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Effects of Different Solid Solution Temperatures on Microstructure and Mechanical Properties of the AA7075 Alloy After T6 Heat Treatment

  • Süleyman Tekeli , Ijlal Simsek , Dogan Simsek and Dursun Ozyurek EMAIL logo
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

In this study, the effect of solid solution temperature on microstructure and mechanical properties of the AA7075 alloy after T6 heat treatment was investigated. Following solid solution at five different temperatures for 2 hours, the AA7075 alloy was quenched and then artificially aged at 120∘C for 24 hours. Hardness measurements, microstructure examinations (SEM+EDS, XRD) and tensile tests were carried out for the alloys. The results showed that the increased solid solution temperature led to formation of precipitates in the microstructures and thus caused higher hardness and tensile strength.

Keywords: AA7075 alloy; aging; solid solution; microstructure; mechanical properties

1 Introduction

7xxx series aluminum alloys maintain their attractiveness due to their high strength and have increasing use in the aviation industry. In recent years, there seems to be a significant increase in the number of studies using different processes to further improve the strength and other properties (e.g. corrosion) of these alloys [1, 2, 3]. The most commonly preferred method to improve the strength of Al-Zn-Mg-Cu alloys is artificial aging (T6) heat treatment. Also, the strength of 7xxx series alloys can be improved significantly using different heat treatment processes (re-aging [RRA]) and high temperature pre-precipitation (HTPP) [4, 5, 6, 7, 8, 9, 10, 11, 12]. Among 7xxx series aluminum alloys, AA7075 is the most preferred. This alloy is used in the aerospace industry in particular due to its good mechanical properties such as high strength, ductility, and toughness. The strength of the AA7075 alloy is improved using different heat treatments. T6 heat treatment applied to this alloy is one of the most important ways that improve the mechanical properties of the alloy with both the solid solution heat treatment and the artificial aging treatment [13, 14]. T6 heat treatment is applied in three steps. The first step is the solution treatment (forming the solid solution), the second step involves the rapid cooling (forming the supersaturated structure), and the final step is the aging treatment (precipitation hardening) [15]. During the hardening of the alloy, some uncontrolled phases form in the structure. The purpose of the solution treatment is to ensure these uncontrolled phases in the structure dissolve during the hardening of the alloy. This treatment is carried out at a temperature below the eutectic temperature or in the single-phase region above the solvus curve. Once the dissolution is completed, the rapid cooling is performed to form the supersaturated solid solution structure. At this stage, a supersaturated solid solution is obtained at room temperature by rapidly cooling the structure with quenching. In the first step, the second phase (MgZn2) precipitates are formed in the structure by applying aging heat treatment at certain temperatures for certain durations. The second phase (MgZn2) precipitates formed in the structure by aging treatment allow for improving the strength of the material. These precipitates formed in the structure by aging depend on the degree to which uncontrolled phases that form in the structure during hardening dissolve. For this reason, this study aims to investigate changes in the microstructure and mechanical properties of the AA7075 alloy solution treated at five different solid solution temperatures after T6 heat treatment.

2 Materials and Method

In the experimental studies, the AA7075 aluminum alloy that is commonly used in the sector of space and aerospace owing to its specific weight, high strength, electrical and thermal conductivities was used in the experimental studies. AA7075 alloy which is used in this study, was taken from ACA METAL Industrial firm. Chemical composition of the AA7075 alloy used in the experimental studies is given in the Table 1. The alloy to be used in the experiments was homogenized for 2 hours at 500∘C (at a heating rate of 10∘C/min) prior to the aging processes. Homogenized stick AA7075 aluminum alloy of 9 mm in diameter was treated sensitively in the turning machine and tensile samples were prepared according to ASTM: B557M-10 standards.

Table 1

The chemical composition of the AA7075 alloy used in the experimental studies.

ElementZnMgCuFeCrSi
% vol.5.92.7341.5610.1960.20.0117
ElementMnTiVZrBAl
% vol.0.06870.03430.00660.00910.0025Bal.

The alloys were solid solution treated at 5 different temperatures (465∘C, 470∘C, 475∘C, 480∘C, and 485∘C) for 2 hours, rapidly cooled and artificially aged at 120∘C for 24 hours. The alloys prepared by standard metallographic procedures were etched using 2 ml HF, 3 ml HCI, 20 ml HNO3, 175 ml H2O (Keller’s) solution for 10-15 seconds. “Jeol JSM-6060” scanning electron microscope (SEM) was used for microstructure examinations and fracture surfaces. Rigaku D-Max Rint-2200 Series device was used for XRD analysis to determine phases formed in microstructure. The hardness measurements were performed using Affri hardness measurement device and the average of five measurements was taken. Tensile test were carried out using Shimadzu AG-IS (50 kN) tensile machine at cross head speed of 2 mm/min.

3 Results and Discussion

Figure 1 shows SEM images of the AA7075 alloy aged at 120∘C for 24 hours following solid solution at 5 different temperatures.

Figure 1 SEM images of the AA7075 alloy aged 120∘C for 24 hours following solid solution at different temperatures of a) 465∘C b) 470∘C c) 475∘C d) 482∘C e) 485∘C.
Figure 1

SEM images of the AA7075 alloy aged 120∘C for 24 hours following solid solution at different temperatures of a) 465∘C b) 470∘C c) 475∘C d) 482∘C e) 485∘C.

SEM images given in Figure 1 show that the structure consisted of α-Al, Al-Zn-Mg eutectic, and micro-gaps formed in the structure. Also, MgZn2 precipitates seem to have formed in the structure after solid solution at different temperatures and aging treatment. Figure 2 shows the XRD results of the specimen after T6 heat treatment. The XRD results showed the MgZn2 precipitates in the microstructure. Second phase precipitates are the most important factors improving the strength of the alloy. It is noted in a previous study that second phases such as Al7Cu2Fe, Al2CuMg, and MgZn2 form in the structure of the AA7075 alloy [16]. Table 2 shows the EDS results of the AA7075 alloy applied solid solution at 485∘C. According to the EDS results, points 1 and 3 number can be seen as Zn-rich regions.

Figure 2 The XRD results of the AA7075 alloy after T6 heat treatment.
Figure 2

The XRD results of the AA7075 alloy after T6 heat treatment.

Table 2

EDS results of the AA7075 alloy applied solid solution at 485∘C.

Point / wt%AlMgZn
187.9582.8849.158
290.9322.1096.959
388.6851.4069.909

Second phase precipitates (MgZn2) formed in the structure after T6 heat treatment are the most important factors improving the mechanical strength of this alloy. On the other hand, intermetallic phases such as Al7Cu2Fe and Al2CuMg are also reported to contribute to improved strength in 7xxx series alloys in a previous study [17]. Precipitates observed in the SEM images given in Figure 1 may be attributed to these compounds. Figure 3 shows the hardness and tensile strength change of the alloy after solid solution at different temperatures followed by aging treatment.

Figure 3 Hardness (a) and tensile strength (b) change of the AA7075 alloys after solid solution and age heat treatments.
Figure 3

Hardness (a) and tensile strength (b) change of the AA7075 alloys after solid solution and age heat treatments.

As shown in Figure 3a, the hardness values of the alloys increased with increasing solid solution temperature. The minimum hardness value was 192 HV for the alloy solid solution treated at 465∘C. The maximum hardness value, on the other hand, was 212 HV for the alloy solid solution treated at 485∘C. This increase in the hardness value may be interpreted as that the dissolution process achieved its purpose by formation of precipitates with the increase in solid solution temperature. Figure 3b shows the effect of the solid solution temperatures on tensile strength. As a result of the tensile tests tensile strength was 610 MPa for the specimen treated at 465∘C, whereas the highest applied to specimens solid solution treated at different temperatures followed by aging, it was seen that the increased solid solution temperature led to an increased in tensile strength. The lowest tensile strength was 632 MPa for the specimen treated at 485∘C. The increase in the solid solution temperature causes compounds which form in the structure during the hardening of the alloy in an uncontrolled manner to further dissolve and the quenched at room temperature leads to more effective formation of the supersaturated solid solution structure. Thus, the supersaturated solid solutions in the structure which occur more effectively and the increased precipitate amount due to aging cause the strength of the material increase further. Mahathaninwong et al. [18] note that alloy compounds completely dissolve without forming brittle and coarse particles due to increased solid solution temperature, the quenched at room temperature leads to formation of compound and element precipitates in the rich solid solutions, and the strength of the alloy increases. Figure 4 shows the fractured surface SEM images of the alloys, which were solid solution treated at different temperatures followed by aging, after the tensile test.

Figure 4 The fractured surface SEM images of the alloys after the tensile tests a) 465∘C b) 470∘C c) 475∘C d) 482∘C e) 485∘C.
Figure 4

The fractured surface SEM images of the alloys after the tensile tests a) 465∘C b) 470∘C c) 475∘C d) 482∘C e) 485∘C.

The fractured surface SEM examinations given in Figure 4 showed pores on the fracture surfaces. The fracture seems to have occurred due to small gaps between aluminum grains separated by grain boundaries joining together with the effect of tension applied to specimens. While there were some small gaps within the alloy, others were formed by dislocation and second phase precipitates formed in the structure due to aging. As seen in Figure 4, the mode of the fracture which occurred after the tensile test was ductile. This was evident from the presence of fine and round pores and large number of pits. The ductile fraction which occurred in the structure was supported by joining of small gaps, which led to formation of larger pits as seen in fractured surface images [11, 19].

4 Conclusion

The following results are obtained in the present study for the specimen solid solution treated at 5 different temperatures for 2 hours and then artificially aged at 120∘C for 24 hours.

  • It was found that the increased solid solution temperature led to formation of precipitates in the alloy’s structure.

  • The increased solid solution temperature led to an increase in the hardness of the alloy.

  • In tensile tests, the maximum tensile strength was observed for the maximum solid solution temperature.

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Received: 2018-08-10
Accepted: 2019-02-04
Published Online: 2019-12-05
Published in Print: 2019-02-25

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

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

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https://doi.org/10.1515/htmp-2019-0050
Keywords for this article
AA7075 alloy; aging; solid solution; microstructure; mechanical properties
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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
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  13. 3D Heat Conductivity Model of Mold Based on Node Temperature Inheritance
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  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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