US20210054486A1

US20210054486A1 - Medium-entropy alloy having excellent cryogenic properties

Info

Publication number: US20210054486A1
Application number: US16/308,517
Authority: US
Inventors: Hyoung-Seop Kim; Jong-Un MOON; Jae-Wung BAE
Original assignee: Pohang University of Science and Technology Foundation POSTECH
Current assignee: Pohang University of Science and Technology Foundation POSTECH
Priority date: 2017-07-26
Filing date: 2017-08-28
Publication date: 2021-02-25
Also published as: KR101910744B1; EP3660178A1; WO2019022283A1; EP3660178A4; JP2019532169A; EP3660178B1

Abstract

Disclosed is a medium-entropy alloy, which is further improved in cryogenic mechanical properties of an existing FCC-based high-entropy alloy and is capable of ensuring price competitiveness, the medium-entropy alloy including 6 to 15 at % of Cr, 50 to 64 at % of Fe, 13 to 25 at % of Co, 13 to 25 at % of Ni, and the remainder of inevitable impurities, wherein the medium-entropy alloy includes a metastable FCC phase, whereby deformation-induced phase transformation from an FCC phase into a BCC phase occurs upon plastic deformation of the alloy, thus manifesting excellent cryogenic mechanical properties.

Description

TECHNICAL FIELD

The present invention relates to a medium-entropy alloy (MEA) having excellent cryogenic mechanical properties, in which inexpensive Fe is included in an amount of 50 at % or more to thus exhibit high price competitiveness, and moreover, in which face-centered cubic (FCC) and body-centered cubic (BCC) phase stability may be adjusted through control of alloying elements to thus cause deformation-induced phase transformation during cryogenic deformation, thereby realizing excellent cryogenic mechanical properties.

BACKGROUND ART

A high-entropy alloy (HEA) is a multielement alloy obtained by alloying five or more constituent elements at a similar ratio without a major element of the alloy. A high-entropy alloy is a metal material having a single-phase structure, such as a face-centered cubic (FCC) phase or a body-centered cubic (BCC) phase, without forming intermetallic compounds or intermediate phases, due to high entropy of mixing in the alloy.
In particular, a Co—Cr—Fe—Mn—Ni-based high-entropy alloy has excellent cryogenic properties, high fracture toughness and high corrosion resistance, and is thus receiving attention as a material suitable for use in extreme environments.
Two important factors in designing such a high-entropy alloy are the composition ratio of the constituent elements of the alloy and the configurational entropy of the alloy system.
Here, the composition ratio of the high-entropy alloy is discussed first. A high-entropy alloy has to be composed of at least five elements, and the fraction of each of the constituent elements of the alloy is set to the range of 5 to 35 at %. Furthermore, when another element is added in the production of a high-entropy alloy, in addition to the main alloying elements, the amount thereof should be 5 at % or less.
Also, alloys are typically divided into high-entropy alloys, medium-entropy alloys (MEAs), and low-entropy alloys (LEAs), depending on the configurational entropy (ΔS_conf) of the composition of alloying elements, and are classified according to the conditions of Equation 2 below based on the configurational entropy value determined by Equation 1 below.
$\begin{matrix} Δ S_{conf} = - R \sum_{i = 1}^{n} X_{i} \ln X_{i} & [Equation 1] \end{matrix}$
(R: Gas constant, X_i: mole fraction of i element, n: number of constituent elements)
ΔS _conf≤1.0·R(LEAs),
1.0·R≤ΔS _conf≤1.5·R(MEAs),
1.5·R≤ΔS _conf(HEAs) [Equation 2]
For a Co₂₀Cr₂₀Fe₂₀Mn₂₀Ni₂₀(at %) alloy, which is a representative cryogenic FCC-based high-entropy alloy, the alloying elements that are added are expensive, resulting in low price competitiveness. Accordingly, despite the excellent cryogenic properties thereof, the above alloy makes it difficult to serve as a replacement for existing steel materials in marine plants, LNG container materials, cryogenic tanks, and ship/marine materials.
Therefore, the industrialization of high-entropy alloys is essentially required to ensure price competitiveness through control of alloying elements and also to realize excellent cryogenic properties.

CITATION LIST

(Patent Document) U.S. Patent Application Publication No. 2002/0159914
(Non-Patent Document) 1. B. Gludovatz, et al., “A fracture-resistant high-entropy alloy for cryogenic applications”, Science, 345 (2014) 1153-1158.

DISCLOSURE

Technical Problem

Accordingly, an objective of the present invention is to provide a medium-entropy alloy, which is capable of exhibiting superior mechanical properties by causing deformation-induced phase transformation at cryogenic temperatures, as well as ensuring price competitiveness by developing an alloy including reduced amounts of expensive alloying elements, in lieu of a conventional Co—Cr—Fe—Mn—Ni-based alloy.

Technical Solution

In order to accomplish the above objective, the present invention provides a medium-entropy alloy, comprising 6 to 15 at % of Cr, 50 to 64 at % of Fe, 13 to 25 at % of Co, 13 to 25 at % of Ni, and the remainder of inevitable impurities.
Moreover, the medium-entropy alloy according to an embodiment of the present invention includes a metastable FCC phase at room temperature and causes deformation-induced phase transformation from the metastable FCC phase into a BCC phase upon cryogenic deformation, and is thus improved in mechanical properties.

Advantageous Effects

According to the present invention, a medium-entropy alloy is configured such that the amount of Fe, which is an inexpensive alloying element, is increased to the range of 50 to 64 at %, thus reducing the amounts of expensive Co, Cr, and Ni elements that are added, thereby ensuring price competitiveness, and moreover, the medium-entropy alloy has superior properties including tensile strength of 1024 MPa or more and elongation of 47% or more at a cryogenic temperature (77 K).
Moreover, according to an embodiment of the present invention, the medium-entropy alloy includes a metastable FCC phase at room temperature (298 K) and causes deformation-induced phase transformation from the metastable FCC phase into a BCC phase upon deformation at a cryogenic temperature to thus exhibit strengthening effects, ultimately obtaining further improved cryogenic mechanical properties.

DESCRIPTION OF DRAWINGS

FIG. 1 shows the results of measurement of X-ray diffraction (XRD) of Co—Cr—Fe—Ni-based medium-entropy alloys of Comparative Examples 1 and 2 and Examples 1 to 4 according to the present invention;

FIG. 2 shows the results of tensile testing at room temperature (298 K) of the Co—Cr—Fe—Ni-based medium-entropy alloys of Comparative Examples 1 and 2 and Examples 1 to 4 according to the present invention;

FIG. 3 shows the results of tensile testing at a cryogenic temperature (77 K) of the Co—Cr—Fe—Ni-based medium-entropy alloys of Comparative Examples 1 and 2 and Examples 1 to 4 according to the present invention; and

FIG. 4 shows the analytical results of electron backscatter diffraction (EBSD) for phase transformation upon deformation at room temperature and at a cryogenic temperature of the Co—Cr—Fe—Ni-based medium-entropy alloy of Example 3 according to the present invention.

BEST MODE

Hereinafter, a detailed description will be given below of preferred embodiments of the present invention with reference to the appended drawings, but the present invention is not limited to the following examples. Accordingly, those skilled in the art will appreciate that various modifications are possible, without departing from the spirit of the invention.
The present inventors have performed thorough study in order to obtain excellent mechanical properties in cryogenic environments while increasing price competitiveness of high-entropy alloys having superior mechanical properties in cryogenic environments, and thus have ascertained that the amount of Fe, which is an inexpensive element, is remarkably increased to the range of 50 to 64 at % compared to conventional high-entropy alloys, and the amounts of alloying elements other than Fe are adjusted, whereby deformation-induced phase transformation may occur during deformation due to changes in FCC and BCC phase stability, resulting in excellent cryogenic mechanical properties.
In particular, the present inventors have revealed that when an alloy is designed so as to include an FCC phase in a metastable state at room temperature, deformation-induced phase transformation from the FCC phase in a metastable state into a BCC phase may occur during deformation in a cryogenic environment, thereby further improving cryogenic mechanical properties, which culminates in the present invention.
In the present invention, when the phase in a metastable state is transformed into a phase in a stable state at the corresponding temperature through deformation-induced phase transformation during plastic deformation, it is judged to be a metastable phase. All of these phases are defined as a metastable phase.
The medium-entropy alloy according to the present invention has an alloy composition comprising 6 to 15 at % of Cr, 50 to 64 at % of Fe, 13 to 25 at % of Co, 13 to 25 at % of Ni, and the remainder of inevitable impurities.
Furthermore, the medium-entropy alloy according to the present invention includes a metastable FCC at room temperature, and enables occurrence of deformation-induced phase transformation from the metastable FCC phase into a BCC phase upon deformation.
If the amount of chromium (Cr) is less than 6 at %, the FCC phase is stabilized. On the other hand, if the amount thereof exceeds 15 at %, the BCC phase is stabilized. Hence, the amount of Cr preferably falls in the range of 6 to 15 at %. Also, since the formation of the metastable FCC phase is more favorable in terms of improving cryogenic mechanical properties, the amount of chromium (Cr) more preferably falls in the range of 7.5 to 12.5 at %.
If the amount of iron (Fe) is less than 50 at %, the FCC phase is stabilized. On the other hand, if the amount thereof exceeds 64 at %, the BCC phase is stabilized. Hence, the amount of Fe preferably falls in the range of 50 to 64 at %. Since the formation of the metastable FCC phase is more favorable in terms of improving cryogenic mechanical properties, the amount of iron (Fe) more preferably falls in the range of 55 to 62.5 at %.
If the amount of cobalt (Co) is less than 13 at %, the FCC phase is stabilized. On the other hand, if the amount thereof exceeds 25 at %, the BCC phase is stabilized. Hence, the amount of Co preferably falls in the range of 13 to 25 at %.
If the amount of nickel (Ni) is less than 13 at %, the BCC phase is stabilized. On the other hand, if the amount thereof exceeds 25 at %, the FCC phase is stabilized. Hence, the amount of Ni preferably falls in the range of 13 to 25 at %.
If the amount of at least one selected from among molybdenum (Mo) and aluminum (Al), which is a component that may substitute for cobalt (Co), is less than 13 at %, the FCC phase is stabilized. On the other hand, if the amount thereof exceeds 25 at %, the BCC phase is stabilized. Hence, the amount thereof preferably falls in the range of 13 to 25 at %.
If the amount of manganese (Mn), which is a component that may substitute for nickel (Ni), is less than 13 at %, the BCC phase is stabilized. On the other hand, if the amount thereof exceeds 25 at %, the FCC phase is stabilized. Hence, the amount thereof preferably falls in the range of 13 to 25 at %.
In general, an interstitial element such as C or N in a metal alloy is subjected to interstitial solid solution in the metal matrix to thus enhance the strength of the alloy due to solid-solution strengthening effects during metal deformation. When at least one element of C and N is added in an amount of 1 at % or more based on the total at % of the alloy, the FCC phase is stabilized. In order to utilize the effect of deformation-induced phase transformation by inducing the metastable FCC phase, it is preferred that the above element be added in an amount of less than 1 at %.
The inevitable impurities are components other than the above alloying elements and are unavoidable components that are inevitably incorporated into the alloying elements or during the production process.
The medium-entropy alloy may be composed of a metastable FCC phase or a combination of a metastable FCC phase and a BCC phase at room temperature. Here, it is preferred that the fraction of the metastable FCC phase be high in the interests of improvements in tensile strength and elongation. The fraction of the metastable FCC phase is preferably 50% or more. However, the fraction of the metastable FCC phase is not necessarily 50% or more.
Also, the medium-entropy alloy may have tensile strength of 500 MPa or more and elongation of 50% or more at room temperature (298 K).
Also, the medium-entropy alloy may have tensile strength of 1000 MPa or more and elongation of 40% or more at a cryogenic temperature (77 K).

Examples 1 to 4

Production of Medium-Entropy Alloy
First, Co, Cr, Fe, and Ni metals having purity of 99.9% or more were prepared.
The metals thus prepared were weighed in the mixing fractions shown in Table 1 below.

	TABLE 1

	Metal mixing fraction (at %)

	Co	Cr	Fe	Ni

Example 1	17.50	10.00	55.00	17.50
Example 2	16.25	10.00	57.50	16.25
Example 3	15.00	10.00	60.00	15.00
Example 4	13.75	10.00	62.50	13.75

The metals prepared in the above fractions were placed in a crucible, heated to 1550° C. and thus melted, and then cast into 150 g of an alloy ingot having a cuboid shape having a width of 33 mm, a length of 80 mm, and a thickness of 7.8 mm, using a mold.
In order to remove the oxide formed on the surface of the cast alloy, surface grinding was performed. The thickness of the ground ingot was 7 mm.
The surface-ground ingot having a thickness of 7 mm was subjected to homogenization heat treatment at 1100° C. for 6 hr and then cold rolling to a thickness from 7 mm to 1.5 mm.
Furthermore, the cold-rolled alloy plate was annealed at 800° C. for 10 min.

Comparative Examples 1 and 2

Production of Alloy for Comparative Examples
The alloys of Comparative Examples were manufactured in the same manner as in Examples using the components in the amounts shown in Table 2 below.

	TABLE 2

	Metal mixing fraction (at %)

	Co	Cr	Fe	Ni

Comparative Example 1	14.50	5.00	66.00	14.50
Comparative Example 2	12.50	10.00	65.00	12.50

The alloy ingot was cast in the same manner as in Examples, followed by homogenization heat treatment at 1100° C. for 6 hr and then cold rolling to a thickness from 7 mm to 1.5 mm in the same manner as in Examples.
Furthermore, the cold-rolled alloy plate was annealed at 800° C. for 10 min in the same manner as in Examples.
Component Analysis Results
The actual components of the alloys manufactured in Comparative Examples 1 and 2 and Examples 1 to 4 after annealing treatment were analyzed using EDS. The results are shown in Table 3 below.

	TABLE 3

	EDS analysis composition (at %)

	Co	Cr	Fe	Ni

Comparative Example 1	14.34	5.10	66.29	14.27
Example 1	17.37	10.52	55.58	16.53
Example 2	16.16	10.21	57.41	16.22
Example 3	14.54	10.68	60.89	13.89
Example 4	13.55	10.27	62.55	13.63
Comparative Example 2	12.23	10.81	65.31	11.65

As is apparent from Table 3, the actual composition falls slightly out of the range of the initial metal mixing fractions, but may be regarded as almost the same level considering the purity of metals and impurities which may be incorporated during the production process. All of Examples fell in the composition range of the medium-entropy alloy according to the present invention, comprising 6 to 15 at % of Cr, 50 to 64 at % of Fe, 13 to 25 at % of Co, and 13 to 25 at % of Ni.
XRD Analysis Results
FIG. 1 shows the results of XRD measurement at room temperature of the annealed alloys of Comparative Examples 1 and 2 and Examples 1 to 4.
XRD measurement was performed after grinding in the order of sandpaper Nos. 600, 800 and 1200 and then electrolytic etching in 8% perchloric acid in order to minimize phase transformation due to deformation during grinding of a test specimen.
As shown in FIG. 1, Comparative Example 1 was composed of the BCC phase, Examples 1 to 4 were composed mainly of the metastable FCC phase, and Comparative Example 2 was composed mainly of the BCC phase and included a small amount of the FCC phase.
Specifically, when the amount of Fe was increased and the amounts of Co and Ni were decreased, the stability of the FCC phase was deteriorated, and consequently the metastable FCC phase was formed in Examples 1 to 4. In Comparative Examples 1 and 2, in which Fe was added in an amount of 65 at % or more, the FCC phase was no longer in the metastable state but became unstable, and the BCC phase was relatively stabilized.
Tensile Test Results
The results of tensile testing at room temperature (298 K) and at a cryogenic temperature (77 K) of the annealed alloys of Comparative Examples 1 and 2 and Examples 1 to 4 according to the present invention are shown in FIGS. 2 and 3 and Table 4 below.
FIGS. 2 and 3 are graphs showing the results of tensile testing at room temperature and at a cryogenic temperature, respectively, in which the horizontal axis designates the engineering strain and the vertical axis designates the engineering stress. Based on the graphs of the test results, the results of analysis of physical properties such as yield strength, tensile strength and elongation of Comparative Examples and Examples 1 to 4 are given in Table 4 below.

	TABLE 4

	Room temperature	Cryogenic temperature (77 K)

	Yield	Tensile	Elon-	Yield	Tensile	Elon-
Test	strength	strength	gation	strength	strength	gation
specimen	(MPa)	(MPa)	(%)	(MPa)	(MPa)	(%)

Comparative	850	975	24	1336	1455	33
Example 1
Example 1	280	550	68	615	1024	126
Example 2	274	568	86	543	1164	118
Example 3	226	534	98	526	1508	82
Example 4	228	787	67	620	1649	47
Comparative	579	996	26	1110	1516	30
Example 2

As is apparent from FIGS. 2 and 3 and Table 3, the tensile properties at room temperature of the medium-entropy alloys of Examples 1 to 4 according to the present invention exhibited yield strength of 226 to 280 MPa, tensile strength of 534 to 787 MPa, and elongation of 67 to 98%.
Furthermore, excellent tensile properties at a cryogenic temperature, such as yield strength of 526 to 620 MPa, tensile strength of 1024 to 1649 MPa, and elongation of 47 to 126%, were manifested.
In contrast, the tensile properties at room temperature of the medium-entropy alloys of Comparative Examples 1 and 2 were as follows: since the initial crystal structure was mostly composed of a BCC structure, there were neither strengthening effects nor elongation enhancement effects due to deformation-induced phase transformation between tensile deformation at room temperature and tensile deformation at a cryogenic temperature, and tensile yield strength and tensile strength were high at room temperature and at a cryogenic temperature due to the BCC structure, but elongation was low, resulting in brittleness.
In particular, the alloy of Example 3, including a large amount of the FCC phase in the metastable state, manifested excellent tensile properties at a cryogenic temperature, such as yield strength of 526 MPa, tensile strength of 1508 MPa, and elongation of 82%, which were not previously reported.
Additionally, in the medium-entropy alloy of the present invention, even when at least one of Mo and Al substituting for Co was added in the same amount as Co under the condition that the amounts of Cr and Fe were maintained, deformation-induced phase transformation occurred during deformation, as was expected in the present invention, whereby ductility and stiffness were observed at a cryogenic temperature.
Also, in the medium-entropy alloy of the present invention, even when Mn substituting for Ni was added in the same amount as Ni under the condition that the amounts of Cr and Fe were maintained, deformation-induced phase transformation occurred during deformation, as was expected in the present invention, whereby ductility and stiffness were observed at a cryogenic temperature.
Furthermore, when at least one of C and N was subjected to solid solution as an interstitial element in the metal matrix of the medium-entropy alloy of the present invention, it was also confirmed that the strength of the alloy was increased due to the solid-solution strengthening effect.
Deformation-Induced Phase Transformation
FIG. 4 shows the analytical results of EBSD for phase transformation of the medium-entropy alloy of Example 3 during deformation at room temperature and at a cryogenic temperature according to the present invention.
As shown in FIG. 4, the alloy of Example 3 included a very small amount of the BCC phase and was composed mainly of the metastable FCC phase before deformation, and the fraction of the BCC phase was remarkably increased after deformation at room temperature (298 K) and at a cryogenic temperature (77 K). In particular, phase transformation from the FCC phase into the BCC phase occurs over the entire region after deformation at a cryogenic temperature, and this phase transformation contributes greatly to the improvement of cryogenic mechanical properties, as shown in FIG. 3.
Therefore, with regard to the cryogenic mechanical properties, the fraction of the FCC phase before deformation is preferably set to 50% or more.

TABLE 5

Before deformation	After deformation	After deformation
(vol %)	(298 K) (vol %)	(77 K) (vol %)

Comparative	91.26	93.96	98.99
Example 1
Example 1	0.34	15.07	28.46
Example 2	0.38	20.26	36.12
Example 3	0.41	27.68	56.71
Example 4	25.68	62.23	85.08
Comparative	87.81	89.20	94.87
Example 2

Table 5 shows the results of ferritescope measurement of the BCC phase fraction (vol %) of the alloys of Comparative Examples 1 and 2 and Examples 1 to 4 according to the present invention, before deformation and after deformation at room temperature and at a cryogenic temperature.
As is apparent from Table 5, the alloys of Examples 1 to 3 included a small amount of the BCC phase before deformation and were increased in the fraction of the BCC phase due to phase transformation between deformation at room temperature and deformation at a cryogenic temperature. Also, the alloy of Example 4 was relatively increased in BCC phase stability compared to the alloys of Examples 1 to 3, and thus it was confirmed that 25.68 at % of the BCC phase was included before deformation and that the fraction of the BCC phase was increased due to phase transformation between deformation at room temperature and deformation at a cryogenic temperature. The alloys of Comparative Examples 1 and 2 were very high in BCC phase stability compared to the alloys of Examples 1 to 4, and thus it was confirmed that 91.26 at % and 87.81 at % of the BCC phases, respectively, were included before deformation and that the fraction of the BCC phase was increased due to phase transformation between deformation at room temperature and deformation at a cryogenic temperature.

Claims

1. A medium-entropy alloy, comprising 6 to 15 at % of Cr, 50 to 64 at % of Fe, 13 to 25 at % of Co, 13 to 25 at % of Ni, and a remainder of inevitable impurities, wherein deformation-induced phase transformation from a face-centered cubic (FCC) phase into a body-centered cubic (BCC) phase occurs upon plastic deformation.

2. The medium-entropy alloy of claim 1, wherein the deformation-induced phase transformation occurs in a metastable FCC phase.

3. The medium-entropy alloy of claim 1, wherein an amount of the Cr is 7.5 to 12.5 at %.

4. The medium-entropy alloy of claim 3, wherein an amount of the Fe is 57.5% to 62.5 at %.

5. The medium-entropy alloy of claim 1, wherein the Co is substitutable with at least one selected from among Mo and Al.

6. The medium-entropy alloy of claim 1, wherein the Ni is substitutable with Mn.

7. The medium-entropy alloy of claim 1, wherein at least one of C and N is included in an amount of less than 1 at % based on a total at % of the medium-entropy alloy.

8. The medium-entropy alloy of claim 6, wherein at least one of C and N is included in an amount of less than 1 at % based on a total at % of the medium-entropy alloy.

9. The medium-entropy alloy of claim 1, wherein the deformation occurs at a temperature equal to or lower than room temperature (298 K).

10. The medium-entropy alloy of claim 2, wherein a fraction of the metastable FCC phase is 50% or more.

11. The medium-entropy alloy of claim 1, wherein the medium-entropy alloy is composed of a combination of a BCC phase and a metastable FCC phase, or is composed of a metastable FCC phase alone.

12. The medium-entropy alloy of claim 1, wherein the medium-entropy alloy has a tensile strength of 226 MPa or more and an elongation of 67% or more at room temperature (298 K).

13. The medium-entropy alloy of claim 1, wherein the medium-entropy alloy has a tensile strength of 1024 MPa or more and an elongation of 47% or more at a cryogenic temperature (77 K).