High Entropy Alloy Having Composite Microstructure and Method of Manufacturing the Same

Abstract

A method of making a metallic alloy, more particularly, a high-entropy alloy with a composite structure that exhibits high strength and good ductility, and is used as a component material in electromagnetic, chemical, shipbuilding, machinery, and other applications, and in extreme environments, and the like.

Claims

1. A method of manufacturing a high-entropy alloy having a composite structure, comprising: preparing metallic elements comprising, by weight %, Fe greater than 5% to 35% or less, Mn greater than 5% to 35% or less, Ni greater than 5% to 35% or less, and Co greater than 5% to 35% or less, and comprising at least one of Cu greater than 3% to 40% or less and Ag greater than 3% to 40% or less; manufacturing an alloy by melting the metallic elements having been prepared in one of casting, arc melting, and powder metallurgy methods; homogenization heat treating the alloy having been manufactured; and cooling the alloy after the homogenization heat treating.

2. The method of manufacturing a high-entropy alloy having a composite structure of claim 1, wherein the homogenization heat treating is performed while the alloy is maintained in a temperature range of 900 C. to 1200 C. for 1 hour to 48 hours.

3. The method of manufacturing a high-entropy alloy having a filamentary composite structure of claim 1, further comprising: performing deformation processing, wherein the deformation processing includes hot working, rolling, drawing, at room temperature and elevated temperatures.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0012] The patent or application file contains at least one drawing executed in color. Copies of this patent or patent application publication with color drawings will be provided by the Office upon request and payment of the necessary fee. The above and other aspects, features, and advantages of the present disclosure will be more clearly understood from the following detailed description taken in conjunction with the accompanying drawings, in which:

[0013] FIGS. 1A and 1B are diagrams illustrating a microstructure of a high-entropy alloy with a composite structure according to the present disclosure. FIG. 1A illustrates a microstructure before deformation processing including rolling, drawing and extrusion, and

[0014] FIG. 1B illustrates a microstructure after deformation processing;

[0015] FIGS. 2A and 2B are images of microstructures of inventive examples 3 and 4, respectively;

[0016] FIGS. 3A and 3B are images of microstructures of inventive examples 1 and 2, respectively;

[0017] FIG. 4 is a flowchart illustrating an example of a manufacturing method according to the present disclosure;

[0018] FIGS. 5A and 5B are images of microstructures of inventive example 5, respectively;

[0019] FIG. 6A is a scanning electron microscope image of a microstructure after casting of inventive example 1, and FIGS. 6B through 6F are elemental mapping images of Mn, Fe, Co, Cu, and Ni alloying elements, respectively for FIG. 6A;

[0020] FIG. 7A is an electron microscope image of a microstructure after processing of inventive example 1, and FIGS. 7B through 7F are elemental mapping images of Mn, Fe, Co, Cu, and Ni alloying elements, respectively, for FIG. 7A; and

[0021] FIG. 8 is an XRD analysis graph of inventive example 1.

DETAILED DESCRIPTION OF THE INVENTION

[0022] The inventors of the present disclosure conducted research into a method of improving mechanical/physical characteristics such as strength, ductility, and the like of a high-entropy alloy. As a result, compared to an alloy in which various alloy elements form a single-phase face-centered cubic or body-centered cubic solid solution, when some compositions of various alloy elements were partially separated therefrom or a different ductile metallic phase was formed instead of hard brittle intermetallic compounds, or when segregation or partial phase separation into ductile phase occurred, it was recognized that ductility and strength were further increased after deformation processing. In addition, when a fine filament structure was distributed through deformation processing, it could be confirmed that a high-entropy alloy with excellent strength and ductility was formed, leading to the present disclosure.

[0023] Hereinafter, a high-entropy alloy with a composite structure according to the present disclosure will be described in detail. First, a composition of a high-entropy alloy according to the present disclosure will be described in detail.

[0024] A high-entropy alloy according to the present disclosure includes, by weight %, iron (Fe) greater than 5% to 35% or less, manganese (Mn) greater than 5% to 35% or less, nickel (Ni) greater than 5% to 35% or less, and cobalt (Co) greater than 5% to 35% or less, and it is preferable to include at least one of copper (Cu) greater than 3% to 40% or less and silver (Ag) greater than 3% to 40% or less.

[0025] Fe, Mn, Ni, and Co are elements forming a high-entropy alloy, are period 4 transition elements, and are elements suitable for formation of a solid solution, or the like, since a difference in atomic radii, and the like, is small. Mn and Ni are elements promoting formation of a face-centered cubic (FCC) solid solution, and Co promotes refinement of a structure. Here, the content of the elements being greater than 5% to 35% or less is to induce a change in a portion of entropy in a uniform and homogeneous microstructure, in which a degree of entropy is significantly increased by as much as possible, high enough for formation of a solid solution.

[0026] Meanwhile, Cu and Ag are elements not for formation of a complete solid solution with Fe, Mn, Ni, and Co, but for partial separation and the formation of a ductile phase to be separated therefrom. Thus, the elements serve to increase ductility, and serve to enhance strength as a filament is formed by elongating the phase after deformation processing. Here, the content of Cu and Ag being greater than 3% to 40% or less is to induce an increase in ductility and strength due to partial separation of the ductile second phase, depending on fraction of a separated phase.

[0027] Hereinafter, a microstructure of a high-entropy alloy according to the present disclosure will be described in detail. FIG. 1 is a diagram schematically illustrating a microstructure of a high-entropy alloy according to the present disclosure, and the present disclosure will be described in detail with reference to FIG. 1.

[0028] In a microstructure of a high-entropy alloy according to the present disclosure, it is preferable that a ductile second phase be distributed in a matrix, a single phase solid solution, as illustrated in FIG. 1A. Meanwhile, after deformation processing so as to turn the ductile second phase into elongated filaments, as illustrated in FIG. 1B, in a high-entropy alloy according to the present disclosure, it is preferable that a filament structure formed by stretching a ductile second phase be distributed in a matrix.

[0029] The matrix refers to a solid solution formed by elements such as Fe, Mn, Ni, and Co.

[0030] The second phase refers to various forms or structures, not solidified in the matrix, such as a solid solution of a phase having a different element (a second solid solution), a single phase dendrite, segregation, a phase separation region, a particle, and the like. In other words, the second phase may refer to a structure different from the matrix. The second phase is distributed, thereby allowing a high-entropy alloy to ensure excellent ductility and strength through distribution of ductile second phase particles, filaments and other forms of ductile second phase.

[0031] The second phase is a Cu-rich phase (CuMnNi phase) or an Ag-rich phase (AgMn phase), which is not fully dissolved in the matrix of a high-entropy alloy, a solid solution. The phase described above is a phase having ductility higher than that of a matrix after casting, thereby having an effect of increasing ductility of a high-entropy alloy. Meanwhile, after deformation processing such as rolling, drawing, extrusion or the like of a high-entropy alloy, the phase described above is stretched to be elongated as a filament, thereby enhancing the strength.

[0032] The second phase exists while having a width of 5 m to 20 m and a length of 30 m to 300 m before processing, as illustrated in FIGS. 2A and 3A. Meanwhile, as illustrated in FIGS. 2B and 3B, after processing, the second phase is stretched. Thus, the second phase exists as an elongated filament having a thickness of 0.05 m to 2 m and a length of 10 m to 1000 m, and thus, a matrix may be strengthened. When the filament exists while having a thickness of 0.05 m to 2 m and a length of 10 m to 1000 m, the filament is not damaged by deformation and deformation resistance is optimized, thereby enhancing strength. The stretched filament exists to be elongated in a high-entropy alloy, and thus, an interface existing as an obstacle to deformation is provided. Thus, the filament serves to strengthen a matrix of a high-entropy alloy.

[0033] In the case of a high-entropy alloy having a filament structure due to the processing, a technical effect of simultaneously improving strength and ductility may be provided.

[0034] Hereinafter, a method of manufacturing a high-entropy alloy according to the present disclosure will be described in detail. FIG. 4 illustrates a schematic procedure of a manufacturing method according to an exemplary embodiment. Next, a manufacturing method according to the present disclosure will be described in detail with reference to FIG. 4.

[0035] According to the present disclosure, preparing a metal material including, by weight %, Fe greater than 5% to 35% or less, Mn greater than 5% to 35% or less, Ni greater than 5% to 35% or less, and Co greater than 5% to 35% or less, and including at least one of Cu greater than 3% to 40% or less and Ag greater than 3% to 40% or less, is included therein; and melting, homogenization heat treating, and cooling are also included. Processing a high-entropy alloy manufactured thereby may be added thereto.

[0036] The melting process is provided to alloy a manufactured metallic material, a method therefor is not particularly limited in the present disclosure, and a method commonly used in a technical field of the present disclosure may be used. For example, the alloy may be manufactured in casting, arc melting, powder metallurgy, and other methods.

[0037] Next, the manufactured alloy is homogenization heat treated. Homogenization is a process for inducing diffusion, and it is preferable to maintain an alloy in a temperature range of 900 C. to 1200 C. for 1 hour to 48 hours.

[0038] Cooling is performed after the homogenization heat treating. A cooling method is not particularly limited, and a method of air-cooling, water-quenching or furnace-cooling may be performed. Through the cooling process, a phase, in which some compositions are separated from a microstructure or having ductility of a different composition, may be formed. Alternatively, segregation or phase separation may occur. Thus, forming a small precipitate.

[0039] With respect to a high-entropy alloy manufactured in the method described above, further processing may be performed. In the present disclosure, a deformation processing method is not particularly limited, and a processing method according to the related art performed in a technical field of the present disclosure may be applied. For example, hot working, rolling, drawing, room temperature processing, and the like may be used. By the deformation processing, as illustrated in FIG. 1B, a second phase inside a high-entropy alloy matrix is changed into a filamentary structure. In other words, when deformation processing is performed, a high-entropy alloy according to the present disclosure has a technical effect of simultaneously improving strength and ductility.

[0040] Hereinafter, an exemplary embodiment of the present disclosure will be described in detail. An exemplary embodiment described below is merely to provide an understanding of the present disclosure, and the present disclosure is not limited thereto.

Exemplary Embodiment

[0041] First, as illustrated in Table 1, high-entropy alloys with the composite structure, according to comparative examples 1 through 3 and inventive examples 1 through 5, were manufactured.

[0042] A metal material having a composition (by weight %) of Table 1 was prepared, and the metal material was arc melted in air or a vacuum or argon atmosphere to manufacture an alloy. Thereinafter, homogenization heat treatment was performed at 1050 C. for 24 hours.

[0043] Meanwhile, with respect to the high-entropy alloys with the composite structure manufactured as described above, according to comparative examples 1, 2, and 3 and inventive examples 1, 2, 3, 4, and 5, deformation processing including rolling was performed at room temperature to manufacture a board having a thickness of 1 mm.

[0044] With respect to the high-entropy alloys manufactured as described above, a tensile test was carried out and mechanical properties were evaluated. The mechanical properties are illustrated in Table 1.

TABLE-US-00001 TABLE 1 Tensile Yield strength strength Elongation Classification Alloy Microstructure (MPa) (MPa) (%) Comparative Co.sub.20Cr.sub.20Fe.sub.20Mn.sub.22Ni.sub.18 Single phase 620 480 40 example 1 Comparative Fe.sub.25Ni.sub.25Co.sub.25Cr.sub.25 Single phase 1000 870 35 example 2 Comparative Fe.sub.20Mn.sub.20Ni.sub.20Co.sub.20Cr.sub.20 Single phase 760 640 17 example 3 Inventive Fe.sub.20Ni.sub.20Co.sub.20Mn.sub.20Cu.sub.20 Matrix + dendrite 1020 730 46 example 1 Inventive Fe.sub.20Ni.sub.20Co.sub.20Mn.sub.20Cu.sub.20 Matrix + filament 1633 1460 32 example 2 Inventive Fe.sub.20Ni.sub.20Co.sub.20Mn.sub.20Ag.sub.20 Matrix + Ag-rich phase 1080 923 43 example 3 Inventive Fe.sub.20Ni.sub.20Co.sub.20Mn.sub.20Ag.sub.20 Matrix + filament 1794 1645 29 example 4 Inventive Fe.sub.17.5Ni.sub.17.5Co.sub.17.5Mn.sub.17.5Cu.sub.30 Matrix + filament 1435 1225 21 example 5

[0045] As illustrated in Table 1, in the case of inventive example 1 including a second phase (a dendrite) in a matrix and inventive example 3 including an Ag-rich phase in a matrix, while satisfying a composition according to the present disclosure, strength was excellent, as compared to a comparative example. In addition, elongation exceeded 40%, and thus, excellent ductility was confirmed. In the case of inventive examples 2, 4, and 5, having a structure of a filament formed by stretching a ductile second phase by deformation processing, high strength and excellent elongation were ensured.

[0046] Meanwhile, FIGS. 2A and 2B are images of inventive examples 3 and 4, respectively. In FIG. 2A, a microstructure before deformation processing is confirmed that an Ag-rich phase, not fully solidified in a matrix, exists in the matrix. In FIG. 2B, a microstructure after deformation processing is confirmed that the Ag-rich phase has a filament structure.

[0047] FIGS. 3A and 3B are images of inventive examples 1 and 2, respectively. In FIG. 3A, a microstructure before deformation processing is confirmed to have a structure in which a dendrite phase exists in a matrix. In FIG. 3B, a microstructure after deformation processing is confirmed to have a filament structure in which the dendrite phase is thinly elongated.

[0048] In addition, FIGS. 5A and 5B are images of inventive example 5. In FIG. 5A, a microstructure before deformation processing is confirmed to have a structure in which a dendrite phase exists in a matrix. In FIG. 5B, a microstructure after deformation processing is confirmed to have a filament structure the Cu-rich phase (CuMnNi phase) is thinly elongated.

[0049] Meanwhile, FIG. 6A is an electron microscope image of a microstructure after casting of inventive example 1. FIGS. 6B through 6F are images of a mapping image of Mn, Fe, Co, Cu, and Ni alloying elements, respectively. In addition, in Table 2, energy dispersive spectroscopy (EDS) analysis values with respect to compositions measured in a dendrite arm and a matrix of inventive example 1 are summarized.

TABLE-US-00002 TABLE 2 Mn Fe Co Ni Cu (at. %) (at. %) (at. %) (at. %) (at. %) Matrix 19.5 21.28 22.13 19.12 18.43 Dendrite 24.97 5.01 5.71 13.14 51.18 arm

[0050] As illustrated in FIG. 6 and Table 2, Cu and Mn are significantly distributed in a dendrite arm, and Co and Fe alloying elements are mainly distributed in a matrix between dendrite arms. In addition, a Ni alloying element is confirmed in a dendrite arm, but mainly distributed in a matrix. In addition, Fe and Co are mainly distributed in a matrix between dendrite arms, but the high content of other alloying elements (Mn, Ni, and Cu), and the like is confirmed. A main alloying element of a dendrite arm is Cu, and a significant amount of Mn and Ni alloying elements is also included therein. Since melting temperatures of Cu and Mn are lower than melting temperatures of Fe and Co, Cu and Mn have a tendency to be separated while being solidified at the beginning. Thus, Cu and Mn may grow as a CuMn dendrite. A melting temperature of an Ni alloying element is higher than melting temperatures of Cu and Mn alloying elements. However, since solid solubility of the Ni alloying element with respect to Cu is significant, a solid solution phase of Ni and Cu is distributed in a matrix in a manner similar to a Cu phase. Cu and Mn form a solid solution at a high temperature (>900 C.). When the content of Mn exceeds 20%, the solid solution is separated into two phases below 700 C.

[0051] FIG. 7A is an electron microscope image of a microstructure after processing of inventive example 1, and FIGS. 7B through 7F are images illustrating a mapping image of Mn, Fe, Co, Cu, and Ni alloying elements, respectively.

[0052] As illustrated in FIG. 7, a filament structure formed by stretching a Cu-rich phase (CuMnNi phase), a ductile second phase after deformation processing, is confirmed. A matrix phase and the Cu-rich phase (CuMnNi phase) have an FCC structure. When lattice constants of two phases are calculated using Vegard's rule, using elements of Table 1, a difference in a size of lattice constants of two phases is not significant. In XRD spectra, it is difficult to observe phase separation.

[0053] FIG. 8 is a graph illustrating an XRD analysis result of inventive example 1. In FIG. 8, diffraction peaks are illustrated as (111), (200), (220), and (311), respectively, and refers to a FCC crystal structure having a lattice constant, a=0.348 nm. In other words, as other peaks are not observed, a FCC crystal structure is confirmed after as-cast and homogenization treatment. In addition, as a portion of a peak (220) is separated on XRD data, it is confirmed that a second phase exists.

[0054] As set forth above, according to an exemplary embodiment, through a combination of a matrix and a ductile second phase of a high-entropy alloy, in addition to a shape, a size, and distribution by deformation processing of a ductile phase, excellent strength and ductility may be implemented. Thus, it is advantageous to variously use a high-entropy alloy.

[0055] While exemplary embodiments have been shown and described above, it will be apparent to those skilled in the art that modifications and variations could be made without departing from the scope of the present invention as defined by the appended claims.