Role of Silicon in the Microstructural Development and Properties of Ti-15Nb-xSi Alloys for Biomedical Applications

Abstract

Ti-Nb alloys are attractive for biomedical implants and the addition of Si can lead to an improved set of properties. This study investigates the effect on the microstructures and properties of solution-treated Ti-15Nb-xSi alloys followed by furnace cooling (FC), and water quenching (WQ). Based on the results, Si acts as a β-stabilizing element by increasing the β volume fraction from 13%–36% in FC samples to a range from 0%–0.55% Si. The elastic modulus decreased under both conditions and reached approximately 63 GPa in WQ samples with 0.35% Si due to an increased α” unit cell volume. On the other hand, hardness increased with increased Si content under FC and WQ conditions to a maximum of 313 HV in the WQ sample containing 0.55% Si.

Keywords
Ti alloys; biomaterial; Vickers hardness; elastic modulus

1. Introduction

β-Ti alloys are the most promising candidates for biomedical implants¹. Their compositions are developed using non-toxic elements (e.g., Nb, Mo, Zr, Ta, Fe, Sn and Si) to reach low elastic moduli^1-3, and in that respect, Ti-Nb alloys attract a good deal of interest^4-8. Moreover, this alloying element has excellent biocompatibility in vivo⁹ and is capable of significantly increasing the mechanical resistance of Ti⁸.

Biomaterials with low elastic moduli are essential for shielding stress reduction, which could lead to early implant rejection¹⁰. The elastic moduli in Ti-Nb alloys changes with Nb concentration in the form of a W-shaped curve with two minimums at approximately 15wt.% and 42wt.%¹¹, and these compositions are an ongoing focus of research^12-15. Accordingly, Ti-15Nb is more favorable than the Ti-42Nb alloy due to its lower Nb content, which could potentially reduce manufacturing costs¹⁶, and its lower density. The Ti-15Nb alloy also exhibits the shape memory effect in martensitic condition¹⁷ and may have similar properties to other titanium alloys with higher concentrations of β-stabilizers in terms of deformability¹⁸ and elastic modulus¹⁷. E is approximately 95 GPa when α and β phases are formed with slow cooling¹⁹ and 59–72 GPa with rapid cooling, due to its martensitic structure^17,18. The latter condition is more attractive and corresponds to the curve profile described above.

Other alloying elements could be added to the Ti-15Nb alloy to improve its properties. Elements such as Zr, Sn, Hf, Fe, Mo, Si, and Ta have previously been added to Ti-Nb alloys with this goal^20-23; however, these studies focused on high Nb concentrations. The addition of Si has resulted in several advantages in these alloys, including a decrease in the elastic modulus by helping to suppress the ω phase in the β-matrix²⁴, and increase in the mechanical resistance due to grain refinement²⁵, and improved resistance to corrosion due to SiO₂ formation and its action as a dopant on TiO₂, which improves the resistive properties of the oxide layer²⁶. However, there is limited understanding about the influence of Si on phases and properties in relatively low Nb concentrations and there is no information in the literature about Ti-Nb-Si alloys at 15% Nb concentration. Therefore, these results contribute to a better understanding of the role of Si in this system. Because these alloys are intended for the manufacture of implants, it is noteworthy that Si is found in relatively high concentrations in active osteoblasts, which are essential for bone extracellular matrix formation. This feature makes Si potentially capable of influencing the cell response at the bone-implant interface²⁷. Consequently, this study investigated the effect on the microstructures, elastic moduli and hardness of solution-treated Ti-15Nb-xSi alloys (x = 0; 0.15; 0.35; 0.55) to FC and WQ.

2. Experimental Procedure

Ti–15Nb-xSi alloys (x = 0; 0.15; 0.35; 0.55) (wt. %) were melted in an arc furnace (Analog Instrumentation and Control, model AN9270) with a tungsten electrode under an argon atmosphere using a water-cooled copper hearth. The purity degree of starting elements Ti, Nb, and Si was 99.84%, 99.99%, and 99.9999%, respectively. A homogenizing treatment was conducted at 1000 °C for 8 h, followed by hot rolling at 1000 °C to get 4-mm thick plates. The alloys were mechanically cleaned and cut into samples of 25 × 20 × 3 mm. Finally, samples were heated at 1000 ºC for 1 h and cooled under two different conditions, namely FC and WQ. The interstitial (oxygen and nitrogen) contents of the FC samples were measured using LECO 400 equipment.

All samples were mounted and ground with different SiC grits (220–1,500) and polished with 6–3 μm diamond paste and a 1μm alumina suspension. Chemical etching consisted of 6 mL HNO₃, 3 ml HF, and 91 ml H₂O. Samples were analyzed by optical microscopy (OM) (Carl ZEISS Axio SCOPE A.1) and scanning electron microscopy (SEM) (JEOL JCM – 5700). Energy dispersive X-ray spectroscopy (EDS) was used to map Si distribution and to determine the Ti, Nb, and Si composition of the polished samples. The mean grain size of each sample under FC and WQ conditions was measured using the ImageJ 1.46r program. XRD patterns were obtained using Rigaku DMAX100 equipment (40 kV, 30 mA) with monochromatic CuKα1 radiation, at angular range from 37°–80° (2θ) in 0.02° step at counting time of 2 s/step. Rietveld's refinement was performed using the General Structure Analysis System II (GSAS-II)²⁸ to determine the structural parameters and volume fractions of the phases.

Elastic moduli were measured by the ultrasonic method using a pulse generator/receiver Panametrics NDT Model 5072 PR, connected to piezoelectric transducers of 5 MHz which were in contact with the samples via coupling gel. The values reported were the mean of three measurements. The Vickers hardness of all samples was measured in a Future Tech FV-700 machine by applying a 2 kg load for 15 s. The reported hardness of each sample corresponded to mean value of 5 times the indentation.

3. Results and Discussion

3.1 Microstructures

The interstitial contents of Ti-15Nb-xSi samples that were heat-treated above β-transus at 1000°C for 1h followed by FC are shown in Table 1. The oxygen and nitrogen contents were in the range of 0.207 ± 0.013 wt.% to 0.261 ± 0.019 wt.%, and 0.0017 ± 0.0000 wt.% to 0.0069 ± 0.0004 wt.%, respectively. These results are consistent with the ASTM B977-19 standard²⁹. Figure 1 presents SEM micrographs of the samples and shows α plates formed from prior β grains. Small amounts of α phase, represented by irregular morphology, were only observed in samples with Si as shown in the optical micrographs in the upper right of Figure 1bd. FC samples show coarse grains with mean sizes of 1001 ± 331, 788 ± 189, 497 ± 158, and 432 ± 109μm for Si concentrations of 0, 0.15, 0.35, and 0.55, respectively. Despite the wide range of these values as illustrated by the high standard deviations, the increase in Si content resulted in grain refinement, particularly in 0.35% Si. The literature notes that grain refinement caused by Si addition is due to the rejection of this alloying element as solidification begins, which provides a constitutional undercooling capable of activating adjacent nuclei resulting in a smaller grain size^30,31. Therefore, the consequence of a higher Si content is higher constitutional undercooling and, in turn, the activation of a larger number of adjacent nuclei.

Table 1
Interstitial contents of furnace-cooled Ti-15Nb-xSi samples.

Nominal content (wt.%)	Interstitial contents (wt.%)
	O	N
Ti-15Nb	0.260 ± 0.003	0.0069 ± 0.0004
Ti-15Nb-0.15Si	0.207 ± 0.013	0.0038 ± 0.0021
Ti-15Nb-0.35Si	0.261 ± 0.019	0.0043 ± 0.0007
Ti-15Nb-0.55Si	0.220 ± 0.006	0.0017 ± 0.0000

Figure 1
SEM micrographs of furnace-cooled samples: (a) Ti-15Nb, (b) Ti-15Nb-0.15Si, (c) Ti-15Nb-0.35Si, (d) Ti-15Nb-0.55Si. Inserts (a-d) present OM micrographs under lower magnifications.

Studies by Hon et al.¹⁹ show that a Ti-Nb alloy with 15% Nb contains both α and β phases, but the α is prevalent. The XRD patterns of all samples under FC conditions confirm the presence of both phases (Figure 2). An in-depth analysis of the effect of Si on the hcp (α-Ti) and bcc (β-Ti) structures was conducted using the Rietveld method. Refinings, in the current study, were obtained from the XRD patterns of solid samples and some refinement indicators are shown in Figure 2 and the difference between observed and calculated patterns is represented by a gray line close to the abscissa axis. Variations in the structural parameters of α and β, and their volume fractions as a function of Si concentration, are shown in Figure 3.

Figure 2
Observed (open circles) and calculated (solid red line) XRD patterns of FC Ti-15Nb-xSi samples. The difference (solid grey line) is shown at the bottom of the image and Bragg reflections are indicated by vertical marks.

Figure 3
Variation of lattice parameters (a, b), unit-cell volumes (c) and phase fractions (d) of α and β as function of Si contents recorded for furnace-cooled Ti-15Nb-xSi samples.

Figure 3a shows that samples with 0.15% and 0.35% Si recorded increased a_α and c_α lattice parameters. These increases were significantly higher in a_α at 0.15% Si and in c_α at 0.35% Si, which reflects their increased unit cell volumes (Figure 3c), with the exception of 0.55% Si, which was slightly lower due to a decreased c_α. Parameters of a_β have a profile similar to that of c_α, which increased the β unit cell volume to 0.35% Si, as shown in Figure 3c. The reduced a_β value observed at 0.55% Si is consistent with the study by Kim et al.²⁴, who assessed the β lattice parameters at Si concentrations ranging from 0.5% to 1.5at.% (0.3 to 0.9wt.%) in an alloy with 26at.%Nb (40.5wt.%Nb). The above authors observed that a_β decreased as Si content increased, and that the reduction followed a non-linear profile. It is also noteworthy that Si addition generated the same effect on the volume of α- and β-phase unit cells. However, the effect was stronger on β, notably at 0.35% and 0.55% Si, and this is coherent with the role of Si as a β-stabilizing element in Ti alloys^24,25. According to Barriobero-Vila et al.³², element partitioning in the alloy between α and β enhances their respective stabilizing elements, i.e., the β phase is richer in Si than α. For higher Nb concentrations, the most significant contribution of Si in terms of the phases formed, is its ability to prevent the occurrence of ω, which normally causes the weakening of alloys³³. In furnace-cooled Ti-Nb alloys, ω precipitates are found in the β matrix in the range of 26–35% Nb^19,33.

Si addition to furnace-cooled Ti-15Nb samples also increased the β volume fraction (Figure 3d). This reached 13 vol.% in the Ti-15Nb sample and increased to 17.7 vol.% at 0.15% Si. Alloys containing 0.35% and 0.55% Si showed 31 vol.% and 36 vol.% β, respectively. Thus, this finding, once again, corroborated the β-stabilizer effect of Si and highlighted that the addition of 0.35% Si more effectively triggered structural changes in the Ti-15Nb sample, considering the concentrations added.

The low Si concentrations used in this study minimize the risk of forming the intermetallic phases that are observed in the Ti-Si diagram³⁴. The Ti₃Si phase resulting from the eutectoid decomposition β → α + Ti₃Si would be the most likely precipitation to occur. However, it is worth noting that the addition of β-stabilizing elements, such as Nb, can make this decomposition reaction slower, even during FC, and this is more likely to occur at higher concentrations³⁵. It is noted that, when solution-treating Ti-15Nb-xSi alloys at 1000 °C, the β-Ti field is narrow, and the continuous increase in Nb content gradually reduces the solubility of Si in the β-Ti phase³⁶. According to Tavares et al.²⁵, for 35 wt.% Nb, the solubility of Si in β-Ti phase was reached at 0.35 wt.%. However, at 0.55 wt.% Si, (Ti,Nb)₃Si particles were observed because the solution treatment of this alloy occurred in the biphasic field β-Ti + (Ti,Nb)₃Si. Comparable results were obtained by Masumoto et al.³⁷, who worked with Ti-37.98Nb-1.71Al-(0.18, 0.29, 0.41, 0.47, and 0.53)Si alloys (wt.%). These authors identified (Ti,Nb)₃Si particles of approximately 200 nm in alloys containing >0.41 wt.% Si, which formed during solution treatment at 1000°C for 30 min. Another study, with a lower concentration of Nb, was conducted by Shevchenko et al.³⁸, who investigated Ti–18Nb–xSi alloys with 0.6–1.2 wt.% Si quenched at temperatures from 800–1200°С. (Ti, Nb)₃Si particles were observed in all alloys, and the number present increased as Si concentration increased. Particles in the Ti-18Nb-1.2Si alloy quenched from 1000°C exhibit an oval shape with cross-sectional size from 0.2–0.3 μm. It is worth noting that the heating processes at these temperatures were carried out in as-cast condition and pre-existing (Ti, Nb)₃Si particles were not dissolved at temperatures ≤ 1000 °C. The lower concentration of Nb, 15 wt.%, in this study increases the solubility of Si in the β-Ti phase and this is verified by the 1000°C isotherm of the Ti-Nb-Si system³⁶, where all compositions studied are within the β-Ti field.

To validate the argument above, SEM images of Ti-15Nb-(0.15; 0.35; 0.55)Si samples, and their corresponding Si distribution maps were obtained by EDS (Figure 4). The Ti, Nb, and Si composition of the samples was also determined, as shown in Table 2. Figure 4df shows homogeneous Si distribution at concentrations close to their nominal compositions (Table 2). This outcome indicates that there was no precipitation of Si-rich phase in the alloys. Therefore, the absence of precipitate in the images shown in Figure 4 is consistent with these observations.

Figure 4
SEM/SEI images of FC Ti-15Nb-xSi samples with x = 0.15 (a), x = 0.35 (b) and x = 0.55Si (c) and EDS mapping of Si (d-f), respectively.

Table 2
Compositions of furnace-cooled Ti-15Nb-xSi samples based on EDS.

Nominal content (wt.%)	EDS-obtained compositions (wt.%)
	Ti	Nb	Si
Ti-15Nb-0.15Si	85.4	14.4	0.2
Ti-15Nb-0.35Si	85.5	14.2	0.3
Ti-15Nb-0.55Si	85.4	14.1	0.5

SEM micrographs of Ti-15Nb-xSi samples heat-treated at 1000°C for 1h and quenched in water resulted in the acicular martensitic structures shown in Figure 5. The Ti-15Nb sample has relatively thick and long primary martensite plates that become thinner as Si content increases. This morphological aspect is also observed when Nb content increases in Ti-Nb alloys³⁹. The optical micrographs displayed in the upper right corner of Figure 5ad show that an increase in Si content results in a decrease in alloy grain size, as observed under FC conditions. The Si concentrations and their resulting mean grain sizes were 0%, 0.15%, 0.35%, and 0.55%, and 952 ± 130μm, 724 ± 171μm, 572 ± 139μm, and 376 ± 92μm, respectively. This effect is stronger in Ti-35Nb-xSi alloys, where β phase retention is observed²⁵, particularly in 0.55% Si due to the formation of (Ti, Nb)₃Si particles, which were mostly located at the grain boundaries thereby preventing their growth⁴⁰ and enhancing the refining effect.

Figure 5
SEM micrographs of WQ samples: (a) Ti-15Nb, (b) Ti-15Nb-0.15Si, (c) Ti-15Nb-0.35Si, (d) Ti-15Nb-0.55Si. Inserts (a-d) present OM micrographs under lower magnifications.

Analysis of the XRD pattern shows that martensitic α”, with spatial group Cmcm, was the only phase formed in water-quenched Ti-15Nb-xSi samples (Figure 6). This is consistent with the study by Bönisch et al.⁴¹, who determined that the transition from α’ to α” takes place at a concentration of 13.85 wt.% Nb. The Ti-15Nb sample showed two values each for the a_α”, b_α” and c_α” lattice parameters that were identified by the Rietveld method, as shown in Figure 6 and Table 3. Based on Bönisch et al.⁴¹, dimensions of unit cell α” are significantly influenced by Nb concentration. It is important to note that the above authors investigated Ti-(9.1-39.3wt.%)Nb alloys homogenized at 1000°C for 24h under WQ. This indicates that the treatment time of 8h at 1000 °C in the β field adopted in the current study was not long enough for Nb to become evenly distributed in the sample, and WQ allowed this condition to remain unchanged. The same result was not observed in the samples with Si (Table 3), which had only one value for each parameter of the α” unit cell. This conforms with previous studies showing that substitutional atoms often diffuse faster along grain boundaries than through the crystal lattice at temperatures considerably below the melting point⁴². As already mentioned, Si-stimulated grain refining required a larger total grain boundary area to increase the chances of achieving better Nb diffusion in β-Ti, because the Nb (D_Nb) diffusion coefficient is slightly lower than the self-diffusion (D_Ti) coefficient within a wide range of temperatures⁴³. On the other hand, it was observed that D_Si is significantly higher than D_Ti; this outcome was attributed to the prevailing effect of atom size on the diffusion of elements in β-Ti⁴⁴. In this case, there is a large difference between the atomic radii of Ti (1.44 Å) and Si (1.18 Å).

Figure 6
Observed (○) and calculated (solid red line) XRD patterns recorded for WQ Ti-15Nb-xSi samples. The difference (solid grey line) is shown at the bottom of the image and Bragg reflections are indicated by vertical marks.

Table 3
Values of lattice parameters and volume fractions of the α” phase recorded for all observable reflections of water-quenched Ti-15Nb-xSi samples.

Nominal content (wt.%)		Lattice parameter (Å)			Volume fraction
		aα”	bα”	cα”
Ti-15Nb	(α1”)	2.92952	5.09708	4.71056	0.685
	(α2”)	2.98719	5.12340	4.68995	0.315
Ti-15Nb-0.15Si		2.99012	5.04406	4.69545	1.000
Ti-15Nb-0.35Si		2.98606	5.06942	4.70482	1.000
Ti-15Nb-0.55Si		2.99021	5.06172	4.70321	1.000

The structural parameters of α” for water-quenched Ti-15Nb-xSi samples as a function of Si concentration are presented in Figure 7. The values recorded for the Ti-15Nb sample were obtained using the α₁” and α₂” lattice parameters and their respective volume fractions (Table 3), and therefore, in this case, they refer to the weighted average values. Significant changes in lattice parameters were observed in the 0.15% Si sample, where a_α” increased as b_α” and c_α” decreased (Figure 7a), although the unit cell volume included a value close to that recorded for the sample without Si (Figure 7b). Changes in the lattice parameters that result in a significant volume increase were only observed from 0.35% Si, given the increased b_α” and c_α” parameters, whereas a_α” remained almost unchanged. The same behavior for the a_α” parameter was also observed in Ti-18Nb-(0.6-1.2)Si alloys quenched from 1100°C when the Si content had increased, although c_α” and b_α” had significantly decreased³⁸.

Figure 7
Variation of the lattice parameters (a) and unit-cell volume (b) of the α” phase as a function of Si content for WQ Ti-15Nb-xSi samples.

3.2 Compositional influence on elastic modulus

Figure 8 shows the effect on the elastic modulus of adding Si to Ti-15Nb-xSi samples under FC and WQ conditions. Comparing the two cooling conditions, higher values are observed for FC than WQ, because the FC samples mostly comprise α phase (Figure 2), whereas the WQ samples are formed by martensitic α” phase (Figure 6). This finding is consistent with the association between phases and the elastic moduli reported by Lee et al.⁴⁵ in the Ti-Nb system, which are given as follows: ω > α > α’ > α” > β.

Figure 8
Elastic modulus of solution-treated samples as a function of Si content. FC: furnace-cooled; and WQ: water-quenched.

The Ti-15Nb sample recorded an E value of 98 ± 1GPa under FC condition, which was consistent with data previously reported by Hon et al.¹⁹. The elastic modulus decreased and reached lower values from Si concentrations of 0.35%, where E = 90 ± 2 GPa. The profile of this curve is a result of the increase in β volume fraction with the addition of Si; the most significant increase is from 0.15% Si (17.7 vol.% β) to 0.35% Si (31 vol.% β) (Figure 3d). Here, it is important to mention that β presents the lowest elastic modulus among all stable and metastable phases⁴⁵. Additionally, it is worth highlighting that in these Si concentrations, the a_β parameter goes from 3.2864 Å in 0.15% Si to 3.2907 Å in 0.35% Si (Figure 3b). This significant increase in the network parameter of β-Ti in 0.35% Si leads to a greater drop in the elastic modulus, because this property is determined by the bond strength between the atoms, which in turn is not only related to the crystalline structure, but also to the interatomic distances⁴⁶.

The Ti-15Nb sample recorded an elastic modulus of 68.1 ± 0.4 GPa under WQ condition. This value accords with data reported by Ozaki et al.¹¹. The curve profile is similar to that of the FC condition, in which the lowest elastic modulus of 63.1 ± 1.5 GPa was observed in the 0.35% Si sample. As previously discussed, only the martensitic α” phase was identified in these samples (Figure 6). Therefore, the reduction is associated with the effect of Si on the orthorhombic structure, i.e., its increased unit cell volume. This effectively takes place from 0.35%Si, as shown in Figure 7b, as a result of the increase in b_α” and c_α” parameters, showing that Si is capable of contributing to bond strength reduction between the atoms, which is responsible for the elastic modulus performance⁴⁶.

3.3 Compositional influence on hardness

Hardness values as a function of Si concentration for Ti-15Nb-xSi samples cooled in FC and WQ conditions are shown in Figure 9. The increase in Si content has assisted the increase in hardness of samples under both conditions.The variation in elastic modulus and hardness in β-type titanium alloys usually follow the same trend because most of these studies are on alloys with high concentrations of β-stabilizing elements, where the precipitation of ω on the β matrix is frequently observed. It is noteworthy that ω phase exhibits the highest elastic modulus among all phases in titanium alloys^46,47, as well as playing an important role in increasing hardness^45,46. Therefore, its presence strongly influences the hardness and elastic modulus profiles of these alloys.

Figure 9
Hardness of solution-treated samples as a function of Si content. FC: furnace-cooled; and WQ: water-quenched.

Increasing Si concentration in Ti-35Nb-xSi alloys, investigated by Tavares et al.²⁵, was associated with a decrease in ω precipitate density on the β matrix, because Si prevents its formation, resulting in an elastic modulus decrease. However, this was not shown for hardness because Si causes distortions in the CCC network (β-Ti) which becomes progressively larger with increasing concentration. Its strong solid-solution-strengthening effect is due to the significant difference between the atomic radii of Ti (1.44 Å) and Si (1.18 Å)²³. A similar effect on hardness with the addition of Si is also seen in other Ti alloys^48-50, as in this study.

Furthermore, (Ti,Nb)₃Si particles were not observed in alloys with the addition of Si, as shown in Figure 4. If (Ti,Nb)₃Si particles were present in Ti-15Nb-xSi alloys, these would be coarse and incoherent with the matrix, as seen in Ti-Nb-Al-Si alloys with Si concentration > 0.41 wt.%³⁷. It is important to note that while the solution temperature was the same in both situations (1000°C), the time was 30 min for Ti-Nb-Al-Si alloys, but 1 h for the alloys investigated in this study, which would stimulate their increase further. This suggests that if (Ti,Nb)₃Si particles were formed, their effect on the hardness would not be so significant on Ti-15Nb-xSi alloys, as the results obtained by Shevchenko et al.³⁸ indicate that for Ti-18Nb-(0.6-1.2)Si alloys quenched from 1000°C resulted in hardness values from approximately 15.5 HRC (Ti-18Nb) to 23.5 HRC (Ti-18Nb-1.2Si). Moreover, according to these authors, the hardness values gradually increase with the addition of higher concentrations of Si due to the more intense saturation of the solid solution. However, as the amount of (Ti,Nb)₃Si particles increases, there is a depletion of silicon in the solid solution, and the influence of the solid-solution hardening is weakened.

Figure 9 shows that the highest hardness values were observed under WQ conditions with values ranging from 262 ± 6 HV (Ti-15Nb) to 313 ± 7 HV (Ti-15Nb-0.55Si), whereas under FC conditions the values ranged from 210 ± 6 HV to 233 ± 5 HV. According to Lee et al.⁴⁵, the association between the phases and the hardness of Ti-Nb is ω > α’ > α” > β > α; this behavior is attributable to the microstructures of WQ samples, which are only composed of a martensitic α” phase. According to the association established by Lee et al.⁴⁵ the bcc structure (β-Ti) contributes more significantly to hardness than the hcp structure (α-Ti), which must be related to the fact that β phase is richer in β-stabilizing elements than α. This finding reinforces the ascending profile of the FC sample curve, because the β volume fraction increases as Si content increases (Figure 3d).

4. Conclusions

This study investigated the effect of silicon on the microstructures and properties of Ti-15Nb-xSi alloys under FC and WQ conditions. The study verified that Si acts as β-stabilizing element because the β volume fraction increased from 13% to 36% in FC samples, as the concentration of added Si varied from 0 to 0.55wt.%. The effect of grain refining was also observed in WQ samples with increasing Si content. The elastic modulus decreased as Si content increased, most significantly in the sample with 0.35wt.%, which recorded 90 ± 2 GPa under FC condition, due to the increased β volume fraction associated with the increase in its unit cell, and 63.1 ± 1.5 GPa under WQ condition as a consequence of increased α” unit cell volume. Hardness values were higher due to increased Si concentrations under both conditions, which can be attributed to its strong solid-solution-strengthening effect. This increase was more pronounced in WQ samples, due to the orthorhombic structure hardness of α”, which reached 262 ± 6 HV in Ti-15Nb and 313 ± 7 HV in Ti-15Nb-0.55Si.

5. Acknowledgments

We are grateful to CNPq for the financial support and to the Brazilian Metallurgy and Mining Company (CBMM) for the supply of Nb. We also express our appreciation to Professor Rubens Caram for making the Physical Metallurgy Laboratory (LABMET/ FEM/ UNICAMP) available for the chemical analyses of the alloys.

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Publication Dates

• Publication in this collection
  22 Mar 2021
• Date of issue
  2021

History

• Received
  15 Sept 2020
• Reviewed
  07 Jan 2021
• Accepted
  16 Feb 2021