# Tribomechanical Properties of a Carbon-Based Nanolayer Prepared by Nitrogen Ion Beam Assisted Deposition for Finger Joint Replacements

Authors: Tomas Horazdovsky; Radka Vrbova
Journal: Journal of Nanomaterials
 (2018)

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## Abstract

This paper presents the tribomechanical test results of Ti6Al4V alloy modified by carbon-based nanolayers with a thickness of 20 nm and 40 nm, prepared by nitrogen ion beam assisted deposition. The presence of carbon and nitrogen compounds was observed in the modified surface after ion bombardment. Nonstoichiometric TiNx was mainly detected near the interface nanolayer/titanium substrate and in the substrate itself. Ion bombardment led to an improved surface hardness of ~13 GPa in comparison to unmodified Ti6Al4V titanium alloy (~5.5 GPa) and alloy coated by carbon nanolayer without nitrogen ion assistance (~7 GPa). The decreasing of friction coefficient was achieved from 0.5–0.6 for untreated Ti6Al4V alloy to 0.1 for treated Ti6Al4V alloy. Wear testing using a joint wear simulator proved that the modified Ti6Al4V alloy has a higher resistance compared to the unmodified Ti6Al4V alloy. The primary local wear fault of the treated surface was observed after 240,000 cycles in comparison to enormous wear on the untreated surface after just 10,000 cycles. Treating the Ti6Al4V load-bearing components of implants with carbon-based nanolayers assisted by nitrogen ions is very promising in terms of extending the lifetime of implants and thereby reduces patient burden.


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## Body

## 1. Introduction

Titanium (Ti) and its alloys are currently the most attractive materials for biomedical applications due to their beneficial biological compatibility and good mechanical properties. They are used mainly for joint replacements such as knee, hip, shoulder, elbow, wrist, and spine or as dental implant materials.The Ti6Al4V alloy is the most commonly used material in current implantology. It is characterized by good biocompatibility, high tensile strength and corrosion resistance, and relatively low Young’s modulus (~110 GPa) compared with currently used surgical metals [1]. Nevertheless, it has a high stiffness compared to human cortical bone (~20 GPa) [2, 3] which can cause stress shielding effect [4, 5]. Alloying elements, such as Al and V, are considered nonbeneficial to the human organism [6, 7]. For these reasons, more favourable titanium alloys (e.g., based on Nb, Ta, Zr, and Cr) with lower Young’s modulus have been developed and optimized [8–10]. Another problem with commonly used Ti6Al4V alloy is its relatively high coefficient of friction [1, 11]. This relates to the lower wear resistance, which may result in debris release. The released ions can activate the immune system [12], induce a local inflammatory reaction, or damage the bone structure, which in turn leads to long-term health problems or aseptic implant loosening [13–15].The longevity of the implant in the human body is influenced by the factors mentioned above. However, the tribological properties and surface hardness play the greatest role, especially in big load-bearing joint replacements. Surface treatment, such as nitriding, carburizing, and oxidation, can improve the wear resistance of Ti materials by forming a hard surface layer [16, 17]. Ti materials coated by a carbon-based nanolayer are very promising for joint’s replacements. These nanolayers are characterized as being biocompatible with excellent low friction properties, high hardness, and good wear resistance in comparison with Ti substrate. Many techniques are used for their deposition, such as chemical vapour deposition (CVD), plasma-enhanced chemical vapour deposition (PECVD), filtered cathode vacuum arc (FCVA), ion beam assisted deposition (IBAD) [18–23], and pulsed laser deposition (PLD) [24–26]. The adhesion of the carbon nanolayer onto the substrate, its microstructure, chemical composition, surface hardness, friction, and internal stress distribution can be improved by the optimization of the deposition conditions and ion bombardment during surface treatment [22, 27–31]. Nitrogen ion assistance leads to atomic mixing on the coating/substrate interface and to the formation of TiNx compounds in the modified zone. Newly formed compounds harden the substrate and significantly participate in the tribomechanical property enhancement of the coated material [32, 33].In this respect, the development of surface modifications aimed at the carbon-based materials bombarded with nitrogen ions is very promising for load-bearing applications. The role of this modifications for real applications needs to be examined in more detail.The purpose of this work is to characterize and test the Ti6Al4V alloy modified by ion beam assisted deposition of carbon-based nanolayer for finger joint replacements. This system is designed to improve the sliding properties of titanium alloy without risk of delamination known in thick diamond like carbon (DLC) coatings.


## 2. Materials and Methods

### 2.1. Specimens Preparation

The Ti6Al4V alloy containingα + β phase was used as a base material for the preparation of test specimens. The chemical composition of this alloy is shown in Table 1. Specimens in the form of a cylinder (20 mm in diameter and 8 mm in height) were cut from the titanium bar. The surface of each specimen was ground by a series of abrasive papers with grit of 150, 320, 500, 800, 1000, and 2000 and polished with diamond paste of 5 μm and 1 μm into the mirror like gloss (Ra = 0.02 μm) using a Leco machine. The substrates were ultrasonically cleaned in isopropyl alcohol for 20 minutes before the deposition process.Table 1
Chemical composition of Ti6Al4V alloy.
Element Content (wt%) Al 5.50–6.75 V 3.50–4.50 Fe 0.30 C 0.10 O 0.20 N 0.05 H 0.0125 Ti Balance


### 2.2. Deposition Process

The deposition of carbon-based nanolayer was performed by ion beam assisted deposition (IBAD). The specimen was placed in a holder positioned on a cooled rotary manipulator in a vacuum chamber. The chamber was evacuated and the work pressure was maintained at about5·10-3 Pa during deposition. The carbon nanolayer was deposited by the electron beam evaporation of a carbon target of high purity (99.9%) with sequential nitrogen ion bombardment. The acceleration voltage was 90 kV and the fluence of the implanted nitrogen ions was 1·1017 cm−2. The deposition rate was about 0.10 nm·s−1. Two groups of specimens with two different thicknesses were prepared. Approximate values of 20 nm (IBAD 20 nm) and 40 nm (IBAD 40 nm) have been determined. The control group contained specimens with carbon nanolayer without nitrogen ion bombardment (C 40 nm) and unmodified specimens (Ti6Al4V). A quartz thickness monitor located in the apparatus measured the thickness of the carbon-based nanolayer.


### 2.3. Characterizations of Treated Surface

The chemical composition of titanium surface modified with implanted nitrogen ions was measured by means of Auger electron spectroscopy (AES) in a PHI SAM 545 spectrometer. For excitation, an electron beam of 3 keV and 1μA, with a diameter of 40 μm, was used. Two symmetrically inclined Ar ion beams of 1 keV sputtered the specimens. For carbon, the sputtering rate is estimated to be 0.7 nm/min.The phase composition of titanium alloy modified by carbon nanolayer with nitrogen ion assistance was established by the X-ray diffraction (XRD) measurement using a PANalytical X’Pert PRO powder diffractometer. Cobalt radiation with a wavelength of 0.1789 nm and geometry with the parallel beam with an incident angle of 0.5° was used.Qualitative changes of carbon bonding structure after ion implantation were analysed by Raman spectroscopy. The Raman spectra were found using a Renishaw RM1000 Raman microscope with an Ar laser and excitation at 514.5 nm.The surface hardness of modified specimens (IBAD 20 nm, IBAD 40 nm, and C 40 nm) and unmodified specimens (Ti6Al4V) was measured by the nanoindentation method on a Hysitron TriboIndenter apparatus with a Berkovich diamond tip. Indents with 10μm separation in the matrix 3 × 4 were applied on each specimen. The maximum indentation force was 5000 μN. The partial load-unload function was used to measure the depth profile of the surface hardness. NanoScratch test method was used for a detection of adhesion behaviour of deposited nanolayer. Scratch testing was performed with conospherical diamond tip (angle 60° tip radius 1 μm). The tip was cleaned with ethanol. The normal forces in scratch testing were continuously increasing from 2 to 3000 μN. The scratch length was 10 μm and the scratching speed was 1 μm/1.5 s.The coefficient of friction was determined on a pin-on-disc tribometer equipped with a 100Cr6 steel ball of 6 mm diameter. Modified specimens (IBAD 20 nm and IBAD 40 nm) were compared with the Ti6Al4V reference specimens. The normal load during the test was 2 N with the velocity of 6 cm·s−1 and a radius of rotation of 4 mm.The distribution of contact pressure between the relatively rigid spherical part of the titanium joint and the much more flexible spherical cup made from polyetheretherketone (PEEK) was calculated by FEM (Finite Element Method, program Abaqus) analysis. Furthermore, the contact pressure was monitored as a function of the position in the cup, from centre to edge, for three values of the coefficient of friction (0.1–0.3).Sliding behaviour was investigated on a finger joint wear simulator (Figure1). For this purpose, the modified Ti6Al4V head (IBAD 40 nm) with a 10 mm diameter and a PEEK cup was used. The normal load of 100 N was applied during the test.Figure 1
Finger joint wear simulator: (a) wear testing component arrangement; (b) test detail.
(a) (b)


## 2.1. Specimens Preparation

The Ti6Al4V alloy containingα + β phase was used as a base material for the preparation of test specimens. The chemical composition of this alloy is shown in Table 1. Specimens in the form of a cylinder (20 mm in diameter and 8 mm in height) were cut from the titanium bar. The surface of each specimen was ground by a series of abrasive papers with grit of 150, 320, 500, 800, 1000, and 2000 and polished with diamond paste of 5 μm and 1 μm into the mirror like gloss (Ra = 0.02 μm) using a Leco machine. The substrates were ultrasonically cleaned in isopropyl alcohol for 20 minutes before the deposition process.Table 1
Chemical composition of Ti6Al4V alloy.
Element Content (wt%) Al 5.50–6.75 V 3.50–4.50 Fe 0.30 C 0.10 O 0.20 N 0.05 H 0.0125 Ti Balance


## 2.2. Deposition Process

The deposition of carbon-based nanolayer was performed by ion beam assisted deposition (IBAD). The specimen was placed in a holder positioned on a cooled rotary manipulator in a vacuum chamber. The chamber was evacuated and the work pressure was maintained at about5·10-3 Pa during deposition. The carbon nanolayer was deposited by the electron beam evaporation of a carbon target of high purity (99.9%) with sequential nitrogen ion bombardment. The acceleration voltage was 90 kV and the fluence of the implanted nitrogen ions was 1·1017 cm−2. The deposition rate was about 0.10 nm·s−1. Two groups of specimens with two different thicknesses were prepared. Approximate values of 20 nm (IBAD 20 nm) and 40 nm (IBAD 40 nm) have been determined. The control group contained specimens with carbon nanolayer without nitrogen ion bombardment (C 40 nm) and unmodified specimens (Ti6Al4V). A quartz thickness monitor located in the apparatus measured the thickness of the carbon-based nanolayer.


## 2.3. Characterizations of Treated Surface

The chemical composition of titanium surface modified with implanted nitrogen ions was measured by means of Auger electron spectroscopy (AES) in a PHI SAM 545 spectrometer. For excitation, an electron beam of 3 keV and 1μA, with a diameter of 40 μm, was used. Two symmetrically inclined Ar ion beams of 1 keV sputtered the specimens. For carbon, the sputtering rate is estimated to be 0.7 nm/min.The phase composition of titanium alloy modified by carbon nanolayer with nitrogen ion assistance was established by the X-ray diffraction (XRD) measurement using a PANalytical X’Pert PRO powder diffractometer. Cobalt radiation with a wavelength of 0.1789 nm and geometry with the parallel beam with an incident angle of 0.5° was used.Qualitative changes of carbon bonding structure after ion implantation were analysed by Raman spectroscopy. The Raman spectra were found using a Renishaw RM1000 Raman microscope with an Ar laser and excitation at 514.5 nm.The surface hardness of modified specimens (IBAD 20 nm, IBAD 40 nm, and C 40 nm) and unmodified specimens (Ti6Al4V) was measured by the nanoindentation method on a Hysitron TriboIndenter apparatus with a Berkovich diamond tip. Indents with 10μm separation in the matrix 3 × 4 were applied on each specimen. The maximum indentation force was 5000 μN. The partial load-unload function was used to measure the depth profile of the surface hardness. NanoScratch test method was used for a detection of adhesion behaviour of deposited nanolayer. Scratch testing was performed with conospherical diamond tip (angle 60° tip radius 1 μm). The tip was cleaned with ethanol. The normal forces in scratch testing were continuously increasing from 2 to 3000 μN. The scratch length was 10 μm and the scratching speed was 1 μm/1.5 s.The coefficient of friction was determined on a pin-on-disc tribometer equipped with a 100Cr6 steel ball of 6 mm diameter. Modified specimens (IBAD 20 nm and IBAD 40 nm) were compared with the Ti6Al4V reference specimens. The normal load during the test was 2 N with the velocity of 6 cm·s−1 and a radius of rotation of 4 mm.The distribution of contact pressure between the relatively rigid spherical part of the titanium joint and the much more flexible spherical cup made from polyetheretherketone (PEEK) was calculated by FEM (Finite Element Method, program Abaqus) analysis. Furthermore, the contact pressure was monitored as a function of the position in the cup, from centre to edge, for three values of the coefficient of friction (0.1–0.3).Sliding behaviour was investigated on a finger joint wear simulator (Figure1). For this purpose, the modified Ti6Al4V head (IBAD 40 nm) with a 10 mm diameter and a PEEK cup was used. The normal load of 100 N was applied during the test.Figure 1
Finger joint wear simulator: (a) wear testing component arrangement; (b) test detail.
(a) (b)


## 3. Results and Discussion

### 3.1. Chemical Composition

The results of the nitrogen depth distribution and elemental chemical composition of the surface area have been published in detail elsewhere [34]. The maximum concentration of nitrogen lies in the substrate matrix, overlaps partially with the mixing area nanolayer/substrate, and interferes with the carbon-based nanolayer. Minimal nitrogen enrichment of the carbon-based nanolayer was observed. High ion energy has caused nitrogen penetration through the nanolayer into the substrate. Nitrogen peak movement deeper into the specimen was observed with the increasing thickness of the nanolayer. Implanted nitrogen behind the carbon-based nanolayer penetrated the substrate in the modified projected range and modified longitudinal straggling, which causes an increase in the maximum nitrogen concentration from approx. 17.4±1.6 at% for specimens with a nanolayer 20 nm in thickness to approx. 18.9±1.9 at% for specimens with a nanolayer 40 nm in thickness. Oxygen contamination below 20 at% was detected in the narrow region on both the surface and nanolayer/substrate interface. The presence of oxygen on the nanolayer/substrate interface is likely caused by air exposure before the deposition process and by imperfect removal in the sputter cleaning.


### 3.2. Phase Composition

X-ray diffraction (XRD) method was used to determine the phase composition of the modified titanium alloy. Figure2 shows XRD spectra of modified specimens IBAD 20 nm and IBAD 40 nm. Nonstoichiometric TiNx phases, TiC, and graphite were detected in the surface area. The structural α-phase of the Ti6Al4V alloy was confirmed, but no β-phase was found in the diffraction pattern. The structural α-phase with incorporated nitrogen α-Ti(+N) was found. The α-Ti(+N) structural phase marks the hexagonal structure derived from the α-Ti phase, but with enlarged lattice parameters due to incorporation of nitrogen in interstitial sites of the Ti matrix [31]. The uneven dispersion of implanted nitrogen with a near-Gaussian distribution [35] induces a TiN and Ti(+N) mixture formation in the implanted region [31].Figure 2
XRD spectra of modified specimens.Nitrogen concentration profiles [34] indicate that the observed TiNx phase forms in the titanium matrix behind the carbon nanolayer. Results indicate the mixed area at the interface of carbon nanolayer and Ti6Al4V alloy due to ion bombardment. Formation of observed TiC compound is expected in this area. The new phases are located on the interface of titanium substrate/carbon-based nanolayer and the titanium sublayer. The results confirmed that the implanted nitrogen stabilizes the α-phase of the Ti6Al4V alloy [32, 33].


### 3.3. Raman Spectroscopy

Qualitative changes of carbon bonding structure after ion implantation were analysed by Raman spectroscopy. Figure3 shows Raman spectra of the carbon-based nanolayers deposited with assistance of nitrogen ions (IBAD 20 nm, IBAD 40 nm) and the spectrum of carbon nanolayer deposited without nitrogen ion bombardment (C 40 nm). The peak parameters are stated in Table 2. Consistent fits are achieved using a combination of three peaks. Peak 1 (1123–1150 cm−1) has responded to nanocrystalline or amorphous diamond fraction [36]. Peak 2 (1385–1402 cm−1), known as a D peak, demonstrates the presence of disordered graphitic carbon, and peak 3 (1565–1567 cm−1), the so-called G peak, belongs to crystalline graphitic carbon occurring in the nanostructure [30, 37]. The results show that ion bombardment during the deposition process increased peak intensity of Raman spectra for both thicknesses of carbon-based nanolayers. The ratio of the areas under the peaks increased due to nitrogen ion bombardment (Table 2). These results indicated that the high energy ion bombardment causes the graphitisation of carbon nanolayer for both applied thicknesses. According to Robertson’s theory [38], ion bombardment helps to form the binding hybridization of amorphous carbon and related materials. The formation of sp2/sp3 binding hybridization is related to the local density produced by ion bombardment at various conditions. Many researchers have confirmed that ion bombardment at low energies (tens and hundreds of eV) induces the formation of sp3 “diamond bonds” [39–41]. The high energy ion bombardment used here causes the accelerated nitrogen to penetrate into the titanium substrate. Part of this energy is dissipated in the atom displacements, and the rest of the energy is dissipated as phonons in due course [34]. Vlcak [29] demonstrated that 45 keV nitrogen ion bombardment modified the carbon bonds in defect sp2 and defect sp3 hybridization, resulting in graphitisation of the carbon. The conversion of sp3 bonds to sp2 bonds with increasing ion energy also confirmed Han et al. [42] and Wei et al. [43].Table 2
The results of Raman spectra.
Peak no. 1 2 3 Layer type Peak position(cm−1) Intensity(a.u.) Peak position(cm−1) Intensity(a.u.) Peak position(cm−1) Intensity(a.u.) RatioI(1 + 2)/I3 IBAD 20 nm 1127 ± 15 (0.818 ± 0.016)E6 1385 ± 16 (4.653 ± 0.044)E6 1565 ± 13 (1.629 ± 0.012)E6 3.36 IBAD 40 nm 1150 ± 16 (0.721 ± 0.008)E6 1402 ± 19 (4.577 ± 0.009)E6 1565 ± 12 (1.672 ± 0.010)E6 3.17 C 40 nm 1123 ± 11 (0.539 ± 0.006)E6 1394 ± 10 (4.286 ± 0.011)E6 1567 ± 18 (1.564 ± 0.009)E6 3.09Figure 3
Raman spectra of carbon-based nanolayers prepared by nitrogen ion beam assisted deposition (IBAD 20 nm; IBAD 40 nm) and carbon-based nanolayer without nitrogen ion bombardment (C 40 nm).


### 3.4. Surface Hardness

The resulting depth profiles of the indentation hardness are presented in Figure4. The depth profile results of the control specimen (Ti6Al4V) show an almost constant trend in comparison with the coated specimens. The hardness increase (HIT 5.5 ± 0.6 GPa) in the near surface region of the control specimen is caused by strengthening after mechanical polishing. The specimens modified by carbon nanolayer without nitrogen ion assistance (C 40 nm) have maximum hardness values HIT 6.8 ± 0.4 GPa. The specimens with carbon-based nanolayers deposited with the assistance of nitrogen ions (IBAD 20 nm, IBAD 40 nm) have comparable values. The maximum hardness is close to HIT 12.9 ± 0.8 GPa and HIT 12.8 ± 0.7 GPa for specimens IBAD 20 nm and IBAD 40 nm, respectively. Depth profiles are characterized by maximum values with a sharply decreasing trend approaching the hardness values of the control specimen. The influence of titanium alloy substrate is assumed near the interface with nanolayer. The nitrogen enrichment of titanium substrate together with the atomic mixing on the nanolayer/substrate interface led to the formation of hard TiNx and TiC compounds. The presence of these phases detected by XRD causes specimen hardening with a graphitic nanolayer on top the surface [18, 22]. The results clearly show that specimen C 40 nm has lower hardness in comparison with specimens IBAD 20 nm and IBAD 40 nm. Relatively low hardness of amorphous carbon is well known [44]. The specimens coated with the carbon nanolayers deposited with nitrogen ion bombardment show a hardness increase due to substrate hardening (nitriding, formation of new hard TiN and TiC compounds). The Raman spectra show graphitisation of carbon nanolayers (degradation) after ion implantation (IBAD 20 nm and IBAD 40 nm) which is in accordance with the literature [29, 38]. However, formation of new compound in the titanium alloy surface causes hardening of the substrate at the same time. Thus specimens IBAD 20 nm and IBAD 40 nm show higher hardness in comparison with specimen C 40 nm which is consistent with other results. Presented results indicated that high energy ion bombardment causes graphitisation of carbon nanolayer (lubricating layer) and surface hardening of the substrate.Figure 4
Depth profiles of the indentation hardness measurements.The comparable surface hardness of modified specimens IBAD 20 nm and IBAD 40 nm is given by applied fluence of implanted nitrogen. Applied fluence of implanted ions was1·1017 cm−2 in both types of specimens (IBAD 20 nm and IBAD 40 nm). Many researchers reported that surface hardness of nitrogen implanted titanium materials increases with increasing fluence [16, 33]. Presented results confirm character of hardening which is the formation of new compounds in the substrate due to nitrogen incorporation. Specimen C 40 nm shows approximately comparable hardness with the substrate. Very low thickness of carbon-based nanolayer is on the detection limit of the nanoindentation method. Therefore, hardness profiles in Figure 4 mainly reflect the structural changes in the substrate.


### 3.5. Adhesion

The adhesion of carbon-based nanolayers to a substrate was investigated by nanoscratch testing. Figure5 presents the typical trends of the scratch force according to the lateral displacement of the tip for the specimens coated by carbon-based nanolayers with ion bombardment (IBAD 20 nm and IBAD 40 nm) and for the specimen coated by a carbon nanolayer without ion bombardment (C 40 nm). The scratch force increases with increasing lateral displacement. A comparison of the curves in Figure 5 shows that the scratch force for the same lateral displacement value is greater for specimen C 40 nm. This indicates easier penetration of the tip into the material which is in agreement with the presented hardness results. The specimens coated by a carbon-based nanolayer with ion bombardment (IBAD 20 nm and IBAD 40 nm) show similar trends. A comparable behaviour is given by a character of substrate hardening. A smooth course of the scratch force along the lateral displacement is observed on specimens coated by carbon-based nanolayers with ion bombardment, while the course of the scratch force on the specimen coated by a carbon nanolayer without ion assistance shows step decrease in the scratch force. The visible jumps (curve discontinuities) indicate delamination of the carbon nanolayer. It is confirmed by the scans of scratches of the tested specimens (Figure 6). The carbon-based nanolayers deposited with ion bombardment show no signs of delamination. It can be assumed that the ion bombardment improved the adhesion of the nanolayers.Figure 5
The trend of the scratch force according to the lateral displacement of the tip.Figure 6
Images of specimen surface after nanoscratch test.


### 3.6. Coefficient of Friction

Figure7 shows the dependence of the coefficient of friction on the number of cycles for the coated specimens (IBAD 20 nm, IBAD 40 nm) and for the control substrate (Ti6Al4V). The lubrication effect of carbon-based nanolayer on Ti6Al4V alloy is demonstrated. The two surface modifications IBAD 40 nm and IBAD 20 nm have comparable coefficient of friction values of 0.106 ± 0.003 and 0.104 ± 0.005, respectively. Carbon-based nanolayers of both thicknesses show much lower coefficient of friction versus the coefficient of friction of 0.635 ± 0.139 for control Ti6Al4V substrate. A thicker nanolayer (IBAD 40 nm) increased the duration of the lubrication effect by more than three times compared to a thinner nanolayer (IBAD 20 nm). The achieved results are consistent with the results of other research works [22, 45]. Step increasing in the coefficient of friction implies the failure of the thin carbon-based nanolayer on specimens IBAD 20 nm and IBAD 40 nm. However, the coefficient of friction does not reach the value of unmodified substrate as in the case of specimen C 40 nm. Hardened substrate by nitrogen implantation poses friction resistant surface with low friction coefficient, typical for nitrogen ion implanted titanium materials. Gordin et al. [46] observed on nitrogen implanted Ti-Nb-Ta titanium alloy comparable value of coefficient of friction of about 0.3.Figure 7
Coefficient of friction versus the number of cycles for modified specimens (IBAD 20 nm, IBAD 40 nm) in comparison with coated specimen without ion bombardment (C 40 nm) and unmodified control specimen (Ti6Al4V).


### 3.7. Contact Pressure Distribution and Joint Wear Simulation

The distribution of contact pressure was calculated by FEM analysis using the Abaqus program. Figure8 shows a 3D model of the finger joint with contact pressure distribution (the head (Ti6Al4V) and the cup (PEEK)). The simulation was performed with load force F = 100 N and coefficient of friction μ = 0.1. The maximum contact pressure of about 4 MPa was found in the deepest point of the cup under the ideal geometrical shape of the head and cup. Values vary from 0 MPa (around the perimeter of the cup, contact angle of 90°) to pmax⁡~4 MPa (at the deepest point of the cup). Figure 9 presents the evolution of contact pressure in the cup in dependence on the contact angle for different values of the coefficient of friction. It is evident that the friction coefficient values affect the course of the contact pressure. The contact pressure varies in dependence on coefficient of friction up to the contact angle of approx. 25° (i.e., in the centre of the cup). Maximum contact pressure decreases with increasing coefficient of friction. Lower values of contact pressure, however, do not mean lower contact stress or transmission of less force. For the higher coefficient of friction, the force transmission is realised mainly through shear stresses instead of normal stresses.Figure 8
Contact pressure distribution between the PEEK cup (a) and Ti6Al4V head (b) simulated by FEM analysis using the Abaqus program.
(a) (b)Figure 9
The calculated contact pressure distribution inside the cup of joint: (a) evaluated trajectory, red arrow; (b) the dependence of contact pressure on the contact angle for different value of coefficients of friction.
(a) (b)The joint wear simulator (Figure1) was used for wear evaluation of the Ti6Al4V alloy head modified by carbon-based nanolayer (IBAD 40 nm). The experimental model of a finger joint replacement, the head from modified Ti6Al4V, and the cup from PEEK were used. The appearance of component surfaces tested by sliding test was evaluated qualitatively. The Ti6Al4V head without a modified surface was used as a control. Enormous wear of the head and cup after 10,000 cycles in comparison with the modified Ti6Al4V head is evident (Figure 10). The first wear signs of the IBAD 40 nm nanolayer were observed after 240,000 cycles and were detected only in a local area (Figure 11). More extensive wear occurred after 510,000 cycles.Figure 10
Unmodified Ti6Al4V head and the cup after 10,000 cycles.Figure 11
First local wear fault of the IBAD 40 nm modification after 240,000 cycles.


## 3.1. Chemical Composition

The results of the nitrogen depth distribution and elemental chemical composition of the surface area have been published in detail elsewhere [34]. The maximum concentration of nitrogen lies in the substrate matrix, overlaps partially with the mixing area nanolayer/substrate, and interferes with the carbon-based nanolayer. Minimal nitrogen enrichment of the carbon-based nanolayer was observed. High ion energy has caused nitrogen penetration through the nanolayer into the substrate. Nitrogen peak movement deeper into the specimen was observed with the increasing thickness of the nanolayer. Implanted nitrogen behind the carbon-based nanolayer penetrated the substrate in the modified projected range and modified longitudinal straggling, which causes an increase in the maximum nitrogen concentration from approx. 17.4±1.6 at% for specimens with a nanolayer 20 nm in thickness to approx. 18.9±1.9 at% for specimens with a nanolayer 40 nm in thickness. Oxygen contamination below 20 at% was detected in the narrow region on both the surface and nanolayer/substrate interface. The presence of oxygen on the nanolayer/substrate interface is likely caused by air exposure before the deposition process and by imperfect removal in the sputter cleaning.


## 3.2. Phase Composition

X-ray diffraction (XRD) method was used to determine the phase composition of the modified titanium alloy. Figure2 shows XRD spectra of modified specimens IBAD 20 nm and IBAD 40 nm. Nonstoichiometric TiNx phases, TiC, and graphite were detected in the surface area. The structural α-phase of the Ti6Al4V alloy was confirmed, but no β-phase was found in the diffraction pattern. The structural α-phase with incorporated nitrogen α-Ti(+N) was found. The α-Ti(+N) structural phase marks the hexagonal structure derived from the α-Ti phase, but with enlarged lattice parameters due to incorporation of nitrogen in interstitial sites of the Ti matrix [31]. The uneven dispersion of implanted nitrogen with a near-Gaussian distribution [35] induces a TiN and Ti(+N) mixture formation in the implanted region [31].Figure 2
XRD spectra of modified specimens.Nitrogen concentration profiles [34] indicate that the observed TiNx phase forms in the titanium matrix behind the carbon nanolayer. Results indicate the mixed area at the interface of carbon nanolayer and Ti6Al4V alloy due to ion bombardment. Formation of observed TiC compound is expected in this area. The new phases are located on the interface of titanium substrate/carbon-based nanolayer and the titanium sublayer. The results confirmed that the implanted nitrogen stabilizes the α-phase of the Ti6Al4V alloy [32, 33].


## 3.3. Raman Spectroscopy

Qualitative changes of carbon bonding structure after ion implantation were analysed by Raman spectroscopy. Figure3 shows Raman spectra of the carbon-based nanolayers deposited with assistance of nitrogen ions (IBAD 20 nm, IBAD 40 nm) and the spectrum of carbon nanolayer deposited without nitrogen ion bombardment (C 40 nm). The peak parameters are stated in Table 2. Consistent fits are achieved using a combination of three peaks. Peak 1 (1123–1150 cm−1) has responded to nanocrystalline or amorphous diamond fraction [36]. Peak 2 (1385–1402 cm−1), known as a D peak, demonstrates the presence of disordered graphitic carbon, and peak 3 (1565–1567 cm−1), the so-called G peak, belongs to crystalline graphitic carbon occurring in the nanostructure [30, 37]. The results show that ion bombardment during the deposition process increased peak intensity of Raman spectra for both thicknesses of carbon-based nanolayers. The ratio of the areas under the peaks increased due to nitrogen ion bombardment (Table 2). These results indicated that the high energy ion bombardment causes the graphitisation of carbon nanolayer for both applied thicknesses. According to Robertson’s theory [38], ion bombardment helps to form the binding hybridization of amorphous carbon and related materials. The formation of sp2/sp3 binding hybridization is related to the local density produced by ion bombardment at various conditions. Many researchers have confirmed that ion bombardment at low energies (tens and hundreds of eV) induces the formation of sp3 “diamond bonds” [39–41]. The high energy ion bombardment used here causes the accelerated nitrogen to penetrate into the titanium substrate. Part of this energy is dissipated in the atom displacements, and the rest of the energy is dissipated as phonons in due course [34]. Vlcak [29] demonstrated that 45 keV nitrogen ion bombardment modified the carbon bonds in defect sp2 and defect sp3 hybridization, resulting in graphitisation of the carbon. The conversion of sp3 bonds to sp2 bonds with increasing ion energy also confirmed Han et al. [42] and Wei et al. [43].Table 2
The results of Raman spectra.
Peak no. 1 2 3 Layer type Peak position(cm−1) Intensity(a.u.) Peak position(cm−1) Intensity(a.u.) Peak position(cm−1) Intensity(a.u.) RatioI(1 + 2)/I3 IBAD 20 nm 1127 ± 15 (0.818 ± 0.016)E6 1385 ± 16 (4.653 ± 0.044)E6 1565 ± 13 (1.629 ± 0.012)E6 3.36 IBAD 40 nm 1150 ± 16 (0.721 ± 0.008)E6 1402 ± 19 (4.577 ± 0.009)E6 1565 ± 12 (1.672 ± 0.010)E6 3.17 C 40 nm 1123 ± 11 (0.539 ± 0.006)E6 1394 ± 10 (4.286 ± 0.011)E6 1567 ± 18 (1.564 ± 0.009)E6 3.09Figure 3
Raman spectra of carbon-based nanolayers prepared by nitrogen ion beam assisted deposition (IBAD 20 nm; IBAD 40 nm) and carbon-based nanolayer without nitrogen ion bombardment (C 40 nm).


## 3.4. Surface Hardness

The resulting depth profiles of the indentation hardness are presented in Figure4. The depth profile results of the control specimen (Ti6Al4V) show an almost constant trend in comparison with the coated specimens. The hardness increase (HIT 5.5 ± 0.6 GPa) in the near surface region of the control specimen is caused by strengthening after mechanical polishing. The specimens modified by carbon nanolayer without nitrogen ion assistance (C 40 nm) have maximum hardness values HIT 6.8 ± 0.4 GPa. The specimens with carbon-based nanolayers deposited with the assistance of nitrogen ions (IBAD 20 nm, IBAD 40 nm) have comparable values. The maximum hardness is close to HIT 12.9 ± 0.8 GPa and HIT 12.8 ± 0.7 GPa for specimens IBAD 20 nm and IBAD 40 nm, respectively. Depth profiles are characterized by maximum values with a sharply decreasing trend approaching the hardness values of the control specimen. The influence of titanium alloy substrate is assumed near the interface with nanolayer. The nitrogen enrichment of titanium substrate together with the atomic mixing on the nanolayer/substrate interface led to the formation of hard TiNx and TiC compounds. The presence of these phases detected by XRD causes specimen hardening with a graphitic nanolayer on top the surface [18, 22]. The results clearly show that specimen C 40 nm has lower hardness in comparison with specimens IBAD 20 nm and IBAD 40 nm. Relatively low hardness of amorphous carbon is well known [44]. The specimens coated with the carbon nanolayers deposited with nitrogen ion bombardment show a hardness increase due to substrate hardening (nitriding, formation of new hard TiN and TiC compounds). The Raman spectra show graphitisation of carbon nanolayers (degradation) after ion implantation (IBAD 20 nm and IBAD 40 nm) which is in accordance with the literature [29, 38]. However, formation of new compound in the titanium alloy surface causes hardening of the substrate at the same time. Thus specimens IBAD 20 nm and IBAD 40 nm show higher hardness in comparison with specimen C 40 nm which is consistent with other results. Presented results indicated that high energy ion bombardment causes graphitisation of carbon nanolayer (lubricating layer) and surface hardening of the substrate.Figure 4
Depth profiles of the indentation hardness measurements.The comparable surface hardness of modified specimens IBAD 20 nm and IBAD 40 nm is given by applied fluence of implanted nitrogen. Applied fluence of implanted ions was1·1017 cm−2 in both types of specimens (IBAD 20 nm and IBAD 40 nm). Many researchers reported that surface hardness of nitrogen implanted titanium materials increases with increasing fluence [16, 33]. Presented results confirm character of hardening which is the formation of new compounds in the substrate due to nitrogen incorporation. Specimen C 40 nm shows approximately comparable hardness with the substrate. Very low thickness of carbon-based nanolayer is on the detection limit of the nanoindentation method. Therefore, hardness profiles in Figure 4 mainly reflect the structural changes in the substrate.


## 3.5. Adhesion

The adhesion of carbon-based nanolayers to a substrate was investigated by nanoscratch testing. Figure5 presents the typical trends of the scratch force according to the lateral displacement of the tip for the specimens coated by carbon-based nanolayers with ion bombardment (IBAD 20 nm and IBAD 40 nm) and for the specimen coated by a carbon nanolayer without ion bombardment (C 40 nm). The scratch force increases with increasing lateral displacement. A comparison of the curves in Figure 5 shows that the scratch force for the same lateral displacement value is greater for specimen C 40 nm. This indicates easier penetration of the tip into the material which is in agreement with the presented hardness results. The specimens coated by a carbon-based nanolayer with ion bombardment (IBAD 20 nm and IBAD 40 nm) show similar trends. A comparable behaviour is given by a character of substrate hardening. A smooth course of the scratch force along the lateral displacement is observed on specimens coated by carbon-based nanolayers with ion bombardment, while the course of the scratch force on the specimen coated by a carbon nanolayer without ion assistance shows step decrease in the scratch force. The visible jumps (curve discontinuities) indicate delamination of the carbon nanolayer. It is confirmed by the scans of scratches of the tested specimens (Figure 6). The carbon-based nanolayers deposited with ion bombardment show no signs of delamination. It can be assumed that the ion bombardment improved the adhesion of the nanolayers.Figure 5
The trend of the scratch force according to the lateral displacement of the tip.Figure 6
Images of specimen surface after nanoscratch test.


## 3.6. Coefficient of Friction

Figure7 shows the dependence of the coefficient of friction on the number of cycles for the coated specimens (IBAD 20 nm, IBAD 40 nm) and for the control substrate (Ti6Al4V). The lubrication effect of carbon-based nanolayer on Ti6Al4V alloy is demonstrated. The two surface modifications IBAD 40 nm and IBAD 20 nm have comparable coefficient of friction values of 0.106 ± 0.003 and 0.104 ± 0.005, respectively. Carbon-based nanolayers of both thicknesses show much lower coefficient of friction versus the coefficient of friction of 0.635 ± 0.139 for control Ti6Al4V substrate. A thicker nanolayer (IBAD 40 nm) increased the duration of the lubrication effect by more than three times compared to a thinner nanolayer (IBAD 20 nm). The achieved results are consistent with the results of other research works [22, 45]. Step increasing in the coefficient of friction implies the failure of the thin carbon-based nanolayer on specimens IBAD 20 nm and IBAD 40 nm. However, the coefficient of friction does not reach the value of unmodified substrate as in the case of specimen C 40 nm. Hardened substrate by nitrogen implantation poses friction resistant surface with low friction coefficient, typical for nitrogen ion implanted titanium materials. Gordin et al. [46] observed on nitrogen implanted Ti-Nb-Ta titanium alloy comparable value of coefficient of friction of about 0.3.Figure 7
Coefficient of friction versus the number of cycles for modified specimens (IBAD 20 nm, IBAD 40 nm) in comparison with coated specimen without ion bombardment (C 40 nm) and unmodified control specimen (Ti6Al4V).


## 3.7. Contact Pressure Distribution and Joint Wear Simulation

The distribution of contact pressure was calculated by FEM analysis using the Abaqus program. Figure8 shows a 3D model of the finger joint with contact pressure distribution (the head (Ti6Al4V) and the cup (PEEK)). The simulation was performed with load force F = 100 N and coefficient of friction μ = 0.1. The maximum contact pressure of about 4 MPa was found in the deepest point of the cup under the ideal geometrical shape of the head and cup. Values vary from 0 MPa (around the perimeter of the cup, contact angle of 90°) to pmax⁡~4 MPa (at the deepest point of the cup). Figure 9 presents the evolution of contact pressure in the cup in dependence on the contact angle for different values of the coefficient of friction. It is evident that the friction coefficient values affect the course of the contact pressure. The contact pressure varies in dependence on coefficient of friction up to the contact angle of approx. 25° (i.e., in the centre of the cup). Maximum contact pressure decreases with increasing coefficient of friction. Lower values of contact pressure, however, do not mean lower contact stress or transmission of less force. For the higher coefficient of friction, the force transmission is realised mainly through shear stresses instead of normal stresses.Figure 8
Contact pressure distribution between the PEEK cup (a) and Ti6Al4V head (b) simulated by FEM analysis using the Abaqus program.
(a) (b)Figure 9
The calculated contact pressure distribution inside the cup of joint: (a) evaluated trajectory, red arrow; (b) the dependence of contact pressure on the contact angle for different value of coefficients of friction.
(a) (b)The joint wear simulator (Figure1) was used for wear evaluation of the Ti6Al4V alloy head modified by carbon-based nanolayer (IBAD 40 nm). The experimental model of a finger joint replacement, the head from modified Ti6Al4V, and the cup from PEEK were used. The appearance of component surfaces tested by sliding test was evaluated qualitatively. The Ti6Al4V head without a modified surface was used as a control. Enormous wear of the head and cup after 10,000 cycles in comparison with the modified Ti6Al4V head is evident (Figure 10). The first wear signs of the IBAD 40 nm nanolayer were observed after 240,000 cycles and were detected only in a local area (Figure 11). More extensive wear occurred after 510,000 cycles.Figure 10
Unmodified Ti6Al4V head and the cup after 10,000 cycles.Figure 11
First local wear fault of the IBAD 40 nm modification after 240,000 cycles.


## 4. Conclusion

The carbon-based nanolayer with nitrogen ion assistance was deposited by IBAD method on the Ti6Al4V substrate. The proposed surface treatment of the titanium alloy, in two thickness variants, leads to an improvement of tribomechanical properties. The formation of TiNx and TiC compounds in the modified surface area was found. Nitrogen ion bombardment had a more positive effect on higher values of indentation hardness than the layer deposited without ion bombardment. The larger thickness of carbon-based nanolayer improves friction test duration, but no influence on surface hardness was observed. The proposed surface modification (IBAD 40 nm) of the Ti6Al4V joint head provides functional surface protection with a resulting reduction in wear and significant increase in lifetime. This modification of the titanium surface is very promising for biomedical application, especially in an area of load-bearing joint replacements.



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*Source: 3749309-2018-05-20.xml*