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Dominant Role of Molybdenum in the Electrochemical Deposition of Biological Macromolecules on Metallic Surfaces

The corrosion of CoCrMo, an alloy frequently used in orthopedic implants, was studied with an electrochemical quartz crystal microbalance (QCM) in three physiologically relevant solutions. Mass changes were measured during potentiodynamic tests, showing material deposition in protein solutions at potential levels that caused mass loss when the proteins were not present. X-ray photoelectron spectroscopy (XPS) data indicated that the deposited material was primarily organic and therefore was most likely derived from proteins in the electrolyte. Material deposition consistently occurred at a critical potential and was not dependent on the current density or total charge released into solution. Corrosion studies on pure Co, Cr, and Mo in protein solutions found material deposition only on Mo. We hypothesize that organic deposition results from the interaction of Mo(VI) with proteins in the surrounding solution. The organic layer is reminiscent of tribochemical reaction layers that form on the surface of CoCrMo hip bearings, suggesting that these types of layers can be formed by purely electrochemical means.


INTRODUCTION
Recently, serious concerns have been reported regarding the mechanical performance and safety of metal biomedical implants. 1−4 Among the many factors that can affect implant performance, the corrosive nature of the physiological environment plays a significant role. Metal-on-metal (MoM) hip replacements, typically made of CoCrMo alloys, degrade because of the synergistic effects of mechanical wear from metal−metal contact and electrochemical reactions with salts, proteins, and other organic species. 5,6 These degradative processes release metal ions and nanoscopic wear particles in vivo that often contribute to implant failure. 7,8 However, studies have shown that a tribofilm, composed of organic and metallic constituents, can form under these same conditions on the surface of CoCrMo implants. 8 Implants with such a tribofilm have demonstrated increased corrosion resistance; the film may also act as a lubrication layer, enabling better wear resistance. 9 The organic constituents of this tribofilm are presumably derived from proteins in synovial fluid, but mechanisms causing the protein decomposition necessary for film formation are unknown. The current theory suggests that frictional processes contribute significantly to its development, with the combination of shear stresses and a rise in local contact temperatures causing protein degradation. 8 Because it has been shown that tribofilms hold Co, Cr, and Mo ions, 10 it is additionally hypothesized that local variations in corrosion kinetics involving proteins and metal ions contribute to the film formation.
In the study described here, we combined standard electrochemical techniques with a quartz crystal microbalance (QCM) mass sensor to delineate corrosion mechanisms of CoCrMo and to investigate if tribofilm-like layers can be generated electrochemically. The QCM enables in situ quantification of surface changes accompanying corrosion and is very sensitive to small changes in the total mass of a thin film. 11−15 Here, it was used to measure mass changes associated with the different sublayers of the alloy surface, including the metal, metal oxide, and any organic deposit, as depicted in the schematic in Figure 1. The instrument contains a thin piezoelectric quartz crystal set between two electrodes. When an oscillating voltage is applied across the electrodes, the quartz vibrates and its resonance frequency can be measured. If the mass on the electrode surface changes, so will the resonance frequency, providing detailed information that quantifies mass changes down to the nanogram level. 16 The QCM is also sensitive to viscoelastic properties that introduce dissipation and reduce the quality factor of the resonance. 17 Although a variety of equivalent measures can be used to quantify this dissipation, we use the half-width at half-maximum of the conductance peak centered at the resonance frequency. The use of this quantity, which we refer to as Γ, has been used extensively by others and is discussed in more detail in a review article by Johannsmann. 18 The QCM has been used to study a variety of corrosion processes in different materials, including Fe−Cr and Au−Pd− In alloys. 11−13 Recently, Valero Vidal et al. 19 employed an electrochemical QCM to investigate passive film growth on CoCrMo films in phosphate-buffered saline (PBS). Mass loss was observed in all anodic potential ranges investigated, even during oxide growth, but was accelerated upon transpassive dissolution. In the present study, the corrosion behavior of CoCrMo thin films was measured in three different fluids that mimic different aspects of the physiological environment. Electrochemical QCM measurements were employed to quantify mass changes associated with the corrosion process. In protein solutions, it was found that an organic layer deposits on the surface of the film at elevated potentials. A series of potentiodynamic and potentiostatic tests indicated critical criteria for deposition of this organic layer. Additionally, similar corrosion tests were conducted on thin films of the individual alloying elements (Co, Cr, and Mo) to determine if a particular ion is responsible for the organic deposition. As we describe in the following sections, it was found that a significantly thick organic film formed on the Mo films, suggesting that Mo ions are essential to promoting organic film formation on the alloy.

Sample Preparation.
Working electrode specimens were prepared on AT-cut, 5 MHz quartz crystals with chrome electrodes (Inficon, East Syracuse, NY). CoCrMo, Cr, and Mo films were fabricated in a magnetron sputter deposition chamber (AJA Orion, N. Scituate, MA) at a base pressure of 10 −7 Torr with Ar as the working gas. CoCrMo was deposited with a multistep sputter method modified from Nakagawa et al., which was designed to control the film's crystallinity and internal stresses. 20 First, the chamber was heated to 300 C at a rate of 14 C/min; crystals were then cleaned with a plasma strike. Subsequently, Cr was sputtered for 200 s at 100 W power and 3 mTorr pressure to produce an adhesion layer. Using a wrought, lowcarbon CoCrMo target (ASTM F1537), a CoCrMo underlayer was deposited by sputtering for 100 s at 180 W power and 0.25 mTorr. Finally, CoCrMo was sputtered for 2000 s at 150 W power and 4 mTorr pressure. Cr films were made by sputtering at 300 C and 3 mTorr pressure for 3000 s at 180 W power following the plasma cleaning step. Mo films were prepared at room temperature. Following the plasma strike, a Cr adhesion layer was deposited by sputtering for 200 s at 100 W power; Mo was then sputtered for 2000 s at 180 W power. Co films were prepared using an Edwards Auto 500 electron beam evaporator (BOC Edwards, Wilmington, MA) evacuated to a base pressure of 10 −5 Torr. A Cr adhesion layer (5 nm thick) was first deposited at a rate of 0.08 nm/s at 40 mA beam current. Co (International Advanced Materials, Spring Valley, NY) was deposited at the same rate at 100 mA beam current to a thickness of between 130 and 300 nm. Low-carbon CoCrMo pins (ASTM F1537) with a diameter of 7 mm were utilized for bulk specimen tests. Prior to testing, pins were ground and polished with standard metallographic methods to a mirror finish (Ra < 0.02 μm).
2.2. Electrochemical QCM. Electrochemical tests were conducted in a custom three-electrode corrosion cell. The sputtered metal films on the quartz substrate acted as the working electrode, with an exposed area of 2.85 cm 2 . Two electrical leads connected the QCM holder to a QCM network analyzer and the potentiostat (BioLogic SP-150, France), as shown schematically in Figure 2. Mammalian Ringer's salt solution (Electron Microscopy Services, Hatfield, PA), buffer solution (pH 7.6), or bovine calf serum (BCS) served as the electrolyte. BCS is commonly used as a testing fluid for wear tests of orthopedic bearings. Its protein content is comparable to that of natural joint fluid (synovial fluid) with 30 g/L protein. Ringer's solution was used as manufactured and consisted of NaCl, KCl, MgCl 2 , CaCl 2 , NaHCO 3 , and glucose. Buffer solution was prepared with 0.154 M NaCl, 0.223 M Tris buffer, and 53.7 mM EDTA, adjusted to pH 7.6 with HCl. BCS was prepared by diluting newborn calf serum (Invitrogen, Grand Island, NY) in buffer solution.
Prior to each experiment, the open circuit potential was measured for 3 min by allowing the potential at the working electrode to equilibrate in the electrolyte. Next, the specimen was held at a cathodic potential of −0.9 V for 10 min to clean the surface and remove any oxide film that may have formed in air. The open circuit potential was then measured after the system was allowed to stabilize for 1 h. Subsequently, potentiodynamic and potentiostatic tests were conducted under varying conditions while the QCM frequency response was measured at the first, third, and fifth harmonics (n = 1, 5 MHz; n = 3, 15 MHz; n = 5, 25 MHz). In many cases, QCM data from only the third harmonic are reported for clarity, but the data showed good agreement among all three harmonics. As discussed in more detail below, the experiments are generally conducted in the range where a simple analysis based on only a single harmonic is sufficient. During potentiodynamic tests, the potential was increased at a rate of 0.25 mV/s from −0.8 to 1.0 V. All potentials are reported against a saturated calomel reference electrode (SCE). The corrosion potential (E corr ) and current (i corr ) were extracted from the polarization curves by the Tafel method 21 conducted with EC-Lab Express software. Tests were conducted at room temperature.
QCM frequency shifts were related to the mass change per unit area (ΔM A ) on the working electrode surface with the Sauerbrey equation 22 where Z q is the theoretical acoustic impedance of quartz (8.84 × 10 6 kg m −2 s −1 ), n is the order of the measured harmonic (1, 3, or 5), and f 1 is the fundamental frequency (5 MHz). The baseline frequency for a given harmonic corresponds to the resonance frequency of the crystal at the outset of a potentiometric scan after the system equilibrated for 1 h and the open circuit potential was measured. The Sauerbrey equation was originally applied to quartz resonators in air or vacuum, but it has been subsequently shown that the analysis can also be applied to mass deposition from a liquid medium. The analysis holds in a liquid medium provided that the reference frequency corresponds to the resonance frequency of the immersed crystal prior to the deposition process and that the dissipation (Γ) due to viscoelastic effects is not very high. 23 The thickness of the metal film prior to testing was also extracted from eq 1 by measuring the resonance frequency before and after film deposition and by assuming that the sputtered density is the same as for the bulk material.
2.3. X-ray Photoelectron Spectroscopy and Energy-Dispersive Spectroscopy. X-ray photoelectron spectroscopy (XPS) was conducted with a Thermo Scientific ESCALAB 250Xi spectrometer (Thermo Fisher Scientific) using a monochromatized Al Kα X-ray source at a 90°takeoff angle. The analysis spot size had a diameter of 500 μm. The base pressure in the analysis chamber was ∼10 −9 mbar. Survey spectra (0−1100 eV) were obtained at a 100 eV analyzer pass energy with a 1.0 eV energy step size. High-resolution spectra of C 1s, O 1s, N 1s, Co 2p, Cr 2p, and Mo 3d were obtained at a 50 eV analyzer pass energy with a 0.5 eV energy step size. A flood gun was employed to control the surface potential throughout spectra acquisition. Peak fitting was conducted with Avantage software (Thermo Scientific) using a Shirley-type background and Gaussian/ Lorentzian peak shapes. Binding energies were referenced by shifting the lowest-energy C 1s peak (hydrocarbon peak) to 284.8 eV. Analysis was performed on three areas for each sample. Five C 1s and O 1s and 10−20 N 1s, Co 2p, Cr 2p, and Mo 3d high-resolution scans were conducted for each area. Peak binding energies and atomic percentages are reported as an average ± one standard deviation.
Energy-dispersive spectroscopy (EDS) was conducted with a Hitachi S-3400-NII scanning electron microscope equipped with an Oxford Incax-act SDD energy dispersive X-ray spectrometer. Analysis was performed at 15−20 keV with a 90 s acquisition time.

RESULTS AND DISCUSSION
3.1. Characterization of the CoCrMo Thin Film. QCM measurements indicated that sputtered CoCrMo films ranged in thickness from 200 to 300 nm. EDS confirmed that the chemical composition matched that of the bulk alloy, with approximately 66% Co, 28% Cr, and 6% Mo by weight. Crystallinity was confirmed with transmission electron microscopy (TEM) in another study 24 that showed the film to have longitudinal, nanocrystalline grains and a hexagonal close-packed (hcp) lattice. Although the microstructure differs from that of the bulk alloy, it is comparable to the deformed subsurface of MoM hip joints, which also exhibits a nanocrystalline hcp structure resulting from a strain-induced phase transformation. 25 To determine how the electrochemical behavior of the sputtered CoCrMo thin film compared to that of the bulk alloy, potentiodynamic tests were conducted on both specimens in a BCS electrolyte. As displayed in Figure 3, both materials exhibit similar electrochemical behavior, which is consistent with the reported literature data. 19,26,27 E corr and i corr of the bulk sample were −0.463 V and 1.85 × 10 −7 A/cm 2 , respectively, and E corr and i corr of the thin films ranged from −0.585 to −0.318 V and 3.79 × 10 −8 to 1.82 × 10 −7 A/cm 2 , depending on the sample. The qualitative features of the potentiodynamic scan for the bulk material can be used to divide the response into the following regimes: (1) a cathodic regime below ∼−0.6 V in which the current is determined by the reduction of water or dissolved oxygen; (2) a passive regime, extending from ∼−0.2 to ∼0.5 V, where the current is nearly independent of the applied potential, indicating the presence of a protective oxide; and (3) a transpassive regime above the breakdown potential at ∼0.5 V. The current peak and subsequent stabilization from 0.65 to 0.8 V is typically attributed to the oxidation of Cr(III) to Cr(VI), although the electrochemical behavior in this potential regime is poorly understood. 26−29 The electrochemical behavior above 1 V could not be studied because the thin film was destroyed under this aggressive oxidizing condition. Overall, the electrochemical behavior is characteristic of behavior previously reported for CoCrMo alloys. 26 The similarity between the bulk and thin-film responses is taken as evidence that the thin films are an accurate model for studying corrosion processes in CoCrMo alloys. The additional information provided by the QCM experiments with the thin films allows us to better understand the processes occurring in the different potential regimes introduced above and is the focus of the remainder of this Article.
3.2. Mass Change Behavior During the Corrosion of CoCrMo Thin Films. Mass changes on CoCrMo films were measured in situ during potentiodynamic tests in Ringer's solution, buffer solution, and BCS; the results are displayed in Figure 4 with the potentiodynamic response. Mass changes as a function of total charge released, obtained by integrating the current over time, are displayed in Figure 5. According to Faraday's law, the amount of mass lost during a corrosion process should scale linearly with the charge. In our notation, we write Faraday's law in the following way 21 where ΔM A is the change in mass per unit area, q a is the charge density in equivalents per unit area, and m q is the molar mass per charge ratio. Our sign convention here is that the current is positive during corrosion processes leading to decreases in the mass. Note that q A is obtained from the integrated charge by dividing by Faraday's constant (96 500 C/equiv). In situations where corrosion mechanisms are changing, the behavior cannot be characterized by a single value of m q . In these cases, we specify an effective value of m q from the slope of a plot of the mass change versus charge: Changes in m q eff indicate a change in corrosion mechanisms or in the valence state of the corroding species.
3.2.1. Ringer's Solution. In each electrolyte, specimens did not exhibit appreciable mass change below 0.4 V, although the current began to increase at 0.3 V. In Ringer's solution (Figure  4a), the alloy continuously lost mass as the potential increased above 0.4 V. Figure 5a illustrates that the alloy corroded with a constant value of 15 g/equiv for m q eff . This value is significantly lower than what would be expected from the ideal mass per charge ratio of the alloy, which can be determined from the following equation 21  (4) in which f i , n i , and a i are the mass fraction, valence state, and molar mass of each alloying element, respectively. If the alloy is considered to have a composition of Co-29Cr-6Mo with valence states of 2, 3, and 4 for the respective elements, 27 then a value of approximately 24 g/equiv is expected for m q . In contrast, if the valence states of the corroding species are considered to be 2, 6 and 6, respectively, then the theoretical m q ratio is 17, which is significantly closer to our measured value. The disagreement between the experimentally determined  value for m q eff and theoretically expected values for m q likely results from the formation of an oxide film in solution, which grows while the alloy is simultaneously corroding. These results are consistent with what was reported by Valero Vidal et al. 19 in PBS.

Buffer Solution.
In buffer solution (Figures 4b and  5b), the film displayed a more distinct passive regime between −0.4 and 0.2 V but again began to lose mass at 0.4 V with m q eff = 16 g/equiv. In contrast to the experiment in Ringer's solution, the film that was corroded in buffer solution exhibited a current peak and subsequent stabilization between 0.65 and 0.8 V.
Here, the rate of mass loss declined. As demonstrated in Figure  5b, m q eff dropped as low as 3.6 g/equiv between 0.75 and 0.85 V. Above 0.85 V, the rate of mass loss began to increase again with the current, approaching 18 g/equiv by the end of the potentiodynamic scan.
3.2.3. Bovine Calf Serum. As indicated in Figure 4c, the corrosion behavior in BCS was similar to that in buffer solution until the potential reached ∼0.8 V. At this point, a substantial increase in the mass was observed, despite the increased current that predicts mass loss. Because the behavior was not seen in Ringer's or buffer solution and was not reported by Valero Vidal in PBS, 19 mass gain presumably results from protein deposition. This deposited film persists to potentials up to about 0.93 V. At higher potentials, the underlying CoCrMo film corroded rapidly and was removed from the quartz crystal surface. The plot of mass change with charge ( Figure 5c) shows that the alloy initially lost mass with an m q eff of 13 g/equiv. The rate of mass gain was not linear with charge, and the rate of final mass loss was not consistent among the samples.

Dissipation Measurements.
Dissipation changes were also measured during potentiodynamic scans. In Ringer's and buffer solution, the dissipation remained relatively constant until the film began to lose mass. Neither the potential nor the degree of mass loss at which dissipation increased was consistent among the tests. In BCS, dissipation increased at approximately the same potential at which mass gain occurred. The ratio of the dissipation shift to frequency shift (ΔΓ/Δf) from a potentiodynamic scan in BCS is shown in Figure 6.
Surface roughness can increase dissipation and cause an incorrectly large mass gain reading on the QCM if surface cavities entrap fluid. 30−33 However, frequency shifts resulting from roughness for samples immersed in a liquid medium scale as n 1/2 , 34 which was not true of our samples. The presence of a viscoelastic (rather than rigid) material on the QCM surface can also enhance dissipation. If viscoelastic effects are small, meaning ΔΓ/Δf ≪ 1, then eq 1 holds and Δf scales with the harmonic order, n. If viscoelastic effects are significant, then ΔM A as calculated from eq 1 will depend on the harmonic and a viscoelastic correction factor must be included in the analysis. 18,35 In our experiments, as demonstrated in Figure 7, the value of ΔM A obtained from the Sauerbrey equation was the same for all three harmonics prior to mass deposition and during the initial stages of the mass deposition process. Above ∼0.85 V, ΔΓ/Δf became significant and ΔM A became dependent on n. Hence, we attribute the enhanced dissipation to the viscoelastic character of this adsorbed layer, which supports the hypothesis that the measured mass increase in BCS results from protein deposition. Additional information about the viscoelastic properties of the deposited layer can be obtained from a more detailed analysis of Δf and ΔΓ in this highly dissipative regime. 17,18,35 This analysis is the focus of an ongoing investigation.

Conditions for Mass Deposition on CoCrMo in BCS.
To determine if there is a critical condition that promotes mass deposition on CoCrMo in BCS, the potential applied to the film was increased from −0.8 V and held constant at various levels. The current density, total charge (current integrated over time), and potential were quantified at the points at which the initial mass loss occurred, the rate of mass loss decreased, the mass increase began, and the final mass loss began. No clear correlation existed between these processes and the current density or integrated charge. However, the potentials at each point of mass change were consistent and are provided in Table  1. Mass deposition begins at potentials near 0.77 V in all cases, always following the current peak and stabilization that is characteristic of the transpassive regime. Thus, it is presumed that mass deposition results from reactions between proteins and the ionic species that are formed near this potential.
The data also indicate that there is a maximum potential for which the deposited film will remain stable for extended periods of time. When the potential was increased from −0.8 V at a rate of 0.25 mV/s and then held at 0.83 V, the film experienced comparable deposition as during the complete potentiodynamic scan but maintained the layer throughout the test, as displayed in Figure 8a,b. In contrast, when the potential was held near the end of the mass gain regime at 0.91 V (Figure  8c), the film corroded in nearly the same manner as when the potential was continuously increased to 1.0 V, even though the current density was comparable to that at 0.83 V (data not shown).
3.4. Individual Alloying Elements. Potentiodynamic tests were also conducted on the pure alloying elements in BCS to determine if a particular ion is responsible for mass deposition on the alloy. Mass changes with potential variation are shown for each metal in Figure 9. Cobalt specimens (Figure 9a) monotonically lost mass as the potential increased. Mass loss began near −0.48 V as the current reached a plateau. The m q eff (Figure 10a) averaged 29.3 ± 4.2 g/equiv, approximately corresponding to the Co(II) oxidation state as expected. Chromium specimens (Figure 9b) gained approximately 3.7 mg/m 2 mass at 0.38 V but continuously lost mass beginning at 0.5 V. The mass gain at 0.38 V is 1 to 2 orders of magnitude smaller than on the alloy and corresponds to a stabilization in the current. Hence, it is likely attributed to an enhancement in the oxide thickness on the chromium surface. The initial value of m q eff (Figure 10b) was approximately 9 g/equiv, nearly corresponding to the dissolution of Cr(VI) ions, but decreased to 6.7 g/equiv above 0.85 V. Molybdenum samples (Figure 9c) exhibited significantly different mass change behavior than cobalt or chromium. The metal film began to lose mass as the potential reached −0.16 ± 0.02 V with m q eff = 15 g/equiv (Figure 10c), corresponding to the dissolution of Mo(VI) ions. As the potential neared 0.06 ± 0.02 V or the current density reached approximately 5 × 10 −4 A/cm 2 , specimens gained at least 450 mg/m 2 mass. Some specimens gained nearly 5000 mg/m 2 mass. The QCM signal was lost at ∼0.10 V because of the large frequency shift; therefore, tests were stopped at this potential. The mass did not increase on Mo films during potentiodynamic tests in either Ringer's or buffer solution. Our hypothesis based on these results is that Mo(VI) ions are critical to the initiation of mass deposition on both the Mo and CoCrMo surfaces.
Neutral Mo oxidizes to Mo(IV), forming MoO 2 according to the following reaction with water above the potential E 0 : 36 This reaction occurs spontaneously at all pH values relevant to our experiment, thus our assumption is that a thin layer of MoO 2 is always present at the metal surface. At higher potentials, Mo(IV) further oxidizes to Mo(VI) according to the following reaction: 36 The equilibrium reduction potential (vs SCE) for this reaction is 36     The measured potential at which oxidation to Mo(VI) occurs is consistent with eq 8 provided that possible changes in the local pH are accounted for. For example, if we assume [MoO 4 −2 ] = 8 mM and a pH equal to the starting pH of the BCS solution (7.6), then we obtain E 0 = −0.6 V from eq 8. At the opposite extreme, we can assume that the BCS solution has no buffering capacity so that the eight protons released by the combination of the reactions shown in eqs 5 and 7 contribute to the decrease in the local pH. In this case, the pH is reduced to ∼1 and we obtain E 0 = 0.182 V from eq 8. Not surprisingly, the measured potential range over which molybdate ions are released into solution is between these two extremes. Kinetic effects will also play a role here because the equilibrium conditions for which eq 8 can be applied quantitatively are not established under the corrosion conditions relevant to our experiments.
It is likely that any change in local pH that occurs upon oxidation of molydenum will induce changes in the surface charge of the Mo specimen and proteins in solution, leading to mass deposition from electrostatic adsorption. However, the magnitude of mass increase measured by the QCM is significantly greater than what would result from a monolayer of adsorbed proteins. For example, Ithurbide et al. found that the adsorption of albumin onto a passivated chromium specimen increased the mass on the surface by only 4 mg/ m 2 , which is 2 to 3 orders of magnitude smaller than what was measured in this study. 38 Thus, whereas the local protein/ substrate interactions may play an important role in the adhesion of the interfacial layer to the metallic substrate, the measured mass gain cannot be explained by adsorption processes that by definition are confined to the immediate vicinity of the metallic surface. It is more appropriate to think of the mass gain as resulting from the formation of some sort of interfacial phase that forms upon the release of Mo(VI) ions (presumably in the form of molybdates) into a solution that contains appropriate macromolecules. On the CoCrMo alloy, the mass gain occurs at potentials within the secondary passive regime where the electrochemical behavior is believed to be controlled by the oxidation of Cr(III) to Cr(VI). However, because mass deposition occurred only on the Mo films and not on Co nor Cr, we conclude that a release of Mo(VI) ions rather than Cr(VI) is necessary to forming the deposit on the CoCrMo surface.
3.5. X-ray Photoelectron Spectroscopy. XPS was used to assess the composition of the deposited layers on QCM specimens that exhibited material deposition without subsequent mass loss. The CoCrMo specimen was prepared by conducting a potentiodynamic scan in BCS from −0.8 to 0.83 V at 0.25 mV/s and then holding the potential at 0.83 V for 30 min. The Mo sample was prepared by conducting a potentiodynamic scan in BCS from −0.8 to 0.08 V. Subsequently, specimens were rinsed once in deionized water and twice in methanol and dried with a compressed air canister to remove any serum that may have simply adhered to the film. A typical survey scan of each surface is shown in Figure 11. The peak binding energy and atomic percentage of each element is included in Table 2. Data confirm that the deposited layer on both metals is primarily organic and derived from proteins: the N 1s peak near 400 eV corresponds to the binding energy of amine or amide bonds, and the N to total C ratio (0.22 ± 0.02 on CoCrMo, 0.23 ± 0.07 on Mo) is the same as that reported for bovine serum albumin powder. 38 Additionally, the decomposition of the C 1s peak (Figure 11b,d) shows evidence of carbon in an organic binding environment. For CoCrMo, the C 1s peak was decomposed into two peaks; the peak at 284.8 ± 0.03 eV corresponds to adventitious carbon, and the peak at 287.3 ± 0.34 eV corresponds to carbon in an amine or amide bond. 39 The C 1s peak on the Mo specimen was decomposed into three peaks. In addition to the adventitious carbon peak, a peak is present at 286.1 ± 0.06 eV, attributed to C−O and C− N bonds, 38,40 and at 287.7 ± 0.06 eV, attributed to peptide bonds. 41 Neither specimen exhibited an appreciable metallic contribution. High-resolution scans at Cr 2p (570−595 eV) and Mo 3d (220−240 eV) on the CoCrMo specimen did not detect either element. Our primary conclusion from these results is that the deposited layer is primarily organic, with a very small metallic component.

SUMMARY
An electrochemical quartz crystal microbalance was utilized to investigate the corrosion of CoCrMo thin films in Ringer's solution, buffer solution, and bovine calf serum. Films were prepared in a manner such that their microstructure and electrochemical behavior model those of MoM hip joint surfaces. The key findings emerging from this work are as follows: (1) If proteins are present in solution, then the QCM measures a mass increase on the alloy surface during corrosion at elevated potentials. (2) Typical values for the mass of the deposited film range from 50 to 200 mg/m 2 . (3) Material is deposited at a critical potential, 0.77 V, and can be maintained for some time at slightly higher potentials, suggesting that deposition results from redox reactions between oxidized alloying elements and proteins in solution. (4) Dissipation of the QCM signal increases with mass gain, providing evidence of a viscoelastic layer. (5) QCM measurements at multiple harmonics scale with the Sauerbrey equation prior to large increases in dissipation, indicating that mass gain measurements are real and not an artifact of roughness effects. (6) During the corrosion of Co, Cr, and Mo films in protein solutions, mass deposition was found only on the Mo films under conditions corresponding to the release of Mo(VI) ions into solution. From this, we infer that the mass gain results from interactions between Mo(VI) ions and proteins in solution. (7) XPS analysis of CoCrMo and Mo films after mass gain reveals a primarily organic surface, further supporting conclusions that mass gain results from protein deposition.
The organic film is reminiscent of tribochemical reaction layers that form on the surface of MoM hip bearings, suggesting the existence of local electrochemical pathways that promote the protein degradation essential for their formation. Because of the reproducibility of the experiments, these purely electrochemical experiments are very well suited for fundamental investigations of tribochemical processes that also involve mechanical forces. Further investigations are being undertaken in order to more completely understand the mechanisms involved in the formation of these electrochemically induced organic reaction layers in vivo and their effects on the tribological performance of CoCrMo alloys.