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Abstract

Among the various metallic implant materials, titanium (Ti) alloy is the best choice for the long-term hard body tissue replacements such as hip and knee joints. It has excellent mechanical, superior biological and strong anticorrosion properties. Besides the appropriate implant material, its surface topology also plays a very important role in the success of any surgery. The surface topology is supposed to be the key factor for the promotion of osseointegration. This research article focuses its attention mainly on surface modification of Ti-based alloys by electric discharge machining process. Electric discharge machining is one of the most popular nonconventional manufacturing methods. Besides machining and surface modification of implants, it finds applications in almost all areas of manufacturing industries. This article reviews the various research work done on surface modification of Ti alloy by electric discharge machining and attempts to bring out the current scenario along with future directions. The area under focus for this research review is orthopedics applications. Furthermore, a new promising advancement in the area of enhancement of electric discharge machining performance for surface modification, particularly with regard to biocompatibility and surface quality of biomaterials, has also been introduced.

Keywords

Titanium biocompatibility osseointegration surface modification electric discharge machining

Introduction

Need for joint replacement

Over the last several decades, demand for joint replacement has increased rapidly.¹ It is estimated that 90% of the people above the age of 40 years suffer from degenerative and inflammatory diseases. Problems such as weakening of the bones (osteoporosis), inflammation in the bone joints (osteoarthritis), inflammation of synovial membrane (rheumatoid arthritis) and weakening of cartilage (chondromalacia) cause degradation of bone in continuous cyclic loading conditions and, thus, may cause degradation of mechanical properties which results in annoyance and loss in function.² This contributes to a rapid growth in the number of surgical procedures involving prosthesis implantation. To solve these problems, total joint replacement (TJR) is the solution where load-bearing joints or dysfunctional joint is replaced with artificial joint or implant.³ Bio-implant is an artificial organ used for restoring the functionality of a dysfunctional natural organ or tissue of the body without adverse effect to other body parts. These can be implanted in the human body and let them become fixed and stable by natural biological self-bone formation process in order to improve the quality of life and longevity of human being.⁴ Among all these implants, the replacements of knee, hip and spinal cord are extremely high. Figure 1 shows a typical hip and knee joint replacement.

Figure 1.

Total hip and knee joint implant replacements.

Properties required for bio-implants

The selection of the right biomaterials for a specific biomedical application depends upon their comprehensive properties such as biodegradability, biocompatibility, mechanical properties, nontoxicity, corrosion or wear resistance and mainly on surface chemistry and morphology.⁵ A biomaterial must satisfy the following requirements.

Biocompatibility

Biocompatibility is determined by the surface characteristics of the implant material. The surface of biomaterials should be nontoxic and remain stable for a long time without causing any inflammatory or allergic responses. The ability of an implant material to withstand an appropriate host response in a specific situation measures the biocompatibility of a material.⁶

Mechanical properties

Bio-implants are taken to defy in the host body under repeated cyclic loads or stresses. It is important that an implant material mimics as closely as possible the mechanical properties of the natural bone, especially elastic modulus equivalent to that of bone (5–30 GPa).² Other properties such as hardness, tensile strength and elongation should also be kept in mind while selecting the material for implant.

Surface topography

The nano-porous structure of interconnected pores with controllable size is required, which increases the surface area and provides a vehicle to interface implant with large-scale cells and tissues. The size of porosity has a favorable impact on cell adhesion, proliferation and new bone formation.⁷ Controlled surface roughness and surface chemistry play a critical role in the formation of new bone ingrowths around implant.

Corrosion and wear resistance

The material of implant should have corrosion and wear resistance; otherwise, implant in body fluid may release ions causing allergic and toxic reactions.² The life of the implant is evaluated by its wear and abrasion performance. The low wear resistance causes loosening of implants and results in excessive pain and loss in functions.

Materials for bio-implant

To meet the joint replacement challenges, the development of various implant material has been witnessed, and the need of biomaterials is increasing rapidly.¹ The biomaterials are categorized as metallic, ceramics and polymers. Common metallic biomaterials are stainless steels (SUS-316L), cobalt-chromium (Co-Cr), titanium (Ti) and its alloys.⁸ The nonmetallic biomaterials are polymeric based such as ultrahigh molecular weight polyethylene (UHMWPE), polyethylene terephthalate, lactide-co-glycolide and polytetrafluoroethylene. Silicon carbide (SiC), silicon nitride (Si₃N₄/TiN), zirconium oxide (ZrO₂), titania (TiO₂), titanium carbide (TiC), titanium nitride (TiN), bioglass, hydroxyapatite (HA) and aluminum oxide (Al₂O₃) are examples of ceramic biomaterials.⁹ The mechanical properties of commonly used metallic implant materials compared with bone are summarized in Table 1.

Table 1.

Mechanical properties of metallic implant materials.⁴

Implant material	Microstructure	Ultimate tensile strength (MPa)	Elastic modulus (GPa)	Yield strength (MPa)
Bone	Viscoelastic	90–140	10–30	10–40
SUS-316L	Austenite	465–950	200	170–750
Cobalt alloy	Austenite	600–1795	275–1585	200–230
Mg	–	230	45	–
CP-Ti	(α)	785	105	692
Ti-6Al-4V	(α + β)	960–970	110	850–900
Ti-6Al-7Nb	(α + β)	1024	105	921
Ti-5Al-2.5Fe	(α + β)	1033	110	914
Ti-12Mo-6Zr-2Fe	Metastable (β)	1060–1100	74–85	1000–1060
Ti-15Mo-5Zr-3Al	Metastable (β)/aged (β + α)	882–975/1099–1312	75/88–113	870–968/1087–1284
Ti-15Mo-2.8Nb-3Al	Metastable (β)/aged (β + α)	812/1310	82/100	771/1215
Ti-13Nb-13Zr	(α′ + β)	1030	79	900
Ti-13Mo-3Nb-0.3O	Metastable (β) + silicides	1020	82	1020
Ti-35Nb-7Zr-5Ta	Metastable (β)	590	55	530
Ti-35Nb-7Zr-5Ta-0.4O	Metastable (β)	1010	66	976

Due to wear and corrosion in the human body environment, the released elements such as cobalt (Co), nickel (Ni) and chromium (Cr) of SUS-316 and Co-Cr are found to cause toxicity within the individual.² In addition to this, ceramics and SUS-316 exhibit higher Young’s modulus and lower fracture strength than bone.¹⁰ Ti and its alloys gained more attention in recent scenario, due to their superior biocompatibility and excellent mechanical properties especially low Young’s modulus, high fatigue performance, high corrosion resistance and low density as compared with other metallic biomaterials.² Earlier, CP-Ti and Ti-6Al-4V were proposed as biometals by the medical industries.¹⁰ But the presence of Al and V restricts the applicability of Ti-6Al-4V because during abrasion, it releases ions and creates cytotoxicity which results in allergic reactions.¹¹ Despite this fact, the results of CP-Ti and Ti-6Al-4V cannot satisfy the requirements of biomaterials. So, the researcher developed biocompatible V andAl-free β-phase Ti alloy such as Ti-Nb,¹² Ti-Zr,¹² Ti-Nb-Zr,¹³ Ti-Nb-Ta-Mo,¹³ Ti-Nb-Ta-Sn¹³ and Ti-Nb-Ta-Zr (TNTZ) alloys to overcome the toxicity of titanium–vanadium-based alloy.¹⁴ Very recently developed β-type Ti alloys have lower elastic modulus of 55 GPa (near to bone 20 GPa), high strength, low density, excellent biocompatibility, good corrosion and wear resistance than CP-Ti and Ti-6Al-4V.¹⁵

Corrosion fatigue behavior of metallic biomaterial

Titanium and its alloys are used for the preparation of implant and instruments used for clinical uses, such as plates, screws and nails, which always serve under cyclic load condition and sometimes fail due to fatigue and corrosion. Fatigue and corrosion fatigue performance are very important mechanical properties of the Ti alloys for biomedical application. Biomedical implants are subjected to pitting and crevice corrosion when intact with the aggressive environment of the body. From the beginning, stainless steel has been used in orthopedic applications. The failure of stainless steel by corrosion fatigue has been studied by Amel-Farzad et al. The dynamic condylar screw (DCS) barrel plate failed due to crevice corrosion.¹⁶ Tavares et al. investigated the root causes of premature failure of stainless steel as orthopedic implant was removed from the patient’s body. The premature failure had occurred due to corrosion fatigue initiated by the high surface roughness. Pitting intergranular corrosion occurred in stainless steel–based implant under corrosion fatigue environment. Stainless steel releases ions and gets oxidized causing toxic and allergic reactions, leading to cause failure of implant.¹⁷ Pitting corrosion occurred in cobalt-based alloy.^18,19 Sudhakar et al. investigated the failure of cobalt alloy–based bone plate by corrosion fatigue. Crevice and pitting corrosion was found at the fractured surface after removal of the implant from the host body.²⁰ There are well-documented reports on the failure of cobalt-based implants by corrosion fatigue.²¹ The crack growth was predicted under air or corrosive environment accelerated by fatigue performance. Moreover, recently, a case report pointed out the failure of cobalt-based femoral neck component of total hip arthoplasty. This was the first reported instance of Co-Cr modular neck failure. Co-Cr-based modular neck was subjected to fretting corrosion.²² Figure 2 shows the failed modular neck of total hip arthoplasty. Figure 2(a) represents the enlarged view of the fracture site in the modular neck (the distal part is still in the female part of the Morse taper of the stem), and Figure 2(b) represents the proximal piece that has been turned over in the horizontal plane, and the two white arrows indicate the anterior and medial parts of the removable cone.

Figure 2.

Failure of Co-Cr based modular neck (a) Represents the enlarged view of the fracture site in the modular neck (the distal part is still in the female part of the Morse taper of the stem). (b) Proximal piece has been turned over in the horizontal plane, and the two white arrows indicate the anterior and medial parts of the removable cone.

Fleck and Eifler studied the fatigue behavior of Ti alloy in air and Ringer’s solution. The fatigue performance in Ringer’s solution is less compared to air. The fatigue performance of (α + β)-type Ti-6Al-7Nb and Ti-6Al-4V was found higher than that of CP-Ti.²³ The fatigue performance of Ti alloys depends upon the microstructure,^24–26 processing technique²⁷ and heat treatment methods.²⁸ So, the fatigue and the corrosion fatigue performance of Ti alloy vary accordingly. The fatigue crack growth behavior of Ti-6Al-4V in the air and NaCl solution was studied in detail.²⁹ The authors studied the fatigue behavior of Ti alloy with distinct microstructure obtained with different heat treatment processes. The results obtained from the study showed that the crack growth increases in saline solution as compared to air. Gregory³⁰ reported that the crack growth accelerated the corrosion fatigue failure in the aggressive body environment. Lee et al.³¹ investigated the corrosion fatigue performance of Ti-6Al-4V in vacuum, air and 3.5% NaCl solution. They found that the crack growth was much higher in air and saline solution than in vacuum. In addition to these, they also pointed out the effect of microstructure on the fatigue performance of the Ti alloy. Niinomi et al. studied the fatigue behavior of Ti-5Al-2.5 Fe alloy in air and Ringer’s solution and compared it with Ti-6Al-4V extra low interstitial (ELI) alloy. The crack growth was accelerated slowly in air for both materials, and from the plots of da/dN versus ΔK, the pure corrosion fatigue behavior was observed in both the materials.³² Williams and Chawla³³ recently reported the failure of Ti-6Al-4V-based hip implant neck by fretting and crevice corrosion. The fretting and crevice corrosion reduces the fatigue strength of Ti-based neck of hip implant. The fatigue crack growth was created by the aggressive body fluid which accelerates the crevice corrosion resulting in failure of the joint. Figure 3 shows the image of fractured neck of the hip joint and presents the evidence of superficial fretting corrosion. From the best knowledge of the authors, most of the published literature available on the failure of Ti-6Al-4V-based implants occurred at the neck.^34–42 Paliwal et al. reported the fatigue failure of three cementless Ti-6Al-4V-based hip stems. The main cause of the failure was surface cracks during fretting fatigue.⁴³ In another study, the hydrogen embrittlement was found to be the main cause for the fretting and corrosive corrosion.⁴⁴ Yokoyama et al.⁴⁵ also reported that Ti-based dental implant becomes brittle and fracture following the exposure to hydrogen. In the case of Ti-6Al-4V alloys, the vanadium ions dissolve and release by crevice corrosion in the aggressive environment of the body, causing an allergic reaction leading to adverse effect to human tissues. In the replacement of harmful vanadium (V) and aluminum (Al) elements, the establishing alloying elements niobium (Nb), tantalum (Ta) and zirconium (Zr) have been offered as an alternative with excellent biocompatibility.^28,46–48 Rubitschek et al.⁴⁹ studied the corrosion fatigue behavior of ultrafine-grained NbZr alloy. The NbZr alloy offers no crack imitation at high cycle corrosion fatigue tests in simulated body fluid (SBF).

Figure 3.

(a) Optical photograph of the fracture surface of the neck that remained in the stem. The surgical damage was created by a tool used to remove the implant from the body. (b) Optical photograph of the fracture surface of the neck that remained attached to the head. Post-fracture damage occurred when the fractured neck slid across the inside of the stem’s taper surface. (c) Exploded model of the modular hip implant, showing where neck fracture occurred. Both the neck and stem were made of Ti-6Al-4V.

Akahori et al. studied the fatigue behavior of TNTZ alloy and compared its performance with Ti-6Al-4V ELI and Ti-6Al-7Nb alloys in air and Ringer’s solution. The specimens were prepared with distinct conditions. The plates are designated as TNTZ_CR when these solutionized bars were cold rolled to the plates with a thickness of 2.5 mm and by a reduction ratio of 87.5% at ambient temperature. These plates are designated as TNTZ_ST when solutionized at 1063 K for 3.6 ks in Ar gas atmosphere followed by water quenching (WQ). The specimens did not fail up to 10⁷ cycles in air at room temperature. Figure 4 shows the comparison of Ti alloy with distinct treatment conditions. The results show that the fatigue strength of a TNTZ alloy increases as the aging temperature increased. The fatigue performance of Ti-6Al-4V ELI equiaxed α is higher than other Ti alloy which is around 880 MPa. The fretting fatigue of TNTZ_ST and TNTZ_ST aged at 673 K was also studied in Ringer’s solution. It was found that TNTZ alloy is not degraded in Ringer’s solution.⁵⁰ Baptista et al. studied the corrosion fatigue behavior of another type of β-phase Ti alloy (Ti-13Zr-13Nb) in air and 0.9 wt% NaCl solution. It was found that the alloy was insensitive to both the environments.⁵¹ Boehlert et al.⁵² have also reported the insensitivity of β-phase-type Ti-15Al-33Nb and Ti-21Al-29Bn alloys against corrosion fatigue.

Figure 4.

S-N curves of TNTZ_ST, TNTZ_CR and TNTZ_ST, and TNTZ_CR conducted with aging at 598, 673 and 723 K for 259.2 ks with those of Ti-6Al-4V ELI and Ti-6Al-7Nb in air.

Need for surface modification

Despite their excellent mechanical properties, Ti-based implants have the shortcoming of inability to meet the requirements of osseointegration, that is, the incomplete bonding between the implant and the surrounding tissues. The surface of implant needs to be subjected to some mechanical treatments to maximize its bioactivity when interfacing with surrounding natural tissue. Surface modification is required for better stability and biological fixation of the implant, so that a homogeneous stress transfer takes place between bone and implants. Surface modification is a process of alteration of the key bulk properties of the material by removing or addition of material on the surface of implant.⁷ In other words, surface modification is basically required for successful bone regeneration and healing. The main events after implantation include adaptation of surrounding tissues and start bone formation by the biological self-healing process. The interaction between the bone and the implant surface at different topographical scales is shown in Figure 5.

Figure 5.

Schematic representation of the interactions between bone and implant surface at different topographical scales.

The past research work shows that surface properties play a critical and a very important role in new bone formation⁵³ and further growth of tissues.⁵⁴ Surface properties such as surface roughness,⁵⁵ surface topography,⁵⁶ surface porosity,⁵⁷ surface chemistry^58,59 and surface energy^60,61 have found significant impact on new tissue generation and collagen or protein absorption during in vivo or in vitro study.^62,63 The surface roughness has been categorized into three different scales, namely, macro (100 µm < R_a > millimeters), micro (1 µm < R_a > 100 µm) and nano (100 nm < R_a > 1 µm).^64,65 These different scales of surface roughness have their own impact on bone ingrowths.⁵⁶ Generally, micro-scale rough surface is preferred because large surface indentations provide a better interaction of implant to the surrounding bone tissues.⁶⁶ This large to surface volume provides a vehicle to interface implant with large-scale cells and tissues;⁶⁷ thus, macro-roughness usually promotes cell adhesion and their spreading.⁶⁸ However, it was found that the surface of micro-scale roughness indentations is an arguable characteristic promoting cells and tissues around implant surface.⁶⁹ Over the last several decades, few researchers have drawn their attention toward the surface with nano-scale roughness irregularity.⁷ It was found that nano-scale surface roughness of the material surface has been considered as the most advantageous and advisable factor for the formation, adhesion, growth and differentiation of new bone cells.⁷⁰ The cell reacts with nano-scale surface and their surrounding.⁷¹ The growth behavior of rat calvaria bone cell on the surface with nanometric features was found.⁷² The nano-structured surface increased the function of osteoblast or cell growth.⁷³

The proper and appropriate surface treatment or modification not only adds or removes material on the implant surface but also improves surface morphology and chemistry as per required by different biomedical applications. Table 2 presents the various surface modification techniques used to enhance the performance of implant.⁸ The design and development of surface modification techniques such as plasma spraying,⁷⁴ physical vapor deposition (PVD),⁷⁵ chemical vapor deposition (CVD),⁷⁶ nitriding,^77,78 anodization⁷⁹ and laser cladding⁸⁰ are essential for improving their surface quality. However, the practice of using these techniques as surface modification for Ti alloys frequently becomes ineffective over a long duration due to poor adhesion and low physical bond strength and enables to serve under cyclic loading condition in a corrosive environment.² These techniques required surface preparation before coating such as shot peening (SP) and grit blasting, which increases the processing cost. More recently, the importance of electric discharge machining (EDM) has been widely acknowledged in fabricating nano-structured biocompatible surface and has found favorable impact on the biological attachment of human osteoblastic cell.⁸¹ EDM is a potential candidate to produce biocompatible surfaces. There is no requirement of surface preparation before EDM and also converts the surface into an oxide layer of controlled thickness, which in turn increases the biocompatibility of the substrate surface and provides a better vehicle for cell attachment and growth. In comparisons to the other surface modification techniques, EDM offers the formation of carbides on the top machined layer which increased the hardness (Hv),⁸² wear⁸³ and corrosion resistance⁸⁴ of the material surface. Apart from this, complex geometry and three-dimensional shapes can be easily fabricated by EDM process. EDM is a nonconventional machining process and has been widely used to machine hard and tough materials which are difficult to machine by conventional machining method. It uses repeated series of electrical discharges to machine the conductive materials. In EDM process, there is no direct contact between the tool and the workpiece. So, vibration and chatters are almost 0, and thus, any conductive and complex shapes within very close tolerances can be machined or manufactured or modified easily.⁸⁵ Because of all these advantages, it finds applications in mold, die, automotive, aerospace and medical industries.⁸⁶

Table 2.

Surface modification techniques for titanium alloy as biomedical implant.⁸

Sr. no.	Surface modification methods	Modified layer	Objective
1	Mechanical methods: machining, grinding, polishing or blasting	Rough or smooth surface formed by subtraction process	Produce specific surface topographies; clean and roughen surface; improve adhesion in bonding
2	Chemical methods: acidic treatment, alkaline treatment or hydrogen hyperoxide treatment	<10 nm of surface oxide layer; ~1 µm of sodium titanate gel; ~5 nm of dense inner oxide and porous outer layer	Remove oxide scales and contamination; improve biocompatibility, bioactivity or bone conductivity
3	Sol–gel	~10 µm of thin film, such as calcium phosphate, TiO₂ and silica	Improve biocompatibility, bioactivity or bone conductivity
4	Anodic oxidation	~10 nm to 40 µm of TiO₂ layer, adsorption and incorporation of electrolyte anions	Produce specific surface topographies; improve corrosion resistance; improve biocompatibility
5	Chemical vapor deposition	~1 µm of TiN, TiC, TiCN, diamond and diamond-like carbon thin film	Improve wear resistance, corrosion resistance and blood compatibility
6	Glow discharge plasma	~1 to ~100 nm of surface-modified layer	Clean, sterilize, oxide, nitride surface; remove native oxide layer
8	Biochemical methods	Modification through silanized titania, self-assembled monolayers, photochemistry, protein resistance, etc	Induce specific cell and tissue response by means of surface immobilized peptides, proteins or growth factors
9	Physical methods: thermal spray, flame spray, HVOF, D-Gun	~30 to 200 µm of coatings, such as titanium, HA, calcium silicate, Al₂O₃, ZrO₂, TiO₂	Improve wear resistance, corrosion resistance and biological properties
10	PVD: evaporation, ion plating or sputtering	~1 µm of TiN, TiC, TiCN, diamond and diamond-like carbon thin film	Improve wear resistance, corrosion resistance and blood compatibility
11	Ion implantation and deposition; beam-line ion implantation and P-III	~10 nm of surface-modified layer and/or ~µm of thin film	Modify surface composition; improve wear, corrosion resistance and biocompatibility
12	Glow discharge plasma treatment	~1 to 100 nm of surface-modified layer	Clean, sterilize, oxide, nitride surface; remove native oxide layer

HA: hydroxyapatite; PVD: physical vapor deposition; HVOF: high-velocity oxygen fuel; D-Gun: Detonation-Gun.

A number of studies are available for the machining of aerospace superalloy⁸⁷ and titanium alloy⁸⁸ by EDM process. Ndaliman et al. investigated the influence of two dielectric fluids on the enhancement of surface properties of Ti-6Al-4V alloy by EDM process. Urea solution and distilled water were used as dielectric fluids, and Cu-TaC was used as electrode. It was found that the distilled water dielectric gave a better surface finish and the urea solution enhanced the surface hardness.⁸⁹ The performance of a special grade of graphite electrode was investigated in the machining of Ti-6Al-4v alloy by EDM. The best results were obtained at negative polarity of the electrode, and TiC was found in the recast layer regime.⁹⁰ Surface integrity, surface topography and electrochemical corrosion resistance of intermetallic titanium aluminide (γ-TiAl) were investigated after EDM process. Copper, graphite and aluminum were used as a tool electrode for surface treatment of γ-TiAl alloy. It was found that the graphite electrode produces carbide phases on the machined sample, and aluminum creates oxides. The samples machined by graphite offer more corrosion resistance than copper and aluminum.⁹¹ The process capability of Ti and its alloy by wire-electric discharge machining (W-EDM) has been studied by various authors. Pure Ti⁹² and Ti-6Al-4V⁹³ alloy have applications in aerospace, marine and biomedical industries and can be processed very precisely by W-EDM process. Three different grades of Ti and its alloys are machined using EDM after deep and shallow cryogenic treatment.⁹⁴ Due to deep and shallow cryogenic treatment, the thermal conductivity of the material was increased, as a result of which, increase in material removal was observed. Some elements were found in energy-dispersive x-ray spectroscopy (EDS), which shows the existence of material migration phenomena. The improvement in the fabrication accuracy of microhole in Ti-6Al-4V alloy by changing polarity in micro-EDM has been attempted recently, which has tremendous applications in biomedical microdevices and automotive, aerospace and microelectromechanical systems.⁹⁵

In the EDM process, a number of efforts have been made in the past to enhance its performance for surface modification. These are (a) rotary motion or orbital motion to electrode;^96,97 (b) ultrasonic vibration assisted^98,99 and (c) powder mixed additive in dielectric fluid of EDM.^100–104 Among all these, powder mixed electric discharge machining (PMEDM) is extremely used, and a number of studies are available on the enhancement of EDM performance by adding conductive or semi-conductive micro-sized¹⁰⁵ and nano-sized powder.¹⁰⁶ Furthermore, Tan and Yeo explored that nano-sized powder mixed dielectric in micro-EDM plays a very vital role to enhance the surface quality and surface properties of workpiece specimen. The effect of nano-powders on surface roughness and recast layer thickness was studied. Low powder concentration, low sub-microsecond pulse duration and tool electrode rotation have shown a significant effect on the reduction of recast layer thickness.¹⁰⁷ Furthermore, they found the application of PMEDM for enhancing the surface hardness of stainless steel and titanium alloy. Tantalum carbide (TaC) powder at a concentration of 25 g/L was added to kerosene dielectric fluid to enhance the surface properties of stainless steel and the surface with improved hardness, and a high corrosion resistance was found.¹⁰⁸ The surface hardness of Ti alloy (Ti-6Al-4v) was enhanced by the use of 10 g/L urea concentration with Cu-TaC electrode. The highest micro-hardness of Ti alloy of 1795 Hv was achieved.¹⁰⁹

After the thorough scrutiny of the available literature on the use of Ti alloy after its machining and surface modification by EDM process, it has been concluded no research article is available which can summarize the latest developments along with the application and future trends in use of EDM for machining and surface modification of Ti alloy for biomedical applications. Thus, this research article summarizes the critically reviewed available literature on machining of Ti alloy by EDM for orthopedic applications. Current review initially describes that among Ti alloys, β-phases are the ultimate choice for biomedical applications. It also describes why surface modification of implant is required prior to implantation in the host body. In section “EDM,” the potential of EDM for surface modification of metallic implants has been explored. Section “Historical perspective for surface modification of metallic implants by EDM” traces the historical view of the diligence of Ti alloy machined or modified by EDM. A new innovative methodology which so far has not been used for surface modification of bio-implants is introduced in section “An innovative method for surface modification by material migration in EDM.” The application and future trends are followed by concluding remarks.

EDM

EDM involves the removal of material from workpiece by thermal energy created by a series of high-frequency electrical sparks between the tool and the workpiece. The conventional representation of the experimental setup is presented in Figure 6. The tool and workpiece maintained a very small gap in dielectric fluid. Figure 7 shows the concept of spark erosion in EDM process.¹¹⁰ When a voltage is put up at a small gap, a high strength electric field is set up, which ionizes the dielectric fluid. Plasma channels are generated, and electrical discharges at very high frequency take place at least resistance point between the electrode and the workpiece. Due to this, a very high temperature around 20,000 °C is generated causing to melt the material from both the tool electrode and the workpiece.¹¹¹ As a result, small craters are formed on both the tool electrode and the workpiece surface. After the final stage of discharge duration, the temperature of plasma drops rapidly,¹¹⁰ and the resulting products of spark erosion are cooled and flushed away in the form of debris,¹¹² and few remain solidified on the surface of the workpiece in the form of a recast layer which is composed of oxides and various carbides.^113,114Figure 8 shows the schematic representation of the principle of spark erosion in EDM process by voltage and current waveform. The electrical sparks that follow are transferred to the next discharge to come about in the closest spot far from the previous release to maintain EDM process stability. Such a discharge location may be the spot where the gap is small or contaminated with eroded debris particles which may weaken the breakdown strength of dielectric liquid.¹¹⁰ Accordingly, the pulse interval (pulse-off) time between pulse discharges must be sufficiently long, so that the plasma generated by the previous discharge can be deionized, and the dielectric breakdown strength around the previous discharge location can be recovered by the time the next pulse voltage is applied.¹¹⁰ The material removal in EDM process is still arguable.¹¹⁵

Figure 6.

Typical experimental setup for EDM process.

Figure 7.

Concept of spark erosion in EDM.

Figure 8.

Principles of spark erosion in EDM process.

Historical perspective for surface modification of metallic implants by EDM

EDM process has been widely used to machine and modify the surface of new intelligent and hard materials. EDM is attracting broad interest in the current research scenario for surface modification of metallic implants for biomedical applications.¹¹⁶ Ti and its alloys are one of them and extremely used in biomedical applications. The use of Ti and its alloy is increasing because of their excellent properties and biocompatibility, which has already been discussed in detail in the previous section. This section identifies the use of EDM in the past to improve the biocompatibility to enhance its biological applications.

Enhancing the osseointegration

EDM has been able to improve the surface properties of implants, in such a manner that the healing time is shortened and the bone formation increases. Following studies have been critically reviewed on the capability of EDM in in vitro and in vivo behavior.

In vitro cast study

Numerous studies have reported on EDM as surface modification method for improving the osteoconductivity of titanium and other alloys. The effect of cell attachment, proliferation and differentiation of human osteoblastic cell has been shown in in vitro analysis. Chen et al.⁸¹ have examined the potential of EDM to modify the surface of Fe-Al-Mn alloy for orthopedics application and dental applications (Figure 9). It is clear from Figure 9 that the surfaces treated by EDM provide better and potential surface for osteoblastic cell attachment. It was also observed that cell highly adopted the specimen treated by EDM after 24 h of cell culture times. The nano-porous surface of Ti implant modified by EDM has found a favorable impact on the adhesion and proliferation of human osteoblast-like MG-63 cell responses to the specimen.^117–119Figure 10 shows the scanning electron microscope (SEM) images of MG-63 cell attachment and proliferation on the unmachined and EDM-treated surface. The cells were widely spread and completely covered the unmachined surface and electric discharge machined (EDMed) surface. It was found that EDMed surface shows the higher growth factor for the attachment of human osteoblastic cells (MG-63).

Figure 9.

SEM image of Fe-Al-Mn alloy attachment after 24 h of culture times.

Figure 10.

MG-63 cells attachment and proliferation on the (a) Untreated specimen. (b) EDMed specimen (at 10µs pulse duration). (c) EDM specimen (at 60µs pulse duration) after day 7 of cell culture.

The biological response in terms of osteogenic gene expression of mesenchymal stem cells on Ti surface processed by W-EDM was investigated by Tamaki et al.¹²⁰ Titanium surface processed by W-EDM promotes the cells attachment. Furthermore, Otsuka et al.¹²¹ also explored the effect of surface topography and chemistry of Ti surfaces machined by W-EDM on the attachment and proliferation of MC3T3-E1 cells. Figure 11(a) and (b) shows an SEM image of the cell attachment morphology and spread of MC3T3-E1 cells cultured for 3 days on conventional machined surface and EDM surface, respectively. MC3T3-E1 cells attached with EDM-treated samples and proliferation reveals that cell numbers increased significantly on the EDM surfaces as compared to the machined surfaces. It was found that cells were elongated in all directions, and pseudopodium-like structures were observed on EDMed surface. The cells were polygonal in shape, with many thin filopodia attached to the Ti surface treated with EDM process.

Figure 11.

(a) SEM image showing the morphology of spread MC3T3-E1 cells cultured for 3 days on a machined surface and (b) morphological assessment of cells cultured on an EDM surface.

A possible application of EDM to fabricate rough biocompatible surface for orthopedic applications was reported by Harcuba et al.¹²² They reported that carbon-enriched highly macro-roughness has a favorable and better surface for adhesion and proliferation of human osteoblast-like MG-63 cells and compared with the sample prepared by plasma sprayed with TiO₂ as represented in Figure 12. Strasky et al.¹²³ reported in their research that the Ti-6Al-4V alloy surface has been modified by combining EDM, acid etching and SP to fabricate biocompatible surface suitable for osteoblast proliferation. The treated surfaces were characterized by SEM and EDS. This work demonstrates that surface morphology has the micro-, macro- and nano-scale structures, which play an important role to promote osseointegration. MG-63 cells were seeded on machined surfaces, and the results show that the introduction of such structures enhances osteoblast differentiation and local factor production. Furthermore, a novel approach has been adapted by Havlikova et al.¹²⁴ to improve the biological performance of Ti-6Al-4V alloy for orthopedic applications by three-step mechanical treatments using the combination of conventional machining processes (SP and chemical milling (CM)) followed by EDM. The surface is modified to provide a more suitable and favorable surface for adhesion and proliferation of human osteoblast-like MG-63 cells.

Figure 12.

(a–c) MG-63 cells in cultures on polystyrene dishes, (d–f) Ti-6Al-4V treated with plasma spraying, (g–i) EDM and (j–l) EDM with subsequent annealing on (a, d, g, j) day 1, (b, e, h, k) day 3 and (c, f, i, l) day 7 after seeding.

Evaluation by in vivo

Carbon-enriched oxide surface has been fabricated on Ti-based implant.¹²⁵ White rabbits are sacrificed in this in vivo analysis. Bone formation response has been observed around EDMed titanium surfaces with different oxide layer thicknesses and sub-micro-meter topography. Furthermore, Yamaki et al.¹²⁶ also studied the bone biocompatibility in vivo. A biocompatible micro-fabricated surface with an irregular morphology was fabricated by W-EDM process as seen in Figure 13 (a) and (b), which show an SEM image of EDM surface and machined surface, respectively. The bone formation around screw shape implant processed by EDM and conventional machining process was investigated by in vivo study using four Japanese white rabbits. Figure 14 represents that higher bone formation takes place around implant processed by EDM than that at machined surface implant. Thus, EDM seems to be a possible technique for surface modification of the implants to support enhanced osseointegration.

Figure 13.

SEM images of the surface morphology of (a) EDM surface and (b) machined surface.

Figure 14.

Micro-CT images of EDM-treated implant surrounded by bone tissue at (a) 0, (c) 1, (e) 2 and (g) 4 weeks of post-implantation and machined implant at (b) 0, (d) 1, (f) 2 and (h) 4 weeks of post-implantation.

Enhancing surface integrity

Controlled surface roughness

The spark-eroding process generates the rough oxide surface containing titanium-, oxygen- and carbon-enriched layers. They found that surface roughness allows bone formation and bone fixation due to surface modification of high roughness values (R_a≈ 7.8 µm).¹²² Under the controlled machining condition, surface roughness has been reduced by micro-EDM. The surface roughness was achieved within the recommended values of R_z and R_a of 3.4 and 0.4 µm, respectively, for biological studies such as implant abutment.¹²⁷

Carbon-enriched highly rough surface at the macro-scale on the Ti-6Al-4V alloy can also be fabricated by the EDM process using high peak current. The graphite electrode with high peak current of 21–79 A was used for rough machining. This makes chemical changes to surface of titanium, and this form of imposing macro-roughness (15.6 µm) has a favorable and a better surface impact on the adhesion and proliferation of human osteoblast-like MG-63 cells.¹²² An effort of the combined effect of CM and SP with EDM has been covered to melt off the surface roughness that is achieved by EDM process.^123,124 Micro- and sub-micro-surface roughness and structure are favorable for orthopedic applications. Surface roughness of samples evaluated by combining (EDM + SP + etching) process was 2.7 µm. The nano-porous biocompatible surface with roughness value 184 nm has been fabricated on titanium alloy by EDM by Peng et al. The surface of nano-scale features has a favorable impact on osteoblastic responses.¹¹⁸

Surface chemistry and topology

The formation of nano-porous biocompatible layer on titanium by EDM was studied by Peng et al.¹¹⁷ It discussed that how EDM generates an α-phase and a γ-TiH-(γ-hydride)-phase on the recast layer by electrical discharging. Among the EDM parameters, the most important parameters are electric current density and pulse duration in the fabrication of biocompatible nano-porous surface. Nano-(δ + γ) hydrides play important role in the formation of nano-porous oxide layers. A γ-hydride microstructure was also formed on the recast layer following electrical discharging. Electric discharging for a short duration leads to the production of thick and nano-porous TiO₂ bioactive layer on titanium. Figure 15 shows the SEM photographs of nano-porous TiO₂ bioactive layer on titanium by EDM process at a scale of 200 nm.¹¹⁷

Figure 15.

SEM photograph of nano-porous TiO₂ bioactive layer on titanium by EDM process.

Bin et al. explored the potential of EDM for surface modification of titanium alloy by electro-spark alloying (ESA). They investigated the ESA layers on Ti surface produced in air, nitrogen gas atmosphere and silicone oil as dielectric medium.¹²⁸ The thickness of ESA layer was found to be 10–20 µm. The layer obtained under silicone oil was a relatively smooth and dense surface with outstanding wear and corrosion resistance. Figure 16 shows the SEM photographs of ESA layer on Ti surface in air, N₂ and silicone oil. The surface obtained in silicone oil during EDM machining was found to have good biocompatibility and was biologically active. The properties of Ti-6Al-4V alloy after EDM treatment have been investigated.

Figure 16.

SEM of surface and cross section of ESA layer: (a and d) ESA in air, (b and e) ESA in N₂ and (c and f) ESA in silicone oil.

Surface roughness, distinctive irregular features and dense oxide layer were observed on the Ti surface by W-EDM process, which makes surface active for the interaction of osteoblastic cells.¹²¹ Graphite electrode with high peak current of 21–79 A was used for rough machining. This causes chemical changes to surface of titanium. Figure 17 shows the carbon-enriched highly rough macro-level surface layer after EDM process.¹²² Micro- and sub-micro-surface roughness and structure are favorable for orthopedic applications (Figure 18). A very high content of carbon and oxygen can be found on the machined surface during EDM treatment that was transferred from hydrocarbon oil. The titanium oxide (TiO₂) fabricated due to the interaction of Ti and O present in the etchant and SP medium. This is because, Ti is an element with high chemical affinity, and during machining process, it is oxidized and forms titanium oxide, so different compounds of titanium oxides and titanium carbides are created on machined surfaces. Increased content of titanium oxide may have a positive effect on the bioactivity of the surface. EDM and subsequent CM lead to a significant improvement of osteoblast proliferation.^123,124

Figure 17.

SEM image of carbon-enriched surface.

Figure 18.

SEM images of the material surface after (a) EDM, (b) EDM + CM, (c) EDM + SP2 and (d) EDM + CM + SP2.

Enhancing the mechanical properties

Fatigue performance

The application of EDM for surface modification of biomaterials has been limited due to its poor fatigue performance.¹²⁹ It is a known fact that high surface roughness and surface micro-cracks after EDM processing decrease fatigue performance due to high notch sensitivity. This has been caused by tensile stresses in near heat-affected region, micro-cracks and high surface roughness. This performance can be further improved by suitable heat treatments.¹³⁰ An attempt has been made by Strasky and colleagues^123,124 to improve the biological and fatigue performance. They have reported a combination of conventional machining techniques (SP and CM) followed by the EDM process to improve the poor fatigue strength of Ti-6Al-4V alloy. It was observed that EDM has least fatigue strength, and this performance would improve if the samples were prepared by a SP process followed by EDM process. Electro-polished standard samples have highest fatigue strength compared to EDM and EDM + SP. Furthermore, high fatigue strength was observed in combination of CM followed by SP and EDM. This proposed combination approach of EDM + SP + CM offers a potential surface for orthopedic applications. Klocke et al. reported that Ti-6Al-4V alloy treated by W-EDM offers higher fatigue performance than grounded. In 10%, 50% and 90% probability of failure, the W-EDM-treated samples offered higher fatigue limit stress than grounded samples.¹³¹ The fatigue performance of Ti-6Al-4V alloy was studied for micro-specimens and compared with Inconel alloys. It was found that Ti alloys exhibit higher fatigue performance than Inconel alloys.¹³² Mower¹³³ described in his study that EDM degrades the fatigue performance of the alloy by 15%–30% of milled samples. Intrinsic fatigue failure occurred due to crack initiation at interior location. The high surface roughness and thick recast layer were the major reason for the degradation of fatigue performance.

Enhancing micro-hardness, wear and corrosion resistance properties

Bin et al. investigated the deposition of TiC on Ti alloy by electrical discharge alloying graphite electrode. The surface micro-hardness was measured, and it was found that it improves by 3.5 times the initial. The high amount of induced hard TiC possessed excellent wear and corrosion resistance in SBF solution.¹²⁸

Summary of current research issues and future directions

The role of EDM process in recent investigations has demonstrated the potential to fabricate the biocompatible nano-porous surface on Ti and its alloy. The surface produced by EDM has superimposed topography that may offer a more suitable surface for osteoblast proliferation and improved implant fixation. EDM process modifies the Ti surface into various types of oxides and alloying elements. The primary aim is to produce biocompatible porous oxide structures for encouraging cell growth and adhesion. The corrosion and wear resistance are also improved using this technique. The present research trend shows that the oxide–carbide–porous layer formed on the titanium substrate by EDM process increases bioactivity. It is well defined from this research scenario that the trend of surface modification has been switched from conventional machining methods to advanced machining methods (laser, plasma, ion and EDM). The adaptation of bone tissues by Ti implants is a very critical and important issue. Surface modifications were often required for fixation and long-term stability of implant in particular biomedical application. EDM process can improve the surface properties and chemistry of biomaterial. EDM process has the potential to machine biocompatible materials, ranging from metals or alloys to ceramics, which have a wide range of application in dental, orthopedics, microdevices and so on. Table 3 describes the other studies carried out on the application of EDM process on Ti and its alloy in other areas.

Table 3.

Surface modification of Ti and its alloys by EDM for biomedical applications.

EDM or W-EDM or micro-EDM	Workpiece	Surface characterization		Fatigue performance	In vivo or in vitro study		Applications
EDM or W-EDM or micro-EDM	Workpiece	SR	BRL	Fatigue performance	In vivo	In vitro	Applications
EDM¹²⁵	Ti alloy	7.8 µm	TiO₂ layer	x	x	Rabbit	Orthopedics
EDM¹²⁷	Ti alloy	3.4 µm	x	x	x	x	Micro-channelsfor biomedical
EDM, 1–5 ASD¹¹⁷	Ti-6Al-4V	x	Nano-porous TiO₂ layer on surface	x	–	x	Bioactive surface for biomedical
EDM, I_p: 5–15 A, T_on: 300 µs, T_off: 30 µs¹¹⁸	Ti-6Al-4V	4.5–7.5 µm	Nano-porous TiO₂ layer on surface	x	MG-63 cell line	x	Biomedical applications
EDM with I_p: 10 A, T_on: 10–60 µs, T_off: 30 µs¹¹⁹	Ti-6Al-4V	124–182 nm	Nano-porous biocompatible layer	x	MG-63 cell line	x	Biomedical implants
EDM¹²⁸	Ti-6Al-4V	1.8–3.2 µm	Biocompatible 40-µm-thick TiC layer	x	MG-63 cell line	x	Biomedical application or clinical uses
EDM with high I_p 29–71 A¹²²	Ti-6Al-4V	11.6 µm	Highly rough biocompatible surface and 20-µm BRL	Low fatigue endurance	MG-63 cell line	x	Orthopedics applications
W-EDM^120,121	Ti-6Al-4V	x	Biocompatible TiO₂ layer on surface of Ti-6Al-4V	x	MC3T3-E1 mouse cell line		Biomedical applications
W-EDM¹²⁶	Ti-6Al-4V	X	TiO₂ layer	x	x	Rabbit	Biomedical applications
EDM with high I_p 29–71 A¹²³	Ti-6Al-4V	0.1–11.6 µm	Biocompatible surface	Improved fatigue performance	MG-63 cell line	x	Orthopedics applications
EDM with high I_p 29 A¹²⁴	Ti-6Al-4V	0.1–11.6 µm	Micro- and macro-scale surface	Improved fatigue performance	MG-63 cell line	x	Orthopedics applications
EDM¹³⁴	Si₃N₄-TiN composite	1.4 ± 0.15 µm	Recast layer was found 10–20 µm	x	Epithelial cells	x	Orthopedics
W-EDM¹³⁵	Magnesium (Mg) alloy WE43	x	85–105 HV harder recast layer	x	x	x	Biodegradable orthopedic implants
Micro-EDM¹³⁶	Ti alloy	x	x	x	x	x	Orthopedic implants
EDM¹³⁷	NiTi-shape memory alloy	x	Biocompatible recast layer	x	x	x	Medical application
EDM¹³⁸	Nitinol	x	Thin recast layer	x	x	x	Dental applications
EDM¹³⁹	CP-Ti	x	TiO₂, TiC biocompatible recast layer	x	x	Dental model	Dental implants
EDM¹⁴⁰	CP-Ti and Co-Cr alloy	x	Biocompatible surface	x	x	x	Dental implants

EDM: electric discharge machining; ASD: average current density; W-EDM: wire-electric discharge machining; ASD: Average Current Density; Ip: peak current; Ton: pulse-on; Toff: pulse-off; SR: surface roughness; BRL: biocompatible recast layer; x: not attempted in study; MG-63 cell line: human osteoblast cell line.

An innovative method for surface modification by material migration in EDM

To satisfy the need to generate bioactive implant surface, a new innovative technology is proposed here. This technology is well explored by Kansal and his team.^{100–102,141–144} This technology has not been employed before to generate the biocompatible surface for biomedical application. Before exploring its real potential, it has been presumed that PMEDM will also fulfill these objectives. A number of experiments have been carried on in parliamentary procedure to generate the biocompatible surface for biomedical application. The results of these explorations are coming up in the subsequent publications.

PMEDM

To enhance the performance of the EDM process, a relatively new advancement is the addition of conductive powder in the dielectric fluid of EDM oil.¹⁴³ This process is termed as PMEDM. PMEDM process as a surface modification technique has brought in a great deal of interest in recent years with regard to productivity and surface quality of workpiece.¹⁴¹ Moreover, the surface developed by PMEDM process has high immunity to corrosion and abrasion. In PMEDM process, machining is performed in a separate tank of the main machining tank. This is to avoid the wastage of dielectric fluid mixed with different powders and at different concentrations. The new machining tank is made up of fiber glass and is transparent. The detailed experimental setup is adopted from Kansal et al.¹⁴³ The machining tank is filled up with dielectric fluid. For better circulation of powder mixed dielectric, a separate stirring system is integrated, which gently stirred dielectric and oil in the machining tank for assuring suitable uniformity of powder concentration in the dielectric fluid and decreasing the chance of particle settling at the tail end of the machining tank.

When a voltage of 80–320 V is applied between the electrode and the workpiece facing each other with a gap of 25–50 µm, an electric field in the range of 10⁵–10⁷ V/m is created. The powder particles become energized and behave in a zigzag fashion as depicted in Figure 19. Under the sparking area, the particles get close to each other and arrange themselves in the pattern of chain-like structures between the tool and the workpiece. The interlocking between the powders particles occurs in the direction of flow of current. The chain formation helps in bridging the discharge gap between the tool and the workpiece. Due to bridging effect, the insulating strength of the dielectric fluid decreases. The easy short circuit takes place, which causes early explosion in the gap. As a consequence, a series of discharges start under the electrode area. The faster sparking within a discharge takes place, which causes faster erosion of the workpiece surface and hence increases the erosion rate. At the same time, the added powder modifies the plasma channel. The plasma channel becomes enlarged and widened. The sparking is uniformly distributed among the powder particles, and hence, the electric density of the spark decreases. Consequently, uniform erosion (shallow craters) occurs on the workpiece surface.¹⁴¹

Figure 19.

Schematic representation of mechanism of PMEDM process.

PMEDM process not only improves the surface finish but also allows the alloying of oxides and carbides in recast layer. During PMEDM process, at high concentration of the powder particles, the suspended powder particles get energized and form a chain-like structure between the tool and the workpiece. As a result, the sparking will take place intermediately between conductive powder particles as seen in Figure 19. Enormous amount of discharge energy is generated which melts the powder particles partially, and the material is removed from the workpiece surface in the form of debris. At the same time, the dielectric breaks down as a result of carbon and oxygen decomposed from it and react (alloyed) with the partially melted powder particles and the micro-droplets of molten metal to form oxides and carbides. Due to high concentration of powder, the eroded debris cannot be flushed out and is entrapped between the discharge gaps and gets migrated toward the workpiece surface and penetrate into the molten pool before solidification.¹⁰³ Followed by secondary discharges, these oxides and carbides get accelerated and induce a negative pressure by means of electrophoresis and are transferred toward the workpiece surface and penetrate the molten pool before solidification. The alloyed layer of oxides and carbides in the form of micro-droplets solidify at the top of the machined workpiece surface like a hemisphere. When these micro-droplets come under the contact of surface, its surface solidifies immediately, and its center part solidifies less rapidly. Advantageously, at the same time, enormous amount of absorbed gas is ejected, which leads to the creation of porosity and foamy-like shape onto the top surface as reported.¹⁴⁴ The migrated layer of alloy reduces the formation of micro-cracks on the workpiece surface and improves the mechanical properties.¹⁴⁵ The principle mechanism of material migration during PMEDM process is shown in Figure 20. The schematic representation of the material migration mechanism in PMEDM process takes place by the following steps: step (i) plasma channel of heat flux between powder particle and workpiece due to sparking; step (ii) after sparking, gathering of hydrocarbon (C) and oxygen molecule (O) between partially melted powder particles and micro-droplets of molten metal; step (iii) formation of carbides (XC, MC) and oxides (MO₂, XO₂) due to the presence of hydrocarbon (C), oxygen molecule (O) and powder particles (X) and step (iv) penetration of oxides and carbide in the molten pool of recast layer before solidification on the workpiece surface in PMEDM process. The previous results revealed that the high concentration of suspended powder, carbon (hydrocarbon) and oxygen (oxide) that decompose from dielectric and penetrate into the molten pool before solidification is substituted in the form of oxides and carbides on the workpiece surface. Furutani et al.¹¹⁴ investigated the formation of titanium carbide (TiC) by PMEDM process and Janmanee and Muttamara¹⁴⁵ investigated the fabrication of very hard layer of tungsten carbide (WC) by electrical discharge coating (EDC) using titanium powder additives. The migrated layer of alloy reduces the formation of micro-cracks on the workpiece surface and improves the mechanical properties. This phenomenon is called as material migration from suspended powder particles in a dielectric fluid of EDM. Many researchers have investigated the modification of machined surfaces of material migration method. Wang et al.¹⁴⁶ reported the fabrication of 20-µm-thick compact layer of Ti ceramic using a Ti powder green compact electrode by EDM. TiN hard layer was obtained on the surface of titanium when urea solution in water is used as dielectric fluid.¹⁴⁷

Figure 20.

Schematic representation of mechanism of surface modification by material migration in PMEDM process.

From the literature survey of surface modification, it is obvious that material migration from suspended powder to workpiece surface is possible, and workpiece surface can be amended in various ways. The surface obtained from PMEDM process has carbide phases, and this increase in the percentage of carbon along the machined surface indicates that suspended powder particles react with products of hydrocarbon dielectric fluid (oxygen and carbon) after a dielectric breakdown at high temperatures of the plasma channel to form carbides. This surface alloying significantly enhances the surface micro-hardness. Moreover, surface hardness has a direct bearing on abrasion resistance, which might serve to improve the surface load-bearing capacity and results in outstanding wear resistance. As discussed in an earlier section, the requirements of biomedical implant surface are controlled surface roughness, surface topography, erosion and wear resistant. The studies indicate that PMEDM technique has potential to enhance the mechanical as well as biocompatibility of bio-implants. The experimental results of this process are clearly discussed in the upcoming publications.

Conclusions

The EDM has potential in treatment and modification of Ti alloy and other metallic materials used for biomedical applications. In comparison to the several existing techniques such as CVD, PVD and anodization, EDM shows better potential for surface treatment of metallic implants. The EDM has been more advantageously employed than other surface modification techniques. These are (a) no surface preparation before EDM; (b) converts the machined surface into oxide and carbide layer of controlled thickness, which increases the biocompatibility and generates a hydrophilic surface; (c) ability to produce nano-porous surface; (d) improves the surface hardness of material and (e) improves the wear and corrosion resistance of the machined surface. The only disadvantage is that the fatigue performance of the highly rough EDMed sample is low, which can be further improved by surface treatment method or by the reduction of recast layer by shot blasting, CM, SP and so on. However, the use of EDM process in the medical arena is still in its early life. The rapidly growing field of biomanufacturing faces significant challenges and opportunities. The role of EDM process for surface modification of biomaterials is still at the experimental stage. A few number of research studies have been reported by taking EDM as surface treatment or modification process for biomaterials; superior biocompatible surface characteristics have been reported, and capability of formation of biocompatible nano-porous surface has been reported. Despite this, there is a gap and the urgent need to study the effect of various input-independent parameters of EDM on the formation of biocompatible surface. Yet, many more issues need to be addressed before the method can be embraced by the biomedical industry.

Footnotes

Declaration of conflicting interests

The authors declare that there is no conflict of interest.

Funding

This work was financially supported by the Department of Science and Technology (DST), Government of India under SERB project with reference number SR/S3/MERC/0028/2012.

References

Yang

Zhao

. New developments of Ti-based alloys for biomedical applications. Materials 2014; 7(3): 1709–1800.

Geetha

Singh

Asokamani

. Ti based biomaterials, the ultimate choice for orthopaedic implants—a review. Prog Mater Sci 2009; 54: 397–425.

Perren

Pohler

OEM

Schneider

. Titanium as implant material for osteosynthesis applications. In: Brunette

Tengvall

Textor

. (eds) Titanium in medicine. Berlin, Heidelberg: Springer-Verlag, 2001, pp.772–823.

Long

Rack

. Titanium alloys in total joint replacements—a material science perspective. Biomaterials 1998; 19: 1621–1639.

Bartolo

Kruth

J-P

Siva

. Biomedical production of implants by additive electro-chemical and physical processes. CIRP Ann: Manuf Techn 2012; 61: 635–655.

Williams

. On the mechanisms of biocompatibility. Biomaterials 2008; 29: 2941–2953.

Gittens

McLachlan

Olivares-Navarrete

. The effects of combined micron-/submicron-scale surface roughness and nanoscale features on cell proliferation and differentiation. Biomaterials 2011; 32: 3395–3403.

Liua

Chu

Ding

. Surface modification of titanium, titanium alloys, and related materials for biomedical applications. Mat Sci Eng R 2004; 47: 49–121.

Izman

Abdul-Kadir

Anwar

. Surface modification techniques for biomedical grade of titanium alloy—towards achieving enhanced properties for diversified applications. Rijeka: Intech, 2008, pp.201–228.

10.

Niinomi

. Metallic biomaterials. J Artif Organs 2008; 11: 105–110.

11.

Nag

Banerjee

Fraser

. Microstructural evolution and strengthening mechanisms in Ti-Nb-Zr-Ta, Ti-Mo-Zr-Fe and Ti-15Mo biocompatible alloys. Mat Sci Eng C: Biomim 2005; 25: 357–362.

12.

Elias

Schneider

. Microstructural and mechanical characterization of biomedical Ti–Nb–Zr(–Ta) alloys. Mat Sci Eng A: Struct 2006; 432: 108–112.

13.

Okazaki

. A new Ti–15Zr–4Nb–4Ta alloy for medical applications. Curr Opin Solid St M 2001; 5: 45–53.

14.

Niinomi

Nakai

Hieda

. Development of new metallic alloys for biomedical applications. Acta Biomater 2012; 8: 3888–3903.

15.

Okazaki

Rao

Ito

. Corrosion resistance, mechanical properties: corrosion fatigue strength and cytocompatibility of new Ti alloys without Al and V. Biomaterials 1998; 19: 1197–1215.

16.

Amel-Farzad

Peivandi

Yusof-Sani

SMR

. In-body corrosion fatigue failure of a stainless steel orthopaedic implant with a rare collection of different damage mechanisms. Eng Fail Anal 2007; 14: 1205–1217.

17.

Tavares

SSM

Mainier

Zimmerman

. Characterization of prematurely failed stainless steel orthopedic implants. Eng Fail Anal 2010; 17: 1246–1253.

18.

Clerc

Jedwab

Mayer

. Assessment of wrought ASTM F1058 cobalt alloy properties for permanent surgical implants. J Biomed Mater Res 1997; 38: 229–234.

19.

Blackwood

. Biomaterials: past successes and future problems. Corros Rev 2003; 21: 97–124.

20.

Sudhakar

. Investigation of failure mechanism in vitallium 2000 implant. Eng Fail Anal 2005; 12: 257–262.

21.

Antunes

De Oliveira

MCL

. Corrosion fatigue of biomedical metallic alloys: mechanisms and mitigation. Acta Biomater 2012; 8: 937–962.

22.

Mencière

Amouyel

Taviaux

. Fracture of the cobalt-chromium modular femoral neck component in total hip arthroplasty. Orthop Traumatol Surg Res 2014; 100: 565–568.

23.

Fleck

Eifler

. Corrosion, fatigue and corrosion fatigue behaviour of metal implant materials, especially titanium alloys. Int J Fatigue 2010; 32: 929–935.

24.

Ghonem

. Microstructure and fatigue crack growth mechanisms in high temperature titanium alloys. Int J Fatigue 2010; 32: 1448–1460.

25.

Lindemann

Wagner

. Mean stress sensitivity in fatigue of α, (α + β) and β titanium alloys. Mat Sci Eng A: Struct 1997; 234–236: 1118–1121.

26.

Chan

. Changes in fatigue life mechanism due to soft grains and hard particles. Int J Fatigue 2010; 32: 526–534.

27.

Boehlert

Cowen

Quast

. Fatigue and wear evaluation of Ti–Al–Nb alloys for biomedical applications. Mat Sci Eng C: Biomim 2008; 28: 323–330.

28.

Afonso

CRM

Aleixo

Ramirez

. Influence of cooling rate on microstructure of Ti–Nb alloy for orthopedic implants. Mat Sci Eng C: Biomim 2007; 27: 908–913.

29.

Bache

Evans

. The fatigue crack propagation resistance of Ti–6Al–4V under aqueous saline environments. Int J Fatigue 2001; 23: S319–S323.

30.

Gregory

. Corrosion fatigue crack growth in titanium alloys. Mater Corros 1999; 50: 7–11.

31.

Lee

Vasudevan

Sadananda

. Effects of various environments on fatigue crack growth in Laser formed and IM Ti–6Al–4V alloys. Int J Fatigue 2005; 27: 1597–1607.

32.

Niinomi

Saga

Fukunaga

K-I

. Long crack growth behavior of implant material Ti–5Al–2.5Fe in air and simulated body environment related to microstructure. Int J Fatigue 2000; 22: 887–897.

33.

Williams

Chawla

. Fractography of a neck failure in a double-modular hip implant. Case Stud Eng Fail Anal 2014; 2: 45–50.

34.

Ellman

Levine

. Fracture of the modular femoral neck component in total hip arthroplasty. J Arthroplasty 2013; 28: 196.e1–196.e5.

35.

Dangles

Altstetter

. Failure of the modular neck in a total hip arthroplasty. J Arthroplasty 2010; 25: 1169.e5–1169.e7.

36.

Wodecki

Sabbah

Kermarrec

. New type of hip arthroplasty failure related to modular femoral components: breakage at the neck-stem junction. Orthop Traumatol Surg Res 2013; 99: 741–744.

37.

Whitehouse

Endo

Masri

. Adverse local tissue reaction associated with a modular hip hemiarthroplasty. Clin Orthop Relat Res 2013; 471: 4082–4086.

38.

Skendzel

Blaha

Urquhart

. Total hip arthroplasty modular neck failure. J Arthroplasty 2011; 26: 338.e1–338.e4.

39.

Sporer

DellaValle

Jacobs

. A case of disassociation of a modular femoral neck trunion after total hip arthroplasty. J Arthroplasty 2006; 21: 918–921.

40.

Wright

Sporer

Urban

. Fracture of a modular femoral neck after total hip arthroplasty: a case report. J Bone Joint Surg Am 2010; 92: 1518–1521.

41.

Wilson

Dunbar

Amirault

. Early failure of a modular femoral neck total hip arthroplasty component: a case report. J Bone Joint Surg Am 2010; 92: 1514–1517.

42.

Sotereanos

Sauber

Tupis

. Modular femoral neck fracture after primary total hip arthroplasty. J Arthroplasty 2013; 28: 196.e7–196.e9.

43.

Paliwal

Allan

Filip

. Failure analysis of three uncemented titanium alloy modular total hip stems. Eng Fail Anal 2010; 17: 1230–1238.

44.

Rodrigues

Urban

Jacobs

. In vivo severe corrosion and hydrogen embrittlement of retrieved modular body titanium alloy hip implants. J Biomed Mater Res B 2009; 88: 206–219.

45.

Yokoyama

Ichikawa

Murakami

. Fracture mechanisms of retrieved titanium screw thread in dental implant. Biomaterials 2002; 23: 2459–2465.

46.

Matsuno

Yokoyama

Watari

. Biocompatibility and osteogenesis of refractory metal implants, titanium, hafnium, niobium, tantalum and rhenium. Biomaterials 2001; 22: 1253–1262.

47.

Niinomi

. Fatigue performance and cyto-toxicity of low rigidity titanium alloy, Ti–29Nb–13Ta–4.6Zr. Biomaterials 2003; 24: 2673–2683.

48.

Geetha

. Effect of thermomechanical processing on evolution of various phases in Ti–Nb–Zr alloys. J Alloy Compd 2004; 384: 131–144.

49.

Rubitschek

Niendorf

Karaman

. Corrosion fatigue behavior of a biocompatible ultrafine-grained niobium alloy in simulated body fluid. J Mech Behav Biomed Mater 2012; 5: 181–192.

50.

Akahori

Niinomi

Fukui

. Fatigue, fretting fatigue and corrosion characteristics of biocompatible beta type titanium alloy conducted with various thermo-mechanical treatments. Mater Trans 2004; 5: 1540–1548.

51.

Baptista

CARP

Schneider

Taddei

. Fatigue behavior of arc melted Ti–13Nb–13Zr alloy. Int J Fatigue 2004; 26: 967–993.

52.

Boehlert

Cowen

Jaeger

. Tensile and fatigue evaluation of Ti–15Al–33Nb (At%) and Ti–21Al–29Nb (At%) alloys for biomedical applications. Mat Sci Eng C: Biomim 2005; 25: 263–275.

53.

Kieswetter

Schwartz

Dean

. The role of implant surface characteristics in the healing of bone. Crit Rev Oral Biol M 1996; 7(4): 329–345.

54.

Schwartz

Boyan

. Underlying mechanisms at the bone-biomaterial interface. J Cell Biochem 1994; 56: 340–347.

55.

Martin

Schwartz

Hummert

. Effect of titanium surface-roughness on proliferation, differentiation, and protein-synthesis of human osteoblast-like cells (MG63). J Biomed Mater Res 1995; 29(3): 389–401.

56.

Boyan

Bonewald

Paschalis

. Osteoblast-mediated mineral deposition in culture is dependent on surface microtopography. Calcified Tissue Int 2002; 71(6): 519–529.

57.

Sul

Johansson

Wennerberg

. Optimum surface properties of oxidized implants for reinforcement of osseointegration: surface chemistry, oxide thickness, porosity, roughness, and crystal structure. Int J Oral Max Impl 2005; 20(3): 349–359.

58.

Buser

Broggini

Wieland

. Enhanced bone opposition to a chemically modified SLA titanium surface. J Dent Res 2004; 83(7): 529–533.

59.

Liu

Lim

Donahue

. Influence of substratum surface chemistry/energy and topography on the human fetal osteoblastic cell line hFOB 1.19: phenotypic and genotypic responses observed in vitro. Biomaterials 2007; 28(31): 4535–4550.

60.

Rupp

Scheideler

Olshanska

. Enhancing surface free energy and hydrophilicity through chemical modification of microstructured titanium implant surfaces. J Biomed Mater Res A 2006; 76: 323–334.

61.

Zhao

Schwartz

Wieland

. High surface energy enhances cell response to titanium substrate microstructure. J Biomed Mater Res A 2005; 74: 49–58.

62.

Schwartz

Raz

Zhao

. Effect of micrometer-scale roughness of the surface of Ti-6Al-4V pedicle screws in vitro and in vivo. J Bone Joint Surg Am 2008; 90(11): 2485–2498.

63.

Att

Tsukimura

Suzuki

. Effect of supramicron roughness characteristics produced by 1-and 2-step acid etching on the osseointegration capability of titanium. Int J Oral Max Impl 2007; 22(5): 719–728.

64.

Vagaska

Bacakova

Filova

. Osteogenic cells on bio-inspired materials for bone tissue engineering. Physiol Res 2010; 59: 309–322.

65.

Vandrovcova

Bacakova

. Adhesion, growth and differentiation of osteoblasts on surface-modified materials developed for bone implants. Physiol Res 2011; 60: 403–417.

66.

Rosa

Beloti

. Effect of CpTi surface roughness on human bone marrow cell attachment, proliferation, and differentiation. Braz Dent J 2003; 14: 16–21.

67.

Webster

Ergun

Doremus

. Specific proteins mediate enhanced osteoblast adhesion on nanophase ceramics. J Biomed Mater Res 2002; 51: 475–483.

68.

Bacakova

Filova

Rypacek

. Cell adhesion on artificial materials for tissue engineering. Physiol Res 2004; 53(1): 535–545.

69.

Zhao

Zinger

Schwartz

. Osteoblast-like cells are sensitive to submicron-scale surface structure. Clin Oral Implants Res 2006; 17(3): 258–264.

70.

Lipski

Pino

Haselton

. The effect of silica nanoparticle modified surfaces on cell morphology, cytoskeletal organization and function. Biomaterials 2008; 29(28): 3836–3846.

71.

Curtis

ASG

Gadegaard

Dalby

. Cells react to nanoscale order and symmetry in their surroundings. IEEE T Nanobiosci 2004; 3(1): 61–65.

72.

Riehle

Dalby

Johnstone

. Cell behavior of rat calvaria bone cells on surfaces with random nanometric features. Mat Sci Eng C: Biomim 2003; 23(3): 337–340.

73.

Ward

Webster

. Increased functions of osteoblasts on nanophase metals. Mat Sci Eng C: Biomim 2007; 27(3): 575–578.

74.

Liu

. Microstructure and dry-sliding wear properties of TiC-reinforced composite coating prepared by plasma-transferred arc weld-surfacing process. Mat Sci Eng A: Struct 2007; 458: 366–370.

75.

Nolan

Huang

Leskovsek

. Sliding wear of titanium nitride thin films deposited on Ti–6Al–4V alloy by PVD and plasma nitriding processes. Surf Coat Tech 2006; 200: 5698–5705.

76.

Yan

Lam

. Characterization and tribological evaluation of MW-PACVD diamond coatings deposited on pure titanium. Mat Sci Eng A: Struct 2000; 282: 38–48.

77.

Vadiraj

Kamaraj

Gnanamoorthy

. Fretting wear studies on uncoated, plasma nitrided and laser nitrided biomedical titanium alloys. Mat Sci Eng A: Struct 2007; 445–446: 446–453.

78.

Yildiz

Yetim

Alsaran

. Plasma nitriding behavior of Ti6Al4V orthopedic alloy. Surf Coat Tech 2008; 202(11): 2471–2476.

79.

Minagar

Berndt

Wang

. A review of the application of anodization for the fabrication of nanotubes on metal implant surfaces. Acta Biomater 2012; 8(8): 2875–2888.

80.

Liu

Meng

Liu

. Development and characterization of laser clad high temperature self-lubricating wear resistant composite coatings on Ti–6Al–4V alloy. Mater Des 2014; 55: 404–409.

81.

Chen

Lin

Chen

. Effect of electro-discharging on formation of biocompatible layer on implant surface. J Alloy Compd 2008; 456: 413–418.

82.

Klocke

Lung

Antonoglou

. The effect of powder suspended dielectrics on the thermal influenced zone by electro discharge machining with small discharge energies. J Mater Process Tech 149: 191–197.

83.

Bonny

De Baets

Vleugels

. Sliding wear of electrically conductive ZrO₂ − WC composites against WC–Co cemented carbide. Tribol Lett 2008; 30: 191–198.

84.

Jabbaripour

Sadeghi

Shabgard

. Investigating surface roughness, material removal rate and corrosion resistance in PMEDM of γ-TiAl intermetallic. J Manuf Process 2013; 15: 56–68.

85.

Newman

. State of the art electrical discharge machining (EDM). Int J Mach Tool Manu 2003; 43: 1287–1300.

86.

Abu-Zeid

. On the effect of electro-discharge machining parameters on the fatigue life of AISI D6 tool steel. J Mater Process Tech 1997; 68: 27–32.

87.

Yadav

Yadava

. Experimental modeling and multiobjective optimization of electrical discharge drilling of aerospace superalloy material. Proc IMechE, Part B: J Engineering Manufacture. Epub ahead of print 12 August 2014. DOI: 10.1177/0954405414539299.

88.

Sivam

Michaelraj

Kumar

. Statistical multi-objective optimization of electrical discharge machining parameters in machining titanium grade 5 alloy using graphite electrode. Proc IMechE, Part B: J Engineering Manufacture 2014; 228: 736–743.

89.

Ndaliman

Khan

Ali

. Influence of dielectric fluids on surface properties of electrical discharge machined titanium alloy. Proc IMechE, Part B: J Engineering Manufacture 2013; 227: 1310–1316.

90.

Amorim

Stedile

Torres

. Performance and surface integrity of Ti6Al4V after sinking EDM with special graphite electrodes. J Mater Eng Perform 2013; 23: 1480–1488.

91.

Jabbaripour

Sadeghi

Shabgard

. The effects of tool materials on machinability, surface topography and corrosion resistance in EDM of γ-TiAl intermetallic. Modares Mech Eng 2011; 11: 135–146.

92.

Kumar

. Investigation of machining parameters and surface integrity in wire electric discharge machining of pure titanium. Proc IMechE, Part B: J Engineering Manufacture 2013; 227: 972–992.

93.

Nourbakhsh

Rajurkar

Malshe

. Wire electro-discharge machining of titanium alloy. Proced CIRP 2013; 5: 13–18.

94.

Kumar

Batish

Singh

. A mathematical model to predict material removal rate during electric discharge machining of cryogenically treated titanium alloys. Proc IMechE, Part B: J Engineering Manufacture. Epub ahead of print 29 April 2014. DOI: 10.1177/0954405414527955.

95.

Pradhan

Bhattacharyya

. Improvement in microhole machining accuracy by polarity changing technique for microelectrode discharge machining on Ti–6Al–4V. Proc IMechE, Part B: J Engineering Manufacture 2008; 222: 163–173.

96.

Yan b Wang

Liu

. Machining characteristics of Al₂O₃/6061Al composite using rotary EDM with a disklike electrode. Int J Adv Manuf Tech 2000; 16: 322–333.

97.

Chattopadhyay

Satsangi

Verma

. Analysis of rotary electrical discharge machining characteristics in reversal magnetic field for copper-en8 steel system. Int J Adv Manuf Tech 2007; 38: 925–937.

98.

Abdullah

Shabgard

Ivanov

. Effect of ultrasonic-assisted EDM on the surface integrity of cemented tungsten carbide (WC-Co). Int J Adv Manuf Tech 2008; 41: 268–280.

99.

Abdullah

Shabgard

. Effect of ultrasonic vibration of tool on electrical discharge machining of cemented tungsten carbide (WC-Co). Int J Adv Manuf Tech 2007; 38: 1137–1147.

100.

Kansal

Singh

Kumar

. Parametric optimization of powder mixed electrical discharge machining by response surface methodology. J Mater Process Tech 2005; 169(3): 427–436.

101.

Kansal

Singh

Kumar

. Numerical simulation of powder mixed electric discharge machining (PMEDM) using finite element method. Math Comput Model 2008; 47: 1217–1237.

102.

Kansal

Singh

Kumar

. Technology and research developments in powder mixed electric discharge machining (PMEDM). J Mater Process Tech 2007; 184: 32–41.

103.

Ekmekci

Ersöz

. How suspended particles affect surface morphology in powder mixed electrical discharge machining (PMEDM). Metall Mater Trans B 2012; 43(5): 1138–1148.

104.

Kozak

Rozenek

Dabrowski

. Study of electrical discharge machining using powder-suspended working media. Proc IMechE, Part B: J Engineering Manufacture 2003; 217: 1597–1602.

105.

Cogun

Ozerkan

Karacay

. An experimental investigation on the effect of powder mixed dielectric on machining performance in electric discharge machining. Proc IMechE, Part B: J Engineering Manufacture 2006; 220: 1035–1050.

106.

Jahan

Rahman

Wong

. Modelling and experimental investigation on the effect of nanopowder-mixed dielectric in micro-electrodischarge machining of tungsten carbide. Proc IMechE, Part B: J Engineering Manufacture 2010; 224: 1725–1739.

107.

Tan

Yeo

. Investigation of recast layers generated by a powder-mixed dielectric micro electrical discharge machining process. Proc IMechE, Part B: J Engineering Manufacture 2011; 225: 1051–1062.

108.

Zain

Ndaliman

Khan

. Improving micro-hardness of stainless steel through powder-mixed electrical discharge machining. Proc IMechE, Part B: J Engineering Manufacture. Epub ahead of print 7 April 2014. DOI: 10.1177/0954406214530872.

109.

Ndaliman

Khan

Ali

. Influence of electrical discharge machining process parameters on surface micro-hardness of titanium alloy. Proc IMechE, Part B: J Engineering Manufacture 2013; 227: 460–464.

110.

Kunieda

Lauwers

Rajurkar

. Advancing EDM through fundamental insight into the process. CIRP Ann: Manuf Techn 2005; 54: 64–87.

111.

Luo

. The dependence of interspace discharge transitivity upon the gap debris in precision electro-discharge machining. J Mater Process Tech 1997; 68: 127–131.

112.

Bojorquez

Marloth

Es-Said

. Formation of a crater in the workpiece on an electrical discharge machine. Eng Fail Anal 2003; 9: 93–97.

113.

Marafona

Chousal

JAG

. A finite element model of EDM based on the Joule effect. Int J Mach Tool Manu 2005; 46: 1–8.

114.

Furutani

Saneto

Takezawa

. Accretion of titanium carbide by electrical discharge machining with powder suspended in working fluid. Precis Eng 2001; 25: 134–144.

115.

Schumacher

. After 60 years of EDM, the discharge process remains still disputed. J Mater Process Tech 2005; 149: 376–381.

116.

Hascalik

Caydas

. Electrical discharge machining of titanium alloy (Ti–6Al–4V). Appl Surf Sci 2007; 253: 9007–9016.

117.

Peng

Lin

. Effect of electrical-discharging on formation of nanoporous biocompatible layer on titanium. J Alloy Compd 2010; 492: 625–630.

118.

Lee

Yang

. Nanoporous biocompatible layer on Ti–6Al–4V alloys enhanced osteoblast-like cell response. J Exp Clin Med 2013; 5(3): 92–96.

119.

Yang

Huang

Wang

. Effect of electrical discharging on formation of nanoporous biocompatible layer on Ti–6Al–4V alloys. Implant Dent 2013; 22: 374–379.

120.

Tamaki

Kataoka

Jang

. Bone regenerative potential of mesenchymal stem cells on a micro-structured titanium processed by W-EDM. Open Mater Sci J 2010; 4: 113–116.

121.

Otsuka

Kataoka

Miyazaki

. Enhanced osteoblast response to electrical discharge machining surface. Dent Mater J 2013; 31(2): 309–315.

122.

Harcuba

Bacakova

Strasky

. Surface treatment by electric discharge machining of Ti–6Al–4V alloy for potential application in orthopaedics. J Mech Behav Biomed Mater 2012; 7: 96–105.

123.

Strasky

Havlikova

Bacakova

. Characterization of electric discharge machining, subsequent etching and shot-peening as a surface treatment for orthopedic implants. Appl Surf Sci 2013; 281: 73–78.

124.

Havlikova

Strasky

Vandrovcova

. Innovative surface modification of Ti–6Al–4V alloy with a positive effect on osteoblast proliferation and fatigue performance. Mat Sci Eng C: Biomim 2014; 39: 371–379.

125.

Wennerberg

Zallgren

Johansson

. Surface characterization and biological evaluation of spark-eroded surfaces. J Mater Sci Mater Med 1997; 8: 757–763.

126.

Yamaki

Kataoka

Ohtsuka

. Micro-CT evaluation of in vivo osteogenesis at implants processed by wire-type electric discharge machining. Dent Mater J 2012; 31(3): 427–432.

127.

Murali

Yeo

. Rapid biocompatible micro device fabrication by micro-EDM. Biomed Microdevices 2004; 6(1): 411–445.

128.

Bin

xin

Zhan

. Electro-spark alloying using graphite electrode on titanium alloy surface for biomedical applications. Appl Surf Sci 2011; 257: 6364–6371.

129.

Janecek

Novy

Strasky

. Fatigue endurance of Ti–6Al–4V alloy with electro-eroded surface for improved bone in-growth. J Mech Behav Biomed Mater 2011; 4: 417–422.

130.

Strasky

Janecek

Harcuba

. The effect of microstructure on fatigue performance of Ti–6Al–4V alloy after EDM surface treatment for application in orthopaedics. J Mech Behav Biomed Mater 2011; 4: 1955–1962.

131.

Klocke

Welling

Dieckmann

. Comparison of grinding and wire EDM concerning fatigue strength and surface integrity of machined Ti6Al4V components. Proced Eng 2011; 19: 184–189.

132.

Kashaev

Horstmann

Ventzke

. Comparative study of mechanical properties using standard and micro-specimens of base materials Inconel 625, Inconel 718 and Ti–6Al–4V. J Mater Res Technol 2013; 2: 43–47.

133.

Mower

. Degradation of titanium 6Al–4V fatigue strength due to electrical discharge machining. Int J Fatigue 2014; 64: 84–96.

134.

Bucciotti

Mazzocchi

Bellosi

. Perspectives of the Si3N4-TiN ceramic composite as a biomaterial and manufacturing of complex-shaped implantable devices by electrical discharge machining (EDM). J Appl Biomater Biomech 2010; 8(1): 28–32.

135.

Klocke

Schwade

Klink

. EDM machining capabilities of magnesium (Mg) alloy WE43 for medical applications. Proced Eng 2011; 19: 190–195.

136.

Hashima

NLS

Yahyaa

Kadira

MRA

. Simulation of micro-EDM servomotor for machining micro pits on hip implant. J Teknol 2013; 61(2): 45–51.

137.

Huang

Zhang

Zhou

. Ultrasonic vibration assisted electro-discharge machining of microholes in Nitinol. J Micromech Microeng 2003; 13: 693–700.

138.

Theisen

Schuermann

. Electro discharge machining of nickel–titanium shape memory alloys. Mat Sci Eng A: Struct 2004; 378: 200–204.

139.

Zinelis

Al Jabbari

Thomas

. Multitechnique characterization of CPTi surfaces after electro discharge machining (EDM). Clin Oral Invest 2014; 18: 67–75.

140.

Zinelis

. Surface and elemental alterations of dental alloys induced by electro discharge machining (EDM). Dent Mater 2007; 23: 601–607.

141.

Kumar

. Development of mirror like surface characteristics using nano powder mixed electric discharge machining (NPMEDM). Int J Adv Manuf Tech 2014; 76: 105–113.

142.

Kumar

Davim

. Role of powder in the machining of Al-10%Sic_p metal matrix composites by powder mixed electric discharge machining. J Compos Mater 2010; 45(2) 133–151.

143.

Kansal

Singh

Kumar

. Effect of silicon powder mixed EDM on machining rate of AISI D2 die steel. J Manuf Process 2007; 9(1): 13–22.

144.

Peng

Zhang

. Fabrication of hollow nickel micro-spheres with high degree of hollowness by silicon powder-mixed spark erosion. Int J Mach Tool Manu 2014; 85: 131–134.

145.

Janmanee

Muttamara

. Surface modification of tungsten carbide by electrical discharge coating (EDC) using a titanium powder suspension. Appl Surf Sci 2012; 258(19): 7255–7265.

146.

Wang

Fang

. Surface modification process by electrical discharge machining with a Ti powder green compact electrode. J Mater Process Tech 2002; 129: 139–142.

147.

Yan

Tsai

Huang

. The effect in EDM of a dielectric of a urea solution in water on modifying the surface of titanium. Int J Mach Tool Manu 2005; 45(2): 194–200.

Electric discharge machining – A potential choice for surface modification of metallic implants for orthopedic applications: A review

Abstract

Keywords

Introduction

Need for joint replacement

Properties required for bio-implants

Biocompatibility

Mechanical properties

Surface topography

Corrosion and wear resistance

Materials for bio-implant

Corrosion fatigue behavior of metallic biomaterial

Need for surface modification

EDM

Historical perspective for surface modification of metallic implants by EDM

Enhancing the osseointegration

In vitro cast study

Evaluation by in vivo

Enhancing surface integrity

Controlled surface roughness

Surface chemistry and topology

Enhancing the mechanical properties

Fatigue performance

Enhancing micro-hardness, wear and corrosion resistance properties

Summary of current research issues and future directions

An innovative method for surface modification by material migration in EDM

PMEDM

Conclusions

Footnotes

Declaration of conflicting interests

Funding

References