The Effect of Heat Treatment on the Evolution of Microstructure and Texture in Ti80 Hot Rolled Pipe

Abstract

In this study, the microstructure and texture evolution of hot rolled Ti80 pipe annealing at 960°C and 990°C in α+β two-phase field have been investigated. The results showed that the dissolution of α phases induced the increase of texture components of primary α phases (α_P) and the α_P were the main factors that determine the final texture at 960°C. At 960°C, the microtextures of secondary α phases (α_S) were very close to that of α_P. As the annealing temperature increased to 990 °C, the main factors affecting the microtextures of α_S changed from the α_P to the recrystallized β grains. The textures of β phases were greatly influenced by the annealing temperature. The β phases at high temperature were not mainly from the grow up of residual β phases. It was formed by the transformation of α phases at room temperature. Consequently, this study could provide some ideas for decreasing the texture intensities of hot rolled Ti80 pipes, such as reducing the area of α colonies before rolling, scattering the crystal orientations of α_P, and controlling the size of recrystallized β grains.

Keywords
Titanium alloys; Texture; Heat treatment; Electron backscattered diffraction (EBSD)

1. Introduction

The near α titanium and its alloys are widely used for structural applications in aerospace, energy related, and marine engineering fields because of their low density, high toughness, high specific strength and good corrosion resistance^1-3. As a newly developed near-α titanium alloy by China, the tubular product of Ti80 alloys are mainly used in offshore oil drilling and nuclear power field. To obtain a good balance between strength and ductility, the bimodal microstructures composed of equiaxed primary α phases (α_P) and lamellar secondary α phases (α_S) are good candidates⁴. It is well known that the mechanical properties including strength, fracture toughness, ductility and fatigue performance are greatly affected by microstructure morphology^5-7. Generally, increase of the volume fraction of α_P could improve the tensile properties and high cycle fatigue performance, but decrease the fracture toughness for bimodal microstructure. In addition, texture is also an important factor affecting the mechanical properties of titanium alloy pipes. The anisotropy of mechanical properties is closely related to macrotexture, which is composed of many microtextures. And the microtexture also has made effect on the nucleation of fatigue cracks. Therefore, it is necessary to study the mechanism of microtextures in Ti80 pipes.

A comprehensive review of the evolution of texture during thermomechanical processing of titanium and its alloys has been reported by Singh⁸. In general, titanium alloy forgings undergo a series of thermomechanical processing steps in α+β phase fields, followed by β to α phase transformation. Therefore, the final texture is determined by processing parameters, such as temperature, mode of deformation (rolling, forging and extrusion), strain, strain rates and cooling rates. And the better understanding of texture forming mechanism induced by every step would be helpful to the establishment of more physically based process modeling. Texture evolution during the hot deformation process has been investigated by previous studies^9-11. As for phase transformation textures, many researchers mainly focused on the variant selection mechanisms during the cooling from above the β transus. Bantounas et al¹². found that the formation of microtexure was associated with variant selection during the β to α phase transformation. It was found that α phases with the same orientations of c-axis preferred to nucleate on both sides of β grain pairs having a common [110] pole in many studies^13-15. The nucleation of α phases with same orientations would induce the large regions of α texture component after β to α transformation. Obviously, the α texture after transformation is closely related to the original β grain. G.C. Obasi reported that the intensities of α texture components increased dramatically with the growth of β grain size¹⁶. In Zhao’s study, the transformed α texture components were greatly influenced by original β texture¹³. The stronger (110) β texture intensity could provide more neighboring β grains with nearly parallel (110) pole. However, very limited research on the texture evolution during the heat treatment in the two-phase region could be found. Germain et al. have investigated the effect of α_P on the texture change by separating the α_P and α_S texture and found that major texture component of the α_S colonies was very similar with that of α_P in the compression of TIMETAL 834 alloy¹⁷. The texture produced at different rolling temperatures in α+β field and subsequent annealing was systematically analyzed by D.G. Leo Prakash¹⁸. In D.G’s study, the precipitated α_S had the same texture components, although the orientation of adjacent β grains had different orientations, which indicates that variant selection was an important factor affecting the texture. Zhao studied the effect of annealing temperature on the texture evolution in the two-phase region¹⁹. They observed that texture type and intensity were changed with the increasing annealing temperature. However, the initial microstructure was obtained by multiple forging and the primary β grain boundary could not be observed before heat treatment. This has made the analysis of texture evolution difficult after heat treatment due to the complexity of the initial texture.

At present, previous researchers have studied the texture evolution and variant selection mechanism of titanium alloys during hot compression and plate rolling. However, the texture of titanium pipe was seldom reported. Although the bimodal microstructure has excellent comprehensive mechanical properties, different morphologies will lead to significant differences in mechanical properties. Therefore, we investigated the effect of microstructure morphology such as the number of α_P and the size of recrystallized β grain on the microtexture in the heat treatment of Ti80 pipe. In this work, the Ti80 pipe after hot rolling was annealed at different temperatures in two-phase region to obtain different microstructures. The development of the microtexture during this process was investigated using EBSD methods.

2. Experimental Procedure

The exact chemical composition of the alloy used in this study is measured by chemical analysis method, as shown in Table 1. The initial microstructure was Widmannstatten structure, which was obtained by cross piercing in β phase field, as shown in Figure 1. The final Ti80 pipe was acquired by hot rolling at 930 °C. The β transus temperature was determined to be 1000 °C by using the metallographic method. The samples were cut along the longitudinal section of the pipe as shown in Figure 2. Two of the samples were annealed at 960°C and 990°C for 30min followed by slow cooling, respectively. The sample surfaces containing rolling direction (RD) and normal direction (ND) were prepared for the analysis of microstructure and texture. The sample surface was prepared by grinding, mechanically polishing and electrolytically polishing with a solution of 6% HClO4 + 64% CH3OH + 30% C4H10O for EBSD observation. The scanning area of the macrotexture is 500 μm × 200 μm, and that of the microtexture is 180 μm × 180 μm. The step size of the larger areas and smaller areas was 2μm and 0.3μm respectively.

Table 1
Chemical composition of Ti80 pipe used in this study.

Elements	Ti	Al	Nb	Zr	Mo	Si	Fe	C	N	O
Contents	Bal.	6.12	3.1	2.07	0.94	0.03	0.02	0.005	0.001	0.10

Figure 1
The microstructure of Ti80 pipe before hot rolling.

Figure 2
Schematic picture of the sample cut from pipe.

2.1. Theoretical calculation methods

As a near α titanium alloy, it is difficult to obtain its crystallographic orientation through EBSD due to the low β phase content at room temperature. Therefore, the crystallographic orientation of the β phase at high temperature are calculated by the crystallographic orientation of the α phases precipitated during the cooling process. According to the Bunge convention, the crystallographic orientation can be described by a set of Euler angles (Φ1, Φ, Φ2)²⁰. The rotation matrix G could be obtained by Eq (1).

$G=\left[\begin{array}{ccc}\cos \Phi 1\cos \Phi 2-\sin \Phi 1\sin \Phi 2\cos \Phi & \sin \Phi 1\cos \Phi 2+\cos \Phi 1\sin \Phi 2\cos \Phi & \sin \Phi 2\sin \Phi \\ -\cos \Phi 1\sin \Phi 2-\sin \Phi 1\sin \Phi 2\cos \Phi & -\sin \Phi 1\sin \Phi 2+\cos \Phi 1\cos \Phi 2\cos \Phi & \cos \Phi 2\sin \Phi \\ \sin \Phi 1\sin \Phi & -\cos \Phi 1\sin \Phi \cdots & \cos \Phi \end{array}\right]$ (1)

The orientation of α grain can be expressed by the matrix ${\text{G}}^{\text{α}}$. ${\text{G}}^{\text{α}}$ can be characterized by a set of 12 rotations by

${\text{S}}_{\text{j}}^{\text{α}}{\text{G}}^{\text{α}}$ (2)

where ${\text{S}}_{\text{j}}^{\text{α}}$ (j= 1, 2, … 12) is a set of rotation matrix for the hexagonal system. The BOR between α and β can be expressed by

$D=\left[\begin{array}{ccc}\frac{1}{2}\left(1+\frac{1}{6^{1/2}}\right)& \frac{1}{2}\left(\frac{1}{3^{1/2}}+\frac{1}{2^{1/2}}\right)& \frac{1}{2^{1/2}}\\ \frac{1}{2}\left(1+\frac{1}{6^{1/2}}\right)& \frac{1}{2}\left(\frac{1}{3^{1/2}}-\frac{1}{6^{1/2}}\right)& \frac{1}{2^{1/2}}\\ \frac{1}{2}\left(1-\frac{2}{6^{1/2}}\right)& \frac{1}{2}\left(\frac{1}{3^{1/2}}+\frac{2}{2^{1/2}}\right)& 0\end{array}\right]$ (3)

Therefore, the orientations of parent β grain can be calculated by

$$D^{-1}{S}_j^{\alpha }{G}^{\alpha }$$ (4)

Due to the symmetry of the cubic system, all possible orientations of parent β grains can be described as follows,

$S_i^{\alpha }{D}^{-1}{S}_j^{\alpha }{G}^{\alpha }$ (5)

Where $S_i^{\alpha }$(i=1, 2, ... 24) is a set of rotational symmetry matrix for the cubic structure.

3. Results

3.1. Microstructure and macrotexture characterization

The microstructures of the Ti80 pipe after rolling and heat treatment are shown in Figure 3. It could be observed that the original β grains were greatly elongated with a width of about 50 ± 5μm and a length of more than 500 ± 50μm. The as-rolled microstructure shows that some of the α_P are still lamellar structure and the others have been globularized within prior β grains. It indicated that the dynamic globularization occurred and the degree of globularization was mainly affected by the crystal direction of α colonies before deformation^21,22. Meanwhile, no α_S were observed in the picture, which indicated that β phase contents were very low during rolling in α+β phase region. After annealing at 960°C, the bimodal microstructure with 20% volume fraction of α_P was obtained according to the statistics by quantitative metallographic image analysis software. This was because a large amount of α phases was transformed to the β phases during the heat treatment in the dual-phase zone. In the subsequent cooling process, the β phases were transformed into the lamellar secondary α phases. As the annealing temperature increased to 990 °C, the content of the α_P decreased from 20% to 9%, and the average size of the recrystallized β grains increased from 30 ± 6 μm to 80 ± 9 μm. This could be attributed to the dissolution of more α_P as the annealing temperature increased. Then the pinning effect of α_P on β grains was reduced, and β grains will further grow up. In addition, it can be seen that the necklace like α_P have been densely distributed along the rolling direction (RD) no matter at 960 °C or 990 °C, and the distance between the necklace like α phases along the ND direction increases with the increase of annealing temperature. This phenomenon was explained in the section 3.3.

Figure 3
Optical microstructure of Ti80 pipe: (a) as-rolled (b) annealing at 960°C (c) annealing at 990 °C.

The macrotextures of samples after rolling and subsequent heat treatment are presented as {0001}/{11-20} pole figures obtained by EBSD, as shown in Figure 4. For the as-rolled sample, it shows a main texture with basal pole perpendicular to the TD direction and located ~40°away from rolling, which will be referred to as RD-40 in the following. The RD-40 was deformation texture formed during hot rolling, the intensity of which is 10 times random. For the sample annealing at 960 °C, the texture was relatively complex and included different main components. Compared with that after rolling, intensity of the texture decreased to 6 times random after annealing at 960°C. The main reason for the change of texture could be attributed to the phase transformation after heat treatment, which is explained in section 3.2. In the process of heat treatment, the dissolution of α phases are related with their morphology and crystal orientation, which will lead to the change of texture intensities and components after heat treatment. In particular, as one of the main components, the RD-40 has been preserved after annealing at 960°C. In the case of 990 °C annealed sample, the RD-40 has almost disappeared and the main texture components differ greatly from that at 960 °C. Meanwhile, the intensity of the main texture has also increased to 19 times random. In short, different annealing temperature will induce the different intensities and components of texture for Ti80 alloys with bimodal structure.

Figure 4
Macrotextures of Ti80 pipe measured using EBSD: (a) As-rolled (b) annealing at 960°C (c) annealing at 990 °C.

3.2. Microtexture of α phases

To obtain more information about the crystallographic orientation of different microstructures, detailed orientation maps were acquired from smaller representative regions. The euler maps and pole figures at three different conditions were shown in Figure 5, 6, 7. As shown in the {0001} pole figures, the main texture components obtained in smaller region are basically the same as that in large region. The representative regions of as-rolled sample has been divided into three areas, including area A, area B and area C. Most α phases have been globularized in area A and area C. The α phases in area B are still lamellar structure. The {0001} pole figure shows that the RD-40 texture mainly comes from two contributions, one is the lamellar α phases, and the other is some of the globularized α phases. At 960°C, the α_P and α_S were clearly separated in order to understand their each contributions. It was observed that the RD-40, as a component of main textures of α_P phases, was maintained. It was known that the equiaxed α_P in bimodal structure were formed by the globularization and growth of α_P lamellae during deformation and subsequent heat treatment. At the same time, the crystal orientations of α phases were almost unchanged by the static globularization according to Roy’s observation²². Therefore, the RD-40 has been preserved. Meanwhile, new texture components of α_P appeared after heat treatment at 960°C. It was because that lamellar structure are more prone to being dissolved compared with equiaxed structure due to higher content of α-stable elements²³. And the lamellar α phases as important components of RD-40 have been dissolved during the heat treatment. Then the texture components became more and the intensities were weakened.

Figure 5
The {0001} pole figures of α phase in represent regions for as-rolled Ti80 pipe.

Figure 6
The euler maps of α_P and α_S phases in represent regions: (a) α_P grains at 960°C, (b) α_S laths at 960°C, (c) α_P grains at 990°C and (d) α_S laths 990°C.

Figure 7
The {0001} pole figure maps of α texture from the representative region.

The microtextures of α_S are very close to the corresponding microtextures of α_P at 960°C, which are similar to other studies^17,18. Generally, there are two reasons for the closeness between α_P and α_S orientations. At first, the Burgers orientation between α_S and surrounding β phases after hot rolling were largely maintained. This was because that some slip systems of α_P and adjacent β grains were compatible across the α_p/β interfaces during the deformation process²⁴. Therefore, the rotations of α_P and β grains can be linked during high-temperature deformation. Meanwhile, the holding of Burgers orientation may be related to the invariance of deformation mode and temperature in this study. And the Burgers orientation between α_P and β grains would be broken under multiple deformations in different directions¹⁹. Secondly, the variants with the same orientation as α_S will be preferentially selected during the β→α_S transformation, so that adjacent α_P/α_S have close orientations. This was because the precipitation of α_S phases with close orientations to α_S phases could generate lower interface energy. With the increase of annealing temperature to 990 °C, the microstructure of RD-40 was greatly weakened. It was because that the microtextures of α_S were different to that of α_P and the texture of secondary α phases were the main components. It indicated that the precipitation of α_S phases was not mainly affected by the α_P phases at 990°C.

In order to understand the relationship between the textures of α_P and α_S phases with increasing temperature, the statistics of misorientation angles between α_P grains and neighboring α_S were shown in Figure 8. The results showed that the fraction of the low angle (less than 10°) between α_P grains and neighboring α_S decreased from 20.2% in 960°C to 7% in 990°C. It indicated that the fraction of α_P grains maintaining Burgers relationship with surrounding β matrix decreased with the increasing temperature. Therefore, this would be one factor that caused inconsistency in the textures of the α_P and α_S. In addition, the textures of α_S were also affected by its variant selection during cooling from β phases. The texture components increased and the intensities were weakened with the decrease of variants selection. In general, the number of different crystallographic orientations varies due to variant selection. Therefore, variant selection can be reflected by the statistical distribution of crystal orientations of correlated grains. The correlated misorientation analysis of the α phases are shown in Figure 9. It could be seen that the low angle boundaries (<10°C) were more dominant in 960°C compared to that in 990°C. The relative frequency of crystal orientations of 60° was higher in heat treatment of 990°C. It was known that angles including 10.5°, 60°, 60.8°, 63.3°and 90° were expected between two α variants within the same β grain²⁵. Meanwhile, the angle 60°, 60.8° and 63.3°could not be directly distinguished due to the accuracy of EBSD measurement. Theoretical calculation showed that the relative frequency of 60° was the highest if there was no variant selection^25,26. Therefore, variant selection of α_S phases occurred either in 960°C and 990°C. Meanwhile, the degree of variation selection at 960°C was higher than that at 990°C. It was because the β grains at 960 °C were smaller than those at 990°C and lamellar α phases were more likely to overgrow the entire grain. Combining with the euler maps (Figure 6), it can be seen that almost all secondary α colonies have close orientation to the adjacent α_P at 960 °C. At the annealing temperature of 990 °C, only some densely distributed α_P exhibited this orientation relationship. For those α_P scattered in the larger β grains, they rarely maintained the close orientations to the surrounding α_S. It is because that the interfaces between the α_P and the surrounding β phase decreased with decreasing α_p grains. And decreasing interfaces would induce insufficient driving force for the precipitation of α_S with similar orientations. Therefore, the growth of recrystallized β grains as well as the decreasing number of α_p would greatly reduce the effect of α_p on the variant selection of α_S. The critical content of the α_p that affects the final texture would be the subject of our future research.

Figure 8
The misorientation angle distribution between α_P and neighboring α_S: (a) 960°C , (b) 990°C.

Figure 9
The correlated misorientation angle distribution of the micromaps.

In summary, the microtextures of α_P were mainly affected by the initial texture and the dissolution degree of α phases during subsequent heat treatment. Meanwhile, the microtextures of α_S were greatly affected by the orientations of α_P when the recrystallized β grains were relatively small. With the increase of temperature and growth of recrystallized β grains, the main factor affecting the final texture changed from α_P to recrystallized β grains.

3.3. The morphology and texture evolution of β grains

As mentioned above, the microstructure and texture evolution of the α phases also were influenced by the β phases. As a near α alloy, only a little fraction of β phases remained at room temperature for Ti80 pipe. To understand the reasons for texture evolution with the increase of annealing temperature, the pole figures and inverse pole figures of original β grains (Figure 10, 11c, d) after heat treatment were reconstructed from measured α_S orientation. For the as-rolled samples, the pole figure of high temperature β phase was obtained by a small amount of residual phases at room temperature. It was because that only a small amount of β phases existed during rolling at 930°C. Figure 10 shows that the β textures changes significantly with the increasing annealing temperature. There are three main components in 100 pole figures for samples after rolling and annealing at 960°C. At the same time, the three components are perpendicular to each other in the 100 pole figure. It means that these three components correspond to an euler angle. As the annealing temperature rose to 990 °C, the components of β texture were more than that in 960 °C, and the intensity of the main texture also increased.

Figure 10
Pole figure maps from the reconstructed β grains: (a) As-rolled, (b) 960°C, (c)990°C.

Figure 11
The statistics of α_P grains maintaining Burgers relationship with neighboring β grains at 960 °C (a) and 990°C (b). Note: Burgers relationship and Non-Burgers relationship was depicted as red lines and black lines, respectively. The inverse pole figures of reconstructed β grains: (c) 960°C , (d)990°C.

The evolution of β grain morphology should be studied to understand the formation of β textures. As shown in Figure 11c, d, the reconstructed β grains were elongated with the same direction of the α_P grains of necklace shape at the annealing temperature of 960°C. The width of β grains was about 30~50μm, which was consistent with that of the secondary α colonies after deformation. It was observed that a large amount of α_P grains located in the boundaries of different β grains. It indicated that the recrystallization of β grains occurred and the growth of grains was hindered when encountered the α phases with no Burgers relationship due to the pinning effect in the process of heat treatment²⁷. At the annealing temperature of 990°C, the size of the β grains further increased due to the dissolution of more α_P. And the grain coarsening of β grains could strengthen specific β texture components²⁸. Then the stronger β texture leads to the stronger texture of α phases at 990°C.

As mentioned above, the formation of β phases at 960°C would be related to the prior β grains after rolling according to similar morphology. It could be seen that the textures of β phases after heat treatment were completely different from those after rolling. Meanwhile, only one α variant maintained the Burgers relationship with the β phases for the as-rolled sample, and more α_P variants held the Burgers relationship with surrounding β phases after heat treatment, as shown in Figure 4 and 10. Therefore, it can be deduced that the β phases at high temperature were not only from the growth of residual β phases at room temperature. It were mainly formed by the transformation of α phases at room temperature. In addition, it could be seen that the α_P grains of necklace shape have the same orientation according to the former euler map. And most of the necklace like α_P grains maintained the Burgers relationship with surrounding β grains according to the statistics, as shown in Figure 11a, b. The fraction of α_P grains maintaining Burgers relationship with β phases decreased as the annealing temperature increased from 960°C to 990°C. This can be explained by that the α phases holding Burgers relationship with adjacent β phases were more prone to phase transition. Combining with the microstructure, it could be known that these necklace like α grains were formed by the globularization of α colonies in the original β grains after rolling. And the elongated β grains were transformed from the original α colonies within deformed β grains. Meanwhile, it should be mentioned that the difference of β textures at different annealing temperature may be caused by two factors, one was the variant selection of β phases at different annealing temperatures, and the other was the change of crystal orientations during the growth of β grains. The mechanism still needs further study.

The research in this paper shows that three main methods could be used to reduce the texture intensities of Ti80 pipe after heat treatment. Firstly, the area of α_S colonies before rolling must be reduced. Secondly, the α_S colonies should be broken as much as possible during the rolling process. Finally, the size of β grains should be controlled during the subsequent heat treatment.

4. Conclusion

A study has been conducted to understand the evolution of microstructure and texture of hot-rolled Ti80 pipe during heat treatment. The following conclusions were drawn.

1. 1

   The as-rolled Ti80 pipe shows a main texture with basal pole perpendicular to the TD direction and located ~40°away from rolling direction. The crystal orientation α_P were not changed during the heat treatment. This texture has been preserved in the pole figure of α_P with the increase of annealing temperature. The dissolution of α_P induce the increase of α texture components at annealing of 960°C.

2. 2

   The textures of α_S are very close to that of α_P at the heat treatment of 960°C. When the annealing temperature increased to 990°C, the textures of α_S were not mainly affected by the crystal orientation of α_P. The necklace like α phases were transformed from the globularization of α colonies within prior β grains after rolling. The fraction of α_P maintaining Burgers relationship with β phases decreased as the annealing temperature increased from 960°C to 990°C.

3. 3

   The morphology of reconstructed β grains were similar to the prior β grains after rolling at the heat treatment of 960°C. And the growth of recrystallized β grains were hindered in the vertical direction of rolling by the necklace like α phases due to the pinning effect during the process of heat treatment. The textures of β phases were greatly influenced by the annealing temperature and the β phases at high temperature were mainly formed by the transformation of α phases at room temperature.

5. Acknowledgement

The work is financially supported by the Program of National Key Research and Development Plan of China (NO.2016YFB0301203). In addition, this work was supported by Aeronautical Science Foundation of China (No. 201911053001), National Natural Science Foundation of China (NO. 51905436), and Natural Science Foundation of Shaanxi province of China (2020JQ-156).

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Publication Dates

• Publication in this collection
  06 Dec 2021
• Date of issue
  2022

History

• Received
  17 June 2021
• Reviewed
  24 Sept 2021
• Accepted
  31 Oct 2021