Evaluation of Flow Behavior of Novel Titanium Ti-3873 Alloy Via Compressive Deformation in Two Phase α/β and Single Phase β Regions
محورهای موضوعی : Thermomechanical
Mahnaz Dabbaghi
1
,
Maryam Morakabati
2
1 - Faculty of Materials and Manufacturing Thechnologies, Malek Ashtar University of Technology, Tehran, Iran
2 - Faculty of Materials and Manufacturing Technologies, Malek Ashtar University of Technology
کلید واژه: Ti-3Al-8Mo-7V-3Cr alloy, recovery, recrystallization, activation energy, processing map,
چکیده مقاله :
Semi-stable β-titanium (Ti-3873) Ti-3Al-8Mo-7V-3Cr alloy with excellent workability properties has been designed based on high demanded aircraft Ti-5Al-5Mo-5V-3Cr alloy according to semi-experimental d-electron approach. The aim of the present research is to investigate the deformation behavior of Ti-3873 alloy via warm compression test. For this purpose, compression test has been conducted in the temperature range of 650-850 °C and strain rates of 0.001,0.1 and 1, 1 s-1 at dual phase α/β and single phase β regions. The test was continued up to plastic strain of 0.7. For establishing the relationship between the microstructure and flow behavior, the initial and subsequent microstructure of the specimens after warm deformation was studied via optical and scanning electron microscopes. The microstructural evaluation and flow curves revealed that dynamic recovery and partial continuous dynamic recrystallization were the dominant restoration mechanisms. The results showed that softening has been increased in the temperature range of 800-850 °C and strain of 0.001 and 0.1 s-1 which is confirmed by the activation energy calculated from the sinus hyperbolic equation. The activation energy for dual phase α/β and single phase β regions are determines as 429 kJ/mol and 353 kJ/mol, respectively. The higher value of activation energy for α/β dual phase region is attributed to dynamic globularization of α lamellas. The preferable regions for hot workability of the alloy were achieved at the temperature range of 800-850 °C and strain rate of 0.01-0.001 s-1 corresponding to the peak efficiency of 39% in the processing map.
Semi-stable β-titanium (Ti-3873) Ti-3Al-8Mo-7V-3Cr alloy with excellent workability properties has been designed based on high demanded aircraft Ti-5Al-5Mo-5V-3Cr alloy according to semi-experimental d-electron approach. The aim of the present research is to investigate the deformation behavior of Ti-3873 alloy via warm compression test. For this purpose, compression test has been conducted in the temperature range of 650-850 °C and strain rates of 0.001,0.1 and 1, 1 s-1 at dual phase α/β and single phase β regions. The test was continued up to plastic strain of 0.7. For establishing the relationship between the microstructure and flow behavior, the initial and subsequent microstructure of the specimens after warm deformation was studied via optical and scanning electron microscopes. The microstructural evaluation and flow curves revealed that dynamic recovery and partial continuous dynamic recrystallization were the dominant restoration mechanisms. The results showed that softening has been increased in the temperature range of 800-850 °C and strain of 0.001 and 0.1 s-1 which is confirmed by the activation energy calculated from the sinus hyperbolic equation. The activation energy for dual phase α/β and single phase β regions are determines as 429 kJ/mol and 353 kJ/mol, respectively. The higher value of activation energy for α/β dual phase region is attributed to dynamic globularization of α lamellas. The preferable regions for hot workability of the alloy were achieved at the temperature range of 800-850 °C and strain rate of 0.01-0.001 s-1 corresponding to the peak efficiency of 39% in the processing map.
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Evaluation of flow behavior of novel titanium Ti-3873 alloy via compressive deformation in two phase α/β and single phase β regions
Abstract
Semi-stable β-titanium (Ti-3873) Ti-3Al-8Mo-7V-3Cr alloy with excellent workability properties has been designed based on high demanded aircraft Ti-5Al-5Mo-5V-3Cr alloy according to semi-experimental d-electron approach. The aim of the present research is to investigate the deformation behavior of Ti-3873 alloy via warm compression test. For this purpose, compression test has been conducted in the temperature range of 650-850 °C and strain rates of 0.001,0.1 and 1, 1 s-1 at dual phase α/β and single phase β regions. The test was continued up to plastic strain of 0.7. For establishing the relationship between the microstructure and flow behavior, the initial and subsequent microstructure of the specimens after warm deformation was studied via optical and scanning electron microscopes. The microstructural evaluation and flow curves revealed that dynamic recovery and partial continuous dynamic recrystallization were the dominant restoration mechanisms. The results showed that softening has been increased in the temperature range of 800-850 °C and strain of 0.001 and 0.1 s-1 which is confirmed by the activation energy calculated from the sinus hyperbolic equation. The activation energy for dual phase α/β and single phase β regions are determines as 429 kJ/mol and 353 kJ/mol, respectively. The higher value of activation energy for α/β dual phase region is attributed to dynamic globularization of α lamellas. The preferable regions for hot workability of the alloy were achieved at the temperature range of 800-850 °C and strain rate of 0.01-0.001 s-1 corresponding to the peak efficiency of 39% in the processing map.
Keywords: Ti-3Al-8Mo-7V-3Cr alloy, warm compression test, recovery, recrystallization, activation energy, processing map.
1. Introduction
Figure 1. Deformation mechanism range for the designed titanium alloys in 
-
diagram [7].
In addition, it was reported that the bonding strength of the Ti-3873 alloy is higher than that of Ti-5553 alloy which is related to its higher stability of β-phase and higher Mo equivalent parameter. Therefore, this alloy has high workability [14]. In Fig. 1, the positions of reference alloy (i.e., Ti-5553) and the designed alloy (i.e., Ti-5873) in 
-
diagram are exhibited. However, lack of sufficient information in the case of high temperature application of the Ti-3873 alloy cause postponing in substituting of this alloy with the Ti-5553 alloy. Previous researches [15-17] revealed that dynamic recovery (DRV) and dynamic recrystallisation (DRX) control the microstructure and mechanical behavior of the β-titanium alloys. The volume fraction of recrystallized grains is related to the stacking fault energy (SFE). As known, SFE is a function of the chemical composition. Therefore, it is expected that by changing the chemical composition of the Ti-5553 alloy and the development of the Ti-3873 alloy, the formability of the novel alloy will be changed. Therefore, optimizing the deformation condition of the novel alloy is needed.
The microstructure and mechanical behavior of the semi-stable β-titanium alloy is usually sensitive to the deformation parameters. During the deformation, recovery and recrystallisation has been extensively occurred leading to achieve excellent mechanical properties. For instance, Momeni et al [18], studied the hot compression behavior of the Ti-5553 alloy at the temperature range of 930-1080 °C and strain rate of 0.001-1 sec-1. The result revealed that the flow behavior of the alloy was predominantly controlled by dynamic recovery and continuous dynamic recrystallisation at temperature of 1080 °C and strain rate of 0.001 sec-1. Other researchers [19] investigated the hot deformation behavior of the Ti-22Al-25Nb alloy by developing the processing map. It has been reported that the main mechanism of the hot deformation of the alloy is the globularization of the initial α grains. Zhu et al. [20] analyzed the flow behavior of the SP-700 alloy by developing the processing map. They evaluate the unstable regions of the map, as well.
The main aim of the present research is to investigate the warm deformation behavior of the
Ti-3873 alloy. The restoration mechanism and activation energy of the deformation at dual phase α/β and single phase β regions have been determined. For this purpose, the compression test has been carried out at different temperatures and strain rates. The flow curves have been predicted using constitutive equations. Consequently, the processing map of the alloy has been developed in order to determine the stable regions during deformation. Subsequently, regarding the power dissipation energy of the processing map, the deformation condition of the Ti-3873 alloy was optimized.
2. Materials and experimental investigation
The studied alloy was manufactured 2 times to ensure chemical homogeneity via melting and remelting process in vacuum arc remelting (VAR) furnace. The first stage includes melting the briquettes of granules of titanium sponge with appropriate alloy-containing material. The second stage is remelting the electrode produced from the previous stage. It should be noted that the ingot was prepared by melting pure elements. In order to obtain homogenous microstructure, the homogenization heat treatment had been carried out at the temperature of 1000 °C for 5 hours. Then the ingot was immediately hot rolled at the same temperature. The reduction in thickness during rolling was approximately 60 %. The chemical composition of the alloy was analyzed using scanning electron microscopy (TESCAN) equipped the EDS detector. The nominal composition of the alloy is summarized in table 1. It was clearly observed that the chemical composition of the Ti-3873 alloy is in accordance with its nominal composition.
Table 1. The EDS analysis of the Ti-3873 alloy.
Element | Cr | V | Mo | Al | Ti |
Nominal composition | 3 | 7 | 8 | 3 | 79 |
Chemical Analysis | 2.8 | 7.1 | 7.8 | 3.1 | 79.2 |
The content of oxygen, nitrogen and hydrogen has been measured by gas analyzer method using Leco-TCH600 machine. The results are reported in table 2.
Table 2. The result of gas analyzer for Ti-3873 alloy (ppm).
Element | N | H | O |
Gas analyzer of the specimen | <1 | <1 | 2150 |
The β-transus temperature of the alloy was determined using metallographic technique in the range of 740-800 °C. According to this method, the Tβ of the alloy was recorded to be 750 ± 10 °C. In order to investigate the effect of temperature and strain rate on the compressive deformation of the Ti-3873 alloy, cylindrical compression specimens with 8 mm in diameter and 12 mm in height were prepared according to the ASTM E209 standard. The graphite powder was used as lubricant. The uniaxial compression test has been carried out at the temperature of the 650, 700, 750, 800 and 850 °C and strain rates of 0.001, 0.1 and 1 s-1. Then specimens rapidly quenched in water. The specimens were preheated for 10 minutes at the temperature of warm compression test. The tests were performed using an Instron 8502 machine equipped with furnace. Prior to compression test, the specimens were homogenized at the single phase β region at 830 °C for 30 minutes. The microstructure of the specimen after homogenization can be observed in Fig. 2. As seen, the microstructure contains the equiaxed grains with mean grain size of 70 µm. To reveal the deformed microstructures, prepared specimens were etched with Kroll's reagent (2 ml HF, 6 ml HNO3, 92 ml H2O).
Figure 2. The microstructure of the Ti-3873 alloy after annealing at 830 °C for 30 minutes.
The relationship between head velocity (V) and strain rate 
during compression test was derived as the following equation (Eq. 1.):
(1)
where, L0 is referred to the initial height of the specimen. During the compression test, height reduction of the specimen leads to variation in strain rate. Decreasing in height of specimen resulted in gradually increasing the strain rate value. Therefore, for remaining constant strain rate value, the head velocity is continuously decreased. Hence, in this condition the ratio of V/L0 keeps unchanged. The strain distribution and temperature gradient via compression test has been simulated using Deform software.
2.1 The Correction of flow curves for heat of deformation
Deformation heating may also result in a temperature increase in an ‘isothermal’ test which leads to flow softening. While sufficient time for dissipation of heat at low strain rates allows deformation to progress isothermally, at higher strain rates the entrapment of deformation heat results in adiabatic heating of specimen. This feature suggests that further factors such as heat transfer constants of the material affect the temperature rise. the materials possessing low heat capacity, low thermal conductivity, and high strength are more sensitive to temperature rise impeding heat transfer to outside. In this work, the effect of heat of deformation on flow stress was calculated. At first step, for each strain and strain rate, the stress level at deformation temperature was extracted and the function of 
was derived. Form the variation of temperature (
), the variation of the stress (
) obtained as the following equation (Eq. 2) [21]:
(2) |
| |||
(3) |
|
where, ro = initial radius (mm), ho= initial height (mm), mf= friction coefficient, σ= corrected flow stress (MPa).
3. Results and Discussion
3.1. Flow stress behavior of the Ti-3873 alloy
The flow curves of the Ti-3873 alloy in dual phase α/β region and single phase β region have been presented in Fig. 3.a and 3.b, respectively. In this figure, only the result of deformation at temperatures of 650 and 850 °C and the applied strain rate of 0.001, 0.1 and 1 s-1 are represented.
As it is seen, at a given temperature, the flow stress increases with increasing strain rate. Two types of stress strain curves are presented in the figure: one type is characterized by a “peak stress” where the true stress is reached to maximum and then it is decreased with increase in strain (Fig. 3.a) . While, the second type is characterized by a “steady state stress” in which the stress remained essentially constant from initial yielding to the maximum strain (Fig. 3.b). As it is known, the first one is related to deformation in dual phase α/β region and the second one is related to deformation in single phase β region. It was clearly observed that the drastically drop in the curves is related to the highest value of the strain rate (i.e., 
). The main reason for this behavior is attributed to the adiabatic heating, the microstructural evolution, phase transformation and the propagation of micro-cracks via deformation [23]. The flow stress drop at the higher strain rates and lower temperatures are noticeably high.
Figure 3. The stress-strain curves of the Ti3873 alloy at strain rates of 0.001, 0.1 and 1 s-1 and temperatures of a) 650 °C, b) 850 °C.
Adiabatic heating leads to non-uniform deformation resulted to the shear band formation at low temperature and high strain rate. In Fig. 4, the appearance of shear bands at the temperature of 650 and 700 °C and strain rate of 1 s-1 is shown. According to this figure, it can be deduced that instability mechanism in this region is predominantly related to the localization of deformation. The orientation between the shear bands and the applied stress which is formed at the temperature of 650 and 700 °C is about 45°. This phenomenon is attributed to the generation of heat at high strain rates. Low thermal conductivity of the titanium alloys in comparison with other metallic materials (like Aluminum and steel) is another important parameter facilitating the localization of deformation at this alloy.
Figure 4. The appearance of shear bands at strain rate of 1 s-1 and temperatures of: a) 650 °C, b) 700 °C.
The strain distribution in the specimens deformed at 800 and 850 °C and strain rate of 0.001 s-1 is presented in Fig. 6. As it is seen, despite applying the plastic strain up to 0.7, some regions of the specimen experience much more strains. The main reason for this phenomenon is that in the region between surface of the specimen and die, friction causes high degree of resistance to the deformation. The comparison of the strain distribution contour for the specimens deformed at 800 and 850 °C, revealed that by decreasing the deformation temperature, the value of the effective strain has been noticeably increased. This is attributed to the fact that the workability of the material decreases by reduction of temperature. Therefore, the dead zone region was increased and the value of the strain which is generated in this region is decreased. Consequently, the strain in the center of the specimen is localized.
Figure 6. The strain distribution of the specimens deformed at strain rate of 0.001 s-1 and temperatures of:
a) 800 °C, and b) 850 °C.
The stress strain curves of the alloy before and after friction and adiabatic heating corrections are shown in Figure 7. It should be noted that the result is only represented for the specimens tested at 650 °C as an example of all test temperatures. As it is seen, by adiabatic heating correction, the uncompensated curves shift to higher values of flow stress confirms the adiabatic heating effect for softening this titanium alloy. Whereas, the flow curves show the inverse behavior after friction correction supports the effect of friction for increasing the force and consequently the stress between specimens and mandrel.
Figure 7. True stress–true strain curves of the alloy before and after (a) adiabatic heating and (b) friction corrections at the temperature of 650 °C.
Figure 8. True stress–true strain curves of the alloy before and after friction and adiabatic heating correction at the temperatures of: a)650 °C, and b)850 °C.
3.2. Microstructural evolution of the Ti-3873 alloy after compression test
The optical micrographs of the alloy after warm deformation at 850 °C and strain rates of the 1, 0.1, and 0.001 s-1 are illustrated in Fig. 9. As it is seen in Fig. 9 (a), dynamic recrystallization has occurred to a limited extent. However, the time for occurrence of dynamic restoration processes was insufficient. By decreasing the strain rate (lower value of Z parameter), grain boundary serrations can be observed clearly. Researchers declared [24] that by increasing the deformation temperature and decreasing the strain rate, as a result of dynamic recovery, the grain boundaries migrate locally in response to the boundary tensions of the subgrains and to local dislocation density variations. Consequently, they become serrated with a wavelength which is closely related to their subgrain size. Therefore, dynamic recovery occurred at the temperature of the 850 °C and strain rates of 0.001 and 0.1 s-1.
Figure 9. The microstructure of the specimens deformed at the temperature of 850 °C and strain rates of
a) 1, b) 0.1, c)0.001 s-1.
According to the previous studies [18], the dynamic recovery is the dominant softening mechanism via warm working of the β- titanium alloy. However, continuous dynamic recrystallization (CDRX) may be occurred at high strains. The required condition for the occurrence of continuous dynamic recrystallization is the gradual rotation or migration of the sub-grains via recovery process and the transition from low angle grain boundaries (LAGBs) to high angle grain boundaries (HAGBs). In Fig. 9 (c), some serrated grain boundaries have been observed. The wavelength of these serrations is much more than that presented in Fig. 8 (b). Some fine equiaxed grains located adjacent to the serrated high angle grain boundaries confirmed that dynamic recrystallization has been slightly occurred.
3.3. Constitutive equations for corrected flow curves of the Ti-3873 alloy
Constitutive equations have been defined in order to establish the relationship between the flow stress of a material (σ, MPa) and deformation parameters like strain rate (
, s-1) and temperature (T, K) according to the (Z) equation (E.q. 4). By manipulating three hyperbolic, exponential and power law, the relationship has been derived as below [25]:
(4)
The common constitutive equation defined for various alloys is sinus-hyperbolic equation (E.q. 5) Where, R, A, α and n are referred to the material's constant. In this equation the value of σ by considering the behavior of the flow curves is corresponding to the peak stress or the steady state flow stress of the material (MPa) [26].
(5)
The slope of the plot of 
gives the average value of n in the α/β dual phase and β phase region (see Fig. 10 (a)).
Figure 10. Plots of a) 
, b) 
, and c) 
at strain of 0.7.
The values of n and α were computed for these regions. It should be mention that for computing these parameters, the specimens were deformed up to strain of 0.7. Then, the value of the s has been determined from the slope of the Ln(sinh(ασ) -1000/T), (see Fig. 10 (b)). Based on Q=nsR relationship, the activation energy of the warm deformation process was computed. Therefore, the activation energy of the Ti-3873 alloy in the temperature range of 650-850 °C and strain rates of 0.001, 0.1 and 1 s-1 for dual phase α/β and single phase β regions are calculated as 429 and 353 kJ/mol, respectively. As a result of the variation of α parameter in single and dual phase regions and due to the difference in the Q value of these regions, the diagrams illustrated in Fig. 10. (b) and 10. (c) are divided into two distinct regions with different equations. The resultants constitutive equations for warm deformation of the alloy in α/β and β regions are as follows:
(6) |
(7) |
Jonas et al [27] demonstrated that the variation of Q for dual phase α/β region in comparison to β phase region is related to the difference between the flow stress of the hard α phase and soft β phase. The other important parameter which affects the variation of Q is the dependence of volume fraction of α phase to the temperature.
It has been proved that at low flow stresses (ασ<0.8), Eq. (5) is changed to a power-law equation as below:
(8)
(9)
where A and n are material constants. In order to determine them, the LnZ vs Lnσ plotted (see Fig. 11).
Figure 11. Plots of (a) 
, b) 
, and c) 
at strain of 0.7.
As it is seen, the value of n for the dual phase α/β and single phase β is obtained as 9.4 and 6.1, respectively. Moreover, using LnZ vs Lnσ diagram, the value of A for dual phase α/β and single phase β regions is determined as 10.3 and 6.8, respectively. Hence, there is a linear relationship between the stress and Z as given by the following equations (Eq. 10 and Eq. 11) for the dual phase α/β and single phase β regions, respectively:
(10)
(11)
Finally, the power-law relation is given by the following equations (Eq. 12 and Eq. 13) for the dual phase α/β and single phase β regions, respectively:
(12)
(13)
At high flow stresses (ασ>1.2), the Eq. (5) is changed to an exponential form as below: [28, 29]:
(14)
where, B and β are referring to the constant parameters of the material. This equation, similar to the previous equation, the sigma is referred to the peak stress or the steady state stress (MPa). For the purpose of determining the constant parameters of the exponential equation, the logarithmic form of the equation 14 was derived. Therefore, the equation was correlated in linear form. For obtaining the exponential relationship, the 
plots were presented in Fig. 12. According to Fig. 12 (a), the n parameter for dual phase and single phase is obtained as 10.31 and 5.3, respectively.
The S parameter can be determined from the slope of the plot of the s -10000/T diagram, as shown in Fig. 12 (b), S determined as 0.53 and 0.61 for dual phase α/β and single phase β regions, respectively. The intercept in the plot of 
, gives the value of A for both regions.
The modified exponential equation is given by the following equations (Eq. 15 and Eq. 16) for the dual phase α/β and single phase β regions, respectively:
(16) |
(15) |
Figure 12. Plots of a) 
, b) 
, and c) LnZ
at strain of 0.7.
From the regression analysis of the relation between the flow stress and Z parameter, the R2 has been computed for each equation as shown in Table 3. As it is seen, the hyperbolic equation represents an acceptable prediction of the experimental flow curves of the Ti-3873 alloy.
Table 3. The derived activation energy (Q), R2, and constitutive equations obtained for the
Ti-3873 alloy.
Adj .R-Square | Constitutive equation
| Energy Activation e (kJ/mol) | region | Approach |
R2=98.5 |
| 429 | α/β | Hyperbolic |
R2=99.8 |
| 353 | β | |
R2=97.7 |
| 510 | α/β | Power-law |
R2=95.7 |
| 314 | β | |
R2=98.1 |
| 453 | α/β | Exponential |
R2=98.1 |
| 268 | β | |
Activation energy (kJ/mol( | Initial microstructure | alloy | |
Dual phase αβ/ | Single phase β | ||
165.2 | 305.5 | Plate-like α phase | SP-700 |
376 | 530 | Equiaxed α phase | Ti-6Al-4V |
275 | 148 | Globular α phase | Ti–5Al–5Mo–5V–3Cr–1Zr |
The main reason for the higher value of the activation energy at dual phase α/β region is the occurrence of the dynamic globularization [26]. In Fig. 13, the SEM microstructure of the specimens deformed at the temperature of 650 and 700 °C and strain rate of 0.001 is exhibited. Both images show the dual phase α/β microstructure. The difference between these two images is the morphology of the phases. As it is seen, the microstructure of the specimen deformed at 650 °C includes lamellar and globular α phase in the β matrix. However, by increasing the temperature to 700 °C, the globularization of α phase has been accomplished. Therefore, dynamic globularization of α phase may cause higher activation energy during deformation of the Ti-3873 alloy.
Figure 13. The SEM images of the specimens deformed at: a) 650 °C and
b) 700 °C and strain rate of 0.001 s-1.
3.4. Prediction of workability of the alloy using processing map
Processing maps have been provided according to the dynamic model of the materials. It was assumed that the energy has been consumed via deformation process of the material. The content of the energy loss for the specified condition of the deformation has been defined based on the variation of the stress versus variation of the strain rate. This parameter (
) is referred to the strain rate sensitivity coefficient. It is obvious that the major part of the energy loss is converted to the heat of the deformation resulted in increasing the temperature of the material via plastic deformation. While a very minor part of the energy loss leads to the evolution of microstructure. The power dissipation efficiency (
) of the material is defined as [32]:
(17) |
|
(18) |
|
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