Evaluation of Chill Cast Co-Cr Alloys for Biomedical Applications

Binary Co-Cr alloys containing various Cr contents were vacuum induction melted and cast into wedge-shaped copper molds. It was intended to develop a microstructure (1) free from interdendritic segregation and porosity; (2) having minimal intermetallic precipitates; and (3) suitable for biomedical applications. The resultant microstructures were evaluated from sections obtained longitudinally and centrally in the plane normal to the diverging wedge faces. All ingots showed a dendritic microstructure with some characteristic features. For instance, in Co-20–30 wt. % Cr alloys, the chilled cast microstructures consisted of columnar dendrites without interdendritic segregation, a minimum of intermetallic precipitates, and the presence of a predominantly athermal HCP ε-martensite (>80 vol. %). In addition, the metastable FCC γ-Co phase was identified by X-ray diffraction and scanning electron microscopy. In the case of 35–44 wt. % Cr cobalt alloys, a eutectic constituent including the σ-phase were found to develop in the interdendritic regions. From this work, a Co-20 wt. % Cr alloy was chosen for further investigation after heat treating below the γ/ε transition temperature. The resultant tensile strength and ductility were further improved after applying a heat treatment at 730 ◦C for 30 min, obtaining values of elongation of 26% as compared with 2.55 < 5 of elongation in the as cast condition. Also, the alloy corrosion resistance in artificial saliva was investigated. It was found that the exhibited corrosion rates for the as-cast and heat-treated conditions are between those reported for other similar systems.


Introduction
Wrought and investment casting Co-Cr-Mo alloys have been widely employed for implant devices replacing hard tissue or in dental restorations in the human body [1,2].These alloys are known to possess excellent biocompatibility, mechanical properties, as well as wear and corrosion resistance [3][4][5].In as-cast cobalt alloys the solidified microstructures consist of a predominantly FCC γ-dendritic structure which is accompanied by segregation, and second phase precipitates within the matrix and along the interdendritic regions.In addition, inherent investment casting defects are of concern as they can lead to early implant failure and inadequate mechanical properties [6].
In general, investment casting Co-Cr-Mo alloys used as biomedical devices exhibit poor ductility, shrinkage porosity, interdendritic segregation, and the presence of intermetallic compounds [7,8].Hence, in order to improve alloy performance for potential biomedical applications, modifications in alloy design and casting technology have been considered in order to enhance the strength and ductility of Co-based alloys [9].In particular, changes in alloy design have been aimed at suppressing brittle-phase formation along the interdendritic regions during solidification.
As Co-Cr-Mo devices are expected to experience increasing use in a growing population of young patients, alloy reliability and safety levels become a major concern.Thus, further improvements in the exhibited mechanical properties of Co-alloys are desirable.One of the ways to achieve this goal has been through microstructural control, such as thermomechanical processing or heat-treating [10][11][12][13][14].In addition, alternatives in alloy design to produce biocompatible-grade Ni-free alloys have been under investigation due to the inherent risks associated with Ni-related allergic responses [15,16].
From the published literature, it is apparent that in order to design a sound Co-based alloy for biomedical applications, the choice of alloying elements, processing conditions and resultant properties need to be clearly identified.In particular, it is desirable to attain optimal alloy strength and ductility, combined with a high corrosion resistance [17].Accordingly, in this work, a novel approach is proposed that leads to optimum casting processing conditions which result in desirable mechanical properties, including corrosion resistance.The investigated alloys were as-cast segregation-free Co-Cr alloys intended for novel biomedical applications.For this purpose, wedge-shaped copper molds were employed in order to vary the cooling rates undergone by the as-cast alloys.The resultant alloy microstructures were subsequently characterized and out of these, the Co-20 wt.% Cr alloy was chosen for further characterization as they did not exhibit interdendritic segregation and the amount of precipitate was minimal.Moreover, in this alloy the effect of implementing a heat treatment below the γ/ε transition temperature on the mechanical properties and corrosion resistance was evaluated and compared with the as-cast condition

Materials Preparation
Cobalt alloys containing 20, 30, 35, 40, and 44 wt.% Cr were melted from pure Co (99.99%) and pure Cr (99.99%) in an alumina crucible using a vacuum induction furnace.Mo was not added because one aim of this work was to achieve a nearly free segregation microstructure with a minimum quantity of precipitates and carbides.The system was evacuated three times with high purity argon prior to vacuum melting.Once the alloy reached 2273 K (approx.2000 • C), both Co and Cr were in liquid state and the chamber was immediately evacuated again to remove any gases dissolved in the liquid bath.At the same time, the temperature was dropped down to 1873 K (approx.1600 • C) and a slag was formed in the bath surface.Afterwards, the liquid alloy was cast into a wedge-shaped copper mold.The wedge mold sides were covered by an alumina sheet to keep the heat flow predominantly in one direction, (see Figure 1).Prior to casting, Pt/Pt-18% Rh thermocouples were centrally inserted into the wedge copper mold at 20, 60, and 90 mm from the tip to the top of the mold cavity, at half thickness locations of 1.0, 3.0, and 4.5 mm, respectively.The as-cast ingots were then longitudinally and centrally sectioned in the plane normal to the diverging wedge faces and mechanically polished and electrolitically etched using a 60 vol.% HNO 3 + 40 vol.% H 2 O solution and 6 volts.

Materials Characterization
The resultant microstructures were identified and characterized using a JEOL 7600 scanning electron microscope (SEM, Jeol, Tokyo, Japan) and a JEOL1200 EX, transmission electron microscope (TEM, Jeol, Tokyo, Japan coupled with energy dispersed X-ray microanalysis (EDS, Jeol, Tokyo, Japan).X-ray diffraction was carried out using a Siemens D-5000 diffractometer with a Kα-Cu (1.5418 Å, Siemens, Munich, Germany) radiation and a scanning angle, 2 from 40° to 96° at a scanning rate of 1 °/min.Ingot sections of an alloy containing 20 wt.% Cr whose microstructures were dendritic, but segregation suppressed, were selected for heat treating.The implemented heat treatment was carried out at 1003.15 K (730 °C) for 60 min under an argon atmosphere [18].This was followed by determinations of mechanical properties in a tensile testing machine, Instron 1210 (MTS Systems Corporation, Eden Prairie, MN, USA), at a strain rate ε  = 1.6 × 10 −4 •s −1 and a travel speed of 0.5 mm/min.

Electrochemical Techniques
Preliminary corrosion tests were carried out using potentiodynamic polarization in a Gill AC potentiostat.For this purpose, the applied potential was varied from −1250 mV-with respect to the free corrosion potential, Ecorr-up to 1250 mV at a scanning rate of 0.5 mV/s.A conventional threeelectrode glass cell was used with graphite as an auxiliary electrode and a saturated calomel electrode (SCE) as the reference.Corrosion current density values, Icorr, were estimated using the Tafel extrapolation method and by considering an extrapolation interval of ±250 mV around the Ecorr value, once stable.The electrolyte employed consisted of artificial saliva whose composition is given in Table 1.

Materials Characterization
The resultant microstructures were identified and characterized using a JEOL 7600 scanning electron microscope (SEM, Jeol, Tokyo, Japan) and a JEOL1200 EX, transmission electron microscope (TEM, Jeol, Tokyo, Japan coupled with energy dispersed X-ray microanalysis (EDS, Jeol, Tokyo, Japan).X-ray diffraction was carried out using a Siemens D-5000 diffractometer with a Kα-Cu (1.5418 Å, Siemens, Munich, Germany) radiation and a scanning angle, 2θ from 40 • to 96 • at a scanning rate of 1 • /min.Ingot sections of an alloy containing 20 wt.% Cr whose microstructures were dendritic, but segregation suppressed, were selected for heat treating.The implemented heat treatment was carried out at 1003.15 K (730 • C) for 60 min under an argon atmosphere [18].This was followed by determinations of mechanical properties in a tensile testing machine, Instron 1210 (MTS Systems Corporation, Eden Prairie, MN, USA), at a strain rate .ε = 1.6 × 10 −4 •s −1 and a travel speed of 0.5 mm/min.

Electrochemical Techniques
Preliminary corrosion tests were carried out using potentiodynamic polarization in a Gill AC potentiostat.For this purpose, the applied potential was varied from −1250 mV-with respect to the free corrosion potential, E corr -up to 1250 mV at a scanning rate of 0.5 mV/s.A conventional three-electrode glass cell was used with graphite as an auxiliary electrode and a saturated calomel electrode (SCE) as the reference.Corrosion current density values, I corr , were estimated using the Tafel extrapolation method and by considering an extrapolation interval of ±250 mV around the E corr value, once stable.The electrolyte employed consisted of artificial saliva whose composition is given in Table 1.

Cooling Rates and Microstructure
Figure 2a shows cooling curves at various locations of the wedge-shaped mold in the temperature range of 1873.15-1673.15K (1600-1400 • C).Notice that the exhibited cooling rates are closely related to the thermocouple locations.In particular, it can be observed that the cooling rate for the Co-20 wt.% Cr alloy was 450 K/s at 20 mm from the tip (curve 1); 230 K/s at 60 mm, center (curve 2); and 120 K/s at 90 mm, top (curve 3).In addition, the location of the various solidified microstructures-including a eutectic and other intermetallic phases in the chilled-cast wedges for the various Cr contents (20, 30, 35, 40, and 44 wt.% Cr)-is shown in Figure 2b.Three dominant microstructures were identified: (1) dendrites; (2) dendrites and a eutectic in the interdendritic region; and (3) dendrites plus a eutectic and the σ-phase in the interdendritic region; this in agreement with other investigations [19].

Cooling Rates and Microstructure
Figure 2a shows cooling curves at various locations of the wedge-shaped mold in the temperature range of 1873.15-1673.15K (1600-1400 °C).Notice that the exhibited cooling rates are closely related to the thermocouple locations.In particular, it can be observed that the cooling rate for the Co-20 wt.% Cr alloy was 450 K/s at 20 mm from the tip (curve 1); 230 K/s at 60 mm, center (curve 2); and 120 K/s at 90 mm, top (curve 3).In addition, the location of the various solidified microstructures-including a eutectic and other intermetallic phases in the chilled-cast wedges for the various Cr contents (20, 30, 35, 40, and 44 wt.% Cr)-is shown in Figure 2b.Three dominant microstructures were identified: (1) dendrites, (2) dendrites and a eutectic in the interdendritic region, and (3) dendrites plus a eutectic and the σ-phase in the interdendritic region; this in agreement with other investigations [19].Figure 3 shows the various microstructures found in the Co-Cr alloys located at 20, 60, and 90 mm from the tip to the top of the wedge, respectively.Notice that the dominant solidified microstructures are made up of columnar dendrites.The presence of interdendrite segregation was not detected for Cr contents ≤30 wt.%, indicating that interdendritic segregation and brittle phase formation can be suppressed through rapid solidification.Figure 3 shows the various microstructures found in the Co-Cr alloys located at 20, 60, and 90 mm from the tip to the top of the wedge, respectively.Notice that the dominant solidified microstructures are made up of columnar dendrites.The presence of interdendrite segregation was not detected for Cr contents ≤30 wt.%, indicating that interdendritic segregation and brittle phase formation can be suppressed through rapid solidification.
Figure 4 shows the dimensions of the interdendritic segregation regions in as-cast Co-alloys processed by the investment casting technique [2,7,[20][21][22][23][24]. Notice that interdendritic segregation regions are on the order of 5-18 µm, but in atomized powders the interdendritic segregation diminishes down to close to 0.3 µm [25].In the present work, interdendritic spaces below 0.25 μm were observed in the bulk microstructure.In addition, randomly distributed precipitates within the matrix and at interdendritic arms were identified by SEM microanalysis.Accordingly, the Co3Cr and CoCr intermetallic phases were found to precipitate with a volume fraction which varied from 2.4 × 10 −3 (20 wt.% Cr) to 2.8 × 10 −3 (30 wt.% Cr).Beyond this Cr content, copious precipitation of Co3Cr and CoCr occurred, so it was no longer possible to make accurate volume fraction determinations (see Figure 3d,e).Moreover,   In the present work, interdendritic spaces below 0.25 µm were observed in the bulk microstructure.In addition, randomly distributed precipitates within the matrix and at interdendritic arms were identified by SEM microanalysis.Accordingly, the Co 3 Cr and CoCr intermetallic phases were found to precipitate with a volume fraction which varied from 2.4 × 10 −3 (20 wt.% Cr) to 2.8 × 10 −3 (30 wt.% Cr).Beyond this Cr content, copious precipitation of Co 3 Cr and CoCr occurred, so it was no longer possible to make accurate volume fraction determinations (see Figure 3d,e).Moreover, from the X-ray diffraction determinations (see Figure 5), it was found that dendrites were composed of athermal HCP ε-Co phase and metastable FCC γ-Co phase, and both phases were found to form in all the rapidly solidified alloys regardless of the Cr content.The amounts of athermal HCP ε-phase were determined by employing the expression proposed by Sage and Guillaud [26]: HCP (vol.%) = I(l0 Īl) HCP/ / I(l0 Īl) HCP + 1.5 I(200) FCC (1) where I(200) FCC and I(l0 Īl) HCP are the integrated intensities of the (200) γ and (l0 Īl) ε diffraction peaks for the FCC and HCP phases, respectively.Accordingly, using the exhibited intensity peaks, the amounts of athermal ε-martensite were estimated as a function of the applied cooling rates and Cr contents, and they are given in Table 2. From this table, it is evident that in segregation-free alloys, the volume fractions of precipitated ε-phase where were 89.6% and 90.1% for 20% Cr and 30% Cr alloys, respectively.These results are given in Figure 6, where the vol.% ε-martensite is plotted as a function of alloy processing.In this regard, the percent of ε-Co phase in investment casting alloys exhibits a value between 2 and 12 vol.% [25,27], while in hot Co-alloy forgings (10% deformation) the amount of ε-phase reached a value of 35 vol.% [10].Additionally, in atomized particles and chilled cast alloys (present work), 64 vol.% and 89.6-90.1 vol.% ε-phase were precipitated, respectively (Figure 6).Accordingly, using the exhibited intensity peaks, the amounts of athermal ε-martensite were estimated as a function of the applied cooling rates and Cr contents, and they are given in Table 2. From this table, it is evident that in segregation-free alloys, the volume fractions of precipitated ε-phase where were 89.6% and 90.1% for 20% Cr and 30% Cr alloys, respectively.These results are given in Figure 6, where the vol.% ε-martensite is plotted as a function of alloy processing.In this regard, the percent of ε-Co phase in investment casting alloys exhibits a value between 2 and 12 vol.% [25,27], while in hot Co-alloy forgings (10% deformation) the amount of ε-phase reached a value of 35 vol.% [10].Additionally, in atomized particles and chilled cast alloys (present work), 64 vol.% and 89.6-90.1 vol.% ε-phase were precipitated, respectively (Figure 6).    Figure 8a is a TEM micrograph with its corresponding diffraction pattern (Figure 8b) showing a fine distribution of elongated athermal ε-plates within the columnar dendritic structure.

Mechanical and Corrosion Properties
Figure 9 shows stress-strain plots corresponding to the Co-20 wt.Cr alloy in both the as-cast and heat-treated conditions.Notice from this figure that the alloy in the as-cast condition exhibits yield and ultimate tensile strengths of 230 MPa and 361 MPa, respectively, but an elongation of only 2.55%.Yet, after isothermal alloy heat treating at 1003.15 K for 60 min the mechanical properties exhibit a dramatic improvement in alloy strength of over 40% (i.e., 346 MPa yield strength and a UTS of 597 MPa).  Figure 8a is a TEM micrograph with its corresponding diffraction pattern (Figure 8b) showing a fine distribution of elongated athermal ε-plates within the columnar dendritic structure.

Mechanical and Corrosion Properties
Figure 9 shows stress-strain plots corresponding to the Co-20 wt.% Cr alloy in both the as-cast and heat-treated conditions.Notice from this figure that the alloy in the as-cast condition exhibits yield and ultimate tensile strengths of 230 MPa and 361 MPa, respectively, but an elongation of only 2.55%.Yet, after isothermal alloy heat treating at 1003.15 K for 60 min the mechanical properties exhibit a dramatic improvement in alloy strength of over 40% (i.e., 346 MPa yield strength and a UTS of 597 MPa).An examination of the fracture surfaces (see Figure 10a) indicates that the as-cast alloy fractured in a somewhat brittle fashion along columnar interdendritic interfaces.Also, the fracture path shows ε-Co phase striations delineating the columnar dendrites.In contrast, the heat-treated alloy exhibited a highly ductile fracture mode which was accompanied by significant plastic deformation (up to 26% elongation) and dimple development (Figure 10b).An examination of the fracture surfaces (see Figure 10a) indicates that the as-cast alloy fractured in a somewhat brittle fashion along columnar interdendritic interfaces.Also, the fracture path shows ε-Co phase striations delineating the columnar dendrites.In contrast, the heat-treated alloy exhibited a highly ductile fracture mode which was accompanied by significant plastic deformation (up to 26% elongation) and dimple development (Figure 10b).An examination of the fracture surfaces (see Figure 10a) indicates that the as-cast alloy fractured in a somewhat brittle fashion along columnar interdendritic interfaces.Also, the fracture path shows ε-Co phase striations delineating the columnar dendrites.In contrast, the heat-treated alloy exhibited a highly ductile fracture mode which was accompanied by significant plastic deformation (up to 26% elongation) and dimple development (Figure 10b).Finally, preliminary testing on the corrosion resistance of the Co-20 wt.% Cr alloy by potentiodynamic polarization in synthetic saliva was used for determinations of corrosion rates.Figure 11 and Table 3 show the corrosion potential, current density, and corrosion rate values found for the Co-20 wt.% Cr alloy in both, the as-cast, and after heat treating conditions.Notice that corrosion rates of 8 × 10 −4 and 3.56 × 10 −3 mm/year were found for the as-cast and treated alloys, respectively.Finally, preliminary testing on the corrosion resistance of the Co-20 wt.% Cr alloy by potentiodynamic polarization in synthetic saliva was used for determinations of corrosion rates.Figure 11 and Table 3 show the corrosion potential, current density, and corrosion rate values found for the Co-20 wt.% Cr alloy in both, the as-cast, and after heat treating conditions.Notice that corrosion rates of 8 × 10 −4 and 3.56 × 10 −3 mm/year were found for the as-cast and treated alloys, respectively.[17] 1.26 Co-Cr as-cast [29] 5.43 Co-Cr Heat treated [29] 0.061

Phases
Figure 12 shows a map of the various phases found as a function of the applied cooling rates and Cr contents where the presence of FCC γ-Co phase/HCP ε-Co phase is observed even for eutectic compositions.In the case of investment casting Co-Cr alloys, a highly inhomogeneous structure is expected to form with large-grained cored dendrites and Co-rich regions.In particular, the interdendritic regions can contain various quaternary Co-rich, Cr-rich, and Cr-and Mo-rich phases [30].The microstructures found in the rapidly solidified Co-35 wt.% Cr, Co-40 wt.% Cr and Co-44   [17] 1.26 Co-Cr as-cast [29] 5.43 Co-Cr Heat treated [29] 0.061

Phases
Figure 12 shows a map of the various phases found as a function of the applied cooling rates and Cr contents where the presence of FCC γ-Co phase/HCP ε-Co phase is observed even for eutectic compositions.In the case of investment casting Co-Cr alloys, a highly inhomogeneous structure is expected to form with large-grained cored dendrites and Co-rich regions.In particular, the interdendritic regions can contain various quaternary Co-rich, Cr-rich, and Cr-and Mo-rich phases [30].The microstructures found in the rapidly solidified Co-35 wt.% Cr, Co-40 wt.% Cr and Co-44 wt.% Cr alloys are in agreement with the ones reported by other workers [21,31,32], but for the binary Co-Cr system.
wt. % Cr alloys are in agreement with the ones reported by other workers [21,31,32], but for the binary Co-Cr system.From this work, it is evident that rapid solidification either reduces or inhibits segregation at Cr contents below 30 wt. % (see Figure 13).Nevertheless, as the Cr-content increases, the columnar dendritic structure becomes heavily segregated at the interdendritic locations.X-ray diffraction determinations confirmed the presence of the eutectic constituent and of the -phase for chromium contents >30 wt.% (see Figure 5c,d).In addition, X-ray intensity peaks corresponding to the FCC γ-Co phase and HCP ε-Co phase were identified.Moreover, as the Cr content increases in the as-cast alloys, a reduction in the primary dendrite arm spacing was observed (see Figure 3).This effect is concomitant with an increase in interdendritic segregation (Co-40 and 44 wt.% Cr alloys) and with the precipitation of both, the eutectic and the σ-phase in agreement with other reports [21].In contrast, in conventionally solidified as-cast microstructures the interdendritic regions are rather wide with spacings oscillating between 7 μm and 18 μm [7,[31][32][33], as shown in Figure 4.

HCP and FCC Phases
In this work, it was found that the HCP ε-Co phase was able to form in all the rapidly solidified alloys regardless of the Cr content.According to the published literature [34], it is well-known that the athermal HCP ε-Co phase occurs by a martensitic transformation from the high temperature stable FCC γ-Co phase.The development of athermal ε-martensite is expected to be favored by rapid cooling from the γ-Co phase [34].Nevertheless, in conventionally investment solidified Co-Cr-Mo-C alloys the reported amounts of precipitated ε-martensite have been found to be relatively small, not exceeding 20 vol.%, in most cases [35,36].A maximum of 64 vol.% was reported in 80 μm water atomized Co-Cr-Mo powders (Figure 6) [25].The amounts of athermal ε-martensite are strongly From this work, it is evident that rapid solidification either reduces or inhibits segregation at Cr contents below 30 wt. % (see Figure 13).Nevertheless, as the Cr-content increases, the columnar dendritic structure becomes heavily segregated at the interdendritic locations.X-ray diffraction determinations confirmed the presence of the eutectic constituent and of the σ-phase for chromium contents >30 wt.% (see Figure 5c,d).In addition, X-ray intensity peaks corresponding to the FCC γ-Co phase and HCP ε-Co phase were identified.Moreover, as the Cr content increases in the as-cast alloys, a reduction in the primary dendrite arm spacing was observed (see Figure 3).This effect is concomitant with an increase in interdendritic segregation (Co-40 and 44 wt.% Cr alloys) and with the precipitation of both, the eutectic and the σ-phase in agreement with other reports [21].In contrast, in conventionally solidified as-cast microstructures the interdendritic regions are rather wide with spacings oscillating between 7 µm and 18 µm [7,[31][32][33], as shown in Figure 4. wt.% Cr alloys are in agreement with the ones reported by other workers [21,31,32], but for the binary Co-Cr system.From this work, it is evident that rapid solidification either reduces or inhibits segregation at Cr contents below 30 wt. % (see Figure 13).Nevertheless, as the Cr-content increases, the columnar dendritic structure becomes heavily segregated at the interdendritic locations.X-ray diffraction determinations confirmed the presence of the eutectic constituent and of the -phase for chromium contents >30 wt.% (see Figure 5c,d).In addition, X-ray intensity peaks corresponding to the FCC γ-Co phase and HCP ε-Co phase were identified.Moreover, as the Cr content increases in the as-cast alloys, a reduction in the primary dendrite arm spacing was observed (see Figure 3).This effect is concomitant with an increase in interdendritic segregation (Co-40 and 44 wt.% Cr alloys) and with the precipitation of both, the eutectic and the σ-phase in agreement with other reports [21].In contrast, in conventionally solidified as-cast microstructures the interdendritic regions are rather wide with spacings oscillating between 7 μm and 18 μm [7,[31][32][33], as shown in Figure 4.

HCP and FCC Phases
In this work, it was found that the HCP ε-Co phase was able to form in all the rapidly solidified alloys regardless of the Cr content.According to the published literature [34], it is well-known that the athermal HCP ε-Co phase occurs by a martensitic transformation from the high temperature stable FCC γ-Co phase.The development of athermal ε-martensite is expected to be favored by rapid cooling from the γ-Co phase [34].Nevertheless, in conventionally investment solidified Co-Cr-Mo-C alloys the reported amounts of precipitated ε-martensite have been found to be relatively small, not exceeding 20 vol.%, in most cases [35,36].A maximum of 64 vol.% was reported in 80 μm water atomized Co-Cr-Mo powders (Figure 6) [25].The amounts of athermal ε-martensite are strongly

HCP and FCC Phases
In this work, it was found that the HCP ε-Co phase was able to form in all the rapidly solidified alloys regardless of the Cr content.According to the published literature [34], it is well-known that the athermal HCP ε-Co phase occurs by a martensitic transformation from the high temperature stable FCC γ-Co phase.The development of athermal ε-martensite is expected to be favored by rapid cooling from the γ-Co phase [34].Nevertheless, in conventionally investment solidified Co-Cr-Mo-C alloys the reported amounts of precipitated ε-martensite have been found to be relatively small, not exceeding 20 vol.%, in most cases [35,36].A maximum of 64 vol.% was reported in 80 µm water atomized Co-Cr-Mo powders (Figure 6) [25].The amounts of athermal ε-martensite are strongly influenced by the annealing temperatures, with increasing volume fractions found in alloys annealed at increasing temperatures [34].In contrast, under the cooling conditions achieved during chill casting of Co-Cr alloys, the amounts of precipitated athermal ε-martensite exceeded 80 vol.% as seen in Table 2.
SEM and TEM observations of the exhibited microstructures (see Figures 7 and 8) are consistent with the ones reported by Rajan [37] for HCP martensite.From the electron diffraction pattern, it is found that the FCC γ-Co possesses a [11] zone axes, and a [01 Ī0] one for the HCP ε-Co.In addition, these phases possess a (1 Ī1)||(0002) orientation relationship.From Figure 8a it is evident that the FCC γ-Co phase is located between fine HCP ε-martensite plates.Apparently, a high density of ε-martensite plates nucleated and grew at expenses of the austenitic matrix, leaving residual γ-Co phase films in-between ε-martensite plates.Thus, copious nucleation of athermal ε-martensite seems to be strongly favored by the rapid cooling effects imposed on these alloys.According to Jones [38], it is expected that rapid solidification will lead to a high density of vacancies and a high volume of planar defects (stacking faults), favoring a martensitic transformation.The outcome of this work indicates that the γ to ε martensitic transformation is dominant under rapid solidification conditions with over 80 vol.% ε-HCP phase developing in most of the investigated alloys.

Mechanical Properties
From the outcome of this work, a Co-20 wt.% Cr alloy was chosen for additional testing, as this alloy exhibited minimal or no segregation with no intermetallic phases.Accordingly, the mechanical properties of this alloy were investigated before and after an isothermal heat treatment at 1003.15 K for 60 min.The heat treatment was intended to remove any internal stresses associated with the alloy rapid solidification.Figure 14 shows the effect of the isothermal heat treatment on the exhibited microstructure in the Co-20 wt.% Cr alloy.Notice that in this condition the morphology of the ε-martensite is rather different from the one in the as-cast condition, in agreement with published reports [39,40].influenced by the annealing temperatures, with increasing volume fractions found in alloys annealed at increasing temperatures [34].In contrast, under the cooling conditions achieved during chill casting of Co-Cr alloys, the amounts of precipitated athermal ε-martensite exceeded 80 vol.% as seen in Table 2. SEM and TEM observations of the exhibited microstructures (see Figures 7 and 8) are consistent with the ones reported by Rajan [37] for HCP martensite.From the electron diffraction pattern, it is found that the FCC γ-Co possesses a [11] zone axes, and a [01Ī0] one for the HCP ε-Co.In addition, these phases possess a (1Ī1)||(0002) orientation relationship.From Figure 8a it is evident that the FCC γ-Co phase is located between fine HCP ε-martensite plates.Apparently, a high density of εmartensite plates nucleated and grew at expenses of the austenitic matrix, leaving residual γ-Co phase films in-between ε-martensite plates.Thus, copious nucleation of athermal ε-martensite seems to be strongly favored by the rapid cooling effects imposed on these alloys.According to Jones [38], it is expected that rapid solidification will lead to a high density of vacancies and a high volume of planar defects (stacking faults), favoring a martensitic transformation.The outcome of this work indicates that the γ to ε martensitic transformation is dominant under rapid solidification conditions with over 80 vol.% ε-HCP phase developing in most of the investigated alloys.

Mechanical Properties
From the outcome of this work, a Co-20 wt.% Cr alloy was chosen for additional testing, as this alloy exhibited minimal or no segregation with no intermetallic phases.Accordingly, the mechanical properties of this alloy were investigated before and after an isothermal heat treatment at 1003.15 K for 60 min.The heat treatment was intended to remove any internal stresses associated with the alloy rapid solidification.Figure 14 shows the effect of the isothermal heat treatment on the exhibited microstructure in the Co-20 wt.% Cr alloy.Notice that in this condition the morphology of the εmartensite is rather different from the one in the as-cast condition, in agreement with published reports [39,40].In particular, notice that the dendritic structure tends to be erased by the isothermal heat treatment.In addition, the amount of ε-martensite increases (from 85 vol.% in the as-cast condition to 96 vol.% after heat treating, see Figure 16).Apparently, under these conditions, isothermal εmartensite develops from the athermal one and also from the remaining FCC γ-Co phase.In addition (see Figure 15a), there is an apparent thickening of ε-martensite plates and the confinement of the FCC γ-Co phase to highly localized narrow regions (see Figure 8a).In particular, notice that the dendritic structure tends to be erased by the isothermal heat treatment.In addition, the amount of ε-martensite increases (from 85 vol.% in the as-cast condition to 96 vol.% after heat treating, see Figure 16).Apparently, under these conditions, isothermal ε-martensite develops from the athermal one and also from the remaining FCC γ-Co phase.In addition (see Figure 15a), there is an apparent thickening of ε-martensite plates and the confinement of the FCC γ-Co phase to highly localized narrow regions (see Figure 8a).A drastic improvement in the alloy ductility was also achieved after the isothermal heat treating (i.e., up to 26% elongation), which is over a 10-fold increase when compared with the alloy in the ascast condition [21,22,41,42].These elongation values are rather similar to the ones reported for other Co-alloys heat treated at high temperatures [41], forged [43] or hot rolled [44], as shown in Figure 17.Notice from the fracture modes that the effect of the prior columnar dendritic structure was not dominant in the final fracture path in the heat-treated condition (see Figure 10).Moreover, the exhibited brittle fracture path in the as-cast alloy is not related to inhomogeneous solute distribution A drastic improvement in the alloy ductility was also achieved after the isothermal heat treating (i.e., up to 26% elongation), which is over a 10-fold increase when compared with the alloy in the as-cast condition [21,22,41,42].These elongation values are rather similar to the ones reported for other Co-alloys heat treated at high temperatures [41], forged [43] or hot rolled [44], as shown in Figure 17.Notice from the fracture modes that the effect of the prior columnar dendritic structure was not dominant in the final fracture path in the heat-treated condition (see Figure 10).Moreover, the exhibited brittle fracture path in the as-cast alloy is not related to inhomogeneous solute distribution as the alloy did not exhibit any significant segregation effects nor precipitation of any intermetallic phases.Thus, the outcome of this work indicates that rapid solidification in Co-Cr alloys promotes microstructural homogeneity.Moreover, through alloy heat treating, the resultant mechanical properties are drastically improved, becoming highly attractive for potential biomedical applications.A drastic improvement in the alloy ductility was also achieved after the isothermal heat treating (i.e., up to 26% elongation), which is over a 10-fold increase when compared with the alloy in the ascast condition [21,22,41,42].These elongation values are rather similar to the ones reported for other Co-alloys heat treated at high temperatures [41], forged [43] or hot rolled [44], as shown in Figure 17.Notice from the fracture modes that the effect of the prior columnar dendritic structure was not dominant in the final fracture path in the heat-treated condition (see Figure 10).Moreover, the exhibited brittle fracture path in the as-cast alloy is not related to inhomogeneous solute distribution as the alloy did not exhibit any significant segregation effects nor precipitation of any intermetallic phases.Thus, the outcome of this work indicates that rapid solidification in Co-Cr alloys promotes microstructural homogeneity.Moreover, through alloy heat treating, the resultant mechanical properties are drastically improved, becoming highly attractive for potential biomedical applications.

Corrosion Properties
The experimental Co-20 wt.% Cr was found to possess an optimum combination of strength and ductility for some potential biomedical applications.Yet another critical alloy requirement is related to a high biocompatibility in the human body, particularly high corrosion resistance.Hence, preliminary testing was carried out to assess the alloy corrosion behavior.This is primarily motivated by the potentially harmful effects associated with the high cytotoxicity of the byproducts generated during the corrosion process [17].From the corrosion results (see Figure 11 and Table 3) it was found that the corrosion properties of the Co-20 wt.% Cr alloy in the as-cast condition are slightly superior to the ones obtained after the heat treatment.In turn, this confirms that the as-cast alloy is highly homogeneous as there are no preferential defects such as intermetallics or alloy segregation that can trigger severe or localized corrosion.Moreover, in both cases, the exhibited corrosion rates are appreciably lower than the ones corresponding with those reported for other Co-Cr alloys [29] under similar corrosion conditions in artificial saliva.Thus, it is evident that through microstructural control using rapid solidification (i.e., suppression of interdendritic segregation and intermetallic precipitation) it is plausible to design a Co-Cr alloy with unique properties for applications such as in dental materials.

Conclusions
(1) In this work an alternative solidification process is proposed that can be used to produce Co-Cr alloys with unique microstructures.(2) Through the use of wedge-shaped copper molds, rapid solidification regimes were achieved in the solidified alloys.(3) In the eutectic composition (Co-44 wt.% Cr alloy) there were some constitutional changes; as a result of rapid solidification, the FCC γ-Co and HCP ε-Co solid solution phases were able to form outside their equilibrium limits (solid solubility extension).In addition, dendrite refinement and elimination or reduction of interdendritic segregation for Co-20, 30, 35, 40, and 44 wt.% Cr alloys was observed, which can be considered as one of the microstructural effects due to rapid solidification.(4) Rapid solidification effects, such as excess vacancies and the development of numerous stacking faults and corresponding intersections, strongly favored the athermal ε-martensite transformation.Amounts of athermal ε-martensite exceeding 80 vol.% were induced at all of the cooling rates imposed on most of the alloys in the as-cast condition.(5) An isothermal heat treatment below the γ-ε phase transformation temperature was implemented in the Co-20 wt.% Cr alloy.In turn, the mechanical strength was found to improve by over 40% whereas the alloy ductility exhibited over a 10-fold increase when compared with the alloy in as-cast condition.SEM and TEM characterization revealed that in the as-cast condition the resultant microstructure is composed of fine athermal ε-martensite plates inside directionally solidified columnar dendrites.After aging, the morphology undergoes a change due to the isothermal transformation of HCP ε-martensite as confirmed by X-ray diffraction data.(6) Potentiodynamic polarization curves indicated that the Co-20 wt.% Cr alloy exhibited the lowest corrosion rates when compared with other Co-based alloys currently in use.In turn, preliminary results indicate that the combination of mechanical strength and corrosion resistance exhibited by this alloy processed by rapid solidification makes it attractive for potential applications as a biomaterial.

Figure 1 .
Figure 1.(a) Wedge-shaped copper mold isolated in both sides by an alumina sheet; (b) "V" shaped ingot showing three different cooling rate zones: 90 mm high: 120 K/s, 60 mm high: 230 K/s, and 20 mm high: 450 K/s.

Figure 1 .
Figure 1.(a) Wedge-shaped copper mold isolated in both sides by an alumina sheet; (b) "V" shaped ingot showing three different cooling rate zones: 90 mm high: 120 K/s, 60 mm high: 230 K/s, and 20 mm high: 450 K/s.

Figure 3 .
Figure 3. Microstructures found in wedge shaped Co-Cr alloy ingots.(a) Co-20 wt.% Cr, (b) Co-30 wt.% Cr, (c) Co-35 wt.% Cr, (d) Co-40 wt.% Cr, and (e) Co-44 wt.% Cr.It is important to note that the heat flux direction is always in the opposite sense with respect to the columnar dendrites growth.

Figure 4 .
Figure 4. Interdendritic segregation reported in Co-alloys.References are given in parentheses and the chill cast corresponds to the present work.

Figure 4 .
Figure 4. Interdendritic segregation reported in Co-alloys.References are given in parentheses and the chill cast corresponds to the present work.

Figure 6 .
Figure 6.Percent of ε-phase as a function of alloy processing.

Figure 7
Figure 7 is an SEM micrograph of the athermal ε-martensite developed within the columnar dendritic structure in a Co-20 wt.% Cr alloy; in particular, notice the typical striations associated with the athermal ε-martensite transformation [28].The exhibited microstructure was further investigated by TEM means.

Figure 6 .
Figure 6.Percent of ε-phase as a function of alloy processing.

Figure 7 18 Figure 7 .
Figure 7 is an SEM micrograph of the athermal ε-martensite developed within the columnar dendritic structure in a Co-20 wt.% Cr alloy; in particular, notice the typical striations associated with the athermal ε-martensite transformation [28].The exhibited microstructure was further investigated by TEM means.Metals 2016, 6, 188 9 of 18

Figure 18 Figure 7 .
Figure8ais a TEM micrograph with its corresponding diffraction pattern (Figure8b) showing a fine distribution of elongated athermal ε-plates within the columnar dendritic structure.

Figure 9 18 Figure 9 .
Figure9shows stress-strain plots corresponding to the Co-20 wt.% Cr alloy in both the as-cast and heat-treated conditions.Notice from this figure that the alloy in the as-cast condition exhibits yield and ultimate tensile strengths of 230 MPa and 361 MPa, respectively, but an elongation of only 2.55%.Yet, after isothermal alloy heat treating at 1003.15 K for 60 min the mechanical properties

Figure 9 .
Figure 9. Stress-strain curves for Co-20 wt.% Cr alloy: (a) in the as-chill cast condition and (b) heat-treated condition.

Figure 11 .
Figure 11.Polarization curves for the Co-20 wt.% Cr alloys in both, the as-chill cast and the heat treated conditions.

Figure 11 .
Figure 11.Polarization curves for the Co-20 wt.% Cr alloys in both, the as-chill cast and the heat treated conditions.

Figure 12 .
Figure 12.Mapping of the various phases found including intermetallics and the eutectic constituent as a function of cooling rates and % Cr.

Figure 13 .
Figure 13.(a) SEM micrograph of the as-chill cast Co-20 wt.% Cr directionally solidified alloy showing a part of columnar dendrites, (b) X-ray mapping of Cr (chromium).

Figure 12 .
Figure 12.Mapping of the various phases found including intermetallics and the eutectic constituent as a function of cooling rates and % Cr.

Figure 12 .
Figure 12.Mapping of the various phases found including intermetallics and the eutectic constituent as a function of cooling rates and % Cr.

Figure 13 .
Figure 13.(a) SEM micrograph of the as-chill cast Co-20 wt.% Cr directionally solidified alloy showing a part of columnar dendrites, (b) X-ray mapping of Cr (chromium).

Figure 13 .
Figure 13.(a) SEM micrograph of the as-chill cast Co-20 wt.% Cr directionally solidified alloy showing a part of columnar dendrites, (b) X-ray mapping of Cr (chromium).

Figure
Figure 15a is a TEM micrograph clearly showing embedded numerous stacking faults together with various ε-martensite bands and a high density of dislocations.The corresponding diffraction pattern (Figure15b) shows that the zone axes for the HCP ε-Co phase is now[1].

Figure
Figure 15a is a TEM micrograph clearly showing embedded numerous stacking faults together with various ε-martensite bands and a high density of dislocations.The corresponding diffraction pattern (Figure15b) shows that the zone axes for the HCP ε-Co phase is now[1].

Figure 17 .
Figure 17.Percent elongation of Co-alloys as a function of alloy processing.Figure 17.Percent elongation of Co-alloys as a function of alloy processing.

Figure 17 .
Figure 17.Percent elongation of Co-alloys as a function of alloy processing.Figure 17.Percent elongation of Co-alloys as a function of alloy processing.

Table 1 .
Chemical composition of the artificial saliva.

Table 1 .
Chemical composition of the artificial saliva.

Table 2 .
Athermal ε-martensite transformation as a function of cooling rates for several Cr contents.

Table 2 .
Athermal ε-martensite transformation as a function of cooling rates for several Cr contents.

Table 3 .
Electrochemical parameters obtained from the polarization curves of Co-20 wt.% Cr alloys polarized in Artificial Saliva Solution.

Table 3 .
Electrochemical parameters obtained from the polarization curves of Co-20 wt.% Cr alloys polarized in Artificial Saliva Solution.