Microstructural Characteristics of High Rate Plastic

Deformation in Elektron™ WE43 Magnesium Alloy

by Joseph Hamilton, Sarah T. Brennan, Yongho Sohn, Bruce Davis,

Rick DeLorme, and Kyu Cho

ARL-RP-363 April 2012

A reprint from the Proceedings of the TMS 141st Annual Meeting and Exhibition, Orlando, FL,

pp. 433–438, 11 March 2012.

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ARL-RP-363 April 2012

Microstructural Characteristics of High Rate Plastic

Deformation in Elektron™ WE43 Magnesium Alloy

Joseph Hamilton, Sara T. Brennan, and Yongho Sohn

University of Central Florida

Bruce Davis and Rick DeLorme Magnesium Elektron North America

Kyu Cho Weapons and Materials Research Directorate, ARL

A reprint from the Proceedings of the TMS 141st Annual Meeting and Exhibition, Orlando, FL,

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Microstructural Characteristics of High Rate Plastic Deformation in Elektron™

WE43 Magnesium Alloy

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Joseph Hamilton,* Sarah T. Brennan,

* Yongho Sohn,

* Bruce Davis,

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Rick DeLorme,† and Kyu Cho

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*University of Central Florida, 12443 Research Parkway, Ste. 304, Orlando, FL 32826

†Magnesium Elektron North America, 1001 College St., P.O. Box 258, Madison, IL 62060

A reprint from the Proceedings of the TMS 141st Annual Meeting and Exhibition, Orlando, FL, pp. 433–438, 11 March 2012.

14. ABSTRACT

High strain rate deformation of WE43 magnesium alloy was carried out by high velocity impacts, and the characteristics and

mechanisms of microstructural damage were examined. Six samples were subjected to a variety of high velocity impact

loadings that resulted in both partial and full damage. Optical, scanning and transmission electron microscopy analyses were

performed in order to identify regions of shear localization. These regions were used to map, both quantitatively and

qualitatively, the effects of deformation on the microstructure. Shear localization was observed in every sample, and its depth

was measured. Evidence of shear localization was observed to a greater extent in samples with partial damage while fracturing

was observed more frequently in samples with full damage.

15. SUBJECT TERMS

magnesium, WE43, high-strain rate, severe plastic deformation, shear localization

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Kyu Cho a. REPORT

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Microstructural Characteristics of High Rate Plastic Deformation in Elektron™ WE43 Magnesium Alloy

Joseph Hamilton1, Sarah T. Brennan1, Yongho Sohn1, Bruce Davis2, Rick DeLorme2, Kyu Cho31University of Central Florida; 12443 Research Parkway, Suite 304; Orlando, FL 32826, USA

2Magnesium Elektron North America;1001 College St.; P.O. Box 258,; Madison, IL 62060, USA3US Army Research Laboratory; 2800 Powder Mill Rd.; Adelphi, MD 20783, USA

Keywords: Magnesium, High-Strain Rate, Severe Plastic Deformation, Shear Localization

Abstract

High strain rate deformation of WE43 magnesium alloy was carried out by high velocity impacts, and the characteristics and mechanisms of microstructural damage were examined. Six samples were subjected to a variety of high velocity impact loadings that resulted in both partial and full damage. Optical, scanning and transmission electron microscopy analyses were performed in order to identify regions of shear localization. These regions were used to map, both quantitatively and qualitatively, the effects of deformation on the microstructure. Shear localization was observed in every sample, and its depth was measured. Evidence of shear localization was observed to a greater extent in samples with partial damage while fracturing was observed more frequently in samples with full damage.

Introduction

Over the past two decades, there has been an increasing interest in the commercial use of magnesium alloys in various applicationswhere a high strength-to-weight ratio is important, such as in aerospace, automotive, and defense industries [1]. Not only is magnesium an extremely lightweight metal, weighing 30% less than aluminum, and 70% less than steel, it also has the highest strength-to-weight ratio among any of the commonly used non-ferrous and ferrous metallic materials [2].

As magnesium is used more often in structural components, there is an increasing demand for a better understanding of the microstructural evolution during deformation. Due to the limited number of independent slip systems in a hexagonal close packed(HCP) crystal structure, basal slip and twinning are the prevalent mechanism of deformation at lower temperatures, such as 200°Cand below, with low strain rates ranging between 1.8 x 10-5 to 1.8 x 10-3 s-1 [3]. Wei et al., showed that at elevated temperatures ranging from 350 to 425°C, and strain rates ranging from 10-3 to 1-1 s-1, magnesium alloys exhibited excellent superplasticity, due to activation of non-basal slip systems, and grain boundary sliding (GBS) deformation mechanism under these conditions [4]. It has been noted that as the temperature is increased above 200°C the critical resolved shear stress for the non-basal slip systems is reduced, and the activation of these additional mechanisms results in an increase in ductility and a decrease of yield and flow stress [5]. However, at high strain rates, such as greater than 103 s-1, the primary mechanism of deformation in metals has been shown to be shear localization [6] [7].

The shear localization seen in high strain rate deformation is characterized by adiabatic shear bands (ASB). These regions of shear deformation are the result of adiabatic shear, shear instabilities, and shear localization. The main mechanisms of deformation within the ASBs are dynamic recrystallization

(DRX), and GBS. It is through these mechanisms that the microstructure accommodates the high kinetic energy seen in severe plastic deformation occurring at high strain rates, such as ~103-106 s-1 [8].

The post-mortem characterization of a deformed microstructure is important to the understanding of the microstructure during deformation, and until a technique is developed that allows real-time diagnostic of the microstructure as it evolves, it will remain as the primary means of investigation of the phenomenon that occur inside shear localization. The purpose of this study was to analyze, through a variety of microscopy techniques, the microstructure of WE43 magnesium alloy samples post-deformation.

Experimental Methods

A post-mortem analysis was performed on six 80mm thick WE43 samples (3.7-4.3% Yttrium, 2.4-4.4% Rare Earths, 0.4% Zirconium, balance Magnesium), that were produced in the T5 condition, thermally quenched after high-temperature rolling, and then artificially aged. The samples were then subjected to high velocity impacts that resulted in varying levels of severe plastic deformation (SPD). The samples were assigned the nomenclature of A, B, and C based on increasing level of damage. The samples were also labeled as Full, or Partial damaged samples based on the extent of SPD. Examples of the cross sectioned regions areshown in Figures 1 and 2.

Figure 1. C-Partial sample, after cross sectioning, arrow indicates direction of impact.

In order to preserve the microstructure, preparation methods were chosen that would induce the least amount of damage. Therefore, waterjet cutting was used to cross-section the deformed samples,

Magnesium Technology 2012 Edited by: Suveen N. Mathaudhu, Wim H. Sillekens, Neale R. Neelameggham, and Norbert Hort

TMS (The Minerals, Metals & Materials Society), 2012

433

and a diamond wafer saw was used to perform further sectioning at low-speed. A map is shown in Figure 3 of the sectioning performed on the sample A-Partial, and this is representative of the method used to section all of the samples. The samples were then mounted in epoxy discs, and mechanically polished to 0.05-µm using alumina. Then the samples were etched by submersion in a acetic-picral etchant (100mL ethanol, 6g picric, 10ml water, 5ml acetic).

Figure 2. C-Full sample after cross sectioning, arrow indicates direction of impact.

Figure 3. Map of sectioning performed on sample A-Partial, the arrow indicates direction of impact.

In order to characterize different aspects of the deformation a variety of approaches were utilized. Optical microscopy (OM), scanning electron microscopy (SEM), and transmission electron microscopy (TEM) were performed on both deformed and undeformed samples in order to identify and characterize regions of interest.

OM was used for both quantitative and qualitative investigation ofshear bands, regions of dynamic recrystallization (DRX), grain size, shear localization, fractures, and damage on the microscale.An Olympus LEXT OLS3000 confocal optical microscope in conjunction with Olympus LEXT software was used for OMimaging. IQ Materials software was used on composite OM images in order to quantify the extent of shear localization.Measurements were made for the depth of the shear localization

that extended from the edge of deformation. The regions of deformed and undeformed material were qualitatively distinguished by the features observed with OM. The regions of shear deformation exhibited elongated grains, with shear bands and DRX. The undeformed regions were composed of equiaxed grains and were similar in microstructure to the bulk material.Measurements were taken normal to the edge, across the deformed microstructure, and stopped once an undeformed region was reached, examples of these types of measurements can be seen in Figure 4. The measurements for each sample were averaged, and then the averages for all of the samples were plotted to show the progression of shear localization through the cross-sectioned sample.

Figure 4. Composite OM image, arrows are example of measurements made of region of shear localization.

SEM was used to further investigate regions of interest at the microscale. A Zeiss Ultra-55 field emission SEM equipped with x-ray energy dispersive spectroscopy (XEDS) was used. TEM was used to investigate the grain size, and formation of precipitates at the nanoscale in regions of DRX found in shear bands, as well as suspected twinning seen throughout the samples. A FEI/Tecnai F30 300keV TEM was utilized for this.

Results and Discussion

Microstructural Characteristics

A section of bulk material was removed and analyzed forcomparison to damaged regions. The bulk microstructure (i.e.undamaged) is shown in Figure 5. It was assumed that any twinning, or other characteristics of deformation seen in the bulk

434

microstructure, was a result of the processing methods used in manufacturing the samples. Although a significant amount of twinning was observed near the surface of the penetration channel, this paper focuses on the shear localization and the formation of shear bands. The presence of profuse twinning was examined by TEM, and will be reported in future publications.

Figure 5. OM of bulk microstructure.

The deformed regions of the samples exhibited a large amount of shear localization, characterized by shear bands and DRX. Shear localization was observed in regions of SPD, and was seen to vary throughout the samples. However, the level of shear localization was highly concentrated in certain areas, and in particular was seen to a greater extent in the Partial-group of samples. These regions were examined further using TEM, and quantified using IQ Materials software.

Figure 6. Macroscopic image of the cross-section of sampleB-Full, showing microstructural deformation regions I, II, and III

In general, throughout all of the samples, there were three separate regions of distinctive deformation characteristics. Figure 6 shows these regions on the B-Full sample. Region I, the initial area of impact, was characterized by a rough fracture surface along the edge, and a microstructure that was similar to that of the bulk microstructure. An OM of region I is shown in Figure 7. The microstructure of region II showed extensive shear localization, with ASB, DRX, and a smooth edge along the channel aspresented in Figure 8. Similar to Region I, region III was composed of a microstructure very similar to that of the bulk microstructure, however, there is a large amount of shear fracturing along the edge. Figure 9 shows the microstructure ofregion III. The Partial-damage samples did not have a region III, but instead were composed of regions I and II, except in the case of C-Partial which exhibited a large amount of bulging petal fractures.

Figure 7. OM image showing typical microstructure of region I.

Figure 8. OM image showing shear localization that characterized region II.

Figure 9. OM image of region III, similar fracture edge and microstructure to that of Region I.

The major variation in these regions, as seen when comparing between each of the sample sets, was the overall size of the regions. Of all of the sample sets, those in sample set A showed the smallest regions I and III, while sample set C showed the largest. As regions I and III were composed of large quantities of shear fracture surfaces, it is likely the higher level of energy transferred during the impacts for sample set C were the largest,

435

thus resulting in a greater amount of shear fracturing instead of localized shear deformation.

Shear Localization Depth

Shear localization was present in every deformed cross-sectioned sample. In order to appreciate the extent of shear localization, composite OM images were formed, and the region of shear deformation was measured using IQ Materials software. Each sectioned sample (as shown in Figure 3 for sample A-Partial), of both the Partial and Full samples of each sample set was analyzed.The measurements for each sample were averaged, and the plotsare presented in Figures 10, 11, and 12.

Figure 10. Shear localization depth of sample set A.

Figure 11. Shear localization depth of sample set B.

Figure 12. Shear localization depth of sample set C.

Sample set A exhibited a similar quantity of shear localization in both the Full and Partial samples. Furthermore, the overall magnitude of shear depth was to a much lesser degree than either the B or C samples which were both subjected to a much greaterlevel of plastic deformation. The lower level of shear present in sample set A was a result of the lower level of kinetic energy transferred from the high velocity impact.

In sample set B, there was a marked difference in the level of shear localization present in the Partial sample, when compared to the Full sample. Overall, the Partial sample exhibited a greater amount of shear localization, as can be seen in locations 5-8 of Figure 12. In the Full sample, in the regions of lower shear localization, there was a high level of shear fracturing observed.

The greatest magnitude of shear localization was measured in sample set C, as was expected due to the gross amount of severeplastic deformation observed. Of note, the sample locations 5, 6,and 7 of the Partial sample were positioned in such a way, in relation to the damaged edge, to make it impractical to measure shear depth. However, qualitatively these samples had a low amount of shear localization, and there was an extensive amount of fracturing observed, as can readily be seen on a macroscopic level on the right side of the sample in Figure 13.

Figure 13. Map of sectioned samples of C-Partial

Overall, shear localization was seen to the greatest extent in the Partial sample group. The shear localization is a result of the microstructure of the material accommodating the kinetic energyfrom the high velocity impact. When the kinetic energy exceeded a certain amount, full penetration of the sample would occur, and this was characterized by a much higher level of fracturing in the microstructure. Below that level, the material would accommodate the kinetic energy not by fracturing, but instead by shear localization.

A limitation of this study is that any region of the sample that was completely fractured away was no longer attached to the sample, and as a result, not available for post-mortem analysis. It is possible that shear localization was present in these portions of the sample, but no analysis was able to be performed.

Adiabatic Shear Bands

Adiabatic shear bands were a ubiquitous characteristic of regions of shear localization. The shear bands were composed of areas of DRX, which is a result of adiabatic temperature rise [8]. Bothregions of DRX, and the transition zone between the DRX and neighboring microstructure, were examined by TEM. The shear band that was analyzed is shown in Figure 14.

436

437

Figure 14. SEM-SE image, with dotted outline of the region of DRX within shear band, that was analyzed by TEM.

DRX I Mg matrix Figure 15. Diagram of shear band, and neighboring

microstructure.

The shear band was composed of two distinct regions as schematically illustrated in Figure 15. The first region of DRX was composed of small equiaxed recrystallized grains (

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Figure 19. Diffraction pattern of large precipitate found in small grain region of bulk material, indexing to be 13 phase.

The smaller precipitates located in the coarse grains were analyzed by XEDS as shown in Figure 20, and the composition was quantified as Mg74.sYn.zNds.o (at%). This suggests that these percipitates are most likely 13" phase: Mg3(Y o.ssNdo.ts).

"' c :> 0 (.)

300 Mg I • EOX HAAOF Detector /Vea 1 I

200

100 Cu

5 10 15 20 Energy (keV)

Figure 20. XEDS results of smaller precipitates contained in coarse grains of bulk microstructure.

Conclusions

After a set of six WE43 magnesium alloy samples were subjected to different high-velocity impacts, which resulted in high-strain rate severe plastic deformation, the microstructures of the deformed samples were analyzed and compared to the bulk material. Shear localization, characterized by bands of dynamic recrystallization, was seen throughout the damaged regions. However, samples that were subjected to impacts that resulted in only partial damage were seen to have a larger quantity of shear localization, compared to those samples that experienced impacts that resulted in full damage. Furthermore, the samples with full damage had a lower occurrence of shear localization in the

regions of high shear fracture. This indicates that the material would accommodate the lower level of kinetic energy, which was insufficient to result in shear fracture, by shear localization in the microstructure.

The regions of shear localization, when analyzed by TEM showed distinct variation from the bulk material microstructure. The bulk material was composed of regions with coarse grains containing small elongated precipitates of the 13" phase, and smaller grain regions with large 13 phase precipitates. Microstructure within the ASB was distinctively different. The shear bands were composed of small (

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0433.pdfWelcomeTMS Proceedings 2012Full-TitleCopyright PagePrefaceAbout the EditorAbout the OrganizersSession ChairsReviewer PoolTable of ContentsMagnesium Technology 2012Magnesium Technology 2012Plenary SessionSession ChairsMagnesium Alloy Development using Phase Equilibria Computation and Microstructure ValidationAtoms-to-Grains Corrosion Modeling for Magnesium AlloysSolid State Joining of Magnesium to SteelGrain Evolution during High Temperature Necking of Magnesium AlloysProduction of Wide Shear-Rolled Magnesium Sheet for Part Forming

Primary ProductionSession ChairsCarbothermal Production of Magnesium: CSIRO's MagSonic\\8482; ProcessMagSonic\\8482; Carbothermal Technology Compared with the Electrolytic and Pidgeon ProcessesScaling-Up Solid Oxide Membrane Electrolysis Technology for Magnesium ProductionFluid Bed Dehydration of Magnesium ChlorideDemonstration of Solar-Pumped Laser-Induced Magnesium Production from Magnesium OxideMolten Salt Electrolysis of MgCl2 in a Cell with Rapid Chlorine Removal FeaturePreparation of Aluminum-Magnesium Alloy from Magnesium Oxide in RECl3- LiF-MgF2 Electrolyte by Molten Salts Electrolysis MethodExperimental Study on Magnesium Extracted from Ascharite Mineral by AluminiumElectrochemical Investigation on Chlorine and Electrolyte Intercalation into Graphite Anodes during Magnesium Electrolysis ProcessOptimization of Preparation for MgO by Calcination from Basic Magnesium Carbonate using Response Surface Methodology

Deformation MechanismsSession ChairsAn Elasto-Plastic Micromechanical Method for Twin Driven PlasticityAnomalous Twin Bands in AZ31 Mg Sheet BendingFormation of Nano-Scale Twins and Low Angle Grain Boundaries during Fracture of Fine Grained Magnesium AlloysTensile and Creep Deformation Mechanisms in Rolled AZ31Structural Origin of Reversible Twinning, Non-Schmid Effect, Incoherent Twin Boundaries and Texture of Hexagonal Close-Packed MetalsLength Changes in Extruded Magnesium Alloy Bars Under Large Strain Free-End TorsionNano-Indentation Studies of Twinned Magnesium Single CrystalsNon-Basal Textures in Magnesium Alloy Strips by Extrusion-MachiningThe Elastic-Plastic Transition in Magnesium Alloys

Casting and SolidificationSession ChairsTwin Roll Casting of Thin AZ31 Magnesium Alloy Strip with Uniform Microstructure and ChemistryMathematical Modeling of the Twin Roll Casting Process for AZ31 Magnesium Alloy ΠEffect of Set-Back DistanceIntermetallic Phase Formation and Growth in the Mg-Y SystemMicrostructure and Mechanical Properties of High Pressure Die Cast AM50 Magnesium Alloy Containing CeMelt Conditioned DC (MC-DC) Casting of Magnesium AlloysEffect of the Solidification Rate on Microstructure of Cast Mg Alloys at Low SuperheatImpact and Energy Dissipation Characteristics of Squeeze and Die Cast Magnesium Alloy AM60Sliding Wear Behavior of Squeeze Cast Magnesium Composite AM60-9% (Al2O3)fSolidification Studies of Mg-Al Binary Alloys

Alloy and Microstructural DesignSession ChairsAge Hardening Behavior of Mg-1.2Sn-1.7Zn Alloy Containing AlEffect of Nano-Alumina and Copper Micron Size Particulates on Microstructure and Mechanical Properties of Magnesium Alloy AZ31Evaluating the Effect of Pre-Ageing Deformation on Beta' Precipitate Size and Distribution in Mg-Zn(-Y) AlloysEffect of Zinc Content on the Microstructure and Mechanical Properties of Extruded Mg-Zn-Y-La Alloys with LPSO PhaseEffect of Ca Addition on the Microstructural and Mechanical Properties of AZ51/1.5 Al2O3 Magnesium NanocompositeEffect of Zn Concentration and Grain Size on Prismatic Slip in Mg-Zn Binary AlloysEffects of Ca on Microstructure and Mechanical Properties of ZA62 AlloysMechanical Properties and High-temperature Oxidation Behaivor of Mg-Al-Zn-Ca-Y Magnesium AlloysEffects of Si on Microstructure and Mechanical Properties of Mg-5Sn-2Sr Alloy

Corrosion and CoatingSession Chairs"Electroless" E-Coating for Mg AlloysThe Influence of Galvanic Current on Cerium-Based Conversion Coatings on Mg, Al, and Galvanized Steel CouplesEffect of Sn4+ Additives on the Microstructure and Corrosion Resistance of Anodic Coating Formed on AZ31 Magnesium Alloy in Alkaline SolutionEffect of Thickness on the Morphology and Corrosion Behavior of Cerium-Based Conversion Coatings on AZ31B Magnesium AlloyMechanical and Corrosion Properties of As-Cast and Extruded MG10GD Alloy for Biomedical ApplicationCorrosion Behavior of Various Steels by AZ31 Magnesium MeltCorrosion of Ultrasonic Spot Welded Joints of Magnesium to SteelEffect of Some Microstructural Parameters on the Corrosion Resistance of Magnesium AlloysInfluence of Aluminum Content on Corrosion Resistance of Mg-Al Alloys Containing Copper and Zinc

High Temperature Processing and PropertiesSession ChairsEffect of Rolling Temperature on the AZ31B Magnesium Alloy MicrostructureHot Formability Curves for Four AZ31B Magnesium Alloy Sheets Obtained by the Pneumatic Stretching TestTexture Evolution during Hot Deformation Processing of Mg-3Sn-2Ca-0.4Al AlloyThe Effects of Strain and Stress State in Hot Forming of Mg AZ31 SheetEffect of Strain Rate on Dynamic Recrystallization in a Magnesium Alloy under Compression at High TemperatureEffect of Strain Rate on the Kinetics of Hot Deformation of AZ31 with Different Initial TexturePrecipitation Behaviour of Micro-Alloyed Mg-Al-Ca Alloys during Heat Treatment and Hot CompressionDiffusion Couple Investigation of the Mg-Zn SystemBiaxial Deformation Behavior of AZ31 Magnesium Alloy at High Temperatures

Processing-Microstructure-Property Relationships ISession ChairsMicrostructure Modeling of Magnesium Alloys for Engineering Property PredictionMicrostructure Modification and Deformation Behavior of Fine-Grained AZ61 Sheet Produced by Thixomolding and Thermomechanical Processing (TTMP)Development of High Strength and Toughness Magnesium Alloy by Grain Boundary ControlEffects of Direct Extrusion Process on Microstructure, Texture Evolution and Yield Strength of Magnesium Alloy AZ31Comparison of Tensile Properties and Crystallographic Texture of Three Magnesium Alloy SheetsStrain Hardening of ZK60 Magnesium AlloysStrain-Rate Effects of Sand-Cast and Die-Cast Magnesium Alloys under Compressive LoadingMechanical Properties of Newly Developed Mg-Alloys AMX602 AND AZXE7111 under Quasi-Static and Dynamic LoadingPhase Field Modeling of Beta1 Precipitation in WE54 Alloy

Advanced Processing and JoiningSession ChairsMicrostructure and Creep Properties of MEZ Magnesium Alloy Processed by ThixocastingThe Effect of Friction Stir Processing on Microstructure and Tensile Behavior of Thixomolded AZ91 Magnesium AlloyEffect of Weld Structure on Fatigue Life of Friction Stir Spot Welding in Magnesium AZ31 AlloyEffect of Corrosion on the Tensile Properties of Friction-Stir Welded AZ31B SheetOn the Effect of Ti2AlC on the Formation of Thermally Stable Mg Nano GrainsExperimental Investigations into the Deformation Behavior of Thixo-Molded Mg AZ61L Sheet AlloyEffects of High Temperature Shot Peening on Surface Characteristics and Fatigue Properties of Forged AZ31 Magnesium AlloysSolid Solution Hardening Effect of Aluminum on the Creep Deformation of AZ91 Magnesium Alloy

Processing-Microstructure-Property Relationships IISession ChairsEnhancement of Strength and Ductility of Mg96Zn2Y2 Rolled Sheet by Controlling Structure and Plastic DeformationMicrostructural Characteristics of High Rate Plastic Deformation in Elektron WE43 Magnesium AlloysMicrostructure and Mechanical Properties of As-Extruded Mg-Sn-Al-Zn AlloysTensile Properties of Three Preform-Annealed Magnesium Alloy SheetsThe Role of Intermetallics on Creep Behaviour of Extruded Magnesium AlloysHigh Performance Mg-System Alloys for Weight Saving Applications: First Year Results from the GREEN METALLURGY EU ProjectEffect of Extrusion Conditions on Microstructure and Texture of Mg-1% Mn and Mg-1% Mn-1.6% Sr AlloysMicrostructural Characterization of Homogenised and Aged Mg-Gd-Nd AlloysOn the Deformed Microstructure of Rolled Mg-2.9Y

Energy and Biomedical / Primary ProductionSession ChairsIn-Vitro Corrosion Studies of Bioabsorbable Magnesium AlloysHigh-Capacity Hydrogen-Based Green-Energy Storage Solutions for the Grid BalancingReaction Sintering of Mg2Si Thermoelectric Materials by Microwave IrradiationCharge-Discharge Mechanism of MgC Powders and Mg-Li Alloy Thin Film MaterialsControl of Yttrium Diffusion Out of Yttria Stabilized Zirconia During SOM Electrolysis for Magnesium ProductionStudy on the Thermodynamic and Experimental Carbothermic Reduction of GarnieriteMechanism of Carbothermic Reduction of Magnesia and Reverse Reaction

Poster SessionSession ChairsCombination of Cooling Curve and Micro-Chemical Phase Analysis of Rapidly Quenched Magnesium AM60B AlloyEffects of Friction Stir Process on the Tensile Properties of AZ61 Magnesium Alloy at Room Temperature to 200?Magnesium Recycling of Partially Oxidized, Mixed Magnesium-Aluminum Scrap through Combined Refining and Solid Oxide Membrane (SOM) Electrolysis ProcessesMicrostructure and Mechanical Properties of Mg-5Sn-5Zn-xCa AlloysPhase Dissolution of Gamma-Mg17Al12 during Homogenization of As-Cast AZ80 Magnesium Alloy and Its Effect on Room Temperature Mechanical PropertiesPrecipitation Formation and Grain Refinement of Mg-Al-Sn Alloy during Hot DeformationThe Effect of Precipitation on the Mechanical Properties of Extruded AZ80Influence of Section Thickness on Microstructure and Mechanical Properties of Squeeze Cast Magnesium Alloy AM60

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