Novel Porous Phosphorus⁻Calcium⁻Magnesium Coatings on Titanium with Copper or Zinc Obtained by DC Plasma Electrolytic Oxidation: Fabrication and Characterization.

In this paper, the characteristics of new porous coatings fabricated at three voltages in electrolytes based on H₃PO₄ with calcium nitrate tetrahydrate, magnesium nitrate hexahydrate, and copper(II) nitrate trihydrate are presented. The SEM, energy dispersive spectroscopy (EDS), glow discharge optical emission spectroscopy (GDOES), X-ray photoelectron spectroscopy (XPS), and XRD techniques for coating identification were used. It was found that the higher the plasma electrolytic oxidation (PEO) (micro arc oxidation (MAO)) voltage, the thicker the porous coating with higher amounts of built-in elements coming from the electrolyte and more amorphous phase with signals from crystalline Ca(H₂PO₄)₂∙H₂O and/or Ti(HPO₄)₂∙H₂O. Additionally, the external parts of the obtained porous coatings formed on titanium consisted mainly of Ti4+, Ca2+, Mg2+ and PO₄3-, HPO₄2-, H₂PO₄-, P₂O₇4- as well as Zn2+ or copper Cu⁺/Cu2+. The surface should be characterized by high biocompatibility, due to the presence of structures based on calcium and phosphates, and have bactericidal properties, due to the presence of zinc and copper ions. Furthermore, the addition of magnesium ions should accelerate the healing of postoperative wounds, which could lead to faster patient recovery.

1. Introduction

The phenomenon of luminescenpan>ce occurring on the surface of metals during the galvanic process was first observed by Sluginov in 1880 [1], and the information was published for the first time by Braun in 1898 [2]. In 1929, Dufford showed that during the electrolysis of metals such as aluminum, zinc, silver, tantalum, tungsten, magnesium, cerium, antimony, and mercury in selected electrolytes, the phenomenon of luminescence was observed [3]. In addition, he noticed that this phenomenon was not observed with lead, iron, copper, nickel, molybdenum, tin, and platinum. Such luminescence phenomenon was developed, inter alia, by McNeill, Gruss, Yerokhin, and Nie [4,5]. In addition, Yerokhin at al. proposed a definition of that process, that it is “an electrolytic treatment of anodically polarized metal surfaces carried out above the dielectric breakdown voltage of the growing oxide film”, as well as an explanation of the formation of porous coatings [5,6]. According to this theory, during small voltage polarization, the passive layer is forming, which may be dissolved with the voltage increase. Further increases of voltage result in film repassivation and growth of a new porous oxide film. In the next step of voltage increase, the electric field strength in the oxide film reaches a critical value, after which the film is broken through due to impact or tunneling ionization (here, luminescent sparks are observed). A further increase of voltage results in the following: thermal ionization, larger arc discharges, film fusing and alloying with electrolyte elements, microdischarges penetrating through to the substrate, powerful arcs, destructive effects, and thermal cracking of the coating. It should be also pointed out that on the same plasma electrolytic oxidation (PEO) treated surface, more than one of the described processes may occur concurrently [5]. Over the years, the phenomenon of galvanic luminescence occurring during the anodic polarization of selected metals and electrolytes has been defined as microplasma oxidation, anode spark electrolysis, plasma electrolytic anode treatment, plasma electrolytic oxidation, or micro arc oxidation [7]. Systematic studies proposed coating growth [8,9,10] and discharging [11,12,13,14] behaviors as well as electrolyte influence on the ignition of plasma electrolytic oxidation processes [15]. Meanwhile, Curran and Clyne described the thermophysical properties of plasma electrolytic oxidation [16] and the porosity of PEO coatings [17]. Other authors studied oxygen evolution during PEO [18] and the effects of electrical parameters on that process [19] as well as phase formation in ceramic PEO coatings [20,21] and their corrosion resistance [22]. The PEO process has been performed by researchers under different conditions, i.e., DC [23,24], AC [25,26], and pulse [27,28] currents, which result in different surface morphology [29,30] and chemical composition [31,32] as well as mechanical [33,34] and electrochemical properties [35,36]. For the most frequently treated materials by PEO processes, aluminum [37,38,39,40] and its alloys [40,41,42,43,44], magnesium [45] and its alloys [46,47,48,49,50,51,52,53,54], titanium [55,56,57,58,59,60] and its alloys [61,62,63,64,65,66,67], zirconium [68,69,70,71,72,73,74,75,76,77] and its alloys [78,79], tantalum [80,81,82,83], niobium [84,85,86,87,88], and hafnium [89] should be included. In the present paper, PEO coatings obtained on titanium in novel electrolytes, which have never been used or described in the literature until now, are presented (Table 1). These electrolytes are based on orthophosphoric acid and three different nitrates.

Table 1

Electrolytes and conditions of the plasma electrolytic oxidation (PEO) process.

Electrolytes	Voltage Current Density	Ref.
H2O, NaAlO2, Na3PO4·12H2O, KOH, NaCl	100–900 mA·cm−2 (f = 50 Hz)	[7]
H2O, Na3PO4·12H2O, KOH, Na2SO4, (HOCH2)3CNH2, (NH4)2HPO4, C2H7NO2	70 mA·cm−2 (f = 50 Hz)	[23]
H3PO4, Ca(NO3)2·4H2O, Mg(NO3)2·6H2O, Cu(NO3)2·3H2O, Zn(NO3)2·6H2O	500, 575, 650 V	[24]
H3PO4, Cu(NO3)2·3H2O	450 V	[32]
H2O, Na2SiO3, (NaPO3)6, NaAlO2 microparticle	80 mA·cm−2 (f = 300 Hz)	[33]
H3PO4, Mg(NO3)2·6H2O, Zn(NO3)2·6H2O	500–650 V	[35]
H2O, Na3PO4, FeSO4	350 V (f = 100 Hz)	[55]
H2O, NaAlO2, KOH	400 V (f = 2000 Hz)	[56]
H2O, (CH3COO)2Ca·H2O, NaH2PO4·2H2O	300, 390 V (f = 900 Hz)	[58]
H2O, Ca(CH3COO)2,Sr(CH3COO)2	400, 450 V (f = 100 Hz)	[59]
H3PO4, Ca(NO3)2·4H2O	500, 575, 650 V	[60]
H2O, Na3PO4, Co(CH3COO)2	350 V (f = 100 Hz)	[61]
H2O, Na3PO4·12H2O, Na2B4O7·10H2O, Na3WO4·2H2O	50 mA·cm−2	[62]
H2O, Na2SiO3, Na2CO3, NaOH	12 mA·cm−2 (f = 100 Hz)	[63]
H2O, C6H18O24P6, KOH, EDTA-Na2, Ca(CH3COO)2	20, 50, 80 V	[64]
H2O, NaAlO2, Na2SiO3, (NaPO3)6	550 V	[65]
H2O, Na2HPO4, C4H6O4Ca·H2O	+400 V/−80 V (f = 250 Hz)	[66]
H2O, C3H9O6P, C4H6O4Ca·H2O	+400 V/−80 V (f = 250 Hz)	[66]
H2O, Na2HPO4, C3H7CaO6P·H2O	+400 V/−80 V (f = 250 Hz)	[66]
H2O, (CH3COO)2Ca·H2O, NaH2PO4·H2O	350–500 V (f = 1000 Hz)	[67]
H2O, Ca(CH3COO)2·H2O	300 V (f = 1000 Hz)	[90]
H2O, (CH1COO)2Ca, C3H7Na2O6P	250–400 V (f = 100 Hz)	[91]
H2O, (CH3COO)2Ca·H2O, C3H7Na2O6P·5H2O	450 V (f = 100 Hz)	[92]
H2O, (CH3COO)2Ca·H2O, C3H7Na2O6P·5H2O	250–500 V (f = 1000 Hz)	[93,94]
H2O, Ca(CH3COO)2·H2O, CaC3H7O6P	190–600 V (f = 660 Hz)	[95,96]
H2O, (CH3COO)2Ca·H2O, C3H7Na2O6P·5H2O	200–500 V (f = 900 Hz)	[97]
H2O, Na4P2O7·10H2O and KOH, NaAlO2	0–300 V	[98]
Na2B4O7·10H2O, (CH3COO)2Mn·4H2O	450–500 V	[99]
H2O, (CH3COO)2Ca·H2O	230 V	[100]
H2O, (CH3COO)2Ca·H2O, NaH2PO4·2H2O	260–420 V	[101]
H2O, CaHPO4, Ca(H2PO4)2, Na6P6O18, Ca(CH3COO)2	20, 100 mA·cm−2	[102]
H2O, KOH	290 V (f = 100–200 Hz)	[103]
H2O, KOH	350 V (f = 1000 Hz)	[104]
H2O, (NaPO3)6, NaF, NaAlO2	150–200 V	[105]
H2O, K2Al2O4, Na3PO4, NaOH	400 V	[106]
H2O, CaCl2 and KH2PO4	320–340 V	[107]
H2O, H2SO4 and Ti2(SO4)3	1100 V	[108]
H2O, Na2(EDTA), CaO, Ca(H2PO4)2, Na2SiO3·H2O	350 V (f = 200 Hz)	[109]
H2O, Na2SiO3, NaOH	280 V	[110]
H2O, CaO, Na6P6O18, Na2H2EDTA⋅5.5H2O, KOH	AC 0.5–2 mA·cm−2	[111]
2O, (NaPO3)6, NaF, NaAlO2	60 mA·cm−2 (f = 100, 600 Hz)	[112]
H2O, Na3PO4, FeSO4, Co(CH3COO)2, Ni(CH3COO)2, K2ZrF6	350 V (f = 100 Hz)	[113]
H2O, Ca(CH3COO)2·H2O, C3H7Na2O6P	150 V	[114]
H2O, Na2SiO3·9H2O, Na3PO4·12H2O, Na2SiO3·9H2O, Na3PO4·12H2O	80 mA·cm−2 (f = 150 Hz)	[115]
H2O, Na3PO4·12H2O, α-Al2O3 nanoparticles	20 mA·cm−2	[116]

It should also be pointed out that in n class="Chemical">hydroxyapatite-like strun class="Chemical">ctures it is possible to substitute the Ca2+ ions for Ca2+, Mg2+, Cu2+, and Zn2+, as well as OH– for Cu+, which will be used in the fabrication of novel PEO coatings. The porous calcium–phosphate coatings obtained on titanium [117,118,119] and enriched with biocompatible magnesium, which causes faster wound healing [120,121,122,123,124,125], as well as antibacterial zinc [126,127,128,129,130,131,132] and copper [133,134,135,136], may be used as biomaterial, which will be fully accepted by the tissue environment.

However, without results inter alia presented in those papers, it is not possible to predin class="Chemical">ct the real possibility of that substitution during plasma treatment in electrolyte in which the ions are present, as well as the thickness and porosity of the PEO coatings. Therefore, in the present paper, the results of x-ray photoelectron spectroscopy (XPS) (10 top nanometers) will be helpful in explaining the oxidation states of those chemical elements as well as chemical composition for all volumes, thicknesses, and pore shapes of obtained coatings by energy dispersive spectroscopy (EDS), XRD, glow discharge optical emission spectroscopy (GDOES), and SEM.

2. Materials and Methods

Porous coatings obtained on titanium samples (10 × 10 × 2 mm) by PEO treatment in electrolyte (constant volume of 500 mL for each experiment) containing phosphoric acid (85% w/w) with the addition of calcium nitrate tetrahydrate Ca(NO3)2·4H2O, magnesium nitrate hexahydrate Mg(NO3)2·6H2O, and copper(II) nitrate trihydrate Cu(NO3)2·3H2O in weight ratios of 1:1:1 (Table 2) at 3 voltages, 500 V (PEO time: 3 min), 575 V (PEO times: 1, 3, 5 min), and 600 V (PEO time: 3 min), using a PWR 1600H power supply (KIKUSUI Electronics Corp., Yokohama, Kanagawa, Japan) were fabricated. For their characterization, the complementary measurement methods SEM, EDS, GDOES, XPS, and XRD [137,138,139,140,141] were used. Descriptions of the setups are presented in Table 3 and are detailed in reference [24].

Table 2

Experimental plan and code sample names.

Sample Name	Voltage	Electrolyte Type	Electrolyte Composition
			Salts	Salt Concentrations (g/L)
Ti_CaMgZn_500V	500 V	Electrolyte 1	Ca(NO3)2·4H2O and Mg(NO3)2·6H2O & Zn(NO3)2·6H2O	166.7 + 166.7 + 166.7
Ti_CaMgZn_575V	575 V
Ti_CaMgZn_650V	650 V
Ti_CaMgCu_500V	500 V	Electrolyte 2	Ca(NO3)2·4H2O and Mg(NO3)2·6H2O & Cu(NO3)2·3H2O	166.7 + 166.7 + 166.7
Ti_CaMgCu_575V	575 V
Ti_CaMgCu_650V	650 V

Table 3

Setups of SEM, energy dispersive spectroscopy (EDS), x-ray photoelectron spectroscopy (XPS), glow discharge optical emission spectroscopy (GDEOS), and XRD equipment.

Technique	Equipment	Manufacturer
SEM	Quanta 650 FEI	Field Electron and Iron Company, Hillsboro, OR, USA
EDS	Noran System Six	EDS, Silicon Drift Detectors: Keith Thompson, Thermo Fisher Scientific, Madison, WI, USA
XPS	SCIENCE SES 2002	Scienta AB, Scienta Omicron, Uppsala, Sweden
GDOES	GD Profiler 2	HORIBA Scientific, Palaiseau, France
XRD	Bruker-AXS D8 Advance	Bruker Corporation, Billerica, MA, USA

3. Results

Figure 1 shows the surface morphologies of coating surfaces formed on titanium at 500 V, 575 V, and 650 V in two different electrolytes based on phosphoric acid. Two solutions were used: Electrolyte 1, containing H3PO4 with the addition of calcium nitrate tetrahydrate Ca(NO3)2·4H2O, magnesium nitrate hexahydrate Mg(NO3)2·6H2O, and zinc nitrate hexahydrate Zn(NO3)2·6H2O; and Electrolyte 2, with additions of calcium nitrate tetrahydrate Ca(NO3)2·4H2O, magnesium nitrate hexahydrate Mg(NO3)2·6H2O, and copper(II) nitrate trihydrate Cu(NO3)2·3H2O. It should be pointed out that all the obtained coatings were porous and had a well-developed surface.

Figure 1

Surface morphologies of surfaces after PEO processing.

In Figure 2 and Table 4, the EDS semiquann class="Chemical">titative results for samples obtained in Electrolyte 1 are presented as Ca/P, Mg/P, Zn/P, and M/P ratios. The Ca/P ratios were equal to 0.051 ± 0.003 natural units (n.u.), 0.063 ± 0.003 n.u., and 0.069 ± 0.003 n.u. for 500, 575, and 650 V, respectively. The Mg/P ratios were equal to 0.051 ± 0.004 n.u. (500 V), 0.058 ± 0.003 n.u. (575 V), and 0.060 ± 0.006 n.u. (650 V). The Zn/P ratios for 500, 575, and 650 V were equal to 0.052 ± 0.004 n.u., 0.065 ± 0.005 n.u., and 0.071 ± 0.010 n.u., respectively. The M/P ratios were equal to 0.153 ± 0.008, 0.187 ± 0.006, and 0.200 ± 0.020 for 500, 575, and 650 V, respectively.

Figure 2

Atomic ratios (EDS) of coatings formed in Electrolyte 1.

Table 4

Statistical description of EDS of coatings formed in Electrolyte 1. n.u., no units.

Ratios	Voltage	x¯	σ	Q1	Q2	Q3
Ca/Pn.u.	500 V	0.051	0.003	0.050	0.052	0.052
	575 V	0.063	0.003	0.062	0.064	0.065
	650 V	0.069	0.003	0.068	0.071	0.071
Mg/Pn.u.	500 V	0.051	0.004	0.049	0.051	0.053
	575 V	0.058	0.003	0.057	0.060	0.060
	650 V	0.060	0.006	0.057	0.063	0.063
Zn/Pn.u.	500 V	0.052	0.004	0.050	0.053	0.054
	575 V	0.065	0.005	0.063	0.068	0.068
	650 V	0.071	0.010	0.065	0.075	0.075
M/Pn.u.	500 V	0.153	0.008	0.149	0.151	0.157
	575 V	0.187	0.006	0.184	0.188	0.190
	650 V	0.200	0.015	0.192	0.195	0.206

Figure 3 and Table 5 present the EDS semiquann class="Chemical">titapan> class="Chemical">tive results for samples obtained in Electrolyte 2 as Ca/P, Mg/P, Cu/P, and M/P. The Ca/P ratios were equal to 0.062 ± 0.003 n.u., 0.068 ± 0.004 n.u., and 0.071 ± 0.003 n.u. for 500, 575, and 650 V, respectively. The Mg/P ratios were equal to 0.058 ± 0.002 n.u., 0.059 ± 0.003 n.u., and 0.064 ± 0.003 n.u. for 500, 575, and 650 V, respectively. The Cu/P ratios for samples obtained at 500, 575, and 650 V were equal to 0.039 ± 0.003 n.u., 0.048 ± 0.002 n.u., and 0.062 ± 0.005 n.u., respectively. The M/P ratios for samples obtained at 500, 575, and 650 V were equal to 0.158 ± 0.006 n.u., 0.175 ± 0.006 n.u., and 0.197 ± 0.004 n.u., respectively.

Figure 3

Atomic ratios (EDS) of coatings formed in Electrolyte 2.

Table 5

Statistical description of EDS of coatings formed in Electrolyte 2. n.u., no units.

Ratios	Voltage	x¯	σ	Q1	Q2	Q3
Ca/Pn.u.	500 V	0.062	0.003	0.060	0.061	0.062
	575 V	0.068	0.004	0.066	0.068	0.071
	650 V	0.071	0.003	0.068	0.072	0.073
Mg/Pn.u.	500 V	0.058	0.002	0.057	0.057	0.059
	575 V	0.059	0.003	0.056	0.060	0.061
	650 V	0.064	0.003	0.064	0.064	0.066
Cu/Pn.u.	500 V	0.039	0.003	0.037	0.040	0.040
	575 V	0.048	0.002	0.047	0.048	0.050
	650 V	0.062	0.005	0.059	0.061	0.063
M/Pn.u.	500 V	0.158	0.006	0.156	0.156	0.159
	575 V	0.175	0.006	0.172	0.176	0.177
	650 V	0.197	0.004	0.195	0.196	0.197

The diffrn class="Chemical">action data of PEO coatings formed in Electrolytes 1 and 2 at three voltages are presented in Figure 4. For both electrolytes, similar phenomena were observed, i.e., for samples oxidized at 500 and 575 V, only signal from titanium as metal matrix was detected, while for 650 V other crystalline phases, such as Ca(H2PO4)2∙H2O and Ti(HPO4)2∙H2O for samples obtained in Electrolyte 1 and Ca(H2PO4)2∙H2O for samples obtained in Electrolyte 2, were recorded. It was also found that voltage growth in PEO coatings caused amorphous phase accretion as well.

Figure 4

Diffractogram XRD results of PEO coatings obtained in (a) Electrolyte 1 and (b) Electrolyte 2.

GDOES data of n class="Chemical">PEO coatings formed in Electrolyte 1 at 500, 575, and 650 V are presented in Figure 5. The top and porous sublayers, which are enriched in Zn, P, and O and depleted in Ca, Mg, and Ti, have thicknesses of about 200, 300, and 500 s of sputtering time for 500, 575, and 650 V, respectively, while the thickness of the second (semiporous) one, which was enriched in calcium, magnesium, zinc, phosphorus, and oxygen and depleted in titanium, was in the range of 700 s (500 V) up to 2000 s (650 V) of sputtering time. On the other hand, the thicknesses of the third (transition) sublayers, in which a decrease of all signals, except titanium, was observed, increased from 800 s (500 V) up to 2000 s (650 V) of sputtering time. In Figure 6, the GDOES results of PEO coatings formed in Electrolyte 2 at the same three voltages are presented.

Figure 5

GDEOS signals (black), first derivatives (red continuous line), and second derivatives (brown dashed line) for samples formed in Electrolyte 1.

Figure 6

GDEOS signals (black), first derivatives (red continuous line), and second derivatives (brown dashed line) for samples formed in Electrolyte 2.

The top and porous sublayers, which are enpan>riched in P and O and depleted in Ca, Mg, Cu, and Ti, have thicknesses related to sputtering times equal to about 100, 300, and 600 s for 500, 575, and 650 V, respectively, while the thickness of the second (semiporous) layer, which is enriched in Ca, Mg, Cu, P, and O and depleted in Ti, is in the range of 600 s (500 V) up to 1900 s (650 V) of sputtering time. Here, the thicknesses of the transition sublayers are in the range from 600 s (500 V) up to 1500 s (650 V) of sputtering time. The part of C, N, and O signals may originate in the first top sublayers from contamination (from air and cleaning compounds). In addition, the H signals maxima, which are always placed in third-transition sublayers, is the end of the coating porosity. It should also be noted that the accretion of voltage caused an increase in coating thickness. In Figure 7 and Figure 8, the XPS spectra of PEO coatings formed in Electrolytes 1 and 2 are presented. Based on the obtained results, it can be concluded that the top external 10 nm layers of the PEO coating consist mainly of phosphorus, oxygen, nitrogen, titanium, calcium, magnesium, and zinc (Electrolyte 1) or copper (Electrolyte 2). The bindings of C with O and N with O can be interpreted as contaminants (cleaning process and adsorbed air). The phosphorus (P 2p) and oxygen (O 1s) spectra were in the range of 133.6–134 eV and 531.3–531.5 eV, respectively, which can be interpreted as the groups PO43−, HPO42−, H2PO4−, and P2O74−. The Cu 2p spectra maxima (331.1–932.9 eV and 934.5–935.8 eV) and Auger Cu LMM (566–567.2 eV) suggest the presence of Cu+ and Cu2+, while Ca2+ is proved by the binding energy (BE) in the range of 347.4−347.7 eV. The BE of Zn 2p (1021.9–1022.4 eV) and Zn LMM (497.9–501.5 eV) proves the existence of Zn2+, while BE in the range of 89.1–92.8 eV (Mg 2s) and 306.2–306.9 eV (Mg KLL) indicates the existence of Mg2+. The BE of titanium Ti 2p3/is in the range of 459.9−460.2 eV, which means that titanium is on the fourth oxidation state (Ti4+). Based on the quantitative XPS of the top 10 nm of PEO coatings obtained in Electrolytes 1 and 2 at three voltages, two ratios, Ca:Mg:Zn and Ca:Mg:Zn, were found. The Ca:Mg:Zn ratios are equal to 8:32:1 n.u. (500 V), 8:28:1 n.u. (575 V), and 14:45:1 n.u. (650 V), while the Ca:Mg:Zn ratios are equal to 5:5:1 n.u. (500 V), 4:7:1 n.u. (575 V), and 6:5:1 n.u. (650 V). (Ca + Mg + Zn)/P and (Ca + Mg + Cu)/P have their maxima equal to 0.48 n.u. and 0.21 n.u., respectively, at 575 V. The same trend was observed for single Me/P ratios, where M {Ca, Mg, Zn, Cu}, i.e., the maxima were recorded for PEO coatings obtained at 575 V.

Figure 7

XPS spectra for titanium samples after PEO treatment in Electrolyte 1.

Figure 8

XPS spectra for titanium samples after PEO treatment in Electrolyte 2.

4. Discussion

In this paper, the charn class="Chemical">acteristics of new porous coatings fabricated at 500, 575, and 650 V in electrolytes based on H3PO4 and Mg(NO3)2·6H2O, Ca(NO3)2·4H2O with Cu(NO3)2·3H2O, and Zn(NO3)2·6H2O were presented. Information on the chemical composition of the PEO coatings was obtained by use of the XPS method (for the first 10 nm) and EDS and XRD (for the whole volume of the coatings). Based on EDS results, which were recorded for the whole volume of the coatings, it was found that increased PEO voltage results in an increase of the average metal-to-phosphorus ratios (Ca/P, Mg/P, Zn/P, and Cu/P), while XPS analysis of 10 nm showed that the maxima of those ratios are achieved for the values of the central voltage (575 V), which indicates that the coatings are layered, as proven by GDOES elemental profiles. All the PEO coatings can be divided into three sublayers: (i) external porous layer, enriched in P, O, and Zn (Electrolyte 1) and depleted in Ca, Mg, and Cu (Electrolyte 2) and Ti, but also the most contaminated (CO2, C2H5OH); (ii) semiporous layer, enriched in Ca, Mg, P, O, and Zn (Electrolyte 1) or Cu (Electrolyte 2), and depleted in Ti; (iii) transition layer, in which the titanium signal increases and depletion of all other elements (P, O, Ca, Mg, Zn, and Cu) is detected. On the basis of these XPS data, it was possible to conclude that the extreme surface of the coatings most likely consists of titanium (Ti4+), calcium (Ca2+), magnesium (Mg2+), and oxygen with PO43−, HPO42−, H2PO4−, and P2O74− as well as Zn2+ or Cu+/Cu2+. Furthermore, the XRD analysis suggests that increasing voltage results in amorphization of the coatings, with the detection of crystalline phases such as Ca(H2PO4)2∙H2O and/or Ti(HPO4)2∙H2O.

It was also observed that un class="Chemical">sing zinn class="Chemical">c ions as a bactericidal element instead of the copper ions in PEO coatings obtained on titanium substrate results in a drastic increase of magnesium incorporated into the obtained structure, combined with a slight increase of calcium ions. The results presented in this paper may be used to design biocompatible and bactericidal coatings due to the creation hydroxyapatite-like structures, in which the Ca2+ may be replaced by others, i.e., Mg2+, Zn2+, Cu2+, and the hydroxy group (OH−) by Cu+ ions. It should be pointed out that while magnesium accelerates the healing of postoperative wounds, the structure composed of calcium and phosphorus is bone-like. Therefore, zinc or copper added in controlled quantities would perform antibacterial functions, which, together with magnesium, would allow faster healing of postoperative wounds.

It is posn class="Chemical">sible to obtain porous pan> class="Chemical">calcium–magnesium–phosphate coatings enriched with copper or zinc.

The higher the voltage of n class="Chemical">PEO treatmenpan>t, the thipan> class="Chemical">cker the porous coatings.

The higher the voltage of n class="Chemical">PEO treatmenpan>t, the higher the amounpan>t of built-in elemenpan>ts pan> class="Chemical">coming from the electrolyte and more amorphous phase in coatings.

The top 10 nm layer of the studied coan class="Chemical">tings consist mainly of Ti4+, Ca2+, Mg2+ and PO43−, HPO42−, H2PO4.