="Subtitle"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Salutation"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Date"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Body Text First Indent"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Body Text First Indent 2"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Note Heading"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Body Text 2"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Body Text 3"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Body Text Indent 2"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Body Text Indent 3"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Block Text"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Hyperlink"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="FollowedHyperlink"/> <w:LsdException Locked="false" Priority="22" QFormat="true" Name="Strong"/> <w:LsdException Locked="false" Priority="20" QFormat="true" Name="Emphasis"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Document Map"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Plain Text"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="E-mail Signature"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="HTML Top of Form"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="HTML Bottom of Form"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Normal (Web)"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="HTML Acronym"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="HTML Address"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="HTML Cite"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="HTML Code"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="HTML Definition"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="HTML Keyboard"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="HTML Preformatted"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="HTML Sample"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="HTML Typewriter"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="HTML Variable"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Normal Table"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="annotation subject"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="No List"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Outline List 1"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Outline List 2"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Outline List 3"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Simple 1"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Simple 2"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Simple 3"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Classic 1"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Classic 2"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Classic 3"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Classic 4"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Colorful 1"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Colorful 2"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Colorful 3"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Columns 1"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Columns 2"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Columns 3"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Columns 4"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Columns 5"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Grid 1"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Grid 2"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Grid 3"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Grid 4"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Grid 5"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Grid 6"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Grid 7"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Grid 8"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table List 1"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table List 2"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table List 3"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table List 4"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table List 5"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table List 6"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table List 7"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table List 8"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table 3D effects 1"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table 3D effects 2"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table 3D effects 3"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Contemporary"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Elegant"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Professional"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Subtle 1"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Subtle 2"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Web 1"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Web 2"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Web 3"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Balloon Text"/> <w:LsdException Locked="false" Priority="39" Name="Table Grid"/> <w:LsdException Locked="false" SemiHidden="true" UnhideWhenUsed="true" Name="Table Theme"/> <w:LsdException Locked="false" SemiHidden="true" Name="Placeholder Text"/> <w:LsdException Locked="false" Priority="1" QFormat="true" Name="No Spacing"/> <w:LsdException Locked="false" Priority="60" Name="Light Shading"/> <w:LsdException Locked="false" Priority="61" Name="Light List"/> <w:LsdException Locked="false" Priority="62" Name="Light Grid"/> <w:LsdException Locked="false" Priority="63" Name="Medium Shading 1"/> <w:LsdException Locked="false" Priority="64" Name="Medium Shading 2"/> <w:LsdException Locked="false" Priority="65" Name="Medium List 1"/> <w:LsdException Locked="false" Priority="66" Name="Medium List 2"/> <w:LsdException Locked="false" Priority="67" Name="Medium Grid 1"/> <w:LsdException Locked="false" Priority="68" Name="Medium Grid 2"/> <w:LsdException Locked="false" Priority="69" Name="Medium Grid 3"/> <w:LsdException Locked="false" Priority="70" Name="Dark List"/> <w:LsdException Locked="false" Priority="71" Name="Colorful Shading"/> <w:LsdException Locked="false" Priority="72" Name="Colorful List"/> <w:LsdException Locked="false" Priority="73" Name="Colorful Grid"/> <w:LsdException Locked="false" Priority="60" Name="Light Shading Accent 1"/> <w:LsdException Locked="false" Priority="61" Name="Light List Accent 1"/> <w:LsdException Locked="false" Priority="62" Name="Light Grid Accent 1"/> <w:LsdException Locked="false" Priority="63" Name="Medium Shading 1 Accent 1"/> <w:LsdException Locked="false" Priority="64" Name="Medium Shading 2 Accent 1"/> <w:LsdException Locked="false" Priority="65" Name="Medium List 1 Accent 1"/> <w:LsdException Locked="false" SemiHidden="true" Name="Revision"/> <w:LsdException Locked="false" Priority="34" QFormat="true" Name="List Paragraph"/> <w:LsdException Locked="false" Priority="29" QFormat="true" Name="Quote"/> <w:LsdException Locked="false" Priority="30" QFormat="true" Name="Intense Quote"/> <w:LsdException Locked="false" Priority="66" Name="Medium List 2 Accent 1"/> <w:LsdException Locked="false" Priority="67" Name="Medium Grid 1 Accent 1"/> <w:LsdException Locked="false" Priority="68" Name="Medium Grid 2 Accent 1"/> <w:LsdException Locked="false" Priority="69" Name="Medium Grid 3 Accent 1"/> <w:LsdException Locked="false" Priority="70" Name="Dark List Accent 1"/> <w:LsdException Locked="false" Priority="71" Name="Colorful Shading Accent 1"/> <w:LsdException Locked="false" Priority="72" Name="Colorful List Accent 1"/> <w:LsdException Locked="false" Priority="73" Name="Colorful Grid Accent 1"/> <w:LsdException Locked="false" Priority="60" Name="Light Shading Accent 2"/> <w:LsdException Locked="false" Priority="61" Name="Light List Accent 2"/> <w:LsdException Locked="false" Priority="62" Name="Light Grid Accent 2"/> <w:LsdException Locked="false" Priority="63" Name="Medium Shading 1 Accent 2"/> <w:LsdException Locked="false" Priority="64" Name="Medium Shading 2 Accent 2"/> <w:LsdException Locked="false" Priority="65" Name="Medium List 1 Accent 2"/> <w:LsdException Locked="false" Priority="66" Name="Medium List 2 Accent 2"/> <w:LsdException Locked="false" Priority="67" Name="Medium Grid 1 Accent 2"/> <w:LsdException Locked="false" Priority="68" Name="Medium Grid 2 Accent 2"/> <w:LsdException Locked="false" Priority="69" Name="Medium Grid 3 Accent 2"/> <w:LsdException Locked="false" Priority="70" Name="Dark List Accent 2"/> <w:LsdException Locked="false" Priority="71" Name="Colorful Shading Accent 2"/> <w:LsdException Locked="false" Priority="72" Name="Colorful List Accent 2"/> <w:LsdException Locked="false" Priority="73" Name="Colorful Grid Accent 2"/> <w:LsdException Locked="false" Priority="60" Name="Light Shading Accent 3"/> <w:LsdException Locked="false" Priority="61" Name="Light List Accent 3"/> <w:LsdException Locked="false" Priority="62" Name="Light Grid Accent 3"/> <w:LsdException Locked="false" Priority="63" Name="Medium Shading 1 Accent 3"/> <w:LsdException Locked="false" Priority="64" Name="Medium Shading 2 Accent 3"/> <w:LsdException Locked="false" Priority="65" Name="Medium List 1 Accent 3"/> <w:LsdException Locked="false" Priority="66" Name="Medium List 2 Accent 3"/> <w:LsdException Locked="false" Priority="67" Name="Medium Grid 1 Accent 3"/> <w:LsdException Locked="false" Priority="68" Name="Medium Grid 2 Accent 3"/> <w:LsdException Locked="false" Priority="69" Name="Medium Grid 3 Accent 3"/> <w:LsdException Locked="false" Priority="70" Name="Dark List Accent 3"/> <w:LsdException Locked="false" Priority="71" Name="Colorful Shading Accent 3"/> <w:LsdException Locked="false" Priority="72" Name="Colorful List Accent 3"/> <w:LsdException Locked="false" Priority="73" Name="Colorful Grid Accent 3"/> <w:LsdException Locked="false" Priority="60" Name="Light Shading Accent 4"/> <w:LsdException Locked="false" Priority="61" Name="Light List Accent 4"/> <w:LsdException Locked="false" Priority="62" Name="Light Grid Accent 4"/> <w:LsdException Locked="false" Priority="63" Name="Medium Shading 1 Accent 4"/> <w:LsdException Locked="false" Priority="64" Name="Medium Shading 2 Accent 4"/> <w:LsdException Locked="false" Priority="65" Name="Medium List 1 Accent 4"/> <w:LsdException Locked="false" Priority="66" Name="Medium List 2 Accent 4"/> <w:LsdException Locked="false" Priority="67" Name="Medium Grid 1 Accent 4"/> <w:LsdException Locked="false" Priority="68" Name="Medium Grid 2 Accent 4"/> <w:LsdException Locked="false" Priority="69" Name="Medium Grid 3 Accent 4"/> <w:LsdException Locked="false" Priority="70" Name="Dark List Accent 4"/> <w:LsdException Locked="false" Priority="71" Name="Colorful Shading Accent 4"/> <w:LsdException Locked="false" Priority="72" Name="Colorful List Accent 4"/> <w:LsdException Locked="false" Priority="73" Name="Colorful Grid Accent 4"/> <w:LsdException Locked="false" Priority="60" Name="Light Shading Accent 5"/> <w:LsdException Locked="false" Priority="61" Name="Light List Accent 5"/> <w:LsdException Locked="false" Priority="62" Name="Light Grid Accent 5"/> <w:LsdException Locked="false" Priority="63" Name="Medium Shading 1 Accent 5"/> <w:LsdException Locked="false" Priority="64" Name="Medium Shading 2 Accent 5"/> <w:LsdException Locked="false" Priority="65" Name="Medium List 1 Accent 5"/> <w:LsdException Locked="false" Priority="66" Name="Medium List 2 Accent 5"/> <w:LsdException Locked="false" Priority="67" Name="Medium Grid 1 Accent 5"/> <w:LsdException Locked="false" Priority="68" Name="Medium Grid 2 Accent 5"/> <w:LsdException Locked="false" Priority="69" Name="Medium Grid 3 Accent 5"/> <w:LsdException Locked="false" Priority="70" Name="Dark List Accent 5"/> <w:LsdException Locked="false" Priority="71" Name="Colorful Shading Accent 5"/> <w:LsdException Locked="false" Priority="72" Name="Colorful List Accent 5"/> <w:LsdException Locked="false" Priority="73" Name="Colorful Grid Accent 5"/> <w:LsdException Locked="false" Priority="60" Name="Light Shading Accent 6"/> <w:LsdException Locked="false" Priority="61" Name="Light List Accent 6"/> <w:LsdException Locked="false" Priority="62" Name="Light Grid Accent 6"/> <w:LsdException Locked="false" Priority="63" Name="Medium Shading 1 Accent 6"/> <w:LsdException Locked="false" Priority="64" Name="Medium Shading 2 Accent 6"/> <w:LsdException Locked="false" Priority="65" Name="Medium List 1 Accent 6"/> <w:LsdException Locked="false" Priority="66" Name="Medium List 2 Accent 6"/> <w:LsdException Locked="false" Priority="67" Name="Medium Grid 1 Accent 6"/> <w:LsdException Locked="false" Priority="68" Name="Medium Grid 2 Accent 6"/> <w:LsdException Locked="false" Priority="69" Name="Medium Grid 3 Accent 6"/> <w:LsdException Locked="false" Priority="70" Name="Dark List Accent 6"/> <w:LsdException Locked="false" Priority="71" Name="Colorful Shading Accent 6"/> <w:LsdException Locked="false" Priority="72" Name="Colorful List Accent 6"/> <w:LsdException Locked="false" Priority="73" Name="Colorful Grid Accent 6"/> <w:LsdException Locked="false" Priority="19" QFormat="true" Name="Subtle Emphasis"/> <w:LsdException Locked="false" Priority="21" QFormat="true" Name="Intense Emphasis"/> <w:LsdException Locked="false" Priority="31" QFormat="true" Name="Subtle Reference"/> <w:LsdException Locked="false" Priority="32" QFormat="true" Name="Intense Reference"/> <w:LsdException Locked="false" Priority="33" QFormat="true" Name="Book Title"/> <w:LsdException Locked="false" Priority="37" SemiHidden="true" UnhideWhenUsed="true" Name="Bibliography"/> <w:LsdException Locked="false" Priority="39" SemiHidden="true" UnhideWhenUsed="true" QFormat="true" Name="TOC Heading"/> <w:LsdException Locked="false" Priority="41" Name="Plain Table 1"/> <w:LsdException Locked="false" Priority="42" Name="Plain Table 2"/> <w:LsdException Locked="false" Priority="43" Name="Plain Table 3"/> <w:LsdException Locked="false" Priority="44" Name="Plain Table 4"/> <w:LsdException Locked="false" Priority="45" Name="Plain Table 5"/> <w:LsdException Locked="false" Priority="40" Name="Grid Table Light"/> <w:LsdException Locked="false" Priority="46" Name="Grid Table 1 Light"/> <w:LsdException Locked="false" Priority="47" Name="Grid Table 2"/> <w:LsdException Locked="false" Priority="48" Name="Grid Table 3"/> <w:LsdException Locked="false" Priority="49" Name="Grid Table 4"/> <w:LsdException Locked="false" Priority="50" Name="Grid Table 5 Dark"/> <w:LsdException Locked="false" Priority="51" Name="Grid Table 6 Colorful"/> <w:LsdException Locked="false" Priority="52" Name="Grid Table 7 Colorful"/> <w:LsdException Locked="false" Priority="46" Name="Grid Table 1 Light Accent 1"/> <w:LsdException Locked="false" 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Accent 4"/> <w:LsdException Locked="false" Priority="46" Name="List Table 1 Light Accent 5"/> <w:LsdException Locked="false" Priority="47" Name="List Table 2 Accent 5"/> <w:LsdException Locked="false" Priority="48" Name="List Table 3 Accent 5"/> <w:LsdException Locked="false" Priority="49" Name="List Table 4 Accent 5"/> <w:LsdException Locked="false" Priority="50" Name="List Table 5 Dark Accent 5"/> <w:LsdException Locked="false" Priority="51" Name="List Table 6 Colorful Accent 5"/> <w:LsdException Locked="false" Priority="52" Name="List Table 7 Colorful Accent 5"/> <w:LsdException Locked="false" Priority="46" Name="List Table 1 Light Accent 6"/> <w:LsdException Locked="false" Priority="47" Name="List Table 2 Accent 6"/> <w:LsdException Locked="false" Priority="48" Name="List Table 3 Accent 6"/> <w:LsdException Locked="false" Priority="49" Name="List Table 4 Accent 6"/> <w:LsdException Locked="false" Priority="50" Name="List Table 5 Dark Accent 6"/> <w:LsdException Locked="false" Priority="51" Name="List Table 6 Colorful Accent 6"/> <w:LsdException Locked="false" Priority="52" Name="List Table 7 Colorful Accent 6"/> </w:LatentStyles> </xml><![endif]--><!-- [if gte mso 10]> <![endif]-->This study investigates microstructure development of AA5182 Al-Mg alloy under various homogenization conditions and how these conditions affect recrystallization processes and texture development during the laboratory hot-rolling. Homogenization treatments were conducted for 16 h at 490°C and at 550°C for various times. Scanning electron microscopy (SEM) characterization including energy-dispersive X-ray spectroscopy (EDX) revealed the presence of Al3(Fe,Mn) and Alm(Fe,Mn) phases as Fe/Mn-bearing microconstituents in as-cast state. These transformed into Al6(Fe,Mn) and α-Al(Fe,Mn)Si during homogenization treatments. The treatments also led to precipitation of Al6(Mn,Fe) and α-Al(Fe,Mn)Si dispersoid particles. Results of electron backscattered diffraction (EBSD) indicated that a weak deformation texture was present after the hot-rolling. The morphology of grains and degree of restoration were significantly influenced by homogenization conditions. The distribution and density of dispersoids had a strong effect on the mechanisms of recovery and recrystallization.
Copyright (c) 2025 Journal of Mining and Metallurgy, Section B: Metallurgy
Algorithm to optimize thermodynamic parameters: A review
Computational thermodynamics provides essential information for materials design. The CALPHAD (CALculation of PHAse Diagrams) method based on thermodynamic databases can be used for thermodynamic optimization and for calculating phase diagrams and thermodynamic properties in multicomponent systems. This article reviews the algorithms implemented in software for optimizing thermodynamic parameters. These software tools offer strong support for developing accurate thermodynamic databases. Recent advances in software and algorithms for thermodynamic parameter optimization are summarized, and their respective characteristics and potential limitations are analyzed. Finally, the development trends of software and algorithms for thermodynamic parameter optimization are discussed. This review will help interested readers understand the principles of thermodynamic optimization and contribute to the advancement of related algorithms.
Dissolution kinetic mechanisms of FeCr₂O₄ spinel in MgO-Al₂O₃-SiO₂ slag system: Elemental dissolution and component diffusion
The molten chromite reduction direct alloying process serves as a pivotal metallurgical technology in stainless steel production, offering advantages such as reduced carbon consumption and improved production efficiency. In this study, to reveal the dissolution mechanism of chromite, pure phase of synthetic FeCr2O4, the main component of chromite, was used to replace chromite with complex compositions. The dissolution kinetics of FeCr2O4 in MgO-Al2O3-SiO2 slag were systematically investigated as functions of stirring intensity, MgO/ SiO2, and temperature, revealing its non-isothermal reactive dissolution characteristics. Experimental results demonstrated that the solubility of Cr2O3 exhibited a trend of initial increase followed by subsequent decrease as the MgO/SiO2 mass ratio increased. The maximum solubility was observed at a MgO/SiO2 mass ratio of 0.56. Additionally, temperature-related studies indicated that the dissolution of FeCr2O4 is progressively enhanced with increasing temperature under elevated thermal conditions (1500-1600 ℃). Meanwhile, scanning electron microscopy (SEM) analyses confirmed that the interfacial reaction between FeCr2O4 and slag components generated MgAl2O4, MgCr2O4 and MgO-xFeO solid solution, forming a boundary layer on the surface of unreacted FeCr2O4.The dissolution reaction on the surface of FeCr2O4 was the rate-controlling step in the dissolution process. The calculated activation energy of the dissolution process was 65.43 kJ·mol-1.
Extraction of vanadium from pet-coke gasification cinder: Part 1 leaching kinetics studies in sulphuric acid medium
Petcoke cinder is a solid by-product generated during the gasification of petcoke, accounting for three to five percent of the petroleum coke mass. It commonly contains valuable metals like V, Ni, Al, and Fe, highlighting the resource's potential for vanadium extraction. Thus, it can be regarded as an emerging secondary source of vanadium and other critical metals. The conventional pyro-cum-hydrometallurgical process for vanadium recovery relied on alkali roasting, which was not only energy-intensive but also contributed to greenhouse gas emissions. Considering environmental concerns and high energy consumption, the current study embodies a state-of-the-art development of an economically viable process for extracting V from petcoke gasification cinders. This paper examines the method of sulfuric acid-leaching of vanadium from gasification cinders and the effects of various parameters, including acid concentration, temperature, process duration, percentage of H2O2, amount of sodium dodecyl sulfate (SDS), and solid-liquid phase ratios. The maximum vanadium yield of 95.62% was achieved under optimal conditions of sulfuric acid concentration, temperature, time, S/L ratio, and amounts of H2O2 and SDS, which were determined to be 4M, 90°C, 3 hours, 20%, and 6%, respectively. The shrinking surface-controlled model was employed to investigate leaching kinetics. The reaction order concerning sulfuric acid concentrations was found to be 1.29. According to the Arrhenius equation, the evaluated apparent activation energy for leaching was approximately 27.67 kJ/mol, and the empirical equation representing the acid leaching kinetics of vanadium is identified as 1-(1-α)1/3 = kt = (9.261 X 103) [H2SO4]1.2916exp[-27674/RT] T.
The influence of cold, warm and hot deformation on microstructure and mechanical properties of Inconel 718 superalloy
This study systematically examines the influence of precipitation on the microstructural and mechanical properties of Inconel 718 superalloy in as-received, solution heat-treated, peak-aged, and overaged conditions. Cold, warm, and hot deformation tests were performed at 25 °C, 400 °C and 800 °C using a constant strain rate of 5.55 × 10⁻⁴ s⁻¹. The results indicated dynamic strain aging during warm deformation at 400 °C in all investigated conditions. However, at temperatures above 400 °C, a pronounced reduction in strength was observed, accompanied by a corresponding increase in elongation for most conditions. Notably, the solution heat-treated samples exhibited anomalous behavior, showing an increase in Rp0.2 after deformation at 800 °C. This suggests the occurrence of dynamic precipitation during hot deformation in the solution heat-treated samples.
Oxidation and property evolution of AISI T5 steel under varying heat treatments
This study evaluates the effect of heat treatment on the mechanical, tribological, and oxidation behavior of AISI T5 steel. The chemical composition was first characterized using spectroscopy and SEM. A two-year oxidation test conducted in humid and relatively dry atmospheres showed strong environmental sensitivity: in humid air, the oxidation rate reached 11.27×10-2 P/P0 per month with a sharp increase after 25 days, whereas in dry air it remained below1.35×10-2 P/P0 per month, following a linear and nearly flat trend indicative of a protective oxide scale. Heat treatment significantly increased hardness from 34.15 ± 0.59 HRC (untreated) to 62.70 ± 0.66 and 60.80 ± 0.48 HRC for water and oil quenched steels, respectively. Impact strength decreased accordingly, with oil quenching offering the best hardness-toughness balance (60.8 HRC, 2.08 Kcv). Instrumented indentation confirmed substantial surface strengthening, with HIT rising to 17.39 ± 0.29 GPa (Q. Water) and 7.68 ± 0.12 GPa (Q. Oil). Under dry sliding, wear rates were reduced by 81.3% (Q. Water) and 62.5% (Q. Oil), with faster run-in in the water-quenched condition. XRD revealed tempered martensite with Fe3W3C/Cr7C3 (Q. Water) and Co3W3C (Q. Oil), consistent with thermal conditions. This study provides new experimental data on the effects of 15-minute austenitization followed by oil or water quenching on the properties of AISI T5 steel, highlighting its potential for process optimization.
The influence of nickel grade and its occurrence state on high pressure acid leaching behavior of lateritic nickel ores
This research evaluates the effects of nickel grade and occurrence state on the leaching behavior of lateritic nickel ores using high-pressure acid leaching (HPAL) at 250 °C with sulfuric acid. Three ores were selected for the study: Ore 1 (ultra-low-grade limonite, 0.73 wt.% Ni), Ore 2 (limonite, 1.34 wt.% Ni), and Ore 3 (saprolite, 2.00 wt.% Ni). Mineralogical studies (XRD, SEM, and EPMA) were conducted to provide insight into nickel-hosting phases and characteristics of the ore matrix. A higher nickel grade does not necessarily result in higher extraction. Ore 1 had the lowest nickel grade but achieved the highest extraction of Ni (97.25%) and Co (98.49%) under experimental conditions using an acid-to-ore (A/O) ratio of 0.40. This significant Ni extraction is attributed to nickel's structural substitution in goethite, an iron oxide mineral that dissolves readily under the HPAL process. Ore 2 also contains goethite as the dominant phase and achieved similarly high recoveries of Ni (97%) and Co (98%), however, Co recovery decreased slightly under higher acid conditions due to co-precipitation with hematite. Ore 3 had the highest nickel grade but the lowest leaching efficiency (<90% Ni). The generally low recoveries may be attributed to nickel being hosted in both goethite (a leachable phase) and lizardite (a less leachable phase). The silicate matrix of lizardite and its elevated magnesium content restricted the effective acid range and thus diminished nickel selectivity during the HPAL leaching process. The results highlight that the mineralogical occurrence state of nickel is more important than nickel grade in determining leaching performance. Therefore, low-grade limonite ores with favorable mineralogy can serve as potential feed sources for environmentally friendly sustainable nickel hydrometallurgical extraction.
The influence of Cu content on microstructure and mechanical properties of PM-fabricated Ti-18Nb-xCu alloy
This research investigated the influence of varying copper (Cu) concentrations (0, 5, 7, and 9 wt.%)on the sintering behaviour, microstructural development, and mechanical characteristics of Ti-18Nb alloy, fabricated through conventional powder metallurgy. Under specific sintering conditions (1150°C for 5 hours), Cu addition led to a more homogeneous microstructure and promoted the complete dissolution of Nb particles. X-ray diffraction (XRD) analysis confirmed the presence of alpha (α) and beta (β) Ti phases, along with the Ti2Cu phase, with its peak intensity increasing as Cu content rose. Mechanical properties were significantly enhanced by Cu addition. Yield strength increased almost linearly with Cu content. Compressive strength notably increased with 7 wt.% Cu, reaching 980 MPa, and slightly exceeded this value with 9 wt.% Cu. Hardness values increased due to solid solution strengthening in the α-Ti phase and the precipitation of the Ti2Cu phase, with the highest hardness (222 HV) observed in the 7 wt.% Cu alloy. The elastic modulus initially increased with 5 wt.% Cu, then subsequently decreased with further Cu additions; the Ti-18Nb-7Cu alloy exhibited the lowest elastic modulus at 13.34 GPa. Furthermore, the resilience of the alloys improved with the formation of the Ti2Cu phase, and a maximum value of 13.15 MJ m−3 was achieved.
Effect of copper addition on the microstructure, mechanical, thermal, and magnetic properties of Fe-Ni-Cu alloys
In this study, FeNiCu alloys with two different copper contents were produced by arc melting. The aim was to investigate the effects of Cu content on the microstructural, mechanical, thermal, and Mössbauer properties of the alloys. Microstructures were examined using SEM micrographs. Vickers hardness tests were conducted to evaluate mechanical strength. Thermal behavior was analyzed using DSC. Magnetic characteristics were studied by Mössbauer spectroscopy. SEM analysis showed the presence of martensitic structures in both alloys, with the alloy containing more Cu exhibiting a higher amount of martensite. Hardness increased from 169.1 HV to 190.2 HV as Cu content increased. DSC results confirmed the martensitic transformation. The alloy with higher Cu content showed a higher transformation temperature and greater transformation energy released. Mössbauer spectra indicated the presence of both magnetically ordered and non-ordered phases in both alloys. Hyperfine parameters demonstrated changes in the local atomic environment due to Cu addition. The weak singlet obtained was associated with the FCC phase. The two sextets were attributed to ferromagnetic BCC phases arising from different environments of the Fe atom. The other sextet, with a low internal magnetic field of around 18 T, was ascribed to possible Ni- and/or Cu-rich surroundings of the Fe atom. Overall, increasing Cu in the alloy altered the microstructure, improved hardness, shifted the martensitic transformation temperature, and modified the magnetic hyperfine interactions. These results may aid in designing advanced Fe-based materials for structural and magnetic applications.
Effects of welding parameters on percentage dilution and mechanical properties in welded joints of ultra-high hardness armour steels
This study investigates the effects of Gas Metal Arc Welding (GMAW) parameters—specifically welding speed and stick-out—on the dilution and mechanical properties of welded joints composed of ultra-high hardness quenched and tempered (UHH-Q&T) armor steel and austenitic stainless steel filler metal. An optimization methodology was used to set constant parameters, including wire diameter, gas flow rate, welding voltage, and wire feed speed, based on equipment capabilities. Experimental trials varied welding speed and electrode stick-out while maintaining a constant current through inductance control. Although the welding parameters affected the melted base and filler metal areas, the dilution percentage remained unaffected. The correlation between dilution and welding current was validated. Microstructural and mechanical analyses confirmed the consistent behavior of the welded joints under the tested conditions.
Effect of reduction ratio on die fill-out and hardness profile of cold-drawn polygonal rods made of acid resistant steel X6CrNiTi18-10
The study investigates the effect of the reduction ratio on strain hardening efficiency and load during the drawing process of austenitic acid-resistant steel X6CrNiTi18-10. The focus is on optimizing geometry-related process conditions to achieve the highest quality and productivity when drawing special-purpose rods with polygonal shapes, specifically square and hexagonal cross-sections. The research addresses how increasing the reduction ratio can enhance strain hardening while reducing the number of drawing passes, ultimately affecting quality and load. Numerical modeling was used to analyze the relationship between strain hardening and load versus the reduction ratio. Proper models and assumptions were formulated and subsequently verified through experiments, which confirmed the validity of the mathematical and numerical models for load estimation. The study quantified the effect of strain on strength properties by mapping of measured hardness along the strain gradient. The application of variable billet diameters produced a similar hardness profiles for both analyzed rod geometries and reversed the effect on underfilling of the corners. The findings indicate a threshold reduction ratio for producing sound rods with square or hexagonal cross-sections. Exceeding this threshold can cause excessive strain hardening, leading to increased hardness that impedes corner fill-out and/or results in failure.
Optimizing calcium additions for a strength–corrosion resistance balance in squeeze-cast Zn–Al–Cu–Mg alloys
In this study, squeeze-cast Zn–Al–Cu–Mg alloys with varying Ca additions (0, 0.5, 1.0, and 1.5 wt.%) were investigated to evaluate the combined effects of microstructural evolution on mechanical and corrosion performance. Microstructural analysis showed a transition from coarse Zn-rich dendrites in the base alloy to a refined and uniform morphology with Ca additions up to 1.0 wt.%, followed by coarsening and increased porosity at 1.5 wt.% Ca due to excessive intermetallic formation. Mechanical testing indicated that the alloy with 1.0 wt.% Ca had the highest hardness (141 HV0.1) and tensile strength (359 MPa), attributed to grain refinement and dispersion strengthening, though with reduced ductility due to intermetallic brittleness. Electrochemical corrosion tests in 3.5 wt.% NaCl solution showed that the corrosion rate decreased from the base alloy to 1.0 wt.% Ca, confirming enhanced corrosion resistance due to microstructural refinement and protective film formation. However, excessive Ca addition (1.5 wt.%) increased the corrosion rate to 0.8109 mpy due to coarse intermetallics and porosity, which promoted localized attack. The results highlight that optimal Ca addition (1.0 wt.%) achieves a balance between strength, hardness, and corrosion resistance, making Ca-modified Zn–Al–Cu–Mg alloys promising candidates for structural and functional applications.
Antimony obtaining by hydrometallurgy - Emphasis on recovery from leach solutions
Antimony (Sb) is listed as a critical raw material in both Europe and the USA. Pyrometallurgical and hydrometallurgical methods are used for its recovery from raw sources. Hydrometallurgy is considered a suitable technology when Sb sources are low-grade ores or technogenic waste. After a brief introduction to the Sb species present in pregnant leach solutions (PLS) obtained by using different leaching reagents, this paper presents various methods for recovering Sb from PLS produced in the leaching hydrometallurgical stage. The discussion covers antimony recovery by hydrolysis and conversion, selective precipitation, crystallization, electrowinning, replacement, liquid-liquid extraction and ion exchange. Factors affecting the effectiveness of these processes and the recent attempts to improve these technologies are presented. Finally, possible future research directions are outlined.
Constitutive analysis of Cu-DHP alloy during hot compression
<!-- [if gte mso 9]><xml> <w:WordDocument> <w:View>Normal</w:View> <w:Zoom>0</w:Zoom> <w:PunctuationKerning/> <w:ValidateAgainstSchemas/> <w:SaveIfXMLInvalid>false</w:SaveIfXMLInvalid> <w:IgnoreMixedContent>false</w:IgnoreMixedContent> <w:AlwaysShowPlaceholderText>false</w:AlwaysShowPlaceholderText> <w:Compatibility> <w:BreakWrappedTables/> <w:SnapToGridInCell/> <w:WrapTextWithPunct/> <w:UseAsianBreakRules/> <w:DontGrowAutofit/> </w:Compatibility> <w:BrowserLevel>MicrosoftInternetExplorer4</w:BrowserLevel> </w:WordDocument> </xml><![endif]--><!-- [if gte mso 9]><xml> <w:LatentStyles DefLockedState="false" LatentStyleCount="156"> </w:LatentStyles> </xml><![endif]--><!-- [if gte mso 10]> <![endif]--> The hot deformation behavior of the deoxidized high-phosphorus copper (Cu-DHP) was investigated during compressive deformation at a wide deformation temperature range of 200 to 1000 °C and strain rates ranging from 0.0005 to 0.4 s-1. The flow curves related to the hot working regime (500 to 1000 °C) generally showed distinct peak stresses with the fall of flow stress after the peak point, revealing the occurrence of dynamic recrystallization (DRX). By increasing the Zener-Hollomon parameter, the cyclic flow curves were replaced by the single-peak ones, and finally by the characteristic dynamic recovery (DRV) curves. At temperatures lower than half of the melting point, only DRV-type curves were observed. Based on the constitutive analysis, the apparent activation energy of 274.1 kJ/mol, hyperbolic sine power of 4.88, and power law stress exponent of 5.27 were obtained, resulting in the flow stress equations to describe material flow in the hot working regime. The power law breakdown and the importance of deformation temperature were also critically discussed based on mathematical fitting, strain rate sensitivity index, and microstructural analysis.
Microstructure changes in welded duplex stainless steel and their effects on hardness and corrosion resistance
Duplex stainless steel (DSS) is extensively employed in a range of applications because it contains equal proportions of the two phases, ferrite and austenite, as well as a specific percentage of alloying elements. These combined benefits provide the material with superior strength, corrosion resistance, and good welding capacity. During the welding process of DSS, equal amounts of both phases are disrupted, resulting in precipitation. To investigate this phenomenon, this study aims to analyze the effect of changes in welding current by adding 10% N2 with Ar (as a shielding gas) on microstructure changes of DSS weldment. The changes were evaluated through the hardness and corrosion resistance. The study found that by increasing welding current, the Cr2N precipitates disappear in the WZ, with a small amount appearing only in the HAZ. However, the very low welding current causes the formation of Cr2N precipitates in both the WZ and HAZ. The results indicate a direct relationship between the volume fraction of austenite and the welding current. Reducing the welding current increases the hardness of DSS welds due to a higher ferrite volume fraction. Moreover, the corrosion resistance of DSS weldment improves with an increase in the welding current due to the increase in the amount of austenite phase.
Microstructure and hardness of Bi-modified magnesium AZ31 alloys subjected to severe plastic deformation
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</xml><![endif]--><!-- [if gte mso 10]> <![endif]--> Magnesium alloys are known as attractive materials because of their low density and good thermal conductivity. However, compared to competing metallic materials such as aluminum alloys, magnesium alloys have lower strength. Among different methods introduced for strengthening metallic materials, severe plastic deformation is notable for its efficiency and relative simplicity. This study investigates the effect of bismuth content on the microstructure evolution and hardness of magnesium AZ31 alloy subjected to severe plastic deformation through equal channel angular pressing. For this purpose, AZ31 alloys with nominal bismuth contents of 0%, 1%, and 3% were processed by up to four passes of equal channel angular pressing at 300 °C. The microstructure evolution of these alloys was then examined using optical and scanning electron microscopy. The hardness of the specimens was measured using the Vickers method. Results show that bismuth-enriched second-phase particles are fragmented during severe plastic deformation. Additionally, increasing the bismuth content leads to more rapid grain refinement during severe plastic deformation due to the pinning effect of these second-phase particles on the grain boundaries. Faster hardening rates during severe plastic deformation were observed for the bismuth-containing AZ31 alloys. This effect is attributed to the more rapid grain refinement and the increase in the Hall-Petch coefficient resulting from the presence of fine bismuth-enriched particles.
Enhancing Corrosion Resistance and Structural Properties of Ni-TiO2 Composite Coatings: The Impact of SDS Surfactant
Ni-TiO2 composite coatings are promising materials for enhancing the corrosion resistance and structural properties of steel substrates in various industrial applications. Corrosion remains a major issue for steel components, prompting the need for effective protective coatings. This study investigates the influence of sodium dodecyl sulfate (SDS) surfactant on the structural, electrochemical, mechanical, and morphological properties of Ni-TiO2 composite coatings electrodeposited on BS2 steel. The coatings were characterized using X-ray diffraction (XRD), scanning electron microscopy (SEM), energy-dispersive X-ray spectroscopy (EDX), microhardness testing, and electrochemical techniques, including potentiodynamic polarization and electrochemical impedance spectroscopy (EIS). The results show that SDS incorporation led to an increase in the crystallite size of the coatings, from 35.92 nm to 80.82 nm, and a significant enhancement in the relative texture coefficient (RTC) along the (200) plane (88.09%). SEM analysis revealed a more compact and uniform surface morphology, with SDS reducing surface porosity from 8.23 × 10-3% to 2.20 × 10-6%. Electrochemical measurements demonstrated a substantial improvement in corrosion resistance, with charge transfer resistance (Rct) increasing from 5.17 kΩ.cm2 to 312.65 kΩ.cm2 and polarization resistance (Rp) rising from 2.5 kΩ.cm2 to 176.38 kΩ.cm2. The microhardness of the coatings decreased slightly from 256.26 kgf.mm-2 to 217.22 kgf.mm⁻², indicating a trade-off between mechanical strength and enhanced corrosion protection. These findings highlight the potential of SDS as a valuable additive for optimizing Ni-TiO2 composite coatings, although further research is needed to explore the impact of SDS concentration, long-term durability, and the performance of these coatings in more aggressive environments.
Gold recovery and migration mechanism in the copper smelting and converting
The gold embedded in the copper concentrate is enriched in the matte phase during copper smelting and transferred into blister copper during subsequent processing, via which the gold was recycled. In the copper smelting, gold dissolved and appeared as Au (Ⅲ) in the formed gold-matte solid solution. This solid solution could be formed in two ways: by exchanging Au atoms for Cu atoms in the Cu5FeS4 (matte) crystal lattice and by doping Au atoms in Cu5FeS4. In the matte converting, the transfer of gold from the matte phase to blister copper occurred spontaneously due to a fact that the surface tension between the gold and matte phases was considerably higher than that between the gold and copper phases. Gold capture by blister copper occurred by Au atoms replacing Cu atoms in the Cu cell.
Effect of adsorption of surfactant mixtures on wettability of sintering dust
In order to improve the wettability of sintering dust, we investigated the action mechanism of Triton X-100 (TX-100), which synergizes with Dodecyl Trimethyl Ammonium Bromide (DTAB). The settling times of nine different types of surfactants were measured, and the optimal ratio of cationic and nonionic surfactants to synergistically improve the wettability of sintering dust was determined from these measurements. The adsorption performance of the surfactants in the mixed solution and their effect on the wetting properties of sintering dust were investigated by sedimentation test, adsorption amount, Fourier transform infrared spectroscopy, and zeta potential determination. The results showed that a synergistic effect could be obtained when DTAB and TX-100 were mixed, and the DTAB: TX-100=2:2 composite solution with a concentration of 0.3% had a good wetting effect on the sintering dust. As the concentration of the surfactant mixtures increased, the content of hydrophilic functional groups and the absolute potential value of the surface of the sintering dust increased accordingly. Among them, DTAB was affected by alkyl interactions and had a greater adsorption affinity, and the hydrophobic tail of TX-100 was entangled with that of DTAB due to hydrophobic interactions and shared an adsorption site. This study contributes to the selection of surfactants for the efficient wetting of sintering dust and provides a theoretical basis for hydrometallurgy and dust control.
Studying the structure and properties of quasi high-entropy alloys of the Fe-Co-Cr-Ni-Mn-Nb system with Mo additives
The paper presents the results of studying the structure, hardness and wear resistance of quasi high-entropy alloys of the Fe-Co-Cr-Ni-Mn-Nb system with Mo additives. As a result of the study, it was shown that quasi high-entropy alloys of the Fe-Cr-Mn-Ni-Co-Nb system smelted with partial use of ferroalloys and additionally alloyed with Mo in the amount of 5-15% by weight, demonstrated very system alloys without Mo additives. The structure of the studied samples is represented by a mixture of solid solutions of Mn, Fe, Co, Ni of the face-centered cubic typе (FCC), Nb and Mo of the body centered cubic type (BCC), as well as interstitial phases: a carbide phase, a Laves phase and a σ-phase.