Characterization and Modeling of Room-Temperature Compressive Creep Behavior of a Near α TA31 Titanium Alloy

Abstract

The creep behavior of a near α TA31 titanium alloy under different compressive pressures has been studied by long-time (up to 500 h) compression tests at room temperature. The experimental results show that several thresholds of the compressive pressure were found to exist in the compression process of the TA31 alloy. When the compressive stress is lower than 0.80Rp0.2, there is no creep. There is a steady-state creep stage at the compressive stresses between 0.85Rp0.2 and 0.93Rp0.2, in which the strain rate is approximately a constant value. When the compressive stress reaches a threshold stress between 0.93Rp0.2 and 0.95Rp0.2, the sample enters the accelerating creep stage directly. The creep model of TA31 alloy has been built by using the regression method, from which the creep strain rate of TA31 titanium alloy in the steady-state creep stage under different compressive stress levels can be calculated. The mean difference between the calculated and the experimental value is 2.54%, indicating the creep model can efficiently predict the creep behavior of TA31 alloy.

1. Introduction

The pressure-resistant structure is the most important carrier and safeguard for deep-sea equipment, such as submarines and submersibles, which determines the diving depth of the equipment. With the increase of submersible depth, it has become more and more difficult to meet the requirements of deep-sea equipment with the traditional steel pressure-resistant structure, while titanium alloy has obvious advantages in replacing traditional materials in deep-sea pressure-resistant structure due to its advantages of high specific strength, corrosion resistance, and low magnetism [1,2,3,4]. As a kind of near α titanium alloy for ship, TA31 titanium alloy also has good plastic toughness and weldability, which has a broad prospect in the field of marine and ocean engineering.

However, metal materials are prone to creep under high pressure in deep sea. Tanaket et al. [5] found that CP-Ti and commercial Ti-6Al-4V titanium alloy still undergoes obvious creep deformation when the stress level is lower than the yield stress at room temperature. Ankem et al. [6] and Oberson et al. [7] analyzed the creep mechanism of titanium alloy at room temperature, in which it has been shown that twinning can be a very slow process and contribute to low-temperature creep deformation. Because the creep is usually a very slow process [8,9], the creep problem generally does not need to be considered when the submersible will be in the deep sea for a short time. However, the creep can have implications in the stability and reliability of stressed components when working in the deep sea for a long time. A large number of studies have been carried out on the tensile creep characteristics of titanium alloy at high temperature environment of aerospace fields [10,11,12,13,14,15], but there is rare study on compressive creep of marine titanium alloys. Therefore, in this paper, we study in detailed the creep behavior of a near α TA31 titanium alloy under different pressure levels has been studied by long-time (up to 500 h) compression tests at room temperature. The creep model of the TA31 alloy has been built by using the regression method. The reliability of the model has been evaluated and verified.

2. Materials and Methods

The TA31 alloy used in this work was taken from a bar with a diameter of 25 mm, which was produced by hot-forging in the α + β temperature range and then followed with a stress relief annealing treatment. The chemical composition of the TA31 alloy plate is given in

Table 1. Chemical composition of the TA31 titanium alloy (mass fraction, %).

Al	Zr	Mo	Nb	C	N	H	O
6.13	2.06	0.97	2.96	0.010	0.005	0.001	0.09

, and the optical microstructure in the as-received condition is shown in Figure 1, which consisted of equiaxed primary alpha phase in a transformed beta matrix. The transit temperature (Tβ) of this alloy was determined as about 1000 °C. The yield strength Rp0.2 of this alloy at room temperature was 765 MPa.

The compression-creep testing was performed at room temperature (20 °C) using an electro-hydraulic servo universal testing machine MTS-370-250KN (MTS, Eden Prairie, MN, USA) as shown in Figure 2a. The geometry of the compression creep specimen is shown in Figure 3, with a gauge section of 10 mm in diameter. The total length of the 10 mm diameter cylinder in the specimen is 30 mm as shown in Figure 3, and the gauge length used in the present study is 20 mm. The extensometer MTS634.11E-24 (MTS, Eden Prairie, MN, USA) was attached to the gauge of the specimen (20 mm length) and compression displacement of the gauge was accurately recorded, as shown in Figure 2b. The compression displacement of the specimen was accurately recorded using the extensometer and transferred to the logger system which displays the corresponding compression strain under the applied stress and time. The compressive-creep tests were carried out at temperature of 20 °C under selected stresses of 0.60Rp0.2, 0.70Rp0.2, 0.80Rp0.2, 0.85Rp0.2, 0.88Rp0.2, 0.90Rp0.2, 0.93Rp0.2, and 0.95Rp0.2 to holding times of 500 h and 200 h, as shown in

Table 2. Processing parameters used in the present study.

Test No.	Compressive Stress	Holding Time	Temperature
1	0.60Rp0.2/459 MPa	500 h	20 °C
2	0.70Rp0.2/535 MPa	500 h	20 °C
3	0.80Rp0.2/612 MPa	500 h	20 °C
4	0.80Rp0.2/612 MPa	200 h	20 °C
5	0.85Rp0.2/650 MPa	200 h	20 °C
6	0.88Rp0.2/670 MPa	200 h	20 °C
7	0.90Rp0.2/688 MPa	500 h	20 °C
8	0.93Rp0.2/711 MPa	500 h	20 °C
9	0.95Rp0.2/726 MPa	500 h	20 °C

.

3. Results and Discussion

3.1. Compressive Creep Behavior

The nominal strain vs time curves of TA31 alloy under different compressive stress levels are shown in Figure 4, from which the variations of nominal strain with time can be directly obtained. The slope at any point of the curve represents the strain rate at the point. As can be seen from Figure 4, under the compression stresses of 0.60Rp0.2, 0.70Rp0.2, and 0.80Rp0.2, the nominal strain increases rapidly to 0.38%, 0.46%, and 0.54% respectively in the initial stage of loading, and then the strain is experimental time independent, and no obvious creep strain is observed, which means there is no creep under the compression stresses of 0.60Rp0.2, 0.70Rp0.2, and 0.80Rp0.2.

As the stress increasing and higher than a threshold stress, the creep strain apparently increases with creep time and significant creep appears. As shown in Figure 4, when the compressive stress is 0.85Rp0.2, 0.88Rp0.2, 0.90Rp0.2, and 0.93Rp0.2, the nominal strain increases gradually with the increase of holding time, which means there is a steady-state creep stage. The steady-state creep rate of TA31 alloy can be obtained by linear fitting of steady-state creep stage, as shown in Figure 5. The steady-state creep rates under compressive stresses of 0.85Rp0.2, 0.88Rp0.2, 0.90Rp0.2, and 0.93Rp0.2 are 4.20 × 10⁻¹⁰ s⁻¹, 9.01 × 10⁻¹⁰ s⁻¹, 1.71 × 10⁻⁹ s⁻¹, and 3.74 × 10⁻⁹ s⁻¹ respectively.

Based on the above analysis, it can be concluded that there should be a threshold stress between 0.80Rp0.2 and 0.85Rp0.2. When the stress is higher than the threshold stress, several deformation mechanisms such as dislocation slip and twinning are possible to be activated, resulting in that the strain is time-dependent and increases gradually with the increase of holding time. The threshold stress can be thought as an important indication of whether or not the creep should be considered. A similar phenomenon has been reported at room temperature creep of titanium metals and alloys under tensile stress. Sato et al. [16] conducted tests on smooth bar specimens of CP-Ti and Ti-6Al-4V titanium alloys, and the work indicated that loads greater than 55% and 75% of the 0.2% offset yield strength (Rp0.2) are needed for the accumulation of significant creep strain for CP-Ti and Ti-6Al-4V titanium alloys respectively. Peng et al. [17] studied the creep of CP-Ti and found that there is a threshold stress in the low and intermediate temperature creep of CP-Ti. These existed literatures mainly focus on creep under tensile stress. By comparing with the published data, it can be concluded that the threshold stress for room temperature creep in the present study is higher than that in the published literature, which may be caused by the two different loading methods of compression and tension. Although the deformation mechanisms of tension and compression are both dislocation slip and twinning, there is anisotropy in tension and compression of titanium alloys [18,19]. Roberts et al. [20] found significant tension–compression asymmetry for <c + a> pyramidal slip in Ti-6Al alloy, and the critical resolved shear stress increase to 820 MPa under compression and decrease to 558 MPa in tension. Jones et al. [21] found that uniaxial compression along the c-axis the <c + a> dislocations cross-slip readily, but they do not do so in uniaxial tension, and a tensile normal stress decreased the critical resolves shear stress compared to a compressive normal stress. Studies on single colony crystals of Ti-6242Si showed significant tension/compression asymmetry in the critical resolved shear stress for <a>-type basal slip. Slip line studies of colony crystals showed very coarse, planar slip in compression, but very homogeneous, wavy slip in tension, which indicate an easier cross slip in tension [22].

When the compressive stress reaches 0.95Rp0.2, the sample loses its stability rapidly. It can be concluded that there should be another threshold stress between 0.93Rp0.2 and 0.95Rp0.2. When the compressive stress reaches threshold stress, the sample enters the accelerating creep stage directly.

Lastly, the extensometer was monitored during the load removal in order to evaluate whether the deformation was elastic or plastic in nature. The strain–stress curves of TA31 alloy under uniaxial compression stress are shown in Figure 6, from which the variation of strain with stress during the loading, stress maintaining, and unloading processes are directly obtained. As can be seen from Figure 6, the strain increases linearly with the increasing of stress in the loading stage. During the stress maintaining stage, the strain gradually increases to the maximum value, and the maximum nominal strain depends on the stress and the stress maintaining time. In the unloading stage, the nominal strain decreases linearly with the decrease of stress, which is caused by the elimination of elastic strain. The strain after the stress is completely removed is called residual strain.

The maximum strain and residual strain in the compression process of TA31 alloy are shown in

Table 3. Maximum strain and residual strain in compression of TA31 alloy.

Test No.	Compressive Stress	Holding Time (h)	Maximum Strain (%)	Residual Strain (%)	Remarks
1	0.60Rp0.2	500	0.381	0.001	-
2	0.70Rp0.2	500	0.463	0.004	-
3	0.80Rp0.2	500	0.543	0.045	-
4	0.80Rp0.2	200	0.543	0.040	-
5	0.85Rp0.2	200	0.674	0.126	-
6	0.88Rp0.2	500	0.868	0.303	-
7	0.90Rp0.2	500	1.048	0.479	-
8	0.93Rp0.2	500	1.364	0.777	-
9	0.95Rp0.2	500	-	-	Loses stability

. As can be seen from Table 3, the maximum strain and the residual strain are 0.543% and 0.040% respectively under the compressive stress of 0.80Rp0.2 to the holding time of 200 h, whereas the two values are 0.543% and 0.045% respectively under the same compressive stress of 0.80Rp0.2 to the holding time of 500 h, from which it is demonstrated that when the compressive stress is 0.80Rp0.2 or lower there is no creep.

3.2. Compression Creep Model

In the creep test of metals and alloys, the most important parameter is the steady-state creep rate [23,24]. The dependence of compressive creep stress on the temperature and strain rate is generally expressed in terms of three kinetic equations given by

$$\dot{\epsilon }\exp \left(\frac{Q}{RT}\right)=A{\left(\sigma \right)}^n$$

(1)

$$\dot{\epsilon }\exp \left(\frac{Q}{RT}\right)=A_1\exp \left(n_1\sigma \right)$$

(2)

$$\dot{\epsilon }\exp \left(\frac{Q}{RT}\right)=A_2\sinh {(\alpha \sigma )}^{n_2}$$

(3)

where A, A₁, A₂, and α are constants; $\dot{\epsilon }$ is the strain rate (s⁻¹), σ is the stress (MPa); Q is the activation energy of deformation (kJ/mol); R is the gas constant (8.3145 J·mol⁻¹·K⁻¹); T is the absolute deformation temperature (K); n, n₁, and n₂ are the stress exponents [25,26,27,28].

Equations (1)–(3) can be written as Equations (4)–(6) respectively by taking a logarithm transformation of both side of the formulas

$$\ln \sigma =\ln \dot{\epsilon }/n+Q/(nRT)-\ln A/n$$

(4)

$$\sigma =\ln \dot{\epsilon }/n1+Q/(n1RT)-\ln A1/n1$$

(5)

$$\ln [\sinh (\alpha \sigma )]=\ln \dot{\epsilon }/n_2+Q/(n_{2}RT)-\ln A_2/n_2$$

(6)

Based on the experimental data, the curve of ln(σ) vs. $\ln \dot{\epsilon }$ can be plotted, as shown in Figure 7, from which it can be concluded that Equation (4) is suitable for the creep model of the TA31 titanium alloy.

When the creep deformation temperature is 20 °C, lnA − Q/(RT) = K is a constant and Equation (4) can be expressed as

$$\ln \sigma =\ln \dot{\epsilon }/n+Q/(nRT)-\ln A/n$$

(7)

The values of n and K can be derived from the slope and intercept of the linear fitting line of ln (σ) vs. $\ln \dot{\epsilon }$ as shown in Figure 7. The values of n and K in the present study are −179.71 and 24.41, respectively.

Therefore, the creep model of TA31 titanium alloy can be expressed as Equation (8)

$$\ln \dot{\epsilon }=-179.71+24.41\ln \sigma ,$$

(8)

which can be written as Equation (9)

$$\dot{\epsilon }=e^{-179.71}{\sigma }^{24.41}$$

(9)

On account of the creep model, the creep rate of TA31 titanium alloy in the steady-state creep stage under different compressive stress levels can be calculated. Figure 8 and

Table 4. Comparison of calculated with experimental creep strain rate of TA31 titanium alloy.

Compressive Stress (MPa)	Strain Rate (s−1)		Error	Remarks
	Experimented	Calculated
650	4.20 × 10−10	4.13 × 10−10	1.62%	☆
670	9.01 × 10−10	8.66 × 10−10	3.91%	△
688	1.71 × 10−9	1.65 × 10−9	3.29%	☆
711	3.74 × 10−9	3.69 × 10−9	1.33%	☆

☆—The experimental data had been used in the establishment process of the model; △—The experimental data had not been used in the establishment process of the model.

illustrate a comparison of the calculated with the experimental strain rate of TA31 titanium alloy. The mean difference between the calculated with the experimental strain rate of TA31 titanium alloy is 2.54%, suggesting the effectiveness and reliability of the creep model in predicting the creep behavior of TA31 alloy.

4. Conclusions

In this work, the creep behavior of a near α TA31 titanium alloy under different compressive pressures has been investigated at room temperature. The creep model of TA31 alloy has been built by using the regression method. The effectiveness and reliability of this model has been verified. The following main results are obtained.

(1)

There is a steady-state creep stage in the TA31 titanium alloy at the compressive stresses between 0.85Rp0.2 and 0.93Rp0.2, in which the strain rate is approximately a constant value. When the compressive stress is 0.80Rp0.2 or lower, there is no creep. When the compressive stress reaches a threshold stress between 0.93Rp0.2 and 0.95Rp0.2, the sample enters the accelerated creep stage directly.

(2)

The creep model of TA31 titanium alloy has been established, from which the creep strain rate of TA31 titanium alloy in the steady-state creep stage under different compressive stresses can be calculated, and the mean difference between the calculated and the experimental value is 2.54%.