Effect of Initial Microstructure on Phase Precipitation and Mechanical Properties during Heat Treatment of TC21 Titanium Alloy ()
1. Introduction
TC21 titanium alloy is widely used in aerospace applications due to its low density-strength ratio, high strength and high toughness [1] [2] [3]. However, it is usually considered to be among the most difficult to process due to its higher yield-tensile ratio and lower elastic modulus [4]. Previous researches on TC21 titanium alloy primarily highlighted the role of conventional hot working methods controlling mechanical properties of TC21 titanium alloy, especially strength and fracture toughness, by adjusting α grain morphology and content [1] [2] [3]. Therefore, it is necessary to develop a new processing technique to improve the formability of TC21 titanium alloy.
Grain refinement is well recognized as an effective approach to enhance the properties of titanium alloys [4] [5] [6] [7]. One factor affecting the level of grain refinement is the initial microstructure of titanium alloys. As a result of deformation-induced continuous dynamic recrystallization, the acicular or lamellar microstructure can be transformed into fine microstructure with increased strength, ductility and superplasticity [4] [5] [6] [8]. As we all know, the fine microstructure becomes instable during moderate and high temperature exposure. However, instable microstructure has a considerable effect on properties of titanium alloys. Besides, little attention was paid to the phase precipitation and mechanical properties of the fine microstructure alloys during heat treatment (high temperature exposure).
The objective of this work was to investigate the microstructure evolution and mechanical properties of TC21 titanium with fine and coarse microstructures during heat treatment.
2. Materials and Procedures
The material of this work was a 220 mm-diameter hot-forged TC21 bar stock with an equiaxed α microstructure (a grain size of ~6 μm). Its chemical compositions were (by wt%) 6.3 Al, 2.13 Sn, 2.89 Mo, 1.63 Cr, 2.3 Zr, 2.02 Nb, 0.11 Si, and 82.62 Ti. The β transus temperature of the material was approximately 940˚C. A section of the TC21 bar stock was rolled at 900˚C to produce an equiaxed α microstructure with a grain size of ~5 μm (coarse microstructure) (Figure 1(a)). Another section of the TC21 bar stock was water quenched at 970˚C to obtain an acicular α microstructure and then was rolled at 900˚C to produce a fine microstructure with a grain size of ~0.5 μm (Figure 1(b)). The volume fractions of equiaxed α phases in the fine and coarse microstructures were both about 60%. Both materials with the fine and coarse microstructures were heat-treated at 900˚C/1h + 550˚C/4h in order to obtain excellent comprehensive properties.
The microstructures of materials were studied using a JMS-6460 scanning electron microscope (SEM) equipped with an OxFORD EDS system and a Hitachi HF 2000 field emission transmission electron microscope (FE-TEM). X-ray diffraction was used to determine the crystallographic texture of materials.
The tensile tests were conducted on cylindrical materials with a gauge diameter of 5 mm and length of 70 mm at room temperature. The fracture mechanics tests were performed on 40 mm wide and 20 mm thickness CT-materials, which were precracked in air at R = 0.1. To demonstrate the influence of initial microstructure on the crack growth behavior, additional CT-materials were selected to perform the same fracture mechanics, but the loading were removed before they broke. Their crack paths were observed using an Olympus optical microscope.
3. Results
3.1. Microstructure and Precipitation
SEM microstructures of TC21 titanium alloy with the coarse and the fine microstructures heat treated at 900˚C/1h + 550˚C/4h were showed in Figure 2(a) and
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Figure 1. SEM micrographs of TC21 titanium alloys with (a) coarse and (b) fine microstructures.
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Figure 2. SEM micrographs of TC21 titanium alloys with (a) fine and (b) coarse microstructures heat-treated at 900˚C/1h + 550˚C/4h.
Figure 2(b), respectively. It was observed that the bimodal microstructure consists of equiaxed and lamellar α-phase grains. The volume fractions of equiaxed α-phase grains in the two materials were same (about 35%). The measured sizes of α- and β-phase grains were ~7 and ~12 μm respectively in the coarse microstructure, while ~3 and ~5 μm respectively in the fine microstructure (Figure 2(b)).
Occurrence of ω precipitates in ~10 nm scale in the two materials were clearly observed by TEM imaging, as shown in Figures 3(a)-(e). Dark field (DF) images of the two materials were shown in Figure 3(c) and Figure 3(f), respectively. The second α precipitates from the two materials exhibited a lamellar morphology. However, the thickness of the second α lamellae (sub-50 nm) in the coarse microstructure was finer than that in the fine microstructure (sub-200 nm). Moreover, the orientation relationships of the two materials between α and β phases was <111>β//<11 - 20>α, {110}β//{0001}α. The second α lamellae exhibited a Burgers orientation relationship with the surrounding β matrix. Similar results were reported in previous studies [9].
ω reflections deviated from the three dimensional positions of ω phase were shown from Figure 3(a) and Figure 3(d). The deviation was normalized as |Δ| = 2u/(k0/3) [10], where k0 was the distance between (-110)β and (1-1-2)β reflections and u was the shift of diffuse scattering from the k0/3 position. Early studies
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Figure 3. TEM images of TC21 titanium alloys with (a-c) coarse and (d-f) fine microstructures heat-treated at 900˚C/1h + 550˚C/4h; (a, d) the SADPs of [110]β zone axis; (b, e) the DF images recorded using ω reflection, marked with a white circle in (a) and (c), respectively; (c, f) the DF images recorded using alpha reflection, marked with a black circle in (a) and (c), respectively.
indicated that ω was destabilized with increasing |Δ| [10] [11]. The coarse and fine microstructures respectively had a |Δ| value of 0.11 and 0.13, suggesting that ω phase in the former was more stable than the latter.
TEM studies were carried out the two materials, as shown in Figure 4. Figure 4(a) was a DF image taken from the coarse microstructure, using one of the α2 phase reflections (Figure 4(b)). The nanometer-scale α2 precipitates were found along the α/β interface (Figure 4(a)). The selected area electron diffraction pattern (SADP) from the fine microstructure showed both fundamental reflections resulting from the α phase and quite faint reflections at the 1/2 {10 - 10}α, which was a direct evidence for the presence of α2 precipitates. Faint reflections suggested that the fine microstructure has α2 phase with much smaller size and lower volume fraction compared to the coarse microstructure.
3.2. Mechanical Properties
The mechanical properties of TC21 titanium alloy with the coarse and the fine microstructures heat treated at 900˚C/1h + 550˚C/4h were displayed in Table 1. The fine microstructure showed excellent comprehensive properties. It was observed its strength is better than that of the coarse microstructure. Meanwhile, the difference between the two microstructures was considerable, approximately 60 Mpa in ultimate tensile stress and 50 MPa in yield stress. The elongation of the fine and coarse microstructures was 8.5% and 7%, respectively, which showed a significant difference of 21.4%. It was noticeable that the fracture toughness of the fine microstructure was approximately 19 MPa·m1/2 higher than that of the
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Figure 4. DF images (a) and the SADPs (b) taken from the coarse microstructure TC21 titanium alloy heat treated at 900˚C/1h + 550˚C/ 4h; The SADPs (c) taken from the fine microstructure TC21 titanium alloy heat treated at 900˚C/1h + 550˚C/4h.
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Table 1. Room temperature mechanical properties of TC21 titanium alloys with fine and coarse microstructures heat-treated at 900˚C/1h + 550˚C/4h.
coarse microstructure. Those results indicated that the fine microstructure material had excellent comprehensive properties.
3.3. Crack Growth Behaviour
Crack path observations in additional CT-materials, which were TC21 titanium alloy with the coarse and fine microstructures heat treated at 900˚C/1h + 550˚C/4h, were illustrated in Figure 5. Microcracks along the interphase and the boundary of β-phase grains were clearly seen in the white ellipses of Figure 5, suggesting that the microcracks might nucleate at the interphase. Meanwhile, some contacts were observed in the two microstructures, as were marked by white arrows in Figure 5. Some bridging elements were only found in the fine microstructure, as are marked by the black arrows of Figure 5(b). In addition, some microcracks near the main crack were also found in the fine microstructure, marked by the black ellipses of Figure 5(b). They merged into the main crack when microcracks coarsened to about 55 μm (Figure 5), which indicated that smaller microcracks tended to form bridging elements. Microcracks in the fine microstructure were smaller than those in the coarse microstructure (Figure 5). Therefore, more bridging elements inducing the stress shilding will generate in the fine microstrucure, which is beneficial to the blunting of crack tips, namely，to reduce the crack growth rate [11].
4. Discussions
4.1. Effect of Initial Microstructure on Phase Precipitations
According to Sections 2 and 3.1, it was obvious that during heat treatment, α grains in the coarse microstructure grew slightly while coarsened greatly in the fine microstructure. This phenomenon may be explained by the typical Ostwald
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Figure 5. Crack paths in heat-treated TC21 titanium alloys with (a) coarse and (b) fine microstructures.
ripening processes [12]. The process consists of two phases. In the first phase, the cube of the average grain radius is proportional to time. In the second phase, the average grain radius remains self-similar when scaled by a certain grain size. The coarsening of the coarse microstructure after heat treatment may follow the first phase of Ostwald ripening processes [12]. However, the coarsening behavior of the fine microstructure can be described by the second phase. The precipitations in tianium alloys are influenced by many factors such as element contents, processing history, and heat treatment, however, essentially result from the compositional fluctuation [13] [14] [15] [16]. With increasing Al content, the size and the volume fraction of α2 precipitation increase [13]. The Al contents of the α in the coarse and the fine microstructures were 7.46 and 5.76 wt%, respectively, as shown in Table 2. It is easy to understand that, at the same heat-treatment condition, the α2 precipitation of the fine microstructure was fewer and smaller than that of coarse microstructure. Moreover, low and high Al contents in the β field were found in the coarse and fine microstructures, respectively (Table 2). Higher addition content of Al results in the formation of alpha phase more effectively than ω phase [10]. Therefore, during the heat treatment, the thicker alpha lamellae and more instable ω phase are found in the fine microstructure.
4.2. Effect of Initial Microstructure on Mechanical Properties
The high combination properties of the heat-treated fine microstructure are very
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Table 2. EDS data of different phases in TC21 titanium alloys with coarse and fine microstructures (wt%).
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Figure 6. ODF sections of α textures from heat-treated TC21 titanium alloys with (a) coarse and (b) fine microstructures.
interesting. First, high strength can be attributed to the fine equiaxed α microstructure according to Hall-Petch equation. Another factor that may contribute to the high ductility is
α//RD fibrous texture (
Figure 6), namely, the orientation of the tensile axis (RD) perpendicular to the [0001]
α. The prismatic gliding ({1 - 100}
α<11 - 20>
α) operates easily during the tensile test, which may result in an increase in ductility [7]. Under the same heat-treatment conditions, the fine microstructure also shows higher fracture toughness, compared with the coarse microstructure. The reasons are as following: First, fine microstructure is beneficial to generate more and smaller microcracks near the crack tip and the main crack, which can reduce stress concentration in this field, namely, to lead to higher energy absorption during deformation; Second, the increased amount of α
2 precipitate may promote the basal slip ((0001) [11 - 20]), which can reduce the fracture of the tested samples [17].
5. Conclusions
1) The initial microstructure of TC21 titanium affects the microstructure evolution and phase precipitates during heat treatment. After heat treatment, the fine microstructure forms a duplex microstructure with small α grains and thick second alpha lamellae while the coarse microstructure develops a duplex microstructure with large α grain and thin second α lamellae. Moreover, more instable ω and α2 precipitates of much smaller size and lower volume fraction are observed in the heat-treated fine microstructure.
2) Crack growth behavior of TC21 titanium greatly depends on the initial microstructure under the same heat treatment condition. The fine microstructure exhibits lower crack growth resistance than the coarse microstructure.
3) During heat treatment, the initial microstructure of TC21 titanium has a great effect on mechanical properties. The compresensive property of fine microstructure is superior to that of the coarse microstructure.
Acknowledgements
The present work is supported by National Natural Science Foundation of China (No. 51301010) and Scientific Research Foundation for Advanced Talents (TZXY2017QDJJ012).