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By E. P. Cadwell

"Throughout the years Cyanamid has been a supplier of cyanide and a supplier of information to the mining industry. In general, the knowledge of mineralogy is greatly overlooked. Mineral deposits in the Western hemisphere have been exceedingly rich in the past but now they are becoming poorer. In other words, we will have to use our talents to the utmost to extract the precious metals and base metals from these ores. Modifications of some of the mineralogical equipment displayed here belong in the mill.Cyanidation of copper has been one of the main projects in our labs in recent years. De-rimming or de-filming of copper in order to upgrade copper concentrate was the main aspect investigated. A study was made as to how wide spread was the filming of secondary copper on pyrite, and to what extent it affected the copper industry. It was very wide.Often there is no conception as to what the minerals are. One open pit copper producer with a chalcopyrite ore was producing a copper concentrate with a 5% copper value whereas chalcopyrite contains 35% copper. They used primary and secondary grinding and a regrinding section. The ore contained about 8 parts chalcopyrite to one part of other copper minerals. In tests, a 3 1/ 2% copper rougher concentrate, cleaned without regrinding but conditioned with cyanide for a low contact time of 30 seconds produced a 30% copper concentrate with 90% recovery by removal of the film. It was of utmost importance that some quantitative mineralogical analysis be made before flow sheet changes were made. Every man should be trained to do his own microscopic examination in order to get quick answers. The fundamental thing in all mineral dressing is to first of all know the minerals and the mineral associations."

Jan 1, 1964

By Will S. Pettitt

Fracture Network Engineering (FNE) is the engineering design of rock mass disturbance through the use of advanced techniques to model fractured rock masses numerically, and then correlate field observations with simulated fractures generated within the models. Microseismic (MS) monitoring is a standard tool for evaluating the geometry and evolution of the fracture network induced during a hydraulic treatment, principally by source locating MS hypocenters and visualizing these with respect to the treatment volume and infrastructure (Figure 1). The integrated use of Synthetic Rock Mass (SRM) modeling of the hydrofracturing with Enhanced Microseismic Analysis (EMA) provides a feedback loop in which the SRM is constrained by the information provided by the MS data and the in-situ behavior of the fracture network is better understood, leading to informed decisions on future field operations. This paper discusses the technologies used in FNE and some of the developmental challenges we face in order to provide a more efficient and robust application of the approach. One particular challenge is the accurate representation of MS source data within the models (locations, magnitudes and mechanisms), and the ability to correlate these data effectively with field results. This challenge is being overcome by the development of more efficient numerical modeling algorithms, providing simulations in three dimensions at reservoir scale, combined with validation of these algorithms using laboratory and field case studies.

Jun 1, 2012

By G. R. Davidge

"Falconbridge Mine has a history of significant microseismic activity dating back to 1955. Since mid-1981, a microseismic monitoring system has been operating in the area around the No .9 Shaft hoist room located 25 m from the are zone at a depth of 1200m. Several mine wide faults dissect this area and have been shown to be microseismic-active due to mining. The microseismic monitor has been interfaced with a small dedicated personal computer and a communications device to perform routine data evaluation and to produce graphical output. The programs are described and selected result s from the monitoring program are presented.IntroductionFalconbridge Mine is located on the southeast rim of the Sudbury Basin. The nickel-copper sulphide ore zone is essentially a tabular orebody striking approximately east-west and dipping at 80 degrees north near surface and rolling to 75 degrees to 80 degree s south by the 1000 level. (Mine level number s represent the approximate depth in feet below ground surface .) This dip is maintained down to the 6000 level. The north wall is comprised of jointed norite and a faulted contact up to 1 m thick exists between the ore zone and the norite. The south wall rock is a greenstone with highly siliceous lenses and often has a faulted contact with the ore zone. No less than five mine wide faults exist, as shown in Fig. I.Mining ha s been carried out from virtually the bedrock contact to depths of 1830 m although the majority of current activity is between 900 and 1500 m below surface. A winze provides access below the 4025 level and the cage hoist room is located on the 3850 level in the north wall 25 m from the contact. Because of concern for the stability of this hoist room, there has been no mining activity within 60 m of the hoist room and by 1980 this block of ore was one of the major blocks of high-grade ore remaining in the mine . Mining of this block was originally scheduled for very late in the decade.Prior to a six-month shutdown in 1982, this mine produced approximately 450,000 tonnes of ore annually, mainly by cut and- fill techniques. Following the shutdown, annual production has been reduced to approximately 200,000 tonnes and production is now mainly by undercut and fill techniques .Mining-induced seismicity has occurred at Falconbridge Mine since at least 1955 and reviews of the microseismic problems for the periods from 1965 - 1970 and from 1971 to 1979 were made by Singh (1971) and Vongpaisal et al. (1980), respectively. The need for instrumentation was addressed by these authors. Following several large events during the spring of 1980, a decision was made to investigate existing microseismic monitors and to apply micro seismic monitoring techniques in Falconbridge Mine. Application of microseismic monitoring to Falconbridge Mine was to concentrate on the No . 9 Shaft hoist room area of the mine, particularly around the 4025 level where a large mechanized cut-and- fill stope was approaching this level. By mid - 1981, the microseismic monitor was fully installed and with in a year , a short-period seismograph and a personal computer had been added to the system."

Jan 1, 1984

By V. Shumila, T. Butler

Microseismic monitoring systems listen to a rockmass and record ground vibrations associated with brittle rock fracture. Modern systems record continuously and can identify as many as one thousand small and possibly larger magnitude events occurring each day from induced stress change and redistribution. This paper presents examples of the real time use of microseismic information in mining applications. It shows how alerts can quickly identify large magnitude events or unexpected clusters of seismicity and how seismic re-entry protocol can help to improve safety decisions. Additionally, newly developed advanced analysis techniques applied to mine seismic data sets are shown including the use of clustering methods to see into a cloud of seismic data to identify significant activity and quantify possible planar features. The use of source parameter trend analysis is shown to be a beneficial method for interpreting changes in relative stress levels. Seismic moment magnitude distributions are analyzed using the TGR (Truncated Gutenberg Richter) and TMD (Tapered Moment Distribution) methods to estimate bvalue and expected maximum magnitude. Seismic hazard analysis is shown as a useful way to simplify a dataset and highlight seismic hot spots. The rockmass response to excavation is a complicated spatial and temporal process and microseismic monitoring is a method that can be used to help understand the location and mechanics of failure occurring in the rock ultimately helping to improve safety and productivity at a mine site.

Jan 1, 2015

By Pavel Vasak

Microseismic monitoring is becoming standard practice in the Canadian mining industry, particularly as mines get deeper. Full-waveform microseismic systems allow the operator to distinguish the event source mechanism, e.g., blast, shear slip or stress-induced fracture. At mine sites that heave a microseismic system operator blasts are manually identified by comparing the event waveform traces to the morning blast logs. However, this procedure is not routinely done at sites where a system operator is not present and this can lead to misinterpretation of the data at a later stage, particularly where the interpretation is outsourced, often many years later. It is critical to improve the microseismic data quality and consistency for processing and interpretation with a reliable technique to filter out blasts and blast related seismicity. This paper presents the development and implementation of a simple blast identification and filtering routine. The routine was developed specifically for Vale?s Creighton Mine about a decade ago, but is made sufficiently general so that it can be used at any mine site with an ESG (Engineering Seismology Group Canada) based full-waveform microseismic systems. The routine is strictly a post-processing procedure developed for use with the Access database data structure used by ESG. The algorithm was tested at Creighton Mine and a success rate of 80 to 90% was achieved, when compared to manual blast picks.

Oct 1, 2010

By M. A. EI Zeky, A. E. El-Nikbaily, M. A. Shahin

"Possible mechanisms of microsilica dust formation and factors affecting its quantity have been discussed. General mathematical models to predict the dust quantity based on electrical and coke consumptions, and flue gas temperature as functions of silicon recovery in the process and silicon content of the alloy have been established. It has also been shown that the flue gas temperature can be used as an additional process control parameter. Comments are made on the effect of the dust formation on the whole process economics and it is pointed out that the formed microsilica dust is a valuable by-product and not an industrial waste. INTRODUCTIONFerrosilicon is produced in electric arc furnaces with submerged electrodes. The charge mixture consist s mainly of quartzite, coke as the reducing agent and iron chips. The products are ferro silicon and carbon monoxide, various other volatile materials, water vapour and silicon monoxide gas. Carbon monoxide and silicon monoxide oxidize at the charge surface when mixed with air entering through the furnace hood openings. The off-gas contains a considerable amount of dust, which is mainly very fine particles of silica formed as a result of oxidation. The emission of dust containing gases to the atmosphere causes serious pollution problems to the environment. Therefore, the control of the formation of the dust, preventing it from escaping to the atmosphere, and dealing with this very fine dust collected from the flue gases represent important technological and economical parameters in the ferrosilicon production industry.This paper is concerned with the relations between the quantity of formed micro silica dust, as a function of both silicon recovery and silicon content in the alloy, and various other technological parameters; and their possible effects on the energy consumption and economics of the whole process."

Jan 1, 1989

By O. A. Ojo, E. Anisimov, A. K. Khan

Electro-spark deposition (ESD) has recently generated a great deal of interest in processing aerospace materials. This is due to its potential for joining and repairing difficult-to-weld precipitation strengthened nickel-based superalloys without having problems of welding cracking that often plaque these materials. The short duration of current pulses involved in the process combined with the intermittent contact results in extremely rapid thermal cycle that produces nearly no heat affected zone in the substrate material. The microstructure of electro-spark deposited superalloy was meticulously studied in this work by scanning electron microscopy (SEM) and analytical transmission electron microscopy (TEM). The results show that in contrast to general assumption, the extreme rapid cooling rates involved in the ESD process did not produce partition-less solidification that is devoid of second phase microconstituents in the material. The secondary microconstituents were found formed along the intercellular regions of the solidification microstructure. The nature of these particles and the possible implication of their formation on mechanical properties of ESD processed material are reported and discussed.

Jan 1, 2015

By D. A. Akinlade, N. L. Richards, D. C. Murray, W. F. Caley

To investigate the effect of adding Ti to a Ni-Cr-Fe powder metallurgy alloy, a thermodynamic software package was used to predict the phase transformations that occurred during thermal processing. Specifically, the effect of adding 3w/o Ti to a 6w/o Al modified ternary Ni-Cr-Fe alloy (the quaternary) was simulated and the phase transformations that might occur in the material on sintering were obtained using the thermodynamic modeling tool. These predictions were subsequently compared with experimental results obtained by X-ray diffraction and metallography. For comparison, selected compacts were prepared containing only the ternary + 3w/o Ti (no Al). Based upon compressibility curves, the optimum pressure for producing the new Ti compacts was 500 MPa vs 600 MPa for the quaternary composition with Ti. In each case, hardness of the base alloy was enhanced by the Ti addition whereas the residual porosity remained relatively constant at about 19%. Finally, although SEM/EDS failed to confirm the presence of Ti in the gamma prime intermetallic, XRD spectra showed a shift in lattice parameter on addition of Ti, suggesting that the intermetallic was of the form Ni3(Al,Ti).

Jan 1, 2010

By T. Cutard, E. Yeugo Fogaing, C. Gault, H. Marzagui, N. Prompt, M. Huger, C. Deteuf

This paper deals with studies made in the field of the French research network PROMETHEREF. Several refractory castables are considered in this program. In the present paper, one of these materials is considered, it is a low cement castable based on andalusite aggregates. A particular attention is paid to microstructural changes during the first heating and on their effects on the high temperature mechanical behavior. Microstructural evolutions have been characterized by the way of dilatometry, scanning electron microcopy and X-ray diffraction. In-situ observations by environmental scanning electron microscopy gave complementary results on these high temperature microstructural changes. They deal with microcrack formation, phase changes, crystallization, liquid phase formation and sintering. By propagation of ultrasonic waves, high temperature continuous measurements of the Young's modulus have been made. Results confirm the existence of microstructural changes and allow to quantify the Young's modulus variations all along specific thermal cycles. High temperature four point bending tests and room temperature tensile tests were made in the same temperature range. Behavior evolutions could be found and interpreted with the help of previously mentioned results.

Jan 1, 2004

By N. A. P. Kiran Kumar

The Zr-Nb alloys are reported to be showing superior resistance to corrosion and substantially lower hydrogen pickup when compared with zircaloys. In the present study zircaloy-4 and Zr-1Nb (E110) alloys were hydride using high pressure hydrogen gas furnace at a pressure of 20 MPa. Thermal cycling was done on the samples at a temperature of 3500C for 10 cycles with 5h soaking time at 3500C per each cycle. The Microstructural observations on zircaloy-4 samples show long and interlinked hydride like chain, oriented along the circumferential direction. Whereas in Zr-1Nb, short hydrides were observed with hydride platelets not showing interlinked chain like structure. The hydrides in Zr-1Nb were observed to be not showing particularly orientation along the circumferential directions. Electron backscatter diffraction was use to understand the hydride precipitation and their orientation in Zircaloy-4 and E110 alloy.

Aug 1, 2010

By J. Beddoes

The various microstructural factors that influence the creep resistance of y-titanium aluminides are presented and discussed. Titanium aluminides have potential for a variety of intermediate temperature applications in both gas turbine and reciprocating engines. While it is well established that the 'fully lamellar' titanium aluminide microstructure offers superior creep properties, the particular influence of lamellar morphology, third phase precipitation, and grain boundary structure in controlling both the primary and tertiary creep behaviour is presented. The results are primarily based on tensile creep experiments undertaken using several titanium aluminide intermetallic compositions processed via powder metallurgical techniques, investment casting and Bridgman directional solidification. The results indicate that lamellar structure and precipitate formation have a major impact on primary creep, while microstructural degradation through both lamellar and precipitate coarsening influence on the onset of tertiary creep leading to fracture. The results are used to design a creep resistant microstructure produced by directional solidification and the effectiveness of this designed microstructure is demonstrated through 10,000 hour creep tests.

Jan 1, 2004

By A. G. Beer

The evolution of microstructure is examined during the annealing of hot worked magnesium alloy AZ31. The influences of deformation and annealing conditions on the developed microstructures are assessed. It is found that annealing at a low temperature (300 °C), after deformation at a low temperature and strain rate (300 °C and 0.001 5-1 respectively), results in the development of abnormally large grains. With increasing values of Z (lower temperatures, higher strain rates), static recrystallization of the dynamically recrystallised structure takes place; smaller annealed grain sizes are attained and the time at which coarsening begins is reduced. Whilst both the deformation and annealing conditions influence the time it takes to reach a stable annealed microstructure, the grain size attained is governed solely by the prior deformation conditions employed.

Jan 1, 2006

By G. K. Quainoo

In the automotive industry, the awareness to meet Corporate Average Fuel Efficiency (CAFE) standards has evolved the need to reduce vehicular weight in new automobile designs, with the overall goal of reducing gas emissions into the atmosphere (Kyoto protocol), One efficient method has been to use lighter materials such as aluminum in outer body panels, Heat treatable AA6111 is one of the materials employed due to its unique combination of formability, paint bake strengthening and superior corrosion resistance characteristics, Researchers have applied various thermo-mechanical processes on 6000 series aluminum alloys and have found an improvement in the mechanical properties of these alloys, For a formed and painted automobile panel, the final mechanical properties involve a combination of strength components arising from cold work, strain aging and precipitation minus recovery. In this study, the evolution of microstructure resulting from the interaction of cold work and precipitation in AA6111 has been studied by means of transmission electron microscopy (TEM) after subjecting samples to various heat treatments, tensile testing and differential scanning calorimetry (DSC), This has been done to understand the evolution of microstructure and its influence on the properties of the alloy, The results show a considerable improvement in strength with a corresponding increase in strengthening precipitates with increasing level of cold work in the alloy. DSC results following the application of various levels of cold work also show acceleration in the precipitate phase formation, as precipitates are observed to form at lower temperatures, with increasing level of cold work/

Jan 1, 2005

By P. H. Shipway, D. G. McCartney, H. Saghafifar

The microstructural changes during thermal ageing at 650ºC in the interfacial region of Alloy 625 weld overlay on a 2.25Cr-1Mo steel was evaluated. Optical microscopy, scanning electron microscopy in SE and BSE modes, electron probe microanalysis and hardness mapping were used to characterize as-welded microstructure and its changes during thermal ageing and precipitates of interfacial region. Carbon migration across the interface was recognised as a major issue. A region of 300 µm wide adjacent to the fusion line, which was found harder in the as-welded condition decarburized during thermal exposure. Studies revealed that this region transformed to a soft region containing large ferrite grains and micron-sized carbides. In the weld overlay, a 50 µm wide hard band (over 650 Kgf mm-2) adjacent to the fusion line formed and carbide precipitates were observed along grain boundaries. Carbide precipitation mostly occured in the 150 µm wide region close to fusion line.

Jan 1, 2017

By B. K. Choi, G. E. Kim, S. Noh, T. K. Kim

Oxide dispersion strengthened (ODS) steel has been developed as the most prospective core structural material for next-generation nuclear systems because of its excellent high strength and irradiation resistance. In ODS steel, finely dispersed nano-oxide particles with a high number density in the homogeneous grains can be very attractive to achieve superior mechanical properties at high temperatures, and these favorable microstructures can be significantly changed using process parameters during the mechanical alloying procedures. In this study, the effects of mechanical alloying times on the microstructure of 10Cr-1Mo ODS martensitic steel were investigated. Pre-alloyed powders with Y2O3 powder were mechanically alloyed for various milling times using a high energy horizontal ball-mill apparatus (model: symoloyer CM20). Powder properties such as the mean particle size, size distribution, and crystallite size were evaluated. Uniaxial hot pressing was employed to consolidate the milled powders. The results of a microstructural observation after the MA and UHP processes indicated that the homogeneity of the martensitic structures was considerably increased with the longer milling time. It is thus concluded that the mechanical properties of the ODS martensitic steel are greatly dependent on the mechanical alloying times.

Jan 1, 2015

By A. R. Farkoosh, J-P. Fortin, M. Pekguleryuz, S. Bagherpour

"Titanium aluminides are structural intermetallics which offer an attractive combination of high temperature strength and light weight. For such properties, these intermetallic alloys have become front-runners in replacing nickel-based superalloys used for several high temperature applications. These alloys are produced from metallic titanium, aluminum and master alloys involving an expensive and difficult process. A low cost alternative to current industrial production method is the new modified aluminothermic process which directly reduces titanium oxide (TiO2) to titanium aluminides. Nevertheless, this process has itself significant challenges in achieving alloys free of oxide inclusions; the close densities of the slag and the titanium aluminides makes slag/molten metal separation a challenging task. Usually, the alloy produced requires a second refining step. In this study, thermodynamic calculations based on CALPHAD method were performed to determine the solidification path and an attempt has been made to develop a criterion to increase the density deference between the slag and the alloy by alloying with appropriate elements. Furthermore, scanning electron microscopy (SEM) and x-ray diffraction (XRD) techniques were utilized to examine the microstructure and phase selection of three Ti-Al alloys produced by the aluminothermic reaction, including the as-cast, refined in a controlled atmosphere and inert-gas-refined alloys. The composition range of the alloys studied was restricted to the a2-Ti3Al + ?-TiAl phase field (Ti-30Al) in the binary Ti-Al phase diagram leading to a lamellar structure with different complex intermetallics as shown in Figure 1.INTRODUCTIONTiAl based alloys are promising structural materials for high temperature aerospace and automotive applications. This is due to some attractive properties such as low density, high specific strength, high specific stiffness and high temperature strength retention (Wen-bin, Xue-wen, Hong-fei, & Yong-feng, 2011). These alloys have become leading candidates to replace Ni-based super alloys in gas turbine engines. Replacement of Ni-based super alloy parts with titanium aluminides is expected to reduce the structural weight of high performance gas turbine engines by as much as 20–30% (Kothari, Radhakrishnan, Sudarshan, & Wereley, 2012)."

Jan 1, 2016

By O. A. Ojo, R. G. Ding, M. C. Chaturvedi

In this study, the fusion zone microstructure of tungsten inert gas weld of a directionally solidified NhAl-base alloy was examined by the standard metallographic techniques involving the use of optical, analytical scanning and transmission electron microscopes equipped with energy dispersive spectrometer. Fusion zone cracking was observed to be closely associated with interdendritic secondary solidification microconstituents identified as consisting of y, y' and NiMo (Y) phases. Depression of solidification temperature to the terminal ternary eutectic reaction temperature of the system during cooling is suggested as an important factor contributing to the fusion zone cracking.

Jan 1, 2006

By N. Birbilis, S. Kairy, C. R. Hutchinson, D. Jiang, D. R. Feenstra, O. Gharbi

"Recent developments in metal-based additive manufacturing (AM) technology have generated considerable interest in multiple industries, owing to flexibility in design and the ability to produce final components in their net shape. The AM of high-strength aluminium alloys has not been widely explored, due to findings of undesirable microstructures leading to short fatigue life and poor fracture toughness; restricting the application of AM to lower strength aluminium alloys (with cast-like Al-alloy compositions) to date. Herein, aluminium alloy AA2024 (Al-3.6Cu-1.2Mg) was additively manufactured via selective laser melting (SLM), with the resultant microstructures and corrosion properties characterised and compared to wrought AA2024-T3. Microstructural characterisation was carried out using transmission electron microscopy (TEM), revealing SLM produced AA2024 included a population of ?-phase (Al2Cu) in preference to S-phase (Al2CuMg) typical of wrought AA2024. Additionally, the corrosion properties were investigated by potentiodynamic polarisation in a range of NaCl concentrations, whilst elemental corrosion rates were also determined (including for open circuit exposure conditions) and quantified in situ with an inductively coupled plasma mass spectrometer coupled with an electrochemical flow cell. Results revealed a significant improvement in the corrosion resistance, and elemental dissolution of AM prepared 2024 relative to wrought AA2024-T3.INTRODUCTION Aluminium alloys remain the preferred candidate materials in applications requiring a balance of low density and strength. The ability to produce net shape components from aluminium alloys has accelerated due to recent developments in metal-based additive manufacturing (AM) technology, including selective laser melting (SLM) and powder bed 3D printing. The AM of Al-alloys, including Al-Si-Mg (namely AlSi10Mg), has become widespread commercially in recent years. Alloys including AlSi10Mg offer reliable and reproducible production by AM, however such alloys (and variants thereof) are not high strength alloys. The pursuit of higher strength AM Al-alloys presents significant merit to multiple industries; however, such higher strength AM Al-alloys have not been widely studied to date. The solidification of high strength Al-alloys during conventional (casting) operations needs to be executed in a manner that avoids so-called =hot-tearing‘, which can arise as a result of the solute type and loading. A report on the solidification of a high strength Al-alloy prepared by AM, along with factors related to solidification, was recently covered by Pollock and co-workers (Martin et al., 2017). It was reported that AM of high-strength aluminium alloys (which have to date been principally based on the compositions of wrought high strength Al-alloys) may lead to undesirable microstructures that reduce fatigue life and result in poor fracture toughness; presently limiting the application of AM to lower strength aluminium alloys (with cast-like Al-alloy compositions) to date."

Jan 1, 2018

By P. Leo

Al-Mg-Si alloys are widely used as medium-strength structural materials; extrusion is the most common processing route. In the present hot deformation investigation of a 6060 alloy, the microstructure of the alloy has been analyzed in the as-cast state, after homogenization heat treatment and after hot deformation by tensile tests in the range 400-490°C and 10-4 to 10-2s-1 on both as cast and homogenized alloys. After deformation the microstructure of the as-cast alloy exhibited cavitation. The flow curves at the lowest test temperature T show a gradual softening after a stress peak, being more evident for the alloy deformed in the homogenized state in association with a high yield stress; at higher T a plateau is attained which is lower as T rises and strain rates decrease. For each fixed T, the ductility decreases as strain rate increases for the homogenized alloy whereas, for the as cast alloy, it rises with strain rate. Constitutive analysis gives Q = 240kJ1mol for the homogenized alloy in agreement with published values; this indicates a more rapid strength decline with rising T than Al, suitable for good hot workability along with the lack of cavitation.

Jan 1, 2011

By P. Bacher, L. Dubourg, M. Jahazi, G. Dezaise

Effect of friction stir welding parameters and natural ageing on weld properties are reported. Using a Taguchi design of experiment, attempt is made to systematically examine the influences of the welding speed, tool rotation speed, forge force, tilt angle and pitch ratio on the weld size and ultimate tensile strength of FSWed joints. One millimetre thick plates of AA7075-T6 were welded in lap joint configuration. Samples were characterized by optical microscopy, hardness and tensile measurements. Trends suggested by the results and directions for further investigation are discussed.

Jan 1, 2006