Home Kinetics of oxide scale growth on a (Ti, Mo)5Si3 based oxidation resistant Mo-Ti-Si alloy at 900-1300∘C
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Kinetics of oxide scale growth on a (Ti, Mo)5Si3 based oxidation resistant Mo-Ti-Si alloy at 900-1300∘C

  • Sanjib Majumdar EMAIL logo , Pankaj Kumar Singh , Ajoy Kumar Pandey and G.V.S. Nageswara Rao
Published/Copyright: December 5, 2019
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High Temperature Materials and Processes
From the journal High Temperature Materials and Processes Volume 38 Issue 2019

Abstract

High-temperature oxidation behaviour of Mo-40Ti-30Si (at.%) alloy was investigated in the temperature regime of 900-1300∘C in air. Isothermal weight change data recorded up to 100 h of exposure revealed parabolic weight gain kinetics at all the tested temperatures. The protective oxide scale composed with SiO2 (silica) and TiO2 (titania) forming a duplex oxide microstructure consisting of TiO2 particles embedded in the continuous SiO2 matrix. The oxide scale showed parabolic growth kinetics, and the activation energies for the scale growth were found to be 72.2 kJ/mol in 900-1200∘C and 324.9 kJ/mol in 1200-1300∘C. The kinetics of the protective scale growth on the alloy surface was mainly controlled by the growth of the silica film and the inward diffusion of oxygen through the duplex oxide layer.

Keywords: High-temperature; Oxidation; Oxide scale; Kinetics; Activation energy

1 Introduction

High-temperature oxidation resistance and room temperature fracture toughness are the two key issues to be resolved for developing molybdenum based materials [1, 2] to replace nickel based superalloys used in energy producing devices operated at high temperatures. Molybdenum shows linear oxidation behaviour when exposed to air with increasing temperature [3]. The oxidation reactions follow Mo→ MoO2→ MoO3 as the temperature is increased from room temperature. MoO3 melts at about 795∘C and it also possesses high vapour pressure at elevated temperatures. Therefore, the oxidation of Mo exhibits an initial increase in weight as the temperature is increased, and beyond certain temperature, weight loss is observed due to volatilization of MoO3 [4]. Mo-Si-B alloy with varying composition with respect to Si and B are studied in detail [5, 6, 7]. The alloy shows improved oxidation resistance as the Si content is increased [5]. Addition of boron (B) leads to the formation of superior oxidation resistant Mo5SiB2 (T2) phase in the three phase Moss- Mo3Si-T2 microstructure. It forms a protective borosilica scale on the alloy surface. For reducing the density and improving the fracture toughness, a part of Mo was substituted with titanium (Ti) and studies were done on Mo-Ti-Si-B alloys [8, 9, 10, 11]. Although, the alloy showed superior creep properties [8, 9], the oxidation resistance has been poor at elevated temperatures. The oxide scale mainly consisted with SiO2-TiO2 type porous duplex scale. Evaporation of B2O3 and MoO3 through the porous SiO2-TiO2 leading to loss of weight was reported [9]. Severe vaporization loss of theMo-Ti-Si-B alloy was observed with increasing temperature beyond 1100∘C. Presence of B2O3 in silica reduces its viscosity at intermediate temperatures 800950∘C. However, beyond 950∘C, B2O3 starts evaporating and the viscosity of the silica rich scale increases. The rate of evaporation of B2O3increases at higher temperatures leading to the formation of pores in the oxide scale which enhances the vaporization of MoO3 and catastrophic oxidation. Therefore, boron-free Mo-Si-Ti alloys are investigated recently [12, 13, 14]. Ti-addition in Mo-Si system would improve the toughness and reduce the density of the materials while upgrading the oxidation performance as well. The density of the Mo-Ti-Si materials was reported to be much lower than that of conventional nickel based super-alloys [14]. The stability of different phases in ternary Mo-Ti-Si system is reported earlier [15].

In the present investigation, the detailed oxidation behaviour of Mo-40Ti-30Si (in at.%) system was studied in a wide temperature regime of 900-1300∘C in static air. The weight change behaviour of the alloy was recorded. The cross-section of the oxide scale was analysed using SEM and EDS. The growth kinetic of the oxide scale was evaluated. The superior oxidation resistance of the alloy was understood using microstructural observations and thermodynamic considerations.

2 Experimental

Mo-40Ti-30Si (in at.%) alloy was produced by adopting powder metallurgical processing route. Mechanical alloying of the elemental powder was carried out using a planetary ball mill. Reactive hot pressing of the alloy powder was conducted at 1600∘C for producing the alloy plates. The detailed preparatory procedure for the alloy is presented earlier [14]. Figure 1 shows the back scattered electron microstructure of the hot pressed alloy. The alloy is composed of the hexagonal type matrix phase (Ti, Mo)5Si3 and (Ti, Mo)3Si precipitates (dark colour) forming a composite type microstructure. The composition and grain structures of the hot pressed alloy were reported earlier [14]. The (Ti, Mo)5Si3 phase contains Ti-34.7 at.%, Mo-26.4 at.%, Si-38.9 at.%, and (Ti, Mo)3Si precipitate is comprised with Ti-63.2 at.%, Mo-14.3 at.%, Si-22.5 at.%. The density of the alloy was measured as 5.8 g/cm3, much lower than that of conventional nickel based superalloys.

Figure 1 BSE microstructure of the Mo-40Ti-30Si system containing (Ti, Mo)5Si3 matrix and (Ti, Mo)3Si precipitates.
Figure 1

BSE microstructure of the Mo-40Ti-30Si system containing (Ti, Mo)5Si3 matrix and (Ti, Mo)3Si precipitates.

Electro-discharge machining (EDM) equipment was used to cut the mall specimens of dimensions 10 mm × 5 mm × 5 mm from the hot pressed plates of the alloy. The specimens were subsequently ground to 1200 grit SiC embedded emery paper. All the sides of the specimens were ground and the sharp edges or corners were removed. The samples were thoroughly cleaned ultrasonically in water and acetone bath. Isothermal oxidation tests of the alloy samples were conducted at 900, 1000, 1100, 1200 and 1300∘C for different time intervals ranging from 0.5 h to 100 h. The samples were kept inside the muffle type furnace using alumina boats and the weight of the boat containing the specimen was measured before and after the oxidation tests. A Sartorius make micro balance was used to measure the weight accurately. The samples were loaded inside the furnace when the required temperature was reached inside the chamber. Each sample was carefully weighed before and after exposure to determine the weight changes during the oxidation. The morphology and the composition of the oxide layer were investigated by observing the surface as well as the cross-section using a Camscan made SEM attached with Oxford EDS (Model: X-max 80). The oxidation-test samples were mounted in conducting mould applying the hot mounting procedure. The metallographic samples were prepared by grinding the mounted specimens up to 1 μm diamond finish and subsequent polishing with colloidal silica solution.

3 Results

3.1 Oxidation behaviour

Mo-40Ti-30Si alloy exhibited the gain in weight behaviour during isothermal oxidation in the temperature regime of 900-1300∘C. The weight change data recorded at different time intervals under isothermal oxidation conditions are plotted as Δw vs t0.5 in Figure 2. The weight change data for 900, 1000 and 1300∘C are taken from the reference 14 for comparison. The weight change data was measured at least three times, and the error in the measured data may be considered as ±5% due to manual handling of the oxidized samples. The alloy showed superior oxidation resistance at 900-1200∘C in air. Although the magnitude of weight gain increased with increasing temperature and time, the absolute value of the maximum weight gain observed at 1200∘C after 100 h was found to be very low (~ 3.7 mg/cm2). At 1300∘C, a faster weight gain was observed, and the value of the weight gain after 50 h of exposure in air was of the order of 25.6mg/cm2. Beyond 50 h, the scale was spalling off and therefore, the weight change data could not be recorded. Therefore, the alloy showed superior oxidation resistance up to 1200∘C for longer exposure times, and at 1300∘C for 50 h. Curve fitting was done to understand the weight gain kinetics of oxidation of the alloy. Linear fitting of weight change (Δw) against t0.5 in Figure 2 indicated that the weight gain kinetics followed a parabolic behaviour. The calculated weight gain rate constant values ranged between 0.12-0.39mg/cm2·h0.5 in 900-1200∘C with a high value of 3.25 mg/cm2·h0.5 at 1300∘C. A drastic increase in the oxidation kinetics was observed from 1200 to 1300∘C, which could be due to the mechanistic change of oxidation of the alloy in this temperature regime. The weight gain rate constant values at 1300∘C were found to be about 10-15 times higher than those for 900-1200∘C.

Figure 2 Weight change data indicating parabolic oxidation behaviour of Mo-40Ti-30Si in static air.
Figure 2

Weight change data indicating parabolic oxidation behaviour of Mo-40Ti-30Si in static air.

3.2 Growth of oxide scale

For accurately measuring the thickness of the oxide scales the metallographic samples were prepared using hot mounting with conducting mould. Back scattered electron image analysis is preferred as the Z-contrast between the substrate and oxide scale is clearly revealed. Figure 3 represents the BSE cross-sectional showing the oxide scale formed at 1100∘C at different time intervals. The similarities are observed in the oxide scale formed at all the four temperatures between 900 and 1200∘C. Therefore, the one set of micrographs from the samples tested 1100∘C are presented here (in Figure 3). The thickness of the oxide scale increased with increasing the time of exposure at 1100∘C. Comparing with the weight gain data presented in Figure 2, a one to one correlation could be established with the gain in weight and increase in thickness of the oxide scale with time at isothermal condition. The thickness of the oxide scale varied between 1 μm and 41 μm at 900-1200∘C temperature regime. The growth rate of the oxide scale was much higher at 1300∘C. The cross-section of the oxide scale along with Mo-40Ti-30Si alloy substrate formed at 1300∘C is presented in Figure 4. The thicknesses of the oxide scales are much higher (~185μmin 50h) at 1300∘C. The values of oxide scale thickness at different times and temperatures are presented in Figure 5. The thicknesses of the oxide scales were measured at about 5 different places. The error in measurement at lower thicknesses (~1 μm) was about ±10 %, whereas for higher thicknesses the measurement was accurate the variation of thickness was in ±5 % range. The analysis of the scale thickness data revealed a parabolic scale growth kinetics obeying the following law.

Figure 3 Cross-sectional BSE images of the Mo-Ti-Si composite oxidized at 1100∘C in air for (a) 1 h, (b) 25 h, (c) 50 h and (d) 100 h.
Figure 3

Cross-sectional BSE images of the Mo-Ti-Si composite oxidized at 1100∘C in air for (a) 1 h, (b) 25 h, (c) 50 h and (d) 100 h.

Figure 4 Cross-sectional BSE images of the Mo-Ti-Si composite oxidized at 1300∘C in air for (a) 0.5 h, (b) 5 h, (c) 25 h and (d) 50 h.
Figure 4

Cross-sectional BSE images of the Mo-Ti-Si composite oxidized at 1300∘C in air for (a) 0.5 h, (b) 5 h, (c) 25 h and (d) 50 h.

Figure 5 Variation of the thickness of the oxide scale with time at different temperatures.
Figure 5

Variation of the thickness of the oxide scale with time at different temperatures.

(1)h2=K1t

or,

(2)h=Kt1/2

where, h is the thickness of the oxide scale, t is the time and K is the scale growth rate constant. Figure 6 shows h vs t1/2 curves obtained from Figure 5 fitted in linear plots. The slope of the linear curves is the growth rate constant (K). Applying Arrhenius equation it follows.

Figure 6 Scale thickness (h) vs t1/2 plots confirming parabolic growth kinetics of the oxide scale.
Figure 6

Scale thickness (h) vs t1/2 plots confirming parabolic growth kinetics of the oxide scale.

(3)K=K0exp⁡(−Ea/RT)
(4)ln⁡K=ln⁡K0−Ea/RT

From the slope of the ln K vs 1/T, the activation energy (Ea) for the oxide scale growth is determined. Arrhenius plot for scale growth is presented in Figure 7. The data points in Figure 7 show two distinct regions of linear fitting indicating the change in mechanism from 900-1200∘C to 1200-1300∘C. The activation energies calculated from the slopes of the plots are respectively, 72.2 kJ/mol (17.2 kcal/mol) in 900-1200∘C and 324.9 kJ/mol (77.3 kcal/mol) in 1200-1300∘C.

Figure 7 Arrhenius plots between scale growth rate constant and 1/T indicating two different regions of oxide scale growth.
Figure 7

Arrhenius plots between scale growth rate constant and 1/T indicating two different regions of oxide scale growth.

4 Discussion

The alloy Mo-40Ti-30Si is composed of a matrix phase of (Ti, Mo)5Si3 along with the second phase precipitates of (Ti,Mo)3Si (Figure 1). The probable reactions occur during high-temperature exposure of the alloy in air are presented in the following.

(5)(Ti,Mo)5Si3+15.5O2→5TiO2+3SiO2+5MoO3
(6)(Ti,Mo)5Si3+8O2→5TiO2+3SiO2+5Mo
(7)3(Ti,Mo)5Si3+4O2→4SiO2+5(Ti,Mo)3Si
(8)(Ti,Mo)3Si+8.5O2→3TiO2+SiO2+3MoO3
(9)5(Ti,Mo)3Si+O2→10TiO2+SiO2+(Ti,Mo)5Si4

The abovementioned reactions are mainly based on stoichiometries. The reactions (5) and (8) predict the complete formation of oxides TiO2, SiO2 and MoO3.MoO3 will vaporize out at all the isothermal oxidation test conditions i.e. in 900-1300∘C. The calculations performed using stoichiometric composition predict a net weight loss of the order of 11.14mg per oxidation of 100mg of Mo-40Ti-30Si (at.%) alloy. However, all the isothermal oxidation data (Figure 2) showed weight gain behaviour. Therefore, oxidation of molybdenum forming MoO3 is suppressed. The probability of the occurrence of the reactions (6), (7) and (9) is higher during the oxidation of the alloy.

Figure 8 represents a clearer image of the oxide scale. The scale mainly consists of dark colour SiO2 (silica) matrix in which brighter TiO2 (titania) particles are embedded. The presence of these phases was confirmed by quantitative EDS analysis and XRD [14]. The brightest particles (marked as Ti-rich) in Figure 8 were found to be composed of two type of compositions namely Ti-50.9, Mo-22.1, Si-27.0 (in at.%) ((Ti, Mo)3Si type) and Ti-49.6, Si-50.4 ((Ti, Mo)5Si4 type). The standard deviation of EDS composition analysis data presented here may be considered as 1 at.% for each element. These analytical results also confirm the oxidation mechanisms following the reactions (7) and (9). Figure 9 shows a BSE image of the scale/substrate cross-section obtained at 1200∘C. A thin TiO2 rich layer is present at the outer layer. The oxide scale is mainly composed with duplex SiO2 (TiO2) oxides. The presence of very fine size bright particles rich in Ti or Mo is also detected throughout the oxide scale. Figure 10 represents a cross-sectional image and EDS X-ray maps for the elements Mo La, Ti Ka, Si Ka and O Ka. EDS maps clearly reveal that O Ka (Figure 10d) is present in the whole area of the scale. Si Ka and Ti Ka spots are clearly demarcated separately in Figures 10(b) and (c), respectively. Figure 10(e) indicates the presence of Mo-rich particles in the oxide scale and enrichment of Mo at the scale/alloy interface. The quantitative EDS analysis at the scale/alloy interface indicates the presence of Si-41.6, Ti-29.8,Mo-28.6 (in at.%) forming a Mo-rich (Ti, Mo)5Si4 type phase at the interface. Therefore, some amount of Mo is released through the reaction (6), which gets distributed in the silicide phases.

Figure 8 BSE image showing the microstructure of the oxide scale and the alloy substrate.
Figure 8

BSE image showing the microstructure of the oxide scale and the alloy substrate.

Figure 9 Cross-sectional BSE image indicating the presence of a TiO2 rich thin outer layer, and a Mo-rich layer at the scale/alloy interface.
Figure 9

Cross-sectional BSE image indicating the presence of a TiO2 rich thin outer layer, and a Mo-rich layer at the scale/alloy interface.

Figure 10 (a) Cross-sectional BSE image and EDS X-ray maps across the scale/alloy interface for (b) Si Ka, (c) Ti Ka, (d) O Ka and (e) Mo La.
Figure 10

(a) Cross-sectional BSE image and EDS X-ray maps across the scale/alloy interface for (b) Si Ka, (c) Ti Ka, (d) O Ka and (e) Mo La.

Thermodynamic stability of different oxides such as TiO2, SiO2, MoO3, and MoO2 are compared. The values of standard free energy of formation at 900∘C are −171.13 kcal/mol, −162.89 kcal/mol, −105.01 kcal/mol, and −85.56 kcal/mol, respectively, for TiO2, SiO2, MoO3, and MoO2. At 1300∘C, the respective free energy values are −158.06 kcal/mol, −150.59 kcal/mol, −91.87 kcal/mol, and −73.59 kcal/mol. The negative free energy values indicate all the oxides are stable at these temperatures. The tendency of formation of the oxides will follow the pattern TiO2 > SiO2 > MoO3 > MoO2. The values of free energy of formation for TiO2 and SiO2 are much lower than those for MoO3 and MoO2. Therefore, the formation of a duplex oxide comprising of TiO2-SiO2 is more probable. The absence of MoO3 or MoO2 in the oxide scale is attributed to two reasons; (1)mobility of Mo in hexagonal (Ti, Mo)5Si3 phase is low and (2) the activity or chemical potential (driving force) for Mo oxide formation is lower. It is reported [13] that the migration barrier of Ti is much lower compared to that of Mo in (Mo, Ti)5Si3 silicides. Ti diffuses through Mo vacancies and Ti is more mobile than Mo. The mobility of Si is also more in these systems. The driving forces for Ti to form TiO2 and Si to form SiO2 are comparable. Oxidation behaviour of titanium silicide based systems was studied in detail [16, 17, 18, 19, 20]. It was reported that the Si concentration of 39 at.% stabilizes SiO2 over TiO2 in the Ti-Si-O system when the oxygen partial pressure is very low [20]. However, both TiO2 and SiO2 are formed in air atmosphere.

The growth of the duplex SiO2 (TiO2) layer on the Mo-40Ti-30Si alloy is pretty interesting. From the microstructures (Figures 3, 4, 8, 9, 10) of the oxide scale, it is clearly understood that SiO2 is forming a sort of matrix type phase in which TiO2 particles are embedded. The whole structure grows with simultaneous formation of both the oxides keeping the scale intact with the substrate alloy. No porosities or cracks are noticed in the scale up to 1200∘C. Pure titanium oxidises intensively beyond 500∘C in air by absorbing oxygen and nitrogen [21]. TiO2 crystals are formed on the surface of Ti, and the oxide layer is non-protective beyond 700∘C forming a porous powdery structure. Non-stoichiometric TiO2 is a metal excess n-type semiconductor, and it shows good conductivities (electronic and ionic) even at lower partial pressure of oxygen [22]. On the contrary, thermal oxidation of Si produces a thin to thick SiO2 layer which is protective in nature up to very high temperatures. Beyond 1250∘C, SiO2 becomes amorphous and less viscous. Kinetics of oxidation of Si is reported to linear to parabolic and growth of oxide layer following parabolic kinetics [23, 24]. The activation energy for silica scale growth in 900-1200∘C was reported to be 28.5 kcal/mol [23]. The activation energy obtained in the current investigation is slightly lower (17.2 kcal/mol) than that of pure silica. This is attributed to the presence of TiO2 particles in the silica phase. However, the reported activation energy for wet-oxygen oxidation of Si is 16.3 kcal/mol [23]. The mechanisms for the scale growth follow three stages; (1) transport of oxygen from air to the outer surface where it is adsorbed, (2) oxygen atoms or ions are transported across the oxide film towards the alloy, (3) reaction at the alloy surface forming a new layer of SiO2 (TiO2). The activation energies for diffusion of oxygen and water through fused silica are reported to be 27.0 kcal/mol and 18.3 kcal/mol, respectively [23]. These values are in reasonably good agreement with activation energy of the scale growth. Therefore, the growth of the duplex protective oxide scale on Mo-40Ti-30Si is mainly controlled by the growth of the matrix silica phase by inward diffusion of oxygen.

The accelerated scale growth was observed in 1200-1300∘C with a much higher value of activation energy (77.3 kcal/mol). This could be due to the change of the structure in the silica accelerating the inward diffusion rate of oxygen. The fraction of TiO2 phase increases in the duplex scale formed at 1300∘C (Figure 4) with increasing time of exposure. This leads to the creation of stresses at the interfaces between SiO2 and TiO2 forming porosities and cracks in the oxide layer. However, the oxide layer remained protective up to 50 h of oxidation at 1300∘C in air. (Mo, Ti)Si2 coatings are reported to improve the oxidation resistance further up to 1500∘C [25]. Therefore, the development of multi-phase Mo-Ti-Si-X alloys possessing superior creep properties [26] and good oxidation resistance would be the focus of further studies.

5 Conclusions

Mo-40Ti-30Si (at.%) alloy comprised of (Ti, Mo)5Si3 matrix with (Ti, Mo)3Si precipitates having a low density (5.8 g/cm3) is a promising material for high-temperature application beyond nickel based superalloys. The alloy showed superior oxidation resistance at 900-1300∘C in air. The detailed isothermal oxidation tests conducted at 900, 1000, 1100, 1200 and 1300∘C revealed parabolic weight gain behaviour with the time of exposure up to maximum of 100 h. The oxide scale structure analysed in detail using SEM and EDS exhibited duplex oxide layer comprising with SiO2 matrix with dispersion of TiO2 particles. Formation and volatilization of MoO3 was hindered due to the formation of the continuous silica layer as matrix and titania as precipitate type morphology in the oxide scale. The growth of the oxide layer followed parabolic kinetics. Arrhenius plots for scale growth rate constant versus temperature showed two regions between 900-1200∘C and 1200-1300∘C indicating the change in mechanisms at higher temperatures due SiO2 becoming amorphous. The calculated activation energy values for scale growth matched well with the reported values for growth of the silica layer. Hence, the dominance of silica formation maintained the oxide layer continuous, adherent and protective at high temperatures.

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Received: 2019-01-07
Accepted: 2019-02-28
Published Online: 2019-12-05
Published in Print: 2019-02-25

© 2019 S. Majumdar et al., published by De Gruyter

This work is licensed under the Creative Commons Attribution 4.0 Public License.

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  30. Deposition Characteristics of Multitrack Overlayby Plasma Transferred Arc Welding on SS316Lwith Co-Cr Based Alloy – Influence ofProcess Parameters
  31. Elastic Moduli and Elastic Constants of Alloy AuCuSi With FCC Structure Under Pressure
  32. Effect of Cl on Softening and Melting Behaviors of BF Burden
  33. Effect of MgO Injection on Smelting in a Blast Furnace
  34. Structural Characteristics and Hydration Kinetics of Oxidized Steel Slag in a CaO-FeO-SiO2-MgO System
  35. Optimization of Microwave-Assisted Oxidation Roasting of Oxide–Sulphide Zinc Ore with Addition of Manganese Dioxide Using Response Surface Methodology
  36. Hydraulic Study of Bubble Migration in Liquid Titanium Alloy Melt during Vertical Centrifugal Casting Process
  37. Investigation on Double Wire Metal Inert Gas Welding of A7N01-T4 Aluminum Alloy in High-Speed Welding
  38. Oxidation Behaviour of Welded ASTM-SA210 GrA1 Boiler Tube Steels under Cyclic Conditions at 900°C in Air
  39. Study on the Evolution of Damage Degradation at Different Temperatures and Strain Rates for Ti-6Al-4V Alloy
  40. Pack-Boriding of Pure Iron with Powder Mixtures Containing ZrB2
  41. Evolution of Interfacial Features of MnO-SiO2 Type Inclusions/Steel Matrix during Isothermal Heating at Low Temperatures
  42. Effect of MgO/Al2O3 Ratio on Viscosity of Blast Furnace Primary Slag
  43. The Microstructure and Property of the Heat Affected zone in C-Mn Steel Treated by Rare Earth
  44. Microwave-Assisted Molten-Salt Facile Synthesis of Chromium Carbide (Cr3C2) Coatings on the Diamond Particles
  45. Effects of B on the Hot Ductility of Fe-36Ni Invar Alloy
  46. Impurity Distribution after Solidification of Hypereutectic Al-Si Melts and Eutectic Al-Si Melt
  47. Induced Electro-Deposition of High Melting-Point Phases on MgO–C Refractory in CaO–Al2O3–SiO2 – (MgO) Slag at 1773 K
  48. Microstructure and Mechanical Properties of 14Cr-ODS Steels with Zr Addition
  49. A Review of Boron-Rich Silicon Borides Basedon Thermodynamic Stability and Transport Properties of High-Temperature Thermoelectric Materials
  50. Siliceous Manganese Ore from Eastern India:A Potential Resource for Ferrosilicon-Manganese Production
  51. A Strain-Compensated Constitutive Model for Describing the Hot Compressive Deformation Behaviors of an Aged Inconel 718 Superalloy
  52. Surface Alloys of 0.45 C Carbon Steel Produced by High Current Pulsed Electron Beam
  53. Deformation Behavior and Processing Map during Isothermal Hot Compression of 49MnVS3 Non-Quenched and Tempered Steel
  54. A Constitutive Equation for Predicting Elevated Temperature Flow Behavior of BFe10-1-2 Cupronickel Alloy through Double Multiple Nonlinear Regression
  55. Oxidation Behavior of Ferritic Steel T22 Exposed to Supercritical Water
  56. A Multi Scale Strategy for Simulation of Microstructural Evolutions in Friction Stir Welding of Duplex Titanium Alloy
  57. Partition Behavior of Alloying Elements in Nickel-Based Alloys and Their Activity Interaction Parameters and Infinite Dilution Activity Coefficients
  58. Influence of Heating on Tensile Physical-Mechanical Properties of Granite
  59. Comparison of Al-Zn-Mg Alloy P-MIG Welded Joints Filled with Different Wires
  60. Microstructure and Mechanical Properties of Thick Plate Friction Stir Welds for 6082-T6 Aluminum Alloy
  61. Research Article
  62. Kinetics of oxide scale growth on a (Ti, Mo)5Si3 based oxidation resistant Mo-Ti-Si alloy at 900-1300∘C
  63. Calorimetric study on Bi-Cu-Sn alloys
  64. Mineralogical Phase of Slag and Its Effect on Dephosphorization during Converter Steelmaking Using Slag-Remaining Technology
  65. Controllability of joint integrity and mechanical properties of friction stir welded 6061-T6 aluminum and AZ31B magnesium alloys based on stationary shoulder
  66. Cellular Automaton Modeling of Phase Transformation of U-Nb Alloys during Solidification and Consequent Cooling Process
  67. The effect of MgTiO3Adding on Inclusion Characteristics
  68. Cutting performance of a functionally graded cemented carbide tool prepared by microwave heating and nitriding sintering
  69. Creep behaviour and life assessment of a cast nickel – base superalloy MAR – M247
  70. Failure mechanism and acoustic emission signal characteristics of coatings under the condition of impact indentation
  71. Reducing Surface Cracks and Improving Cleanliness of H-Beam Blanks in Continuous Casting — Improving continuous casting of H-beam blanks
  72. Rhodium influence on the microstructure and oxidation behaviour of aluminide coatings deposited on pure nickel and nickel based superalloy
  73. The effect of Nb content on precipitates, microstructure and texture of grain oriented silicon steel
  74. Effect of Arc Power on the Wear and High-temperature Oxidation Resistances of Plasma-Sprayed Fe-based Amorphous Coatings
  75. Short Communication
  76. Novel Combined Feeding Approach to Produce Quality Al6061 Composites for Heat Sinks
  77. Research Article
  78. Micromorphology change and microstructure of Cu-P based amorphous filler during heating process
  79. Controlling residual stress and distortion of friction stir welding joint by external stationary shoulder
  80. Research on the ingot shrinkage in the electroslag remelting withdrawal process for 9Cr3Mo roller
  81. Production of Mo2NiB2 Based Hard Alloys by Self-Propagating High-Temperature Synthesis
  82. The Morphology Analysis of Plasma-Sprayed Cast Iron Splats at Different Substrate Temperatures via Fractal Dimension and Circularity Methods
  83. A Comparative Study on Johnson–Cook, Modified Johnson–Cook, Modified Zerilli–Armstrong and Arrhenius-Type Constitutive Models to Predict Hot Deformation Behavior of TA2
  84. Dynamic absorption efficiency of paracetamol powder in microwave drying
  85. Preparation and Properties of Blast Furnace Slag Glass Ceramics Containing Cr2O3
  86. Influence of unburned pulverized coal on gasification reaction of coke in blast furnace
  87. Effect of PWHT Conditions on Toughness and Creep Rupture Strength in Modified 9Cr-1Mo Steel Welds
  88. Role of B2O3 on structure and shear-thinning property in CaO–SiO2–Na2O-based mold fluxes
  89. Effect of Acid Slag Treatment on the Inclusions in GCr15 Bearing Steel
  90. Recovery of Iron and Zinc from Blast Furnace Dust Using Iron-Bath Reduction
  91. Phase Analysis and Microstructural Investigations of Ce2Zr2O7 for High-Temperature Coatings on Ni-Base Superalloy Substrates
  92. Combustion Characteristics and Kinetics Study of Pulverized Coal and Semi-Coke
  93. Mechanical and Electrochemical Characterization of Supersolidus Sintered Austenitic Stainless Steel (316 L)
  94. Synthesis and characterization of Cu doped chromium oxide (Cr2O3) thin films
  95. Ladle Nozzle Clogging during casting of Silicon-Steel
  96. Thermodynamics and Industrial Trial on Increasing the Carbon Content at the BOF Endpoint to Produce Ultra-Low Carbon IF Steel by BOF-RH-CSP Process
  97. Research Article
  98. Effect of Boundary Conditions on Residual Stresses and Distortion in 316 Stainless Steel Butt Welded Plate
  99. Numerical Analysis on Effect of Additional Gas Injection on Characteristics around Raceway in Melter Gasifier
  100. Variation on thermal damage rate of granite specimen with thermal cycle treatment
  101. Effects of Fluoride and Sulphate Mineralizers on the Properties of Reconstructed Steel Slag
  102. Effect of Basicity on Precipitation of Spinel Crystals in a CaO-SiO2-MgO-Cr2O3-FeO System
  103. Review Article
  104. Exploitation of Mold Flux for the Ti-bearing Welding Wire Steel ER80-G
  105. Research Article
  106. Furnace heat prediction and control model and its application to large blast furnace
  107. Effects of Different Solid Solution Temperatures on Microstructure and Mechanical Properties of the AA7075 Alloy After T6 Heat Treatment
  108. Study of the Viscosity of a La2O3-SiO2-FeO Slag System
  109. Tensile Deformation and Work Hardening Behaviour of AISI 431 Martensitic Stainless Steel at Elevated Temperatures
  110. The Effectiveness of Reinforcement and Processing on Mechanical Properties, Wear Behavior and Damping Response of Aluminum Matrix Composites
https://doi.org/10.1515/htmp-2019-0056
Keywords for this article
High-temperature; Oxidation; Oxide scale; Kinetics; Activation energy
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Articles in the same Issue

  1. Frontmatter
  2. Review Article
  3. Research on the Influence of Furnace Structure on Copper Cooling Stave Life
  4. Influence of High Temperature Oxidation on Hydrogen Absorption and Degradation of Zircaloy-2 and Zr 700 Alloys
  5. Correlation between Travel Speed, Microstructure, Mechanical Properties and Wear Characteristics of Ni-Based Hardfaced Deposits over 316LN Austenitic Stainless Steel
  6. Factors Influencing Gas Generation Behaviours of Lump Coal Used in COREX Gasifier
  7. Experiment Research on Pulverized Coal Combustion in the Tuyere of Oxygen Blast Furnace
  8. Phosphate Capacities of CaO–FeO–SiO2–Al2O3/Na2O/TiO2 Slags
  9. Microstructure and Interface Bonding Strength of WC-10Ni/NiCrBSi Composite Coating by Vacuum Brazing
  10. Refill Friction Stir Spot Welding of Dissimilar 6061/7075 Aluminum Alloy
  11. Solvothermal Synthesis and Magnetic Properties of Monodisperse Ni0.5Zn0.5Fe2O4 Hollow Nanospheres
  12. On the Capability of Logarithmic-Power Model for Prediction of Hot Deformation Behavior of Alloy 800H at High Strain Rates
  13. 3D Heat Conductivity Model of Mold Based on Node Temperature Inheritance
  14. 3D Microstructure and Micromechanical Properties of Minerals in Vanadium-Titanium Sinter
  15. Effect of Martensite Structure and Carbide Precipitates on Mechanical Properties of Cr-Mo Alloy Steel with Different Cooling Rate
  16. The Interaction between Erosion Particle and Gas Stream in High Temperature Gas Burner Rig for Thermal Barrier Coatings
  17. Permittivity Study of a CuCl Residue at 13–450 °C and Elucidation of the Microwave Intensification Mechanism for Its Dechlorination
  18. Study on Carbothermal Reduction of Titania in Molten Iron
  19. The Sequence of the Phase Growth during Diffusion in Ti-Based Systems
  20. Growth Kinetics of CoB–Co2B Layers Using the Powder-Pack Boriding Process Assisted by a Direct Current Field
  21. High-Temperature Flow Behaviour and Constitutive Equations for a TC17 Titanium Alloy
  22. Research on Three-Roll Screw Rolling Process for Ti6Al4V Titanium Alloy Bar
  23. Continuous Cooling Transformation of Undeformed and Deformed High Strength Crack-Arrest Steel Plates for Large Container Ships
  24. Formation Mechanism and Influence Factors of the Sticker between Solidified Shell and Mold in Continuous Casting of Steel
  25. Casting Defects in Transition Layer of Cu/Al Composite Castings Prepared Using Pouring Aluminum Method and Their Formation Mechanism
  26. Effect of Current on Segregation and Inclusions Characteristics of Dual Alloy Ingot Processed by Electroslag Remelting
  27. Investigation of Growth Kinetics of Fe2B Layers on AISI 1518 Steel by the Integral Method
  28. Microstructural Evolution and Phase Transformation on the X-Y Surface of Inconel 718 Ni-Based Alloys Fabricated by Selective Laser Melting under Different Heat Treatment
  29. Characterization of Mn-Doped Co3O4 Thin Films Prepared by Sol Gel-Based Dip-Coating Process
  30. Deposition Characteristics of Multitrack Overlayby Plasma Transferred Arc Welding on SS316Lwith Co-Cr Based Alloy – Influence ofProcess Parameters
  31. Elastic Moduli and Elastic Constants of Alloy AuCuSi With FCC Structure Under Pressure
  32. Effect of Cl on Softening and Melting Behaviors of BF Burden
  33. Effect of MgO Injection on Smelting in a Blast Furnace
  34. Structural Characteristics and Hydration Kinetics of Oxidized Steel Slag in a CaO-FeO-SiO2-MgO System
  35. Optimization of Microwave-Assisted Oxidation Roasting of Oxide–Sulphide Zinc Ore with Addition of Manganese Dioxide Using Response Surface Methodology
  36. Hydraulic Study of Bubble Migration in Liquid Titanium Alloy Melt during Vertical Centrifugal Casting Process
  37. Investigation on Double Wire Metal Inert Gas Welding of A7N01-T4 Aluminum Alloy in High-Speed Welding
  38. Oxidation Behaviour of Welded ASTM-SA210 GrA1 Boiler Tube Steels under Cyclic Conditions at 900°C in Air
  39. Study on the Evolution of Damage Degradation at Different Temperatures and Strain Rates for Ti-6Al-4V Alloy
  40. Pack-Boriding of Pure Iron with Powder Mixtures Containing ZrB2
  41. Evolution of Interfacial Features of MnO-SiO2 Type Inclusions/Steel Matrix during Isothermal Heating at Low Temperatures
  42. Effect of MgO/Al2O3 Ratio on Viscosity of Blast Furnace Primary Slag
  43. The Microstructure and Property of the Heat Affected zone in C-Mn Steel Treated by Rare Earth
  44. Microwave-Assisted Molten-Salt Facile Synthesis of Chromium Carbide (Cr3C2) Coatings on the Diamond Particles
  45. Effects of B on the Hot Ductility of Fe-36Ni Invar Alloy
  46. Impurity Distribution after Solidification of Hypereutectic Al-Si Melts and Eutectic Al-Si Melt
  47. Induced Electro-Deposition of High Melting-Point Phases on MgO–C Refractory in CaO–Al2O3–SiO2 – (MgO) Slag at 1773 K
  48. Microstructure and Mechanical Properties of 14Cr-ODS Steels with Zr Addition
  49. A Review of Boron-Rich Silicon Borides Basedon Thermodynamic Stability and Transport Properties of High-Temperature Thermoelectric Materials
  50. Siliceous Manganese Ore from Eastern India:A Potential Resource for Ferrosilicon-Manganese Production
  51. A Strain-Compensated Constitutive Model for Describing the Hot Compressive Deformation Behaviors of an Aged Inconel 718 Superalloy
  52. Surface Alloys of 0.45 C Carbon Steel Produced by High Current Pulsed Electron Beam
  53. Deformation Behavior and Processing Map during Isothermal Hot Compression of 49MnVS3 Non-Quenched and Tempered Steel
  54. A Constitutive Equation for Predicting Elevated Temperature Flow Behavior of BFe10-1-2 Cupronickel Alloy through Double Multiple Nonlinear Regression
  55. Oxidation Behavior of Ferritic Steel T22 Exposed to Supercritical Water
  56. A Multi Scale Strategy for Simulation of Microstructural Evolutions in Friction Stir Welding of Duplex Titanium Alloy
  57. Partition Behavior of Alloying Elements in Nickel-Based Alloys and Their Activity Interaction Parameters and Infinite Dilution Activity Coefficients
  58. Influence of Heating on Tensile Physical-Mechanical Properties of Granite
  59. Comparison of Al-Zn-Mg Alloy P-MIG Welded Joints Filled with Different Wires
  60. Microstructure and Mechanical Properties of Thick Plate Friction Stir Welds for 6082-T6 Aluminum Alloy
  61. Research Article
  62. Kinetics of oxide scale growth on a (Ti, Mo)5Si3 based oxidation resistant Mo-Ti-Si alloy at 900-1300∘C
  63. Calorimetric study on Bi-Cu-Sn alloys
  64. Mineralogical Phase of Slag and Its Effect on Dephosphorization during Converter Steelmaking Using Slag-Remaining Technology
  65. Controllability of joint integrity and mechanical properties of friction stir welded 6061-T6 aluminum and AZ31B magnesium alloys based on stationary shoulder
  66. Cellular Automaton Modeling of Phase Transformation of U-Nb Alloys during Solidification and Consequent Cooling Process
  67. The effect of MgTiO3Adding on Inclusion Characteristics
  68. Cutting performance of a functionally graded cemented carbide tool prepared by microwave heating and nitriding sintering
  69. Creep behaviour and life assessment of a cast nickel – base superalloy MAR – M247
  70. Failure mechanism and acoustic emission signal characteristics of coatings under the condition of impact indentation
  71. Reducing Surface Cracks and Improving Cleanliness of H-Beam Blanks in Continuous Casting — Improving continuous casting of H-beam blanks
  72. Rhodium influence on the microstructure and oxidation behaviour of aluminide coatings deposited on pure nickel and nickel based superalloy
  73. The effect of Nb content on precipitates, microstructure and texture of grain oriented silicon steel
  74. Effect of Arc Power on the Wear and High-temperature Oxidation Resistances of Plasma-Sprayed Fe-based Amorphous Coatings
  75. Short Communication
  76. Novel Combined Feeding Approach to Produce Quality Al6061 Composites for Heat Sinks
  77. Research Article
  78. Micromorphology change and microstructure of Cu-P based amorphous filler during heating process
  79. Controlling residual stress and distortion of friction stir welding joint by external stationary shoulder
  80. Research on the ingot shrinkage in the electroslag remelting withdrawal process for 9Cr3Mo roller
  81. Production of Mo2NiB2 Based Hard Alloys by Self-Propagating High-Temperature Synthesis
  82. The Morphology Analysis of Plasma-Sprayed Cast Iron Splats at Different Substrate Temperatures via Fractal Dimension and Circularity Methods
  83. A Comparative Study on Johnson–Cook, Modified Johnson–Cook, Modified Zerilli–Armstrong and Arrhenius-Type Constitutive Models to Predict Hot Deformation Behavior of TA2
  84. Dynamic absorption efficiency of paracetamol powder in microwave drying
  85. Preparation and Properties of Blast Furnace Slag Glass Ceramics Containing Cr2O3
  86. Influence of unburned pulverized coal on gasification reaction of coke in blast furnace
  87. Effect of PWHT Conditions on Toughness and Creep Rupture Strength in Modified 9Cr-1Mo Steel Welds
  88. Role of B2O3 on structure and shear-thinning property in CaO–SiO2–Na2O-based mold fluxes
  89. Effect of Acid Slag Treatment on the Inclusions in GCr15 Bearing Steel
  90. Recovery of Iron and Zinc from Blast Furnace Dust Using Iron-Bath Reduction
  91. Phase Analysis and Microstructural Investigations of Ce2Zr2O7 for High-Temperature Coatings on Ni-Base Superalloy Substrates
  92. Combustion Characteristics and Kinetics Study of Pulverized Coal and Semi-Coke
  93. Mechanical and Electrochemical Characterization of Supersolidus Sintered Austenitic Stainless Steel (316 L)
  94. Synthesis and characterization of Cu doped chromium oxide (Cr2O3) thin films
  95. Ladle Nozzle Clogging during casting of Silicon-Steel
  96. Thermodynamics and Industrial Trial on Increasing the Carbon Content at the BOF Endpoint to Produce Ultra-Low Carbon IF Steel by BOF-RH-CSP Process
  97. Research Article
  98. Effect of Boundary Conditions on Residual Stresses and Distortion in 316 Stainless Steel Butt Welded Plate
  99. Numerical Analysis on Effect of Additional Gas Injection on Characteristics around Raceway in Melter Gasifier
  100. Variation on thermal damage rate of granite specimen with thermal cycle treatment
  101. Effects of Fluoride and Sulphate Mineralizers on the Properties of Reconstructed Steel Slag
  102. Effect of Basicity on Precipitation of Spinel Crystals in a CaO-SiO2-MgO-Cr2O3-FeO System
  103. Review Article
  104. Exploitation of Mold Flux for the Ti-bearing Welding Wire Steel ER80-G
  105. Research Article
  106. Furnace heat prediction and control model and its application to large blast furnace
  107. Effects of Different Solid Solution Temperatures on Microstructure and Mechanical Properties of the AA7075 Alloy After T6 Heat Treatment
  108. Study of the Viscosity of a La2O3-SiO2-FeO Slag System
  109. Tensile Deformation and Work Hardening Behaviour of AISI 431 Martensitic Stainless Steel at Elevated Temperatures
  110. The Effectiveness of Reinforcement and Processing on Mechanical Properties, Wear Behavior and Damping Response of Aluminum Matrix Composites
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