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Tribological Performance of CoCrMo Alloys with Boron Additions in As-Cast and Heat-Treated Conditions

: The present study evaluates the effect of boron additions on the tribological performance of CoCrMo alloys. The alloys were prepared with boron ranging from 0.06 to 1 wt%. The materials were characterized using metallographic techniques, scanning electronic microscopy, and roughness and hardness tests. Tribological evaluation was made by means of ball-on-disc tests for sliding distances of 4, 8 and 12 km. The samples were in the as-cast condition and after a heat treatment at 1200 ◦ C for 1 h, ﬁnished by water quenching. The results showed that wear resistance was inﬂuenced by the microstructure and the number of secondary phases. The volume loss decreased as the boron content increased. Due to hard phases, abrasion wear was observed. Delamination fatigue was also detected after long sliding distances. Both wear mechanisms diminished in higher boron content alloys.


Introduction
CoCrMo alloys are widely used in artificial joints due to their high wear and corrosion resistance [1][2][3]. The clinical use of these alloys for long periods of time has shown good biocompatibility in bulk form [4]. The alloy ASTM F799, i.e., the wrought version of ASTM F75, is currently the most frequently used alloy in structural materials for permanent implants at load-bearing sites, such as artificial joints, and is intended to provide at least 20 years of service [1]. However, medical concerns exist due to metal ion release and material loss caused by tribocorrosion [5,6]. Wear debris and corrosion products have resulted in adverse local tissue reactions and implant retrieval and replacement [1,6,7]. The metal particles are generally very small (in the order of nanometers) and together provide a large surface area that can simplify the reaction with the medium [6,8,9]. Studies have been carried out to understand and improve this performance.
The typical microstructure in the casting condition of a cobalt base alloy presents a dendritic α-FCC matrix metastable at room temperature, and precipitates composed mainly of block carbides M23C6 appearing in interdendritic regions and grain boundaries [10][11][12]. Coarse block carbides act as dislocation anchors and stacking faults when the material is subjected to mechanical loads although, they can also lead to fragility along the grain boundary [12][13][14][15]. A better performance in wear resistance has been found for alloys with high carbon content [5,[16][17][18]. In addition, studies reported that a fine carbide distribution and fine grain size also enhanced the wear performance [16,19]. Although carbides are essential to strengthen CoCrMo alloys, they are also detrimental to the materials due to detachment from the matrix which leads to abrasive wear [6]. Research reported that carbides would be torn from the matrix during the tribocorrosion process due to the preferential dissolution of the boundary area under the action of galvanic corrosion and tribological contact [20].
The effect of boron in different cobalt-based alloys has been reported. In cobaltboron alloys microstructure refinement of columnar grains was observed due to boron additions [21]. Boron additions in the range of 0.09-1.48 wt% to a heat-resistant Co-based alloy found an important reduction in the incubation time of carbides, refinement of primary phases for small boron amounts, and metallic borides for larger contents [22]. Studies reported that the formation of borides around the grain boundaries improved the bond strength among the grains [23,24]; with 0.05 atom % of boron the strengthening increased creep resistance [23]. It was also observed that boron content higher than 0.04% in an atom reduced yield strength at room temperature due to precipitate-depleted zones around grain boundaries [23,24]. These detrimental zones were eliminated by heat treatment [24]. It was reported for a CoCrMo alloy with nickel additions and traces of aluminum, titanium, and boron that mechanical properties were improved [25]. This alloy also exhibited improved fatigue resistance due to the presence of Ni and the elimination of microstructural casting defects caused by trace elements [26]. Boronizing CoCrMo alloys at high temperatures formed a coating of metallic borides at the surface that improved the wear resistance due to the high surface hardness [27,28]. Regardless of this, a reduction in the corrosion resistance was reported [29]. A study in as-cast CoCrMo alloys with boron contents of 0.28, 0.61 and 0.98 wt% found important changes in the microstructure due to this element that increased the secondary phase content; wear resistance of these alloys evaluated in ball-on-disc tests increased as the boron content increased [30].
In summary, CoCrMo alloys present important advantages for their use in artificial joints; nevertheless, there are still issues due to metal ion release and material loss. The state of the art about the influence of boron on different cobalt-based alloys has been presented. In the present study, the effect of boron in the wear resistance of a CoCrMo biocompatible alloy was evaluated under as-cast and heat-treated conditions. These alloys were previously evaluated in corrosion and fatigue resistance [31,32].

Materials
The cobalt-based alloys studied were obtained by investment casting. The chemical composition specified in ASTM F75 was used as a reference and boron was added in 0.06, 0.25, 0.5 and 1% by weight, as shown in Table 1. The samples were studied in the as-cast condition and after a heat treatment. The heat treatment consisted of 1 h at 1200 • C followed by water quenching. The identification of alloys is showed in Table 2. The microstructure of the alloys was characterized by means of scanning electron microscopy (SEM) in a JEOL JSM-6510LV (Tokyo, Japan). Hardness was measured on an INCOR TH320 hardness tester. Microhardness was assessed with a SHIMADZU HMV. The identification of phases was performed by X-ray diffraction; results were presented in a previous study [31]. The volume fraction of the HCP phase in the alloys was quantitatively calculated according to Equation (1), using the method of Sage and Guillaud [33].

Tribological Tests
Tribological tests were developed in a ball-on-disc tribometer, as shown in Figure 1. The balls used were of zirconium oxide (95% purity stabilized with Y 2 O 3 ) and had a 10 mm diameter. The CoCrMo samples were discs of a 35 mm diameter with a 10 mm thickness. The surfaces to be evaluated were polished to a mirror finish by standard metallographic procedures. Prior to the tribological tests, the roughness (Ra) was measured using a SURFCOM 1500SD2 profilometer. During ball-on-disc tests, a load of 60 N was applied on the ball which corresponded to 1.81 GPa of maximum Hertzian contact pressure. A ringer solution was used as a lubricant (8.6 g of NaCl, 0.3 g of KCl and 0.33 g of CaCl 2 per liter of distilled water). The tests were carried out at 314 mm/s for sliding distances of 4, 8 and 12 km. These high contact pressure and long sliding distances were chosen to achieve severe wear conditions. Three samples for every condition were evaluated. The coefficient of friction was measured every 200 m; it is presented as an average at each point. After the ball-on-disc tests, the samples were ultrasonically cleaned in acetone for 10 min. The volumetric wear was calculated through wear track by measuring the profiles in different zones using the profilometer. The wear tracks on the specimens were also analyzed by SEM.
in a previous study [31]. The volume fraction of the HCP phase in the alloys was tatively calculated according to Equation (1), using the method of Sage and Guilla HCP wt% I 101 1 I 101 1 1

.5 I 200
where HCP (wt%) is the fraction of martensite in weight percentage and I(200) and are the integrated intensities of the austenite (200) and martensite (101 1) peaks, tively.

Tribological Tests
Tribological tests were developed in a ball-on-disc tribometer, as shown in F The balls used were of zirconium oxide (95% purity stabilized with Y2O3) and h mm diameter. The CoCrMo samples were discs of a 35 mm diameter with a 10 mm ness. The surfaces to be evaluated were polished to a mirror finish by standard m graphic procedures. Prior to the tribological tests, the roughness (Ra) was measure a SURFCOM 1500SD2 profilometer. During ball-on-disc tests, a load of 60 N was on the ball which corresponded to 1.81 GPa of maximum Hertzian contact pres ringer solution was used as a lubricant (8.6 g of NaCl, 0.3 g of KCl and 0.33 g of Ca liter of distilled water). The tests were carried out at 314 mm/s for sliding distance and 12 km. These high contact pressure and long sliding distances were chosen to severe wear conditions. Three samples for every condition were evaluated. The coe of friction was measured every 200 m; it is presented as an average at each poin the ball-on-disc tests, the samples were ultrasonically cleaned in acetone for 10 m volumetric wear was calculated through wear track by measuring the profiles in d zones using the profilometer. The wear tracks on the specimens were also analy SEM.

Microstructure
The microstructures of the alloys are presented in Figures 2 and 3 for the as-c heat-treated conditions, respectively. In the as-cast alloys, a change in the morpho secondary phases can be observed, along with the increase in boron content. T treatment promoted a globular shape in precipitates and their even distribution structure. The identification of current phases in these alloys by X-ray diffraction w sented in a previous study [31].

Microstructure
The microstructures of the alloys are presented in Figures 2 and 3 for the as-cast and heat-treated conditions, respectively. In the as-cast alloys, a change in the morphology of secondary phases can be observed, along with the increase in boron content. The heat treatment promoted a globular shape in precipitates and their even distribution in the structure. The identification of current phases in these alloys by X-ray diffraction was presented in a previous study [31].   Table 3 presents the amount of HCP phase in the alloys according to the Sage and Guillaud method [33]. In the reference material, the alloy without boron, a decrement in HCP volume fraction after heat treatment was observed, compared with the as-cast condition. This effect was also observed in the very low content alloys, the 0.06B. However, in the 0.25B alloys, the trend changed and after heat treatment the HCP volume fraction increased; this increment was more evident in the 0.5B and 1B alloys. It is worth noting that in the as-cast alloys, higher boron contents diminished the HCP volume fraction; it is also more clearly observed in higher boron contents, 0.5B-AC and 1B-AC.    Table 3 presents the amount of HCP phase in the alloys according to the Sage and Guillaud method [33]. In the reference material, the alloy without boron, a decrement in HCP volume fraction after heat treatment was observed, compared with the as-cast condition. This effect was also observed in the very low content alloys, the 0.06B. However, in the 0.25B alloys, the trend changed and after heat treatment the HCP volume fraction increased; this increment was more evident in the 0.5B and 1B alloys. It is worth noting that in the as-cast alloys, higher boron contents diminished the HCP volume fraction; it is also more clearly observed in higher boron contents, 0.5B-AC and 1B-AC.   Table 3 presents the amount of HCP phase in the alloys according to the Sage and Guillaud method [33]. In the reference material, the alloy without boron, a decrement in HCP volume fraction after heat treatment was observed, compared with the as-cast condition. This effect was also observed in the very low content alloys, the 0.06B. However, in the 0.25B alloys, the trend changed and after heat treatment the HCP volume fraction increased; this increment was more evident in the 0.5B and 1B alloys. It is worth noting that in the as-cast alloys, higher boron contents diminished the HCP volume fraction; it is also more clearly observed in higher boron contents, 0.5B-AC and 1B-AC.

Hardness and Roughness
In Table 4, the hardness, microhardness and roughness of the alloys is presented. In the as-cast alloys, the HRC values increased along with boron content. This was attributed to the increment of hard phase precipitation due to boron. Studies reported for CoCrMo alloys that heat treatment at high temperatures (1200-1350 • C) dissolved carbides into the matrix which reduced the hardness in the material [10,19]. In the present study, this was observed in the alloy without boron. However, in alloys with some boron content the hardness increased after heat treatment due to the enrichment of the secondary phases and the higher hardness of borides than carbides. This can be noticed in the Vickers Hardness (HV) of microstructural components (Table 4); the matrix hardness decreased after heat treatment while the secondary phases hardened. It was also observed that the precipitate hardness increased with boron content and with heat treatment. The roughness measurements show the influence of boron in surface features, as shown in Table 4. The 0.06B-AC alloy presented a lower roughness than the as-cast alloy without boron. This could be due to the elimination of casting defects caused by the small addition of the element, as reported for trace elements [26]. Alloys with higher boron content exhibited higher roughness, up to 0.044 µm in the 1B-AC alloy. The high roughness could be related to the amount of precipitates present in higher boron content alloys. The heat treatments diminished the roughness with regard to the as-cast condition, which was probably caused by the homogenization of these secondary phases. Figure 4 shows the friction coefficient obtained during the ball-on-disc tests. No direct relationship between the roughness values and friction was observed. In the as-cast condition, the 0.06B-AC alloy, that exhibited the lowest roughness, also showed one of the highest friction coefficients. The 0.25B-AC and 0.5B-AC alloys had comparable Ra, but their friction coefficient was not similar. The 0.5B-AC alloy showed the lowest friction coefficient while in the 0.5B-HT the largest one was observed; the 0.5B-AC had higher roughness than the 0.5B-HT. The friction coefficient could be related to the wear mechanisms that acted at the different stages of the tribological tests; Section 3.4 presents the surface analysis. Figure 5 presents the volumetric wear measured according to material condition, boron content and the sliding distance. In as-cast condition, a high volumetric wear can be observed in the 0B-AC alloy, especially after 12 km. For this alloy without boron, the heat treatment improved its wear resistance, particularly in the long sliding distance where a reduction of 60% was observed; for 4 and 8 km the volumetric wear was similar to the as-cast condition. The volume loss considerably decreased with the increment in boron content in the as-cast condition alloys, as previously reported [30]. For heat-treated alloys, the volume wear loss was in general comparable to that in the as-cast condition.   Figure 5 presents the volumetric wear measured according to material condition, boron content and the sliding distance. In as-cast condition, a high volumetric wear can be observed in the 0B-AC alloy, especially after 12 km. For this alloy without boron, the heat treatment improved its wear resistance, particularly in the long sliding distance where a reduction of 60% was observed; for 4 and 8 km the volumetric wear was similar to the ascast condition. The volume loss considerably decreased with the increment in boron content in the as-cast condition alloys, as previously reported [30]. For heat-treated alloys, the volume wear loss was in general comparable to that in the as-cast condition. In the present study, the influence of friction coefficient or roughness on the wear resistance was not observed. The alloys containing 1%B exhibited high values in these features but also presented high wear resistance; whereas, the 0B-AC alloy presented low roughness and friction coefficient with high wear. It was previously reported that there is good wear resistance for samples with high roughness [16]. Previous investigations re- In the present study, the influence of friction coefficient or roughness on the wear resistance was not observed. The alloys containing 1%B exhibited high values in these features but also presented high wear resistance; whereas, the 0B-AC alloy presented low roughness and friction coefficient with high wear. It was previously reported that there is good wear resistance for samples with high roughness [16]. Previous investigations reported enhanced wear behavior for grain refinement and globular carbides evenly distributed [16,19,34,35]. In the present study, the boron in the alloys homogenized microstructures, promoting an even distribution of hard precipitates, which led to improved wear resistance. Even a small addition of this element had influence, as observed in the studies regarding these alloys to corrosion and fatigue resistance [31,32].

Surface Analysis
The surface analysis after the tribological test found abrasion to be the main wear mechanism. It was caused by fractured and detached precipitates, which are harder than the matrix. Figure 6 presents the wear tracks of some samples where the holes of those pulled out secondary phases from base material can be observed. Figure 7 shows a higher magnification of broken precipitates. In Figure 8, grooves of abrasive wear in different samples are observed. Abrasion caused by carbide detachment has been widely reported [19,20,35,36]. Some studies have even suggested that alloys with lower carbon and carbide content present better wear resistance, since abrasion is reduced and alloys are more prone to strain-induced martensitic transformation [36,37]. In the present study, the carbides dropped off and abrasion grooves were more noticeable in samples without boron and up to 0.25% of this element. In alloys with 0.5 and 1%B, the precipitates were larger and harder, and this phenomenon was less frequent, which suggests a strong bond with the cobalt-rich matrix. In addition, research reported that carbides drop from the matrix during tribocorrosion due to the dissolution of the boundary area of carbides under the galvanic action [20]; while in the study of corrosion resistance of these alloys, improved resistance due to boron additions was observed [31]. Those findings, along with the high hardness of precipitates, could explain the high wear resistance observed in this study in alloys with a high amount of precipitates. The abrasion could also be the cause of the rises and falls in the friction coefficient due to the fracture and detachment of the hard precipitates.     The delamination of the material was also observed, which was a product of surface fatigue in samples with sliding distances of 8 and 12 km, as shown in Figure 9. This fatigue delamination diminished in samples with 0.5 and 1%B. In the as-cast condition, in the 0.5B-AC alloy delamination was only observed after 12 km and in 1B-AC, it was not detected. In the heat treatment condition, delamination was clearly observed in the 0.5B-HT alloy and in 1B-HT it was very slight. A previous study on these alloys reported a decrease in fatigue resistance for heat-treated alloys containing boron respecting the same composition in the as-cast condition [32]. It was found in some cases that this delamination stopped due to hard precipitates under the surface (Figure 9f). The delamination of the material was also observed, which was a product of surface fatigue in samples with sliding distances of 8 and 12 km, as shown in Figure 9. This fatigue delamination diminished in samples with 0.5 and 1%B. In the as-cast condition, in the 0.5B-AC alloy delamination was only observed after 12 km and in 1B-AC, it was not detected. In the heat treatment condition, delamination was clearly observed in the 0.5B-HT alloy and in 1B-HT it was very slight. A previous study on these alloys reported a decrease in fatigue resistance for heat-treated alloys containing boron respecting the same composition in the as-cast condition [32]. It was found in some cases that this delamination stopped due to hard precipitates under the surface (Figure 9f). fatigue in samples with sliding distances of 8 and 12 km, as shown in Figure 9. This fatigue delamination diminished in samples with 0.5 and 1%B. In the as-cast condition, in the 0.5B-AC alloy delamination was only observed after 12 km and in 1B-AC, it was not detected. In the heat treatment condition, delamination was clearly observed in the 0.5B-HT alloy and in 1B-HT it was very slight. A previous study on these alloys reported a decrease in fatigue resistance for heat-treated alloys containing boron respecting the same composition in the as-cast condition [32]. It was found in some cases that this delamination stopped due to hard precipitates under the surface (Figure 9f).

Conclusions
The present study evaluated the effect of boron in the tribological behavior of CoCrMo alloys in as-cast and heat treatment conditions. This is the first report that shows the influence of heat treatment on the wear resistance of these alloys with this element and the effect of long sliding distances in wear mechanisms. The study resulted in the following conclusions:

1.
Wear resistance was significantly improved by the presence of boron. The more boron content, the less was the wear loss. It was attributed to the precipitation of the harder secondary phases and the even distribution of these phases.

2.
The wear resistance was not influenced by the roughness or friction coefficient, but by microstructure, the number of secondary phases and their hardness.

3.
The main wear mechanism observed was abrasion caused by the harder secondary phases.

4.
Surface delamination due to fatigue was observed after longer sliding distances. It noticeably diminished in 0.5 and 1%B as-cast alloy.

5.
Heat treatment at 1200 • C improved the wear resistance of alloy without boron. The alloys with some content of this element had a similar volumetric wear loss in the as-cast and heat-treated condition. However, heat treatment increased surface delamination. Funding: This research received no external funding.

Conflicts of Interest:
The authors declare no conflict of interest.