Processing and Characterization of Porous Titanium for Orthopedic Implant Prepared by Argon-atmospheric Sintering and Arc Plasma Sintering

Abstract

Porous titanium is proposed to be an effective orthopedic implant with a lower elastic modulus and supports osseointegration during implantation. To produce porous titanium, powder metallurgy (PM) assisted with a space-holder is used in this study. Pure titanium is used as the starting material, and salt (NaCl) is used as the space-holder. Argon-atmospheric sintering and arc plasma sintering (APS) methods are applied for the sintering process. NaCl content was varied from 0–40 wt%. The temperature sintering was at 1100 °C for the argon-atmospheric sintering, and the current process was at 75 A for the APS. The formation of pores, total porosity, pore distribution, phase formation, and mechanical properties were examined by the optical microscope, scanning electron microscope (SEM), X-ray diffraction (XRD), and compression testing. Titanium with the addition of 20 wt% of NaCl is shown to be a potential biomaterial for the orthopedic implant, having a porosity of 38–39%, the elastic modulus of 3.2–5 GPa, and the yield strength of 141–150 MPa (argon-atmospheric sintering and APS) which shown to be similar to the properties of cortical bone.

Keywords:  Porous Titanium; Space-Holder; Powder Metallurgy; Argon-atmospheric Sintering; APS

1. Introduction

Titanium and its alloys are commonly used as orthopedic implant materials as they have high mechanical properties, high corrosion resistance, and biocompatible properties ¹. However, long-term implantation of titanium in the human body may cause stress shielding phenomena and bone resorption, leading to premature implant failure due to the elastic mismatch between titanium (100-110 GPa) and the bone (4-25 GPa)^2,3. Moreover, titanium drawback as the orthopedic implant is the bioinert character of titanium resulting in poor osseointegration⁴. Accordingly, lower elastic modulus titanium⁵ and porous structure titanium^6,7 are proposed to address the stress-shielding phenomenon. Further, the porous structure can also increase the osseointegration of the titanium implants by new bone tissue⁸.

Porous structure in titanium would have detrimental mechanical properties, compared to the bulk metal to reach the properties of bone. Reduction in elastic modulus is the main purpose so that the distribution pattern of stress can be improved, and as a consequence, implant loosening and bone resorption can be avoided⁶. Several studies and reviews have shown optimum porosity to promote bone ingrowth with 20–50% porosity and 100–500 μm of pore size^6,9-11.

The porous titanium manufacturing process can be approached through liquid state metallurgy such as casting or solid-state processing such as powder metallurgy (PM). However, due to the high-temperature reactivity of titanium, liquid state manufacturing of porous titanium could be difficult¹². Reactivity with oxygen and nitrogen might reduce the ductility, and some reactions with the mold might occur. Therefore, porous titanium fabrication through the solid-state process, by using the powder metallurgy method, is preferable because it allows a lower temperature process¹². In principle, powder metallurgy of titanium foam generates porosity which is were created and maintained while bonding between particles via sintering occurs at a temperature below the melting point¹³. Moreover, powder metallurgy offers a near-net-shape manufacturing process which may reduce scrap metal produced during titanium manufacture.

There are several ways to produce porous titanium by using the powder metallurgy method, such as partial sintering ¹⁴, bubble entrapment ¹⁵, polymer foam impregnation ^13,16, and space-holder technique ¹⁷. However, the space-holder technique ^10,18 is beneficial because of its low-cost routes, simple process, and possibility to produce pores in various sizes. In the space-holder technique, a temporary material is added into the mixture of titanium alloy, which will be further removed through the thermal process or the dissolution process. The commonly used space-holder are NaCl^19,20, ammonium bicarbonate (NH₄HCO₃)^21,22, carbamide^23,24, Mg²⁵, or even saccharose ²⁶.

Since titanium is highly reactive, the sintering process of the metal is conducted mainly in a high vacuum or argon atmosphere ²⁷. PM can also be modified by using arc plasma sintering (APS), a method using plasma as an energy source in the powder consolidation process to shorten the duration of the sintering process and reduce the energy consumption²⁸. The schematic diagram of APS is shown in Figure 1. In previous studies, APS was able to sinter some magnesium-based alloy (Mg-Zn), oxides dispersed alloy (Fe-25Cr-Y₂O₃), and also bulk titanium alloy (Ti6Al4V) in a relatively short time (less than 1 hour)^29-31.

Figure 1
Schematic Diagram of APS.

In this study, porous titanium was produced by using NaCl as the space-holder, while the sintering process was conducted under argon atmosphere and the APS. The effect of the NaCl content on the pore formation and the sintering process would be studied to achieve a high performance of porous titanium for orthopedic implants.

2. Materials and Methods

2.1. Materials

Commercially produced pure titanium powder (CP-Ti) supplied by Chengdu Huarui Industrial China was used as the starting powder. The space-holder used was NaCl provided by Merck. The weight ratio of Ti powder to NaCl was controlled to have a specified composition of 0–40 wt% NaCl (equal to 0–58 vol%). Binder was not used in the mixture to prevent additional oxidation and impurity. The detailed composition and the processing parameter of each specimen and its code are shown in Table 1.

Table 1
Sample codes and composition.

Specimens Codes	Composition (wt%)		(vol.% spacer)	Sintering Condition
	Titanium	NaCl
Ti-0 1100	Balance	-	-	Argon
Ti-20 1100	Balance	20	34	Argon
Ti-30 1100	Balance	30	47	Argon
Ti-40 1100	Balance	40	58	Argon
Ti-20 APS 2min	Balance	20	34	APS for 2 minutes
Ti-20 APS 3min	Balance	20	34	APS for 3 minutes
Ti-30 APS 3min	Balance	30	47	APS for 3 minutes

2.2. Processing of porous titanium

In order to prepare porous titanium, the blend of Ti-NaCl powder was mixed in a shaker for 30 minutes. The volume for each mixture was fixed to a specific value then uniaxially pressed at a pressure of 560 MPa for 3 minutes to form the green compacts. The green bodies had a shape of a cylinder having a diameter of 15 mm. The green compacts were sintered under two conditions; the first condition would be under the argon-atmospheric tube furnace (argon-atmospheric sintering route). In contrast, the second condition would be done inside the Arc Plasma Sintering device (APS route).

For the argon-atmospheric sintering route, a preheat treatment was conducted to remove the space-holder. The green bodies were preheated at 800 °C for 2 hours, followed by the sintering process at 1100 °C for 2 hours with a heating rate equal to 5 °C/minute. Finally, the samples were furnace-cooled to reach room temperature. For the APS route, the samples were preheated at 50 A (current) for 2 minutes (turned upside down), followed by the sintering process at 75 A (current). The duration of the sintering process was varied for 2–3 minutes. The resulted porous titanium was cooled rapidly after the sintering process inside the APS device. Subsequently, the samples were ground on emery paper and ultrasonically cleaned to remove the remaining oxide layer on the surface, followed by a leaching process in distilled water. The samples were immersed in distilled water above the room temperature (the water temperature was 50–60 °C) for three cycles (each cycle is for 3 hours). The wet samples were dried and then weighed to ensure the dissolution of NaCl. The leaching process was done until no further reduction on the specimen.

2.3. Characterization of porous titanium

The microstructure of porous titanium was examined by using an optical microscope and a scanning electron microscope (SEM, Jeol) equipped with Energy Dispersive X-Ray Analysis (EDX). Before the image analysis, the samples were prepared following some metallographic steps. The pore characteristics of the porous titanium were evaluated for total porosity and pore size. The total porosity was determined by the Archimedes method (P_Ar) and based on image analysis (P_IA). Phase formation in the sintered porous titanium was observed through X-ray diffraction (XRD; Rigaku, Cu-Kα). Compressive tests were conducted based on ASTM E-9 by using a universal testing machine (Shimadzu) for the mechanical properties. Compression specimens were cut by an electric discharge machine followed by polishing with the SiC emery sheets.

3. Results and Discussion

3.1. Preliminary evaluation of the starting powder and the salt leaching process

The morphology of the titanium powder and the space-holder are shown in Figure 2. These starting powders show irregular morphology. The NaCl particle has a wide distribution of size (80–500 µm). Broad distribution particle size is expected to give a better interconnectivity of pores ¹⁸. On the other side, irregular titanium has better mechanical interlocking than the spherical powder does¹⁰.

Figure 2
SEM images of a) NaCl powder and b) Ti powder.

In the manufacture of porous titanium with space-holders, it is very likely that the residue remains. Therefore, after the sintering process, the salt leaching process should be conducted. The progressive change in the weight during the leaching process is shown in Figure 3. There is no further weight reduction on the specimen after three cycles.

Figure 3
Reduction of weight vs immersion time.

3.2. Morphology and microstructural properties

The macro images and the microstructure images of the as-sintered samples under Argon-atmosphere are shown in Figure 4. In comparison, the APS samples are displayed in Figure 5. Further, Table 2 summarizes the pore characteristics.

Figure 4
Photograph and optical microscope images of porous titanium prepared by Argon-atmosphere; (a) Ti-0 1100, (b) Ti-20 1100, (c)Ti-30 1100, (d) Ti-40 1100.

Figure 5
Photograph and optical microscope images of porous titanium prepared by APS (a) Ti-20 APS 2min, (b) Ti-20 APS 3min, (c) Ti-30 APS 3min.

Table 2
Pore characteristics of the as sintered porous titanium.

Samples	PAr (%)	PIA (%)	Macro Pore Size (μm)
Ti-0 1100	11.3± 0.1	9.2± 2	_
Ti-20 1100	39 ± 2	32± 8	100-800
Ti-30 1100	49.8 ± 1	44.6 ± 5	100-800
Ti-40 1100	58 ± 0.3	52.1 ± 4	100-800
Ti-20 APS 2min	38.1% ± 3.8	32.6 ± 5	100-800
Ti-20 APS 3min	38.0% ± 5.6	38.5 ± 8	100-800
Ti-30 APS 3min	47.5% ± 0.2	52.9 ± 6	100-800

Based on Figure 4, Argon-atmospheric sintering was shown to be able to produce metallic titanium. When NaCl was not added, as seen in Figure 4a, the pores were formed due to the incomplete densification process; therefore, the resulted pores had small sizes (micropores, only a few μm). Meanwhile, when the NaCl was added (Figure 4b-d), the as-sintered titanium showed two types of pores (micro and macropores).

The macropores showed a typical shape of NaCl confirming the function of the space-holder. Different porosities and distributions were affected by the addition of NaCl. Increasing NaCl content up to 40 wt% would make the pores larger and more distributed. In general, NaCl content has the highest effect on the formation of macroporosity. The increasing porosity based on Archimedes method and image analysis shows a similar tendency.

The corresponding porosity related to the content of NaCl is shown in Figure 6. Figure 6 shows a different value between porosities based on both Archimedes method and image analysis. The Archimedes method is a volumetric method, while the image analysis would take a fraction from the total volume of the sample ³. Furthermore, a higher deviation number of the P_IA indicates a non-homogeneous porosity for a different observation area. The hygroscopic nature of NaCl may lead to the accumulation of the space-holder. When the NaCl content is more than 30 wt%, it will make the space-holder agglomerates, creating a larger pore size. The higher porosity might happen since the densification during the sintering process is not entirely conducted. Another consideration for the pore formation is when the space-holder is not fully dissolved and remains in the isolated pores.

Figure 6
Corresponding porosity related to the NaCl for different sintering process; (a) Argon sintering, (b) APS.

Figure 7 shows the SEM images and the EDX detection for the as-sintered titanium. Different pore structures and pore walls can be seen more clearly. During sintering, there would be some changes: dimensional change of the pores, pore walls, and the shrinkage of the whole samples ²³. Since temperature sintering in this study was relatively lower than the titanium's melting temperature, the shrinkage of the entire specimen was insignificant. There was also no evidence of the reduction of the sample height after the sintering process.

Figure 7
SEM and EDS characterization for the porous titanium (a) Ti-0 1100, (b) Ti-20 1100, (c) Ti-40 1100, and (d) Ti-20 APS 3min.

Figure 7a shows the pore structure of Ti-0 1100, while the EDX reveals some impurity that remains inside the pore. Since metallographic steps were applied to the samples, the SiC paper and the alumina paste (Al₂O₃) might contaminate the samples. Figure 7b-d shows a type of irregular shapes in a macro size (>100 μm). The observed pore structure in this study was a compromise of the raw NaCl (cuboid, irregular, large particle size) with a wide variety of sizes and the sintering process. Figure 7b shows a type of closed pores with some micropores, influenced by the addition of 20 wt% of NaCl. Microporosity (<10 μm) has been recognized to be an essential factor in increasing scaffold osteoinduction ³².

Figure 7c, when 40 wt% of the space-holder was added, shows a type of interconnected pores with macro and microporosity. Since the same sintering temperature was applied to Ti-20 1100 and Ti-40 1100, the pore walls of these specimens were also similar. The rough pore walls could be observed, implying that the densification was not finished. Figure 7d, when the APS is applied to the 20 wt% of Ti-NaCl mixture, also shows a closed pore type, consisting of micro- and macroporosity. However, the pore walls were seen to be much rougher than in the case of Argon-atmospheric sintering, indicating that a less densification process had occurred. Further, the EDX reveals the Na element in the alloy. Although the APS is shown to be able to sinter the porous titanium, less processing time might also result in the incomplete process of space-holder removal. Less densification on the pore walls may deteriorate the mechanical properties of porous titanium.

Figure 8 shows the XRD pattern for the as-sintered porous titanium. Phases on porous titanium after Argon-atmospheric sintering consists of Ti phases and a small peak of the TiO₂ phase (Figure 8a). There is no other chemical reaction product during sintering under the Argon-atmosphere. Meanwhile, in Figure 8b, peak characteristics of porous titanium after APS consists of titanium phases, TiO₂ phases, and NaCl phase. The NaCl phase in the APS specimens indicates the residue of NaCl. It means the leaching process could not remove the space-holder thoroughly as there was probably not enough diffusion time for the space-holder removal process. The APS was conducted in only several minutes (2–3 minutes); therefore, the duration should be studied further to find the optimum processing time.

Figure 8
XRD spectra of porous titanium after (a) Argon sintering, (b) APS.

3.3. Mechanical properties

Figure 9 shows the typical compressive stress-strain curve of the porous titanium. Meanwhile, the mean value and the standard deviation for the mechanical properties are shown in Table 3. Further analysis of the mechanical properties and the porosity is shown in Figure 10.

Figure 9
Compressive stress-strain curves of samples having various porosities obtained by Argon-sintering and APS.

Table 3
Mechanical Properties of Porous Titanium.

Specimen	Elastic Modulus (GPa)	Yield Strength (MPa)
Ti-0 1100	10.41 ± 2.42	550 ± 33.9
Ti-20 1100	3.19 ± 0.85	141 ± 17.67
Ti-30 1100	0.825 ± 0.1	90.95 ± 24.53
Ti-40 1100	0.27 ± 0.14	59.85 ± 19.44
Ti-20 APS 3min	5.08 ± 0.6	150.5 ± 4.95

Figure 10
Compressive Mechanical Properties vs Porosity for porous titanium prepared by Argon-sintered and the APS; (a) elastic modulus, (b) yield strength.

As shown in Figure 9, the porosity and the sintering process influence the compressive properties of porous titanium. For the Argon-atmospheric sintering route, the mechanical properties depend on the total porosity of the samples. Higher porosity as a result of more addition NaCl results in lower mechanical strength. The compressive behavior of porous titanium in this study is similar to cellular materials, consisting of the initial linear elastic region, the plateau region, and the densified region ³³. However, for the APS samples (Ti-20 APS 3min), the porosity content is similar to the Ti-20 1100 sample, but the compressive stress-strain curve is different. For the APS samples, the compressive curve only consists of the elastic region and the plateau region. Further, the specimen failed below 50% strain (40% in this study).

Table 3 and Figure 10 show the elastic modulus and yield strength are inversely proportional to the porosity. Not only the space-holder content but the manufacturing process also influences the mechanical properties. Hence, the porous titanium must have a similar characteristic to that of human bone. In other words, the mechanical properties should follow the cortical bone properties; the elastic modulus should be in a range of 7–30 GPa, and the yield strength should be in a range of 120–160 MPa^6,34. Therefore, Ti20-1100 and also Ti20 APS 3min have fulfilled the mechanical properties requirement. These three porous titanium specimens show the possibility of being used as a permanently orthopedic implant. The microporosity and the macroporosity are also hypothesized to increase the osseointegration of porous titanium. Further study should be conducted to clarify this assumption.

4. Conclusions

It follows from this study that porous titanium can be prepared by both Argon-atmospheric sintering and APS process using NaCl as the space-holder. The porosity of the titanium is inversely proportional to the space-holder addition. The lower sintering temperature for the Argon-atmospheric sintering and the short time of APS correlate with the formation of microporosity. The microporosity in the alloys would increase the value of total porosity, which made the obtained porosity higher than expected. Compared to the APS, Argon-atmospheric sintering was shown to produce a porous material with a denser pore wall, less contamination, and oxidation product reaction. However, the built-up APS machine, with several minutes of processing times, has shown a potential alternative method in titanium manufacturing. Based on the porosity and the mechanical properties, porous titanium with 20 wt% of NaCl proves promising to be used as orthopedic implants.

5. Acknowledgements

This research is fully supported by Direktorat Riset dan Pengabdian Masyarakat Universitas Indonesia (DRPM UI) through PUTI Doktor Research Grant No: NKB-682/UN2.RST/HKP.05.00/2020. The authors would also like to thank the Research Center for Metallurgy and Materials, Indonesia Institute of Sciences, for the laboratory facilities.

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Publication Dates

• Publication in this collection
  20 Sept 2021
• Date of issue
  2021

History

• Received
  10 Mar 2021
• Reviewed
  30 July 2021
• Accepted
  15 Aug 2021