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УДК 539.3
Определение упругих свойств состаренного медицинского сплава Ti-6Al-4V ELI методом измерения скорости ультразвуковых волн
H. Carreon1, M. Carreon-Garciduenas2, M.L. Carreon3, V. Almanza2
1 Металлургический исследовательский институт, Морелия, 58000-888, Мексика 2 Факультет стоматологии при Металлургическом исследовательском институте, Морелия, 58330, Мексика 3 Университет Талсы, Оклахома, 74104-9700, США
В работе получены экспериментальные значения модуля Юнга и модуля сдвига, определенных по изменению скорости ультразвуковых волн в процессе эволюции микроструктуры в сплавах Ti-6Al-4V с бимодальной и видманштеттоновой микроструктурой. Микроструктуру двух типов подвергали термической обработке старением при температуре 515, 545 и 575 °С в интервале от 1 мин до 576 ч с целью инициировать выделение фаз. Для установления прямой зависимости с данными измерений скорости ультразвуковых волн и упругих свойств после термической обработки искусственным старением проведены ультразвуковые измерения скоростей поперечных и продольных волн, анализ РЭМ-изображений, оптико-микроскопическое исследование и измерения микротвердости. Результаты показывают характерное изменение скорости ультразвуковых волн в ходе старения в зависимости от процесса выпадения частиц Ti3Al внутри а-фазы. Предлагаемый метод позволяет быстро и эффективно определять упругие свойства состаренного материала, поскольку выпадение частиц приводит к повышению твердости микроструктуры материала и тем самым влияет на его конечные механические свойства.
Ключевые слова: микроструктура, упругие свойства, микроскопия, ультразвук, сплав Ti-6Al-4V ELI (со сверхнизким содержанием примесей внедрения)
DOI 10.24411/1683-805X-2019-11002
Determination of the elastic properties at aging of medical Ti-6Al-4V ELI alloy by ultrasonic velocity measurements
H. Carreon1, M. Carreon-Garciduenas2, M.L. Carreon3, and V. Almanza2
1 Instituto de Investigaciones Metalurgicas (UMSNH), Ciudad Universitaria, Morelia, 58000-888, Mexico 2 Facultad de Odontologia, Estudios de Posgrado e Investigacion (UMSNH-CUEPI), Morelia, 58330, Mexico 3 Russell School of Chemical Engineering, University of Tulsa, Oklahoma, 74104-9700, USA
In this paper, we report the experimental data of the elastic properties of the Young's modulus and shear modulus based on the variation in the ultrasonic velocity parameter during the microstructural evolution in a Ti-6Al-4V alloy with two—bimodal and Widmanstatten—varying microstructures. The two different initial microstructures were treated thermally by aging at 515, 545, and 575°C at different times from 1 min to 576 h to induce a precipitation process. Ultrasonic measurements of shear and longitudinal wave velocities, scanning electron microscopy image processing, optical microscopy, and microhardness measurements were performed, establishing a direct correlation with the measurements of the ultrasonic velocity and the elastic properties developed during the thermal treatment by artificial aging. The results of the ultrasonic velocity show a very clear trend as the aging time progresses, which is affected by precipitation of Ti3Al particles inside the а phase. In this way, we can find, in a fast and efficient way, the elastic properties developed during the heat treatment by long-term aging, since the presence of these precipitates hardens the material microstructure, thus affecting the final mechanical properties.
Keywords: microstructure, elastic properties, microscopy, ultrasound, Ti-6Al-4V ELI (extra low interstitial) alloy
1. Introduction
The use of Ti-6Al-4V alloy in the aerospace and biomaterials industry [1-3] has been led by the demand for
further development of characterization techniques to figure the microstructure-property relations in this metallic
alloy. It is also of main concern to examine phase transformations that occur during processing in order to design microstructures that possess excellent properties specific to these applications. On the biomedical field, metal implants must have a mechanical compatibility with the sub-
© Carreon H., Carreon-Garciduenas M., Carreon M.L., Almanza V., 2019
stituted bone, which is achieved through the combination of low Young's modulus, high flexural and fatigue strengths. In the case of the medical Ti-6Al-4V ELI alloy, when this titanium alloy is overaged at 500-600°C, precipitation of nanometer-sized phases such as a2(Ti3Al) can be observed in the titanium alloy matrix, increasing the mechanical properties of the metallic material [4-7].
On the other hand, the behavior of ultrasonic wave propagation in metals provides information on the microstructure, mechanical and physical properties of the material under investigation. The measurements of the two main ultrasonic parameters such as attenuation and velocity can be used to estimate the material microstructural changes and properties [8]. The ultrasonic wave velocity is related to the elastic constants and density of the medium while the ultrasonic wave attenuation stands on microstructure and crystalline defects [9-11]. In the present research study, we applied the contact ultrasonic pulse-echo technique using buffer media to calculate the ultrasonic propagation velocity in the artificially aged Ti-6Al-4V ELI alloy. Combined with the theory of diffraction correction of the ultrasonic velocity in solid media, the influence of the two microstructures (bimodal and acicular) on the ultrasonic propagation velocity in different aging conditions was discussed. In addition, hardness measurements and microstructural examinations using optical and scanning electron microscopy were carried out by relating elastic properties such as Young's modulus and shear modulus to the observed microstructure.
2. Experimental Method
2.1. Material
The material used in this study was a medical Ti-6Al-4V ELI alloy in the form of a plate 6.76 mm thick, and its exact chemical composition is 6.10Al-3.93V-0.17Fe-0.12O-0.009C-0.005N-0.002H-Ti (wt %). This alloy plate was subjected to different heat treatments to obtainWidmanstâtten and bimodal microstructures. The Widmanstâtten microstructure was obtained by holding the material at 1020°C for 20 min (above the P transformation temperature), then it was cooled down to 850°C and held for 2 h, followed by water quenching. The bimodal microstructure was obtained by holding at 950°C (a + P region) for 1 h, followed by water cooling/quenching. These two microstructures were overaged at 515, 545, and 575°C for different aging times ranging from 1 min to 576 h to promote the formation of very fine a2(Ti3Al) precipitates.
2.2. Microscopic techniques
For optical and scanning electron microscopy inspection, heat-treated specimens were mounted in bakelite, ground, and polished down to a 1 ^m diamond cloth. Microstructural features were unveiled using Kroll's reagent (H2O 100 ml, HF 100 ml, HNO3 100 ml). The main micro-
structural features for the medical Ti-6Al-4V ELI alloy were calculated using an image analyzer. To evaluate micro-hardness variations amongst the specimens, Vickers hardness measurements were carried out by applying a load of 500 g for 30 s to the unaged and aged specimens. Prior to a microhardness test, the specimens were cross-sectioned and metallographically prepared in a similar fashion as for the optical microscopy observation but using a much finer finishing approach with a colloidal silica solution (0.05 ^m).
2.3. Ultrasonic technique
Ultrasonic compressional and transverse velocities were calculated by measuring the travel time for the ultrasonic waves through the titanium specimens. Figure 1 illustrates a schematic diagram of the ultrasonic measurements. A broadband longitudinal transducer (Aerotech) with a central frequency of 10 MHz and element diameter of 6 mm was used to generate compressional ultrasonic waves. A broadband shear transducer (Aerotech) with a central frequency of 5 MHz and element diameter of 12 mm was operated to induce transverse ultrasonic waves. In order to evade the nonuniform amplitude near the transducer field, a buffer rod (fused silica) was used to add a time delay between the excitation pulse and echoes returning from the measured specimen. The ultrasonic transducer was placed on the specimen and excited by a Panametrics 5072PR broadband pulser. The ultrasonic signal was digitized and averaged by a LeCroyWavesurfer 432 oscilloscope and then sent to the computer for data processing.
In experimental measurements, the beam diffraction usually generated considerable additions to the ultrasonic velocity parameter as measured by the pulse-echo technique [12-14]. In order to prevent the effect of diffraction on the echo waveforms, it was necessary to realize corrections to the two echo waveforms. First, a normalized distance S is calculated for each echo zk
S =-
(1)
where z is the propagation distance, a is the transducer radius, and X is the wavelength. The phase shift leads to a
Couplant Sample
Transducer Buffer
Fig. 1. Experimental drawing for the ultrasonic velocity measurements using the diffraction correction method
Fig. 2. Optical micrographs of the Widmanstatten (a) and bimodal (b) microstructures etched with Kroll's reagent. In these micrographs, a is the white/bright phase and P is the black/dark phase
travel time diffraction correction as
t = t + At, (2)
where t is the measured travel time between the echoes n and m (first and second), t is the corrected travel time, and At is the travel time correction. The expression for the travel time correction is given by
<(S„) -<(sm )
At = -
2f
(3)
where the phase < is calculated at the normalized distance S for the echoes n and m at the operating frequency.
Finally, the ultrasonic compressional and transverse velocities are related to the elastic and shear moduli by the following equations [15]:
E =
C2p(1 + a)(1 - 2 a) 1 -a
(4)
and
G = Cs2p, (5)
where E is the Young's modulus (GPa), G is the shear modu-
lus (GPa), a is the Poisson ratio, Cc is the compressional velocity (m/s), Cs is the transverse velocity (m/s), and p is the density of the specimen (g/cm3).
3. Results and discussion
Figure 2 shows optical micrographs of the Widmanstatten and bimodal microstructures. In the Widmanstatten microstructure, a-phase grains (white/bright) develop along prior P grain boundaries (black/dark) and colonies of the lath-type P and a lamellar structure are observed inside prior P grains (Fig. 2, a). The colony size, thickness of a/P platelets, volume fraction of the a phase, volume fraction of the P phase were measured to be 973 ^m, 5 ^m, 56%, and 44%, respectively. The bimodal microstructure consists of equiaxed a grains (white/bright) and tempered martensite with a small amount of residual P phase (black/ dark). The a-grain size was measured to be 10 ^m, and volume fractions of the a and P phases were measured to be 52 and 48%, respectively, as shown in Fig. 2, b.
Table
Quantitative analysis results of the microstructures of Ti-6Al-4V
Microstructure Parameter Unaged Aged 2 h Aged 144 h Aged 576 h
Temperature, °C
515 545 575 515 545 575 515 545 575
Widmanstatten Colony size, ^m 973 611 726 1061 790 899 843 1074 692 771
a GB thickness, ^m 4 7.5 10 6 7 9 8 10 7 9
Amount of the a-phase, % 56 62 60 60 64 64 63 64 65 65
Amount of the P-phase, % 44 38 40 40 36 36 37 36 35 35
a/P platelet, |im 5 6 8 5 8 8 7 10 9.5 9.5
Bimodal a-grain size, ^m 10 11 11 12 11 11 13 13 12 13
Amount of the a-phase, % 52 54 54 54 56 56 56 57 57 58
Amount of the P-phase, % 48 46 46 46 44 44 44 43 43 42
GB stands for grain boundary.
Fig. 3. Scanning electron microscopy micrographs of the overaged acicular microstructure at the 1000x (a-c) and 30000x (d-f) magnification for 575°C at the three different aging times 2, 144, and 576 h, respectively, showing very fine a2 phases homogeneously distributed in the a phase. Etched with Kroll's reagent
Table summarizes the main microstructural features in the unaged and aged conditions for the two microstructures of the Ti-6Al-4V ELI alloy after holding for 2, 144 and 576 h at the three different aging temperatures. It is observed from the analysis data that the aging treatment changes the percent of the a and P phases present initially in the unaged condition for both the Ti-6Al-4V ELI alloy microstructures (Widmanstatten and bimodal). A slight increase in the percent of the a phase is noticed.
An understanding of the two Ti-6Al-4V ELI microstructures is essential to interpret the results on ultrasonic velocities as well as the elastic and shear modulus data. There are some differences in the high-magnification scanning electron microscopy micrographs of the aged acicular and bimodal microstructures as shown in Figs. 3 and 4. Fine a2-phases 50-200 nm in size are homogeneously dis-
tributed in a phases (black/dark) in the acicular microstructure (see Figs. 3, d-3,f). In the Widmanstatten microstructure, the platelet size increases significantly with aging, and thus a higher number density of nucleation sites available for a2 precipitates is formed (Figs. 3, a-3, c). On the other hand, Fig. 4 also shows that the amount of precipitates increases with respect to the aging time for the bimodal microstructure (see Figs. 4, d-4,f). Figures 4, a and 4, d correspond to the aging time 2 h, in which the presence of a2 precipitates was observed in grain boundaries of the a phase (black/dark). At 144 h (Figs. 4, b and 4, e), the precipitates are more homogeneous within and at the a-phase boundary. The size and morphology of the intermetallic a2 precipitates remain constant. For the aging time 576 h (Figs. 4, c and 4, f), these a2 precipitates are found in a greater number, being located mainly in large groups (clusters) within
Fig. 4. Scanning electron microscopy bright-field images of the overaged bimodal microstructure at the 1000x (a-c) and 30000x (d-f magnification for 575°C by the three different aging times 2, 144, and 576 h, respectively, showing very fine a2 phases homogeneously distributed in the a phase. Etched with Kroll's reagent
the a matrix, as shown in Fig. 4, f. The precipitation of these a2(Ti3Al) nanoparticles induces hardening of the Ti-6Al-4V matrix [16].
The alloy element separation effect has the aftermath that a lamellae produced from the P-phase upon cooling have a lower concentration of elements (oxygen), which induces age-hardening by the formation of coherent a2 particles. In this stage, the temperature parameter is more relevant than the time parameter since the temperature being either below or above the a2 solvus temperature figures whether age-hardening by a2 particles takes place in the a phase or not. In the medical Ti-6Al-4V ELI alloy, the a2 solvus temperature is ~600°C, which indicates that aging at 500°C will precipitate a2 particles while the heat treatment at 600°C or above will be only a stress relieving treatment. In this research work, the three overaging tempera-
tures (515, 545, and 575°C) will induce age-hardening by Ti3Al particles.
Figure 5 presents the Vickers microhardness modification in the two initial medical Ti-6Al-4V ELI microstructures—Widmanstatten and bimodal—as a function of different aging times at 515, 545, and 575°C. The micro-hardness of the bimodal microstructure is greater than that of the Widmanstatten microstructure. This is probably due to the presence of a huge volume fraction of the tempered martensite in the bimodal microstructure. The microhard-ness results for the medical Ti-6Al-4V ELI alloys (Fig. 5) show an important tendency to increase with aging times for both the microstructures. This phenomenon is attributed to the precipitation of a2(Ti3Al) particles inside the a phase. This is due to a greater volume fraction of the a phase after aging in the microstructures and thus a higher number
460
>
420
3380 •o
340
300
Bimodal microstructure
515°C ;545°C 575°C
Widmanstatten microstructure 515°C
■ ■ t575°C
0
200 400 Aging time, h
600
Fig. 5. Microhardness measurements in the acicular and bimodal microstructures with different aging parameters in a medical Ti-AI-4V ELI alloy (color online)
density of nucleation sites available for a2 precipitates. The precipitation of these nanoparticles occurs mainly at the boundary and within the a2-phase, resulting in a micro-hardness increment. After 300 h, the hardness data tend to remain constant with increasing the aging time due to the thickening of a/P platelets (Widmanstatten) and a grains (bimodal) because of precipitates of smaller sizes.
Figure 6 shows the variations in the Young's and shear moduli in the Widmanstatten and bimodal microstructures with different aging parameters at the medical Ti-Al-4V ELI alloy. The Young's and shear moduli were calculated from Eqs. (4) and (5), respectively, by using the diffraction correction of the ultrasonic compressional and transverse velocities, p = 4.43 g/cm3 and a = 0.35. The Young's modulus of the bimodal microstructure is larger than that of the Widmanstatten microstructure, as shown in Fig. 6, a. The shear modulus of the bimodal microstructure is also larger than that of the Widmanstatten microstructure, as shown in Fig. 6, b. In general, the ultrasonic velocities were found to be lower in the coarse grain medium [10]. In the Widmanstatten microstructure, a/P platelets have different orientations, forming colonies (see Fig. 2, a). Strongly preferential orientations of these coarse colonies increase the morphological anisotropy while equiaxed a grains (bimodal microstructure) decrease it. Due to the inverse relation between ultrasonic velocity and density, an increase in the ultrasonic velocity must be related to an increase in the Young's modulus and shear modulus [17-19].
From these results, it is evident that the ultrasonic velocity is very sensitive to the stages of the precipitation process in both the Ti-6Al-4V ELI microstructures in different aging conditions. This is attributed to the fact that the ultrasonic velocities depend on the elastic properties of the material, which are very sensitive to any phase transformation and degree of morphological anisotropy. The first stage of precipitation (i.e. incubation) influences the Young's and shear moduli of the material and in turn the compressional and transverse ultrasonic velocities. The depletion of precipitate-forming elements from the matrix to the a phase induced by aging leads to an increase in the
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Bimodal microstructure * *
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515 545 575
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545
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575°C
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200 400 Aging time, h
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600
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515°C 545°C 575°C
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600
Fig. 6. Influence of artificial aging in a medical Ti-Al-4V ELI alloy on the Young's (a) and shear (b) modulus with different microstructures (color online)
Young's modulus and shear modulus of the two varying medical Ti-6Al-4V ELI alloy microstructures, i.e. bimodal and Widmanstätten, respectively.
4. Conclusions
The precipitation behavior in the two varying medical Ti-6Al-4V ELI alloy microstructures (Widmanstatten and bimodal) has been studied using the microscopic and ultrasonic techniques. The study clearly reveals that the change of the ultrasonic compressional and transverse velocities arises mainly from the contrast in the elastic properties of the a and P phases which are affected by the degree of lattice distortion and misorientation. The ultrasonic com-pressional and transverse velocities are more sensitive to the early stage of precipitation whereas the effect of precipitation on hardness can be perceived only after the precipitates earn a minimum size to influence the movement of dislocations. These observations are consistent with the electron microscopy studies. The ultrasonic diffraction correction velocity method can be used to calculate the Young's and shear moduli in a medical Ti-6Al-4V ELI alloy. The ultrasonic velocity parameter is very sensitive to microstructural changes; it can be used reliably for the monitoring of precipitates in aging processes of metallic alloys. Finally, the proposed nondestructive ultrasonic technique demonstrates an important assessment in the biomedical field and its applications. Moreover, it could be extrapolated to the phase transformation in more complex metallic
and nonmetallic alloys. However, the identification of small microstructural changes with the strong effect on the mechanical properties requires new inspection methods, which should consider additional physical variables.
Funding
This work was performed at the Universidad Michoaca-na de San Nicolas de Hidalgo (UMSNH, Mexico) and partially funded by the Consejo Nacional de Ciencia y Tecnologia (CONACYT, Mexico) under Projects CB-2015/ 256013 and Prodep/CA-140.
References
1. Li Y., Yang C., Zhao H., Qu S., Li X., Li Y New developments of Ti-based alloys for biomedical applications // Materials. - 2014. - V. 7. -P. 1709-1800.
2. Sidambe A.T. Biocompatibility of advanced manufactured titanium implants—A review // Materials. - 2014. - V. 7. - P. 8168-8188.
3. Carreon H. Thermoelectric detection of fretting damage in aerospace materials // Russ. J. Nondestruct. Test. - 2014. - V. 50. - P. 684-692.
4. Attanasio A., Gelfi M, Pola A., Ceretti E., Giardini C. Influence of material microstructures in micro-milling of Ti6Al4V alloy // Materials. - 2013. - V 6. - P. 4268-4283.
5. Carreon H., San Martin D., Caballero F.G., Panin V.E. The effect of thermal aging on the strength and the thermoelectric power of the Ti-6Al-4V alloy // Phys. Mesomech. - 2017. - V 20. - No. 4. - P. 447456.
6. Lutjering G. Influence of processing on microstructure and mechanical properties of (a + P) titanium alloys // Mater. Sci. Eng. A. - 1998. -V. 243. - P. 32-45.
7. Lee D.G., Lee Y.H., Lee C.S., Lee S. Effects of volume fraction of tempered martensite on dynamic deformation properties of a Ti-6Al-4V alloy having a bimodal microstructure // Metall. Mater. Trans. A. -2005. - V 36. - No. 13. - P. 741-748.
8. Ping H. Determination of ultrasonic parameters based on attenuation and dispersion measurements // Ultrasound Imaging. - 1998. - V. 20. -P. 275-280.
9. Sung C.S., Mean J.K. Evaluation of material degradation of 1Cr-1Mo-0.25V steel by nondestructive method // Mater. Sci. Eng. A. - 2005. -V. 395. - P. 141-147.
10. Wang W., Rokhlin S.I., Lippold J.C., Adler L. Relationship between ultrasonic measurements and microstructural characteristics of type 308 stainless steel welds // Mater. Eval. - 1989. - V. 47. - No. 12. -P. 1388-1395.
11. Rosen M., Ives L., Biancaniello F., Mehrabian R. Correlation between ultrasonic and hardness measurements in aged aluminum alloy 2024 // Mater. Sci. Eng. - 1985. - V. 74. - P. 1-10.
12. Bhatia A.B., Moore R.A. Scattering of high frequency sound waves in polycrystalline materials II // J. Acoust. Soc. Am. - 1959. - V. 31. -P. 1140-1146.
13. Papadakis E.P. Ultrasonic diffraction loss and phase change in anisotropic materials // J. Acoust. Soc. Am. - 1966. - V. 40. - P. 863-876.
14. Papadakis E.P. Diffraction of ultrasound radiating into an elastically anisotropic medium // J. Acoust. Soc. Am. - 1964. - V. 36. - P. 414422.
15. Gur C.H., Tuncer B.O. Characterization of microstructural phases of steels by sound velocity measurement // Mater. Charact. - 2005. -V. 55. - P. 160-166.
16. Carreon H., Carreon M., Duecas A. Assessment of precipitates of aged Ti-6Al-4V alloy by ultrasonic attenuation // Philos. Mag. -2017. - V. 97. - No. 1. - P. 58-68.
17. Freitas V., Albuquerque C., Silva E., Silva A., Tavares J. Nondestructive characterization of microstructures and determination of elastic properties in plain carbon steel using ultrasonic measurements // Mater. Sci. Eng. A. - 2010. - V 527. - No. 16. - P. 4431-4437.
18. Freitas V., Normando G., Albuquerque C., Silva E., Silva A., Tavares J. Nondestructive characterization and evaluation of embrittlement kinetics and elastic constants of duplex stainless steel SAF 2205 for different aging times at 425°C and 475°C // J. Nondestr. Eval. - 2011. -V. 30. - No. 3. - P. 130-136.
19. Hu E., Wang W. The elastic constants measurement of metal alloy by using ultrasonic nondestructive method at different temperature // Math. Prob. Eng. - 2016. - P. 1-7.
Received 09.10.2018, revised 09.10.2018, accepted 07.11.2018
CeedeHua 06 aemopax
Hector Carreon, PhD, Full Professor, Ciudad Universitaria, Mexico, [email protected]
Maria Carreon-Garcidueñas, PhD, Full Professor, Facultad de Odontología, Estudios de Posgrado e Investigacion (UMSNH-CUEPI), Mexico, mgcarreon3012@gmail. com
Maria L. Carreon, PhD, Full Professor, University of Tulsa, USA, [email protected]
Vidal Almanza, PhD, Full Professor, Facultad de Odontologia, Estudios de Posgrado e Investigacion (UMSNH-CUEPI), Mexico, [email protected]
