The Effects of Niobium and Molybdenum on the Microstructures and Corrosion Properties of CrFeCoNiNbxMoy Alloys

The present work systematically investigated the effects of niobium and molybdenum on the microstructures and corrosion properties of high-entropy CrFeCoNiNbxMox and CrFeCoNiNbxMo1−x alloys, the maximum content of (Nb + Mo) was 20 at.%. All of the alloys were prepared by arc melting under an argon atmosphere. In CrFeCoNiNbxMox alloys (x = 0.15, 0.3 and 0.5), increasing Nb and Mo content would change the microstructure of the alloy from a hypoeutectic structure (x ≤ 0.3) to a hypereutectic one (x = 0.5). All of the CrFeCoNiNbxMo1−x alloys (x = 0.25, 0.5 and 0.75) had a hypereutectic microstructure. Only two phases were analyzed in these alloys, which were face-centered cubic (FCC) and hexagonal close packing (HCP). Increasing the content of Nb and Mo increases the hardness of the alloys by the effects of the solid solution strengthening and formation of the HCP phase. The potentiodynamic polarization curves of these alloys were also measured in 1 M sulfuric acid and 1 M sodium chloride solutions to evaluate the corrosion resistance of these alloys. The CrFeCoNiNb0.3Mo0.3 alloy had the smallest corrosion rate (0.0732 mm/yr) in 1 M deaerated H2SO4 solution, and the CrFeCoNiNb0.15Mo0.15 alloy had the smallest corrosion rate (0.0425 mm/yr) in 1 M deaerated NaCl solution. However, the CrFeCoNiNb0.5Mo0.5 alloy still had the best combination of corrosion resistance and hardness in the present study.


Introduction
The alloys used in this study were prepared under the high-entropy alloy concept [1][2][3]. This high-entropy alloy concept provides researchers to develop new materials with suitable properties for applications. Researchers can smartly select the elements to prepare the materials, and many high-entropy alloys (HEAs) were thus produced with excellent mechanical, physical and chemical properties. Moreover, the shapes of high-entropy materials can be bulk alloys, thin films or coating alloys. For example, the casting, homogenization, cold rolling, recrystallization and deformation mechanism of equiatomic CoCrFeMnNi high-entropy alloy were well investigated [4,5]. The microstructures and compression properties of CoCrFeNiTiAl x high-entropy alloys were tested, and results indicated that the CoCrFeNiTiAl alloy had good compressive strength and elastic modulus [6]. The elements with a high melting point were selected to produce the refractory alloys, such as NbMoTaW, VNbMoTaW and HfTaTiNbZr-based alloys [7,8]. The high-entropy alloys can be prepared by mechanical alloying (MA) to obtain the alloys with nanocrystalline structures and enhance the properties [9,10].
Cobalt, chromium and nickel are wildly used to produce alloys with good corrosion resistance. Other elements are selected and added into CoCrNi alloy to change the microstructures and enhance the mechanical properties, such as CoCrFeMnNi alloy [11]. Co-CrFeNiSn has good passivation in sodium chloride solution compared with stainless steels [12]. The AlCoCrFeNiTi 0.5 coating was fabricated by laser cladding coating and showed the optimal performance of corrosion and mechanical properties [13]. Minor additions of molybdenum could improve the corrosion resistance of the AlCrFe 2 Ni 2 alloy by suppressing pit formation [14]. The addition of molybdenum could increase the corrosion resistance was observed in the (CoCrFeNi) 100−x Mo x high-entropy alloys [15]. The study on the Al 0.4 CrFe 1.5 MnNi 0.5 Mo x alloys indicated that adding molybdenum can effectively improve the impedance of passive film and reduce the corrosion current density and thus form a more stable passivation film [16]. The non-equimolar Cr 19 Fe 22 Co 21 Ni 25 Mo 13 alloy possessed better corrosion resistance compared with 304 stainless steel in both deaerated 1 M HNO 3 and 1 M HCl solutions [17]. The corrosion resistance of FeCuNbSiB and CrFeCoNiNb x alloys can be improved by adding niobium [18,19].
In our previous study on the corrosion properties of FeCoNi and CrFeCoNi alloys [20], the FeCoNi alloy had a better corrosion resistance by comparing with CrFeCoNi alloy. After adding molybdenum, the corrosion resistance of FeCoNiMo was not as good as that of the CrFeCoNiMo alloy [21]. This indicates that chromium is a very important element in developing a corrosion-resistant alloy. Therefore, the present work studied the effect of adding Nb and Mo on the CrFeCoNi alloy and evaluated the potential of the application.

Materials and Methods
The CrFeCoNiNb x Mo x and CrFeCoNiNb x Mo 1−x alloys were prepared by arc-melting under argon atmosphere after accurate weighting. Each melt was about 100 g. Table 1 lists the nominal compositions of the alloys. The microstructures of the alloys were examined by a scanning electron microscope (SEM, JEOL JSM-6335, JEOL Ltd., Tokyo, Japan) after regular metallurgical processes. The compositions of the alloys and the phases existing in the alloys were analyzed by an energy dispersive spectrometer (EDS). An X-ray diffractometer (XRD, Rigaku ME510-FM2, Rigaku Ltd., Tokyo, Japan) was used to identify the phases in the alloys, and the scanning rate was fixed at 0.04 degrees per second. A Vicker's hardness tester (Matsuzawa Seiki MV1, Matsuzawa Ltd., Akita, Japan) was used to measure the hardness of the alloys, and the loading force was 19.61 N (2000 gf). The potentiodynamic polarization curves of the alloys were tested by a three-electrode electrochemical device (Autolab PGSTAT302N, Metrohm Autolab B.V., Utrecht, The Netherlands). One electrode was the specimens mounted in epoxy resin with an exposed area of 0.196 cm 2 (0.5 cm in diameter). The second electrode was a counter (a platinum wire). The third electrode was a reference one, which was a saturated silver chloride electrode (Ag/AgCl, SSE). This potential of the reference Ag/AgCl electrode was 0.197 V higher than the standard hydrogen electrode (SHE) at 25 • C [22]. All of the potentiodynamic polarization curves were tested at 30 • C, and the scanning rate of the potentiodynamic polarization test was 1 mV per second. Nitrogen bubbled through the process to degas the oxygen in the solutions. The solutions of 1 M sulfuric acid and 1 M sodium chloric solutions were prepared by reagent-grade acids and deionized water.

Results and Discussion
This work was divided into two parts to investigate the effect of Nb and Mo content on the effects of CrFeCoNiNb x Mo y alloys. Part 1 was the CrFeCoNiNb x Mo x alloys, and x was 0.15, 0.3 and 0.5. The same amount of Nb and Mo was added to the CrFeCoNi alloy. The microstructure revolution of CrFeCoNiNb x Mo x alloys were studied in this part; the relationships between the properties and the microstructures were also investigated. Part 2 studied the properties of CrFeCoNiNb x Mo 1−x alloys, where x was 0.25, 0.5 and 0.75. This part studied the effect of different ratios of Nb and Mo on the microstructures and properties of the alloys. The total amount of Nb and Mo was fixed at one part (20 at.%) because the alloys would easily crack during solidification if an excess amount of Nb and Mo was added.

CrFeCoNiNb x Mo x Alloys
The microstructures of as-cast CrFeCoNiNb x Mo x alloys, x = 0.15, 0.3 and 0.5, are shown in Figure 1. In our previous study, the CrFeCoNi alloy had an FCC-structured granular microstructure and some Cr-rich precipitates with HCP structure [20]. After adding Nb and Mo, the microstructures of as-cast CrFeCoNiNb x Mo x alloys became dendritic ones. The dendrites of CrFeCoNiNb x Mo x alloys showed a single phase, and the interdendrities of CrFeCoNiNb x Mo x alloys showed a eutectic structure. Table 2 shows the chemical compositions of the alloys and the phases existing in the alloys. According to our previous study [23], the HCP phase had higher Nb and Mo content, and FCC had higher Cr-Fe and Ni content. Therefore, the FCC and HCP phases were easy to identify by detecting the compositions. The dendrites of CrFeCoNiNb 0.15 Mo 0.15 and CrFeCoNiNb 0.3 Mo 0.3 alloys were an FCC phase and the dendrites of CrFeCoNiNb 0.5 Mo 0.5 alloy were an HCP-structured laves phase. All of the interdendrites of CrFeCoNiNb x Mo x alloys were a eutectic structure with two phases which were FCC and HCP phases (laves phase). This indicated that the alloy changed from a hypoeutectic alloy to a hypereutectic one. That is, CrFeCoNiNb 0.15 Mo 0.15 and CrFeCoNiNb 0.3 Mo 0.3 alloys were hypoeutectic alloys, and CrFeCoNiNb 0.5 Mo 0.5 alloy was a hypereutectic alloy. process to degas the oxygen in the solutions. The solutions of 1M sulfuric acid and 1M sodium chloric solutions were prepared by reagent-grade acids and deionized water.

Results and Discussion
This work was divided into two parts to investigate the effect of Nb and Mo content on the effects of CrFeCoNiNbxMoy alloys. Part 1 was the CrFeCoNiNbxMox alloys, and x was 0.15, 0.3 and 0.5. The same amount of Nb and Mo was added to the CrFeCoNi alloy. The microstructure revolution of CrFeCoNiNbxMox alloys were studied in this part; the relationships between the properties and the microstructures were also investigated. Part 2 studied the properties of CrFeCoNiNbxMo1−x alloys, where x was 0.25, 0.5 and 0.75. This part studied the effect of different ratios of Nb and Mo on the microstructures and properties of the alloys. The total amount of Nb and Mo was fixed at one part (20 at.%) because the alloys would easily crack during solidification if an excess amount of Nb and Mo was added.

CrFeCoNiNb x Mo x Alloys
The microstructures of as-cast CrFeCoNiNbxMox alloys, x = 0.15, 0.3 and 0.5, are shown in Figure 1. In our previous study, the CrFeCoNi alloy had an FCC-structured granular microstructure and some Cr-rich precipitates with HCP structure [20]. After adding Nb and Mo, the microstructures of as-cast CrFeCoNiNbxMox alloys became dendritic ones. The dendrites of CrFeCoNiNbxMox alloys showed a single phase, and the interdendrities of CrFeCoNiNbxMox alloys showed a eutectic structure. Table 2 shows the chemical compositions of the alloys and the phases existing in the alloys. According to our previous study [23], the HCP phase had higher Nb and Mo content, and FCC had higher Cr-Fe and Ni content. Therefore, the FCC and HCP phases were easy to identify by detecting the compositions. The dendrites of CrFeCoNiNb0.15Mo0.15 and CrFeCoNiNb0.3Mo0.3 alloys were an FCC phase and the dendrites of CrFeCoNiNb0.5Mo0.5 alloy were an HCP-structured laves phase. All of the interdendrites of CrFeCoNiNbxMox alloys were a eutectic structure with two phases which were FCC and HCP phases (laves phase). This indicated that the alloy changed from a hypoeutectic alloy to a hypereutectic one. That is, CrFeCoNiNb0.15Mo0.15 and CrFeCoNiNb0.3Mo0.3 alloys were hypoeutectic alloys, and CrFeCoNiNb0.5Mo0.5 alloy was a hypereutectic alloy.
(a)      [24]. Therefore, the hardness of the CrFeCoNiNb x Mo x alloys increased due to the solid solution strengthening effect. Our previous work indicated that increasing niobium and molybdenum content increases the density of dislocation in the FCC phase [23]. This was another effect enhancing the hardness of the alloys. Additionally, the hardness of the HCP-structured laves phase was higher than that of the FCC phase because the slip system of the HCP phase was less than that of the FCC phase. The hardness of CrFeCoNiNb x Mo x alloys increased after adding more niobium and molybdenum elements due to the increase in the HCP phase and solid solution strengthening effect.     [24]. Therefore, the hardness of the    Table 3. The potentiodynamic polarization curves of the alloys with potential negative than corrosion potential (Ecorr) was the cathode. The potentiodynamic polarization curves of the alloys with potential positive than corrosion potential was the anode. The corrosion potential (Ecorr) of CrFeCoNiNb x Mo x alloys was very close. The standard electrode potential of the elements used in present work is listed in Table 4 [25]. The niobium is more active than the other elements because the standard electrode potential of niobium is more negative. Therefore, the corrosion potential of CrFeCoNiNb0.5Mo0.5 alloy had the most negative corrosion potential (Ecorr). The corrosion current densities (icorr) of CrFeCoNiNb x Mo x alloys were all around 10 μA/cm 2 . The potentiodynamic polarization curve of CrFeCoNiNb0.15Mo0.15 alloy had an apparent anodic peak, and the other alloys had no anodic peak. The passivation potential (Epp) and critical current density (icrit) of the anodic peak of CrFeCoNiNb0.15Mo0.15 alloy is listed in Table 3. Thus, the CrFeCoNiNb0.3Mo0.3 and CrFeCoNiNb0.5Mo0.5 alloys easily entered into the passivation regions and formed the passive films during corrosion in H2SO4 solution. The lowest passivation current densities (ipass) of these alloys were about 12 A/cm 2 . All the passivation regions of these alloys were breakdown at a potential (Eb) of about 1.2 V (SHE) due to oxygen evolution reaction [26].   Table 3. The potentiodynamic polarization curves of the alloys with potential negative than corrosion potential (E corr ) was the cathode. The potentiodynamic polarization curves of the alloys with potential positive than corrosion potential was the anode. The corrosion potential (E corr ) of CrFeCoNiNb x Mo x alloys was very close. The standard electrode potential of the elements used in present work is listed in Table 4 [25]. The niobium is more active than the other elements because the standard electrode potential of niobium is more negative. Therefore, the corrosion potential of CrFeCoNiNb 0.5 Mo 0.5 alloy had the most negative corrosion potential (E corr ). The corrosion current densities (i corr ) of CrFeCoNiNb x Mo x alloys were all around 10 µA/cm 2 . The potentiodynamic polarization curve of CrFeCoNiNb 0.15 Mo 0.15 alloy had an apparent anodic peak, and the other alloys had no anodic peak. The passivation potential (E pp ) and critical current density (i crit ) of the anodic peak of CrFeCoNiNb 0.15 Mo 0.15 alloy is listed in Table 3. Thus, the CrFeCoNiNb 0.3 Mo 0.3 and CrFeCoNiNb 0.5 Mo 0.5 alloys easily entered into the passivation regions and formed the passive films during corrosion in H 2 SO 4 solution. The lowest passivation current densities (i pass ) of these alloys were about 12 A/cm 2 . All the passivation regions of these alloys were breakdown at a potential (E b ) of about 1.2 V (SHE) due to oxygen evolution reaction [26].

CrFeCoNiNb x Mo 1−x Alloys
The microstructures and properties of CrFeCoNiNb x Mo 1−x alloys were studied in this part. The total amount of Nb and Mo of these alloys was kept as one part; the amount of Nb and Mo thus equaled 20 at.%. The microstructures of as-cast CrFeCoNiNb x Mo 1−x alloys, x = 0.25 and 0.75, are shown in Figure 6. All of the CrFeCoNiNb x Mo 1−x alloys, x = 0.25, 0.5 and 0.75, had a hypereutectic microstructure because a large amount of Nb and Mo were added into these alloys. The dendrites of CrFeCoNiNb x Mo 1−x alloys were an HCP phase (laves phase), and the interdendrites of CrFeCoNiNb x Mo 1−x alloys were a eutectic structure with FCC and HCP phases (laves phase). Table 6 lists the chemical compositions of the alloys and the phases existing in the alloys. As described above, the Nb and Mo content in the HCP phase of the alloys is higher than that in the FCC phase.

CrFeCoNiNbxMo1−x Alloys
The microstructures and properties of CrFeCoNiNbxMo1−x alloys were studied in this part. The total amount of Nb and Mo of these alloys was kept as one part; the amount of Nb and Mo thus equaled 20 at.%. The microstructures of as-cast CrFeCoNiNbxMo1−x alloys, x = 0.25 and 0.75, are shown in Figure 6. All of the CrFeCoNiNbxMo1−x alloys, x = 0.25, 0.5 and 0.75, had a hypereutectic microstructure because a large amount of Nb and Mo were added into these alloys. The dendrites of CrFeCoNiNbxMo1−x alloys were an HCP phase (laves phase), and the interdendrites of CrFeCoNiNbxMo1−x alloys were a eutectic structure with FCC and HCP phases (laves phase). Table 6 lists the chemical compositions of the alloys and the phases existing in the alloys. As described above, the Nb and Mo content in the HCP phase of the alloys is higher than that in the FCC phase.     Figure 7 shows the XRD patterns of the CrFeCoNiNb x Mo 1−x alloys. Two phases existing in these alloys were FCC and HCP-structured laves phases. The HCP phase was the main phase in these CrFeCoNiNb x Mo 1−x alloys, and the FCC phase became the minor phase in these alloys. Figure 8 displays the hardness of CrFeCoNiNb x Mo 1−x alloys, some of the data were from our previous study [23]. According to our previous study, the overall hardness of the alloy was contributed by the hard HCP dendrites and the soft interdendrities (HCP + HCC). The hardness of both HCP and FCC phases increased with increasing the content of Nb and Mo due to solid solution strengthening. However, the hardness of the FCC phase was still softer than that of the HCP phase. Because the hardness of interdendrities was softer than that of dendrites, increasing the volume fraction of interdendrite would decrease the overall hardness of the alloy. The CrFeCoNiNb 0.5 Mo 0.5 alloy had the lowest hardness among these alloys because of the largest ratio of interdendrities in this alloy. The CrFeCoNiNb 0.75 Mo 0.25 alloy had the highest hardness of 625 HV among the alloys in the present study.   hardness of interdendrities was softer than that of dendrites, increasing the volume fraction of interdendrite would decrease the overall hardness of the alloy. The CrFeCoNiNb0.5Mo0.5 alloy had the lowest hardness among these alloys because of the largest ratio of interdendrities in this alloy. The CrFeCoNiNb0.75Mo0.25 alloy had the highest hardness of 625 HV among the alloys in the present study.  Hardness of as-cast CrFeCoNiNbxMo1−x alloys. Each value is the average hardness of the alloy. Some of the data are from our previous study [23]. Figure 9 shows the potentiodynamic polarization curves of the as-cast CrFeCoNiNbxMo1−x alloys in 1M deaerated H2SO4 solution at 30 °C. The potentiodynamic polarization data of these polarization curves are listed in Table 7. The corrosion potential (Ecorr) and the corrosion current densities (icorr) of CrFeCoNiNbxMo1−x alloys were very close; the CrFeCoNiNb0.25Mo0.75 alloy had the lowest icorr of about 5 μA/cm 2 . The potentiodynamic polarization curve of CrFeCoNiNb0.25Mo0.75 and CrFeCoNiNb0.75Mo0.25 alloys had apparent anodic peaks, but the CrFeCoNiNb0.5Mo0.5 alloy had no anodic peak. The passivation potential (Epp) and critical current density (icrit) of the anodic peaks of the alloys are listed in Table 7. This indicated that the CrFeCoNiNb0.5Mo0.5 alloys easily entered the passivation regions and formed the passive films during corrosion in H2SO4 solution among these alloys. The current densities of the passivation regions (ipass) of CrFeCoNiNb0.5Mo0.5 and CrFeCoNiNb0.75Mo0.25 alloys were about 12 A/cm 2 , but the   Table 7. The corrosion potential (E corr ) and the corrosion current densities (i corr ) of CrFeCoNiNb x Mo 1−x alloys were very close; the CrFeCoNiNb 0.25 Mo 0.75 alloy had the lowest i corr of about 5 µA/cm 2 . The potentiodynamic polarization curve of CrFeCoNiNb 0.25 Mo 0.75 and CrFeCoNiNb 0.75 Mo 0.25 alloys had apparent anodic peaks, but the CrFeCoNiNb 0.5 Mo 0.5 alloy had no anodic peak. The passivation potential (E pp ) and critical current density (i crit ) of the anodic peaks of the alloys are listed in Table 7. This indicated that the CrFeCoNiNb 0.5 Mo 0.5 alloys easily entered the passivation regions and formed the passive films during corrosion in H 2 SO 4 solution among these alloys. The current densities of the passivation regions (i pass ) of CrFeCoNiNb 0.5 Mo 0.5 and CrFeCoNiNb 0.75 Mo 0.25 alloys were about 12 A/cm 2 , but the CrFeCoNiNb 0.25 Mo 0.75 alloy had a larger passivation current density (i pass ). The passivation regions of these alloys were all breakdown at a potential (E b ) of about 1.2 V (SHE) because of oxygen evolution reaction [26]. In order to compare the properties of corrosion potential, corrosion current density, anodic peak and passivation region of each alloy in the present study, the CrFeCoNiNb 0.5 Mo 0.5 alloy had the best corrosion resistance among the alloys in H 2 SO 4 solution.   Figure 10 shows the potentiodynamic polarization curves of the as-cast CrFeCoNiNbxMo1−x alloys in 1M deaerated NaCl solution at 30 °C. The potentiodynamic polarization data of these polarization curves are listed in Table 8. The cathodic limit current density (iL) was found in these CrFeCoNiNbxMo1−x alloys. The cathodic limit current density meant that the maximum reaction rate was limited because of the diffusion rate of hydroxyl ions (OH -) in the solution [26]. The corrosion potential (Ecorr) of CrFeCoNiNb0.25Mo0.75 alloy was more positive than the other alloys; the corrosion potential (Ecorr) of CrFeCoNiNb0.5Mo0.5 and CrFeCoNiNb0.75Mo0.25 alloy was very close. Moreover, the corrosion current density (icorr) of CrFeCoNiNb0.25Mo0.75 alloy was larger than the other alloys. The corrosion current density (icorr) of CrFeCoNiNb0.5Mo0.5 and CrFeCoNiNb0.75Mo0.25 alloys were about 10 μA/cm 2 . All of the CrFeCoNiNbxMo1−x alloys had apparent anodic peaks in 1M deaerated NaCl solution. The passivation regions of CrFeCoNiNb0.5Mo0.5 and CrFeCoNiNb0.75Mo0.25 alloys were better than that of   Figure 10 shows the potentiodynamic polarization curves of the as-cast CrFeCoNiNb x Mo 1−x alloys in 1 M deaerated NaCl solution at 30 • C. The potentiodynamic polarization data of these polarization curves are listed in Table 8. The cathodic limit current density (i L ) was found in these CrFeCoNiNb x Mo 1−x alloys. The cathodic limit current density meant that the maximum reaction rate was limited because of the diffusion rate of hydroxyl ions (OH − ) in the solution [26]. The corrosion potential (E corr ) of CrFeCoNiNb 0. 25   The corrosion rate of the alloys in deaerated 1M H2SO4 and 1M NaCl solutions can be calculated by assuming that all of the corrosion types of the alloys in these solutions are a type of uniform corrosion. Therefore, the relationship between corrosion depth of one year and corrosion current density is listed as the following Equation [27]: where M is the average atomic mass (g/mol), icorr is the corrosion current density (A/cm 2 ), t is the corrosion time (31,536,000 s, 1 yr), ρ is the average density (g/cm 3 ), n is the number of average valence electron and F is the Faraday constant (96,500 C/mol). This study assumes that the average density of an alloy is ρ=∑Xiρi, where Xi and ρi are the molar fraction and density of element i. The corrosion rates (mm per year) of the alloys in deaerated 1M H2SO4 and 1M NaCl solutions are listed in   The corrosion rate of the alloys in deaerated 1 M H 2 SO 4 and 1 M NaCl solutions can be calculated by assuming that all of the corrosion types of the alloys in these solutions are a type of uniform corrosion. Therefore, the relationship between corrosion depth of one year and corrosion current density is listed as the following Equation [27]: where M is the average atomic mass (g/mol), i corr is the corrosion current density (A/cm 2 ), t is the corrosion time (31,536,000 s, 1 yr), ρ is the average density (g/cm 3 ), n is the number of average valence electron and F is the Faraday constant (96,500 C/mol). This study assumes that the average density of an alloy is ρ = ∑X i ρ i , where X i and ρ i are the molar fraction and density of element i. The corrosion rates (mm per year) of the alloys in deaerated 1 M H 2 SO 4 and 1 M NaCl solutions are listed in However, the CrFeCoNiNb 0.5 Mo 0.5 alloy still possessed the best combination of corrosion resistance and hardness among these alloys.

Conclusions
The microstructures, hardness and corrosion properties of hypoeutectic CrFeCoNiNb x Mo x alloys (x = 0.15 and 0.3) and hypereutectic CrFeCoNiNb x Mo 1−x alloys (x = 0.25, 0.5 and 0.75) were studied. There were two phases (FCC and HCP) in these alloys. The dendrites of hypoeutectic CrFeCoNiNb x Mo x alloys (x = 0.15 and 0.3) were an FCC phase; the interdendrities of these alloys were a eutectic structure which the phases were HCP and FCC phases. The dendrites of hypereutectic CrFeCoNiNb x Mo 1−x alloys (x = 0.25, 0.5 and 0.75) were an HCP-structured laves phase, and the interdendrities of these alloys were a eutectic structure with HCP and FCC phases. Increasing the content of Nb and Mo would increase the hardness of the alloys because of the formation of the hard HCP phase and the effect of solid solution strengthening. The CrFeCoNiNb 0.75 Mo 0.25 alloy had the highest hardness of 625 HV among the alloys in present study. After potentiodynamic polarization test in deaerated 1 M H 2 SO 4 and 1 M NaCl solutions at 30 • C, the CrFeCoNiNb 0.5 Mo 0.5 alloy had the best corrosion resistance among these alloys by comparing the properties of corrosion potential, corrosion current density, anodic peak and passivation region of the alloys. Therefore, CrFeCoNiNb 0.5 Mo 0.5 alloy was the best alloy among these alloys by comparing the corrosion properties and hardness.