Advances in Materials Science and Engineering

Advances in Materials Science and Engineering / 2013 / Article

Research Article | Open Access

Volume 2013 |Article ID 512606 |

Woo Young Jung, Tae Kwon Ha, "High Temperature Deformation Behavior of 8090 Al-Li Alloy", Advances in Materials Science and Engineering, vol. 2013, Article ID 512606, 9 pages, 2013.

High Temperature Deformation Behavior of 8090 Al-Li Alloy

Academic Editor: S. Miyazaki
Received25 Mar 2013
Accepted17 Jun 2013
Published29 Jul 2013


High temperature deformation behavior, especially the superplasticity of an 8090 Al-Li alloy, was studied within the recent framework of the internal variable theory of structural superplasticity. In this study, a series of load relaxation tests were conducted at various temperatures ranging from 200°C to 530°C to obtain the flow curves of log  versus log . The effect of grain size was also examined by varying the grain sizes through a proper thermomechanical treatment. The flow curves were found to be composite curves consisting of contributions from grain boundary sliding (GBS) and grain matrix deformation (GMD) at superplastic temperatures. The activation energy obtained for GMD was 124.9 kJ/mole in the temperature range from 470°C to 530°C, very similar to that for self-diffusion in pure Al.

1. Introduction

The high temperature deformation behavior, including superplasticity, of crystalline materials has generally been described phenomenologically by a power-law relation between the two external variables, namely, flow stress () and strain rate (), as follows [1, 2]: where is a constant. The strain rate sensitivity parameter, , can then be defined as the slope of the versus curves. This parameter has widely been used as one of the most important parameters characterizing the superplastic deformation behavior [13]. The value of is, however, observed to vary continuously along the versus curves, unable to provide a critical value above which superplastic deformation can be predicted [4]. When it comes to structural superplasticity (SSP), it is apparent that the external or phenomenological variables such as , , and alone cannot adequately describe SSP.

Superplasticity is a deformation process that produces large elongation of more than several hundred percent in crystalline materials, usually deformed in tension at a very low level of stress. Grain boundary sliding (GBS) is widely accepted as the most important deformation mechanism of superplasticity. In general, superplastic properties are exhibited in materials having a stable, equiaxed, and extremely fine microstructure only under a very narrow range of strain rate and temperature normally above 0.5, where is an absolute melting temperature [3].

A new approach to structural superplasticity (SSP) has been made by taking the dislocation glide mechanism as the major accommodation process for GBS [5], instead of the generally accepted high temperature diffusion process [6]. The justification for this approach comes from the observation that the superplastic deformation usually occurs in the strain rate range coinciding with that of plastic deformation caused by a dislocation glide.

After obtaining the various grain sizes through a proper thermomechanical treatment, a series of load relaxation and tensile tests were conducted at temperatures ranging from 200°C to 530°C in this study. The load relaxation test provided the flow data in a much wider range of strain rate with minimal microstructural change or constant microstructure during the test [7, 8], making it possible to analyze the flow curves within the framework of the internal variable theory of SSP. The effect of grain size and temperature on the flow behavior of 8090 Al-Li alloy was specifically investigated based on the internal variable theory of SSP, and a critical condition for superplastic deformation is proposed. The next section provides a brief description of the internal variable theory of SSP.

2. Internal Variable Theory of SSP

The typical internal variable model, proposed by Chang and Aifantis [9], has described in detail a constitutive framework to consider inelastic deformation based on the notion of internal strain and internal spin tensors together with their precise micromechanical origin. Repeating here some important concepts of the model, a simple rheological model has been proposed by considering the grain matrix deformation (GMD) as a major accommodating process for GBS [5]. The two deformation mechanisms, that is, GBS and GMD, compete with each other in high temperature deformation of polycrystalline materials when it is not confined to SSP.

An elementary material volume bounded by the surface within and across which dislocations are allowed to move in response to a stress field () is considered here. When the material boundary acts as a strong barrier partially blocking the passage of dislocations, some of dislocations would remain inside the material volume, giving rise to an internal strain (), while at the same time the rest of the dislocations will pass through to produce an externally observable plastic deformation (). These simultaneous processes of accumulation within and the passage through of dislocations are believed to be the most fundamental deformation mechanism responsible for various mechanical phenomena, such as plasticity [10], phase transformation [11], and fracture.

Instead of using the phenomenological power law relation between and , a simple rheological model is used in this study. This model given in Figure 1 shows that GBS is mainly accommodated by a dislocation process, giving rise to an internal strain () and plastic strain rate (). For the model given in Figure 1, we derived the following stress relation and kinematic relation among the deformation rate variables, , , and , due to GBS:

The internal variables and represent the internal stress required to overcome a long-range interaction force among glide dislocations and the friction stress to surmount a short-range interaction force between dislocations and lattices, respectively. The time rate denotes the materials time rate [12] of change of internal strain tensor similar to that prescribed by Hart [13]. A topological representation for this model is given in Figure 2.

The constitutive relations between the stress variables and the deformation rate variables for grain matrix plastic deformation have been prescribed [5] in a form similar to that of Hart [13] from the viewpoint of simple dislocation kinetics. These relations can be written as follows: where , , , and are the material constants. and in (4) are the internal strength variable and its conjugate reference strain rate, respectively, and they are related by (5) with jump frequency, an activation energy, and an internal modulus [5]. Equation (4) is, in fact, a kinetic rate equation of a mechanical activation process for a leading dislocation to overcome grain boundaries. Equation (6) represents the friction glide process of dislocations in lattice. and are the static friction stress and its conjugate reference strain rate, and they are related by (7) with jump frequency, an activation energy for this process, and a shear modulus.

Considering the GBS as a viscous drag process similar to the frictional glide process of dislocations, the following power-law relation has been prescribed as [5] where and denote material constants. The constitutive parameters and are the static friction stress and its conjugate reference rate for GBS, respectively. Equation (8) is again viewed as a thermally activated process of GBS with now denoting the activation energy for GBS.

At high temperature range as that used in this study, is in general very small compared to  , and can be neglected if the relaxation test is conducted uniaxially at a steady state. We can, therefore, describe high temperature deformation behavior of crystalline materials with the constitutive relations for and elements.

3. Experimental Procedure

The 8090 A1-Li alloy used in this study was supplied in the form of a plate with the thickness of 44.5 mm, solution-treated, 6% stretched, and naturally aged condition (T3771). This material, known as LITHAL together with 8091 Al-Li alloy in generic name, had the chemical composition given in Table 1. A proper thermomechanical treatment (TMT) is required before expecting the superplasticity for this alloy, because the as-received material has elongated and pancake-shaped microstructure. The basic concept of thermomechanical treatment (for grain refinement of precipitation hardening aluminum alloy) proposed by Wert et al. [14] was employed with some modifications in this study.


The as-received plate was first solution treated at 530°C for 3 hrs followed by a rapid quenching in cold water. The plate was then overaged at 400°C for 12 hrs. The specimen with a larger grain size of μm was obtained by recrystallizing at 530°C for 3 hrs in a salt bath after warm rolling at 300°C. After an additional overaging and cold rolling process, finer grain sizes of μm and μm were obtained by recrystallizing at 530°C and 580°C for 1 hr, respectively. All specimens after the recrystallization process were directly quenched into cold water. The optical micrographs of thermomechanically treated specimens are given in Figure 3.

Load relaxation tests were then carried out at various temperatures between 200°C and 530°C by using a computer-controlled electromechanical testing machine attached with a high temperature furnace capable of maintaining the temperature fluctuation within ±0.5°C. The specimens for the load relaxation test have a square cross-section (2 mm × 2 mm) with 15 mm gauge length. In the load relaxation test employed in this study, a specimen was loaded first in tension to a certain predetermined extension value followed by stopping cross-head motion. The load was then recorded as a function of time at the fixed cross-head position. The variation of the load () was monitored through a digital voltmeter (HP 3456A DVM) and stored in a personal computer for further processing. The flow stress and inelastic strain rate were then calculated from the load-time data following the usual procedure described in the literature [15].

Tensile tests were also performed at the temperature range mentioned previously under the various initial strain rates ranging from 10−2/s to 5 × 10−4/s. The tensile test specimens were plate type with dimensions of 2 mm in thickness and 5 mm in gauge length. All specimens were pulled to fracture at a constant cross-head speed.

4. Experimental Results

4.1. Load Relaxation Tests

The relaxation test results obtained at various temperatures are shown in Figure 4 for the specimens with the average grain size of 50 μm. The flow curves shifted noticeably toward the lower stress and the higher strain rate region as the temperature increases from 200°C to 530°C. The values of constitutive parameters were determined by fitting the experimental data to (4), and the results are presented in Table 2. The solid lines in Figure 4 are the predicted curves representing the flow behavior of element described by (4) constructed with the constitutive parameters listed in Table 2. They show a good agreement with experimental data. It is clear from the figure that the specimens with such a large grain size reveal only the plastic deformation behavior of element regardless of test temperatures.

Temp. (°C)log log


A very similar result was obtained for the specimens with the average grain size of 18 μm except at 530°C as shown in Figure 5. The flow curve at 530°C shows a concave portion within the strain rate range of roughly 10−5/s ≤ ≤ 10−3/s, indicating the existence of some contributions from GBS. The solid lines in Figure 5 again represent the predicted curves from (4) constructed with the values of constitutive parameters listed in Table 3, and they are also in good accord with the experimental data.

Temp. (°C)log log


The flow curves of specimens with the average grain size of 10 μm are given in Figure 6, and the determined constitutive parameters are presented in Table 4. For the purpose of obtaining an activation energy for plastic deformation, a relatively narrow range of temperature has been chosen for specimens of   μm. Again, only the plastic flow behavior of element could be observed at the lower temperatures of 470°C and 490°C. The flow curve obtained at 530°C, on the other hand, showed more noticeable concave portion within a strain rate range much broader than the flow curve of 18 μm specimen, which will be examined in detail later in relation to GBS. The effect of raising temperature is manifested by the lower values of internal strength parameter as one can readily see in the tables.

Temp. (°C)log log


It is also interesting to note that the value of parameter characterizing dislocation permeability of strong barriers, that is, grain boundaries [9], was obtained as 0.15 regardless of testing temperatures or grain sizes, confirming the results reported previously [5, 13]. The value of this parameter is believed to strongly depend on the boundary properties, including its geometry and the properties of dislocations. From this point of view, it is necessary to examine the effect of variation in crystal structure on the value of this parameter, and interesting results have been obtained in Sn and Sn-containing alloys [5, 10]. The value of in these alloys is 0.1, much lower that that of materials with the close packed crystal structure. In the case of load relaxation test employed in this study, total strain applied to a specimen is about , very small in every case. Therefore, the parameter depends strongly on the boundary characteristics. A more systematic research in this regard is needed including microstructure observation.

4.2. Tensile Tests

The selected results of tensile tests conducted on the specimens having various grain sizes by varying the initial strain rate at the temperature of 530°C are given in Figure 7. The largest elongation of about 800% was obtained in the specimen having m under the initial strain rate of  /s. As usually reported by other researchers, when the grain size was decreased and the initial strain rate lowered, the elongation clearly increased.

5. Discussion

One of the most important features of the internal variable approach employed in this study is that each deformation mechanism of high temperature deformation, that is, GMD and GBS, can be considered individually. It is, therefore, possible within this framework to quantitatively examine the respective contributions from GMD and GBS especially in SSP.

5.1. Grain Boundary Sliding

As mentioned earlier, the concave portion appears in the flow curves obtained at 530°C for the grain sizes of 10 μm and 18 μm. By taking the difference between obtained directly from the relaxation test and estimated from (4) as the strain rate due to GBS, , according to (3), the flow curves for GBS could be constructed as shown in Figure 8. The constitutive parameters required in (8) were then determined again by a nonlinear curve fitting method, and the results are given in Table 5. The bold solid lines in Figure 8 represent the composite curves predicted by (3), (4), and (8) assuming , and they show a good agreement with the experimental data. The most significant result obtained by this analysis is that the GBS can, in fact, be described as a Newtonian viscous flow characterized by the power index value of , which can be confirmed experimentally by the work of Raj and Ashby [16]. As pointed out in an earlier work [5], they directly measured the sliding by loading helical springs wound of silver wire with a bamboo structure and found that the boundaries slide in a Newtonian viscous manner at high temperatures within a certain stress range. Above this range of stress, sliding appeared to be accompanied (~0.7) by plastic flow in the grains, leading to non-Newtonian behavior. Their result is very consistent with the analysis result of the present study, although the materials used in each study are very different. Experimental data themselves in Figure 6 do not show a Newtonian viscous behavior at all. The situation where the flow curves were obtained is thought to be very similar to the latter case of the study of Raj and Ashby [16], and it is clear that the intragranular slip plays an important role in SSP.

( m)log log


Under the optimal condition of SSP, the contribution of GBS to the total deformation has been reported to be 0.60.8 [4]. In the situation where GBS is fully accommodated, has been proved to be over 0.9 [17]. It is, therefore, unlikely that diffusion creep can make a significant contribution more than 40% of total superplastic elongation [18]. While several measurements [19] indicated very limited dislocation activity in region II, recent direct measurements of the intragranular strain in a superplastic Pb-Sn eutectic alloy have shown that the strain is oscillatory in nature, with both positive and negative components, and it makes no net contribution to the total elongation of the specimen [20]. This result is consistent with our discovery that the grains remain nearly equiaxed after superplastic deformation. Most of the determinations of in superplasticity experiments have relied upon the method proposed by Bell and Langdon [21]. We estimated value indirectly from Figure 6 to be about 0.6 at the stress level of  MPa, which is within the range obtained by other experimental results mentioned previously.

In this study, the strain rate ranges, within which the effect of GBS is predominant, are 10−5/s 10−3/s and 5 × 10−5/s ≤ ≤ 5 × 10−3/s for flow curves of specimens with and 10 μm, respectively. Perevezentsev et al. [22, 23] estimated that the upper and lower limits of strain rates, within which GBS can operate, would be an important deformation mechanism based on the concept of an “excited state” of boundary. The lower bound was calculated to be 10−6/s~10−4/s and the upper bound to be about 5 × 10−2/s with the typical values of SSP parameters, especially the grain size of 1~10 μm. The strain rate ranges for superplastic deformation due to GBS obtained in this study are also within these upper and lower bounds. We obtained the largest elongation of about 800% at the initial strain rate of = 5 × 10−4/s and at temperature of 530°C for the specimen with the average grain size of μm as in Figure 7, and this initial strain rate is clearly within the strain rate range mentioned previously in connection with the effect of GBS.

5.2. Temperature Effect

The experimental results given in Figures 4 to 6 reveal the effect of temperature on the flow behavior of 8090 Al-Li alloy. As previously mentioned, the effect of raising temperature is seen to make the flow curves shift noticeably toward the lower stress and the higher strain rate region. Figures 4 to 6 show that GBS is greatly affected by the test temperature. The contribution from GBS can be expected only at 530°C for the specimens of relatively small grain sizes, and this is verified by the tensile test result shown in Figure 7.

The value of the internal strength parameter decreases with the increase of temperature as in Tables 2 to 4. We believe that this is caused by a thermal softening effect which influences the mechanical properties of metals. The value of in (4) represents the hardness state, as it was first used by Ha et al. [10], characterizing a typical microstructure of tested materials during the relaxation test. As shown in Table 4, in the temperature range within which the variation of is negligible, the effect of increase in temperature is to increase the value of reference strain rate , and so the flow curve shifts in the higher strain rate region. This effect combined with the thermal softening makes the flow curves shift toward the higher strain rate and the lower stress region.

From Figure 6 and Table 4, it is possible to determine the activation energies for the high temperature deformation mechanisms employed in this study. However, only the activation energy for GMD element was obtainable due to the restrictions of experimental conditions and the difficulty in data analysis. The activation energy can be determined from the following relation obtained by differentiating (5):

Since the values of obtained for the specimens with the grain size of 10 μm do not change appreciably in the temperature range from 470°C to 530°C as seen in Table 4, the relation between ln and is plotted in Figure 9 to determine the value of . The activation energy obtained was = 124.9 kJ/mole, which is very close to that for self-diffusion in Al (about 134 kJ/mole) [24]. Very similar results have been reported by Pu et al. [25] and Kwon et al. [26]. This value was also found to be very similar to the activation energy of Al-3Li-1.5Cu-1Mg-0.1Zr alloy (about 140 kJ/mole) [27] in the as-extruded condition prior to the thermomechanical treatment for superplasticity. Under this condition, GBS cannot operate as an active deformation process for Al-3Li-1.5Cu-1Mg-0.1Zr alloy, and the activation energy of about 140 kJ/mole is thought to be responsible for the plastic deformation by dislocation activities.

5.3. Grain Size Effect

To see the effect of grain size on the flow behavior of 8090 Al-Li alloy, the flow curves obtained at 530°C were replotted as in Figure 10. As the grain size decreases, the flow curves appear to shift toward the direction of the lower and higher at 530°C. Figure 10 clearly shows the effect of GBS on the flow behavior of materials. As seen in the tables, the value of internal strength parameter increases with the decrease of grain size regardless of temperatures. In the cases where GBS can operate as a major deformation process, however, the flow stress of the specimen with smaller grain size appears to be much lower than that of specimen with larger grain size.

The values of at 530°C listed in Tables 2 and 4 were next plotted against the grain size as shown in Figure 11. Although the number of available grain sizes is not sufficient to determine the exact relation, a rough estimation for the slope of versus provides the value of −0.52, suggesting a modified Hall-Petch type relation between  and : where is a constant. It seems rather reasonable to replace the flow stress () in the classical Hall-Petch type relation with an internal structural variable since the grain size () is also a structural variable representing the microstructure. The temperature 530°C was chosen to exclude other dynamic effects, such as the precipitation of phase, during the tests. Very similar result has been obtained for 7475 Al alloy [28].

5.4. Condition for SSP

Judging from the test results discussed previously, the   versus   curve at high temperatures can, in fact, be considered to be a composite curve consisting of GBS () and GMD () and accommodating the incompatibility caused by GBS. It can also be suggested that the superplastic deformation due to the GBS can only be observed under the following condition:

To achieve this necessary condition for superplastic deformation caused by GBS, the temperature must be raised to reduce the static friction stress for GBS () together with the increase in , which can be achieved through grain refinement according to the modified Hall-Petch relation given by (11).

6. Conclusions

By conducting a series of load relaxation and tensile tests on 8090 Al-Li alloy at high temperatures and by analyzing the results within the framework of the internal deformation variable theory, the following important results were obtained.(1)The plastic flow curves of versus can precisely be described by (4) for 8090 Al-Li alloy at temperatures ranging from 200°C to 530°C.(2)Our interpretation of the flow curves of superplastic 8090 Al-Li alloy led us to conclude that they consist of contributions from the GBS () and the accommodating grain matrix plastic deformation () at high temperatures.(3)The GBS appears to be a Newtonian viscous flow process characterized by the power index value of regardless of grain sizes.(4)We proposed that a modified Hall-Petch type relation is occurring between the grain size and the internal strength variable () replacing the flow stress ().(5)The necessary condition for structural superplasticity was found to be .


This work was partly supported by the National Hazard Mitigation Research Group of Korea (NHMRG), Grant funded by the National Emergency Management Agency (NEMA) (no. NEMA-NH-2011-49), and partly by the Ministry of Education, Science, and Technology (MEST), Gangwon province, Gangneung city, Gangneung Science Industry Foundation (GSIF) as the R&D Project for Gangneung Science Park program. Woo Young Jung is grateful for the financial support by the National Research Foundation of Korea (NRF) Grant funded by the Korean Government (MEST) (no. 2011-0028531).


  1. K. Sotoudeh and P. S. Bate, “Diffusion creep and superplasticity in aluminium alloys,” Acta Materialia, vol. 58, no. 6, pp. 1909–1920, 2010. View at: Publisher Site | Google Scholar
  2. T. G. Nieh and J. Wadsworth, “Fine structure superplastic intermetallics,” International Materials Reviews, vol. 44, no. 2, pp. 59–75, 1999. View at: Google Scholar
  3. K. A. Padmanabhan and G. J. Davis, Superplasticity, Springer, Berlin, Germany, 1980.
  4. O. D. Sherby and J. Wadsworth, “Superplasticity—recent advances and future directions,” Progress in Materials Science, vol. 33, no. 3, pp. 169–221, 1989. View at: Google Scholar
  5. T. K. Ha and Y. W. Chang, “An internal variable theory of structural superplasticity,” Acta Materialia, vol. 46, no. 8, pp. 2741–2749, 1998. View at: Google Scholar
  6. M. F. Ashby and R. A. Verrall, “Diffusion-accommodated flow and superplasticity,” Acta Metallurgica, vol. 21, no. 2, pp. 149–163, 1973. View at: Google Scholar
  7. E. W. Hart, Stress Relaxation Testing, vol. 676 of ASTM Special Technical, ASTM International, Baltimore, Md, USA, 1979, A. Fox. Ed.
  8. E. W. Hart and H. D. Solomon, “Load relaxation studies of polycrystalline high purity aluminium,” Acta Metallurgica, vol. 21, no. 3, pp. 295–307, 1973. View at: Google Scholar
  9. Y. W. Chang and E. C. Aifantis, Proceedings of the 2nd International Conference on Constitutive Laws for Engineering Materials: Theory and Application, Eds. C. S. Desai et al., Tucson, Ariz, USA, Jan. 5–8, 1987, Elsevier, New York, NY, USA, 1987.
  10. T. K. Ha, C. S. Lee, and Y. W. Chang, “Plastic equation of state and load relaxation behavior of pure tin,” Scripta Materialia, vol. 35, no. 5, pp. 635–640, 1996. View at: Publisher Site | Google Scholar
  11. H. C. Choi, T. K. Ha, H. C. Shin, and Y. W. Chang, “Formation kinetics of deformation twin and deformation induced ε-martensite in an austenitic Fe-C-Mn steel,” Scripta Materialia, vol. 40, no. 10, pp. 1171–1177, 1999. View at: Publisher Site | Google Scholar
  12. L. E. Malvern, Introduction to Mechanics of a Continuous Media, Cambridge University Press, New York, NY, USA, 1975.
  13. E. W. Hart, “A phenomenological theory for plastic deformation of polycrystalline metals,” Acta Metallurgica, vol. 18, no. 6, pp. 599–610, 1970. View at: Google Scholar
  14. J. A. Wert, N. E. Paton, C. H. Hamilton, and M. W. Mahoney, “Grain refinement in 7075 aluminum by thermomechanical processing,” Metallurgical Transactions A, vol. 12, no. 7, pp. 1267–1276, 1981. View at: Google Scholar
  15. D. A. Woodford, “Measurement of the mechanical state of a low alloy steel at elevated temperature,” Metallurgical Transactions A, vol. 6, no. 9, pp. 1693–1697, 1975. View at: Publisher Site | Google Scholar
  16. R. Raj and M. F. Ashby, “On grain boundary sliding and diffusional creep,” Metallurgical Transactions A, vol. 2, no. 4, pp. 1113–1127, 1971. View at: Publisher Site | Google Scholar
  17. T. G. Langdon, “An evaluation of the strain contributed by grain boundary sliding in superplasticity,” Materials Science and Engineering A, vol. 174, no. 2, pp. 225–230, 1994. View at: Google Scholar
  18. T. G. Langdon, “A unified approach to grain boundary sliding in creep and superplasticity,” Acta Metallurgica et Materialia, vol. 42, no. 7, pp. 2437–2443, 1994. View at: Google Scholar
  19. L. K. L. Falk, P. R. Howell, G. L. Dunlop, and T. G. Langdon, “The role of matrix dislocations in the superplastic deformation of a copper alloy,” Acta Metallurgica, vol. 34, no. 7, pp. 1203–1214, 1986. View at: Google Scholar
  20. R. Z. Valiev and T. G. Langdon, “An investigation of the role of intragranular dislocation strain in the superplastic Pb-62% Sn eutectic alloy,” Acta Metallurgica et Materialia, vol. 41, no. 3, pp. 949–954, 1993. View at: Google Scholar
  21. R. L. Bell and T. G. Langdon, “An investigation of grain-boundary sliding during creep,” Journal of Materials Science, vol. 2, no. 4, pp. 313–323, 1967. View at: Publisher Site | Google Scholar
  22. V. N. Perevezentsev, V. V. Rybin, and V. N. Chuvil'deev, “The theory of structural superplasticity—I. The physical nature of the superplasticity phenomenon,” Acta Metallurgica et Materialia, vol. 40, no. 5, pp. 887–894, 1992. View at: Google Scholar
  23. V. N. Perevezentsev, V. V. Rybin, and V. N. Chuvil'deev, “The theory of structural superplasticity—II. Accumulation of defects on the intergranular and interphase boundaries. Accomodation of the grain-boundary sliding. The upper bound of the superplastic strain rate,” Acta Metallurgica et Materialia, vol. 40, no. 5, pp. 895–905, 1992. View at: Google Scholar
  24. O. D. Sherby and P. M. Burke, “Mechanical behavior of crystalline solids at elevated temperature,” Progress in Materials Science, vol. 13, pp. 323–390, 1968. View at: Google Scholar
  25. H. P. Pu, F. C. Liu, and J. C. Huang, “Characterization and analysis of low-temperature superplasticity in 8090 Al-Li alloys,” Metallurgical and Materials Transactions A, vol. 26, no. 5, pp. 1153–1166, 1995. View at: Publisher Site | Google Scholar
  26. Y. N. Kwon, H. J. Koh, S. Lee, N. J. Kim, and Y. W. Chang, “Effects of microstructural evolution on superplastic deformation characteristics of a rapidly solidified Al-Li alloy,” Metallurgical and Materials Transactions A, vol. 32, no. 7, pp. 1649–1658, 2001. View at: Google Scholar
  27. J. Wadsworth, A. R. Pelton, and R. E. Lewis, “Superplastic Al-Cu-Li-Mg-Zr alloys,” Metallurgical Transactions A, vol. 16, no. 12, pp. 2319–2332, 1985. View at: Publisher Site | Google Scholar
  28. T. K. Ha, H. J. Sung, K. S. Kim, and Y. W. Chang, “An internal variable approach to the grain size effect on the superplastic deformation behavior of a 7475 Al alloy,” Materials Science and Engineering A, vol. 271, no. 1-2, pp. 160–166, 1999. View at: Publisher Site | Google Scholar

Copyright © 2013 Woo Young Jung and Tae Kwon Ha. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

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