CN108823481A - A kind of high-entropy alloy and preparation method thereof - Google Patents
A kind of high-entropy alloy and preparation method thereof Download PDFInfo
- Publication number
- CN108823481A CN108823481A CN201810752440.0A CN201810752440A CN108823481A CN 108823481 A CN108823481 A CN 108823481A CN 201810752440 A CN201810752440 A CN 201810752440A CN 108823481 A CN108823481 A CN 108823481A
- Authority
- CN
- China
- Prior art keywords
- alloy
- entropy alloy
- entropy
- preparation
- present
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C22/00—Alloys based on manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/30—Ferrous alloys, e.g. steel alloys containing chromium with cobalt
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Metal Rolling (AREA)
Abstract
The present invention provides a kind of high-entropy alloys, are related to technical field of metal material.High-entropy alloy provided by the invention is by including that the element of following atomic percentage content is prepared：Fe 39.0~41.0%, Co 9.0~11.0%, Mn 39.0~41.0%, Cr 9.0~11.0%.High-entropy alloy stacking fault energy theoretical value of the invention is about 35mJ/mol, which is conducive to high-entropy alloy when placing lower than room temperature environment, still keeps single phase austenite structure；When the load that meets with stresses under cryogenic, in addition to dislocation movement by slip and Praw texturing occurs, also deformation occurs induces austenite to martensite transfor mation.From embodiment as can be seen that high-entropy alloy of the invention is in 173K, yield strength 670M, for extensibility up to 62%, tensile strength reaches 750MPa；Plasticity and intensity are higher than the mechanical property of the cryogenic steel product prepared with conventional method.
Description
Technical field
The present invention relates to technical field of metal material more particularly to a kind of low temperature no nickel high-entropy alloy and its preparation sides
Method.
Background technique
High-entropy alloy breaks through the single pivot alloy design concept of tradition, by multiple element according to equal atomic ratios or close to etc. originals
Son is than a kind of novel alloy made of alloying.Since it is with the incomparable high intensity of conventional metals, high rigidity, high abrasion
The excellent properties such as corrosion resistance and high fever/resistance, in fields such as aircraft, ship, high-speed cutting cutter and petrol resources exploitations
Show huge application potential.High-entropy alloy may also be faced during processing preparation and subsequent military service zero degrees celsius with
Under even lower temperature use environment, this does not require nothing more than it high intensity under severe conditions, also to have certain uniformly modeling
Property deformation ability.
The research in high-entropy alloy field concentrates on designing by more pivot ingredients so that the entropy of system maximizes, to obtain
Stable phase structure, including face-centered cubic, body-centered cubic or close-packed hexagonal and it is single-phase with a small amount of amorphous, nanocrystalline coexist
For design object.Similar with conventional alloys, this kind of alloy is by hindering dislocation motion to improve the intensity of material.Specifically mechanism is：
Atomic size difference is influenced between by element, and the distortion of lattice inside alloy hinders dislocation movement by slip；Secondly, the amorphous of Dispersed precipitate
It can produce reinforcing, nanocrystalline interior dislocation-free exists.Two aspect collective effects make strong/hardness of alloy improve and be plastically deformed more
Add difficulty.However, when such metal material be placed in low temperature environment meet with stresses load when, it may be speculated that its internal dislocation
The ability of movement can be very faint due to lacking the activation energy that dislocation is started as in conventional alloys, to seriously reduce
The plasticity of material.
It is a kind of element that metal material can be made to have good plasticity at low temperature in view of nickel, there is research
(B.Gludovatz,A.Hohenwarter,D.Catoor,E.H.Chang,E.P.George,R.O.Ritchie,A
fracture-resistant high-entropy alloy for cryogenic applications,Science,
2014,345:The cryogenic stretching performance for 1153-1158) reporting the high-entropy alloy iron cobalt manganese chromium nickel of face-centred cubic structure, through examining
It surveys high-entropy alloy iron cobalt manganese chromium nickel and is not only one of most hard metal material recorded at present, and intensity, ductility at low temperature
Instead than being all improved under room temperature.Therefore, become the best high entropy alloy material of cold plasticity.It is anti-under the Alloy At Room Temperature
Tensile strength is 750MPa, uniform elongation 55%；When deformation temperature is 200K, tensile strength 900MPa uniformly extends
Rate is 60%；When deformation temperature is 77K, tensile strength 1200MPa, uniform elongation reaches 70%.However, in the alloy
Five kinds of alloying elements be equal atomic percents, i.e. the atom content of nickel is up to 20%, and cost is too high.Height in relation to not adding nickel
Entropy alloy also has been reported that in the literature.The prior art (Z.Li, K.G.Pradeep, Y.Deng, D.Raabe, C.C.Tasan,
Metastable high-entropy dual-phase alloys overcome the strength-ductility
trade-off,Nature,vol.534,pp.1,2016；Z.Li,F.B.Grabowski,J.Neugebauer,
D.Raabe,Ab initio assisted design of quinary dual-phase high-entropy alloys
With transformation-induced plasticity, Acta Mater., vol.136, pp.262,2017) it reports
It is larger atomic ratio by regulation alloying element content, obtains with face centered cubic austenite and the mixing of close-packed hexagonal martensite
The iron cobalt manganese chromium high-entropy alloy of structure, wherein austenite and Martensite Volume Fraction are respectively 72% and 28%.At room temperature, this
It is reported in the literature with optimal strength and plasticity that the tensile strength and elongation at break of kind two-phase high-entropy alloy are above front
The FeCoMnCrNi alloy matched.However, when Service Environment temperature is reduced to 173K, due to six side horses inside the two-phase alloys
The intracorporal dislocation mobility of family name is significantly reduced well below austenite, the whole plasticity of alloy, and maximum extension rate is only 16%.
Therefore it provides a kind of high-entropy alloy without nickel with excellent mechanical performance at low temperature is extremely urgent.
Summary of the invention
In view of this, the purpose of the present invention is to provide a kind of high-entropy alloys and preparation method thereof.High entropy of the invention closes
Gold has excellent cryogenic mechanics performance in 173K.
In order to achieve the above-mentioned object of the invention, the present invention provides following technical scheme：
The present invention provides a kind of high-entropy alloys, are prepared by the element for including following atomic percentage content：Fe 39.0
~41.0%, Co 9.0~11.0%, Mn 39.0~41.0%, Cr 9.0~11.0%.
Preferably, the high-entropy alloy is in 173K, yield strength 670M, and up to 62%, tensile strength reaches extensibility
750MPa。
The present invention also provides the preparation methods of high-entropy alloy described in above-mentioned technical proposal, include the following steps：
(1) raw metal is smelted, obtains smelting liquid alloy water；
(2) the smelting liquid alloy water for obtaining the step (1) is closed successively through casting ingot, forged and hot rolling
Golden precursor；
(3) the alloy precursor for obtaining the step (2) obtains high-entropy alloy successively through solid solution, cold rolling and calcining.
Preferably, the temperature smelted in the step (1) is 1700~1900 DEG C.
Preferably, the temperature being hot-forged in the step (2) is 1150~1250 DEG C.
Preferably, the temperature of hot rolling is 850~900 DEG C in the step (2).
Preferably, the opposite volume under pressure of hot rolling is 40~60% in the step (2).
Preferably, the temperature being dissolved in the step (3) is 1150~1250 DEG C.
Preferably, the soaking time being dissolved in the step (3) is 1.5~2h.
Preferably, the temperature calcined in the step (3) is 850~900 DEG C.
The present invention provides a kind of high-entropy alloys, are prepared by the element for including following atomic percentage content：Fe 39.0
~41.0%, Co 9.0~11.0%, Mn 39.0~41.0%, Cr 9.0~11.0%.The present invention, which passes through, determines Fe 39.0
~41.0%, Co 9.0~11.0%, Mn 39.0~41.0%, Cr 9.0~11.0% keeps the stacking fault energy of high-entropy alloy theoretical
Value is about 35mJ/mol, which is conducive to make high-entropy alloy when placing lower than room temperature environment, still keeps single phase austenite
Structure；When the load that meets with stresses under cryogenic, in addition to dislocation movement by slip and Praw texturing occurs, also deformation occurs induces Ovshinsky
Body is to martensite transfor mation.It illustrates, during low temperature deformation, the generation of martensite cenotype does not result in material in low temperature
Plasticity reduces during military service, and martensitic traoformation and dislocation, twin synergistic effect make high-entropy alloy while being strengthened
Still there is good uniform plastic deformation ability.From embodiment as can be seen that high-entropy alloy of the invention is in 173K, surrender is strong
Degree is 670M, and for extensibility up to 62%, tensile strength reaches 750MPa；Plasticity and intensity are higher than the cryogenic steel prepared with conventional method
The mechanical property of product.
Detailed description of the invention
Fig. 1 is the X ray diffracting spectrum of 1 high-entropy alloy of embodiment；
Fig. 2 is 1 high-entropy alloy of embodiment and the engineering for being dissolved simple tension under the conditions of 298K and 173K of state high-entropy alloy
Stress-engineering strain curve graph；
Fig. 3 is the electron backscatter diffraction photo figure of 1 high-entropy alloy of embodiment；
Fig. 4 is the stereoscan photograph of 1 high-entropy alloy of embodiment simple tension fracture under the conditions of 298K and 173K；
Fig. 5 is the X ray diffracting spectrum of 1 high-entropy alloy of comparative example；
Fig. 6 is the electron backscatter diffraction photo figure of 1 high-entropy alloy of comparative example.
Specific embodiment
The present invention provides a kind of high-entropy alloys, are prepared by the element for including following atomic percentage content：Fe 39.0
~41.0%, Co 9.0~11.0%, Mn 39.0~41.0%, Cr 9.0~11.0%.
In the present invention, prepare the high-entropy alloy raw material include atomic percentage content be 39.0~41.0% Fe,
Preferably 39.4~40.6%, more preferably 39.8~40.2%.In the present invention, the source of the ferro element is preferably purity
Iron powder or iron block greater than 99.9wt%.
In the present invention, prepare the high-entropy alloy raw material include atomic percentage content be 9.0~11.0% Co, it is excellent
It is selected as 9.4~10.6%, more preferably 9.8~10.2%.In the present invention, the source of the cobalt element is preferably that purity is greater than
The cobalt dust or cobalt block of 99.9wt%.
In the present invention, prepare the high-entropy alloy raw material include atomic percentage content be 39.0~41.0% Mn,
Preferably 39.4~40.6%, more preferably 39.8~40.2%.In the present invention, the source of the manganese element is preferably purity
Manganese powder end or manganese block greater than 99.9wt%.
In the present invention, prepare the high-entropy alloy raw material include atomic percentage content be 9.0~11.0% Cr, it is excellent
It is selected as 9.4~10.6%, more preferably 9.8~10.2%.In the present invention, the source of the chromium is preferably that purity is greater than
The chromium powder end of 99.9wt% or chromium block.
The high-entropy alloy formed by the raw material of above-mentioned atomic percentage content is single phase austenite tissue at room temperature；In low temperature
When lower military service, deformation occurs induces austenite to martensite transfor mation, to keep material plasticity and intensity all very high.Height of the invention
Entropy alloy stacking fault energy theoretical value is about 35mJ/mol, which is conducive to make high-entropy alloy when placing lower than room temperature environment,
Still keep single phase austenite structure；When the load that meets with stresses under cryogenic, in addition to dislocation movement by slip and Praw texturing occurs, also
Deformation occurs, induces austenite to martensite transfor mation.It illustrates, the generation of martensite cenotype is simultaneously during low temperature deformation
Not resulting in high-entropy alloy plasticity during low temperature is on active service reduces, and martensitic traoformation and dislocation, twin synergistic effect make metal
Still there is good uniform plastic deformation ability while being strengthened.
The present invention also provides the preparation methods of high-entropy alloy described in above-mentioned technical proposal, include the following steps：
(1) raw metal is smelted, obtains smelting liquid alloy water；
(2) the smelting liquid alloy water for obtaining the step (1) is closed successively through casting ingot, forged and hot rolling
Golden precursor；
(3) the alloy precursor for obtaining the step (2) obtains high-entropy alloy successively through solid solution, cold rolling and calcining.
The present invention smelts raw metal, obtains smelting liquid alloy water.In the present invention, the temperature of the smelting is preferred
It is 1700~1900 DEG C, more preferably 1750~1850 DEG C, most preferably 1780~1820 DEG C.In the present invention, the smelting
Time be preferably 15~20min, more preferably 16~19min, most preferably 17~18min.In the present invention, the smelting
Atmosphere be preferably atmosphere of inert gases；The inert gas is preferably argon gas.In the present invention, the number of the smelting is preferred
>=5 times.In the present invention, the smelting can make the full and uniform mixing of metallic element.The present invention does not have the device of the smelting
There is special restriction, using smelting device well known to those skilled in the art, specifically, such as vaccum sensitive stove.
It obtaining after smelting liquid alloy water, the present invention will smelt liquid alloy water successively through the ingot, forged and hot rolling of casting,
Obtain alloy precursor.In the present invention, the time of the casting ingot is preferably 60~120s, more preferably 80~110s,
Most preferably 90~100s.In the present invention, the mold material of the casting ingot is preferably high-temperature alloy steel.Of the invention
In embodiment, casting ingot has obtained cylindrical body ingot casting.
In the present invention, the temperature of the hot forging is preferably 1150~1250 DEG C, more preferably 1180~1230 DEG C, optimal
It is selected as 1190~1210 DEG C.In the present invention, the time of the hot forging is preferably 5~20min, more preferably 10~15min, most
Preferably 11~12min.In the present invention, hot forging become ingot casting cross section is square, as cast condition crackle is few, dense structure
Rectangular solid ingot.
In the present invention, the temperature of the hot rolling is preferably 850~900 DEG C, and more preferably 860~890 DEG C, most preferably
870~880 DEG C.In the present invention, the opposite volume under pressure of the hot rolling is preferably 40~60%, and more preferably 45~55%, most
Preferably 48~52%.The present invention does not have special restriction to the device of the hot rolling, and use is well known to those skilled in the art
Hot-rolling arrangement, specifically, such as 400 New-type asynchronous hot rolling experimental mills；The roller diameter of the milling train is preferably 0.4m.?
In the present invention, as-cast structure in rectangular solid ingot can be changed into deformed microstructure by the hot rolling, improve the processing performance of ingot casting.
After obtaining alloy precursor, the alloy precursor successively through solid solution, cold rolling and calcining, is obtained high entropy by the present invention
Alloy.In the present invention, the temperature of the solid solution is preferably 1150~1250 DEG C, and more preferably 1180~1230 DEG C, most preferably
It is 1190~1210 DEG C.In the present invention, the soaking time of the solid solution is preferably 90~120min, more preferably 95~
115min, most preferably 100~110min.In the present invention, after solid solution, before the alloy that the present invention preferably obtains solid solution
Body water cooling obtains solid solution state high-entropy alloy to room temperature.In the present invention, the temperature of the water cooling is preferably 15~35 DEG C, more
Preferably 20~30 DEG C, most preferably 25 DEG C~28 DEG C.In the present invention, the solid solution can make the Ovshinsky in alloy precursor
Body eliminates internal stress while abundant dissolution, improves the plasticity of high-entropy alloy.
In the present invention, the deflection of the cold rolling is preferably 60~90%, and more preferably 65~85%, most preferably 70
~80%.In the present invention, the cold rolling number preferably >=3 times.It is special that the present invention does not have the deflection of each cold rolling
It limits, as long as the total deformation of cold rolling is 60~90%.In the present invention, cold rolling can make alloy reach desired ruler
It is very little, and it is capable of the crystal grain of refining alloy.
In the present invention, the temperature of the calcining is preferably 850~900 DEG C, and more preferably 860~890 DEG C, most preferably
870~880 DEG C.In the present invention, the soaking time of the calcining is preferably 2~3min, more preferably 2.5min.The present invention couple
The device of the calcining does not have special restriction, using calciner plant well known to those skilled in the art, specifically, such as salt
Liquid furnace.In the present invention, the calcining can eliminate the microstrain in cold rolling alloy, while promote tiny recrystal grain
It generates.
After calcining, calcined alloy is preferably air-cooled to room temperature by the present invention.In the present invention, it is described it is air-cooled can
Stress after release cold rolling in alloy is concentrated, while being only capable of forming tiny recrystal grain, without significantly reducing the strong of alloy
Degree and plasticity.
Method of the invention combines smelting, rolling, solid solution and annealing technology, by rationally adjusting each processing step and ginseng
Number, prepares the high-entropy alloy with single phase austenite tissue and fine grained structure, average grain size is about 7 μm, due to it
Special fine grain heterogeneous microstructure and deformation can strain induced martensite effect, make it have very high cryogenic tensile plasticity and
Intensity obtains stable single phase austenite structure, average grain size is used in the high-ductility low temperature that different scale range is distributed
High-entropy alloy.
High-entropy alloy provided by the invention and preparation method thereof is described in detail below with reference to embodiment, but not
They can be interpreted as limiting the scope of the present invention.
In embodiment, ferro element used, manganese element, cobalt element and chromium use purity for the Fe powder of 99.9wt%
End, purity are the Co powder of 99.9wt%, the Cr powder that the Mn powder and purity that purity is 99.9wt% are 99.9wt%.
Embodiment 1
A kind of high-entropy alloy is prepared by the element for including following atomic percentage content：Fe 40.0%, Co
10.0%, Mn 40.0% and Cr 10.0%.
The preparation method of above-mentioned high-entropy alloy, includes the following steps：
(1) above-mentioned raw metal is smelted 5 times in vaccum sensitive stove in 1800 DEG C, obtains smelting liquid alloy water；
(2) the smelting liquid alloy water for obtaining the step (1) is successively through being cast into the ingot casting of cylindrical body, by cylindrical body
Ingot casting in 1200 DEG C of forged 10min, so that cylindrical body ingot casting is become cross section and be square (80 × 80mm2) cuboid casting
Ingot, then by rectangular solid ingot in 900 DEG C of progress hot rollings, the opposite volume under pressure of hot rolling is 50%, obtains the conjunction that plate thickness is 40mm
Golden precursor；
(3) the alloy precursor for obtaining the step (2) is in 1200 DEG C of solid solution 2h, water cooling to room temperature；Obtain solid solution state
Then high-entropy alloy carries out 5 passage cold-rolling treatments to solid solution state high-entropy alloy, cold rolling overall reduction is 60%, and alloy is finally thick
Degree is 16mm；By cold rolling alloy in salt bath furnace 900 DEG C of heat preservation 3min, be then air-cooled to room temperature, obtain high-entropy alloy.
Using the microstructure of X-ray diffraction studies high-entropy alloy, as a result as shown in Figure 1.High entropy closes as can be seen from Figure 1
The alloy structure of gold is single phase austenite.
Using mechanical property of the GB/T 228.1-2010 detection high-entropy alloy at 298K and 173K, result is：In 298K
When, the yield strength of high-entropy alloy is 268MPa, tensile strength 550MPa, extensibility 52%；In 173K, high-entropy alloy
Yield strength be 380MPa, tensile strength 750MPa, extensibility 62%.Fine grain state high-entropy alloy is (i.e. in the present embodiment
Finally obtained high-entropy alloy) and solid solution the simple tension of state high-entropy alloy engineering stress-strain curve it is as shown in Figure 2；In Fig. 2
It is solid solution state high-entropy alloy in 298K, thin that line where open triangles, triangles, hollow square and closed square, which respectively represents,
Simple tension engineering of the crystalline state high-entropy alloy in 298K, solid solution state high-entropy alloy in 173K and fine grain state high-entropy alloy at 173K
Load-deformation curve.As can be seen from Figure 2：The intensity and plasticity of state high-entropy alloy and fine grain state high-entropy alloy are dissolved under 173K
The performance being above under the conditions of 298K (room temperature).
Using the composition of the energy spectrum analysis method analysis high-entropy alloy of scanning electron microscope, the results are shown in Table 1.
The element composition of high-entropy alloy prepared by embodiment 1
| Element | Content (%) |
| Fe | 39.11 |
| Co | 9.85 |
| Mn | 40.41 |
| Cr | 10.63 |
The stacking fault energy value that high-entropy alloy is obtained using theoretical calculation is about 35mJ/mol.It is observed using electron backscatter diffraction
The microstructure of high-entropy alloy, as a result as shown in Figure 3；In figure, solid black lines are crystal boundary, and solid white line is 3 type annealing twin of ∑
Boundary.As can be seen from Figure 3：The high-entropy alloy that the present embodiment obtains is fine grain austenite, and average grain size is about 7 μm.
In 298K and 173K, the stereoscan photograph of high-entropy alloy simple tension fracture is as shown in figure 4, a is in figure
The stereoscan photograph of high-entropy alloy simple tension fracture under 298K, b are the scanning of high-entropy alloy simple tension fracture under 173K
Electromicroscopic photograph.From fig. 4, it can be seen that the visible a large amount of dimples of high-entropy alloy incision position at a temperature of two kinds, and 173K high-entropy alloy
Dimple it is deep compared with room temperature high-entropy alloy, this, which shows high-entropy alloy at low temperature, has good plasticity.
Embodiment 2
A kind of high-entropy alloy is prepared by the element for including following atomic percentage content：Fe 40.0%, Co
10.0%, Mn40.0% and Cr 10.0%.
The preparation method of above-mentioned high-entropy alloy, includes the following steps：
(1) above-mentioned raw metal is smelted 5 times in vaccum sensitive stove in 1800 DEG C, obtains smelting liquid alloy water；
(2) the smelting liquid alloy water for obtaining the step (1) is successively through being cast into the ingot casting of cylindrical body, by cylindrical body
Ingot casting makes cylindrical body ingot casting become cross section and is square (80 × 80mm in 1200 DEG C of forged 10min2) rectangular solid ingot,
Then by rectangular solid ingot in 900 DEG C of progress hot rollings, the opposite volume under pressure of hot rolling is 50%, before obtaining the alloy that plate thickness is 40mm
Body；
(3) the alloy precursor for obtaining the step (2) obtains solid solution state in 1200 DEG C of solid solution 2h, water cooling to room temperature
Then high-entropy alloy carries out 8 passage cold-rolling treatments to solid solution state high-entropy alloy, cold rolling overall reduction is 90%, and alloy sheets are final
With a thickness of 4mm；By cold rolling alloy in salt bath furnace 900 DEG C of heat preservation 3min, be then air-cooled to room temperature, obtain high-entropy alloy.
Using mechanical property of the detection method test high-entropy alloy of embodiment 1 at 273K and 173K, result is：?
When 298K, the yield strength of high-entropy alloy is 505MPa, tensile strength 709MPa, extensibility 43%；In 173K, high entropy
The yield strength of alloy is 670MPa, tensile strength 928MPa, extensibility 26%.
Using the microstructure of detection method observation high-entropy alloy same as Example 1, result is：The present embodiment obtains
High-entropy alloy be fine grain austenite, average grain size is about 4 μm.
It is as a result same as Example 1 using the element composition of method analysis gained high-entropy alloy same as Example 1.
Embodiment 3
A kind of high-entropy alloy is prepared by the element for including following atomic percentage content：Fe 40.0%, Co10.0%,
Mn40.0% and Cr 10.0%.
The preparation method of above-mentioned high-entropy alloy, includes the following steps：
(1) above-mentioned raw metal is smelted 5 times in vaccum sensitive stove in 1800 DEG C, obtains smelting liquid alloy water；
(2) the smelting liquid alloy water for obtaining the step (1) is successively through being cast into the ingot casting of cylindrical body, by cylindrical body
Ingot casting makes cylindrical body ingot casting become cross section and is square (80 × 80mm in 1200 DEG C of forged 10min2) rectangular solid ingot,
Then by rectangular solid ingot in 900 DEG C of progress hot rollings, the opposite volume under pressure of hot rolling is 50%, before obtaining the alloy that plate thickness is 40mm
Body；
(3) the alloy precursor for obtaining the step (2) obtains solid solution state in 1200 DEG C of solid solution 2h, water cooling to room temperature
Then high-entropy alloy carries out 5 passage cold-rolling treatments to solid solution state high-entropy alloy, cold rolling overall reduction is 60%, and alloy is finally thick
Degree is 16mm；By cold rolling alloy in salt bath furnace 900 DEG C of heat preservation 2min, be then air-cooled to room temperature, obtain high-entropy alloy.
Using mechanical property of the detection method test high-entropy alloy of embodiment 1 at 298K and 173K, result is：?
When 298K, the yield strength of high-entropy alloy is 350MPa, tensile strength 634MPa, extensibility 41%；In 173K, high entropy
The yield strength of alloy is 472MPa, tensile strength 780MPa, extensibility 54%.
Using the microstructure of test method test high-entropy alloy same as Example 1, result is：The present embodiment obtains
High-entropy alloy be fine grain austenite, average grain size is about 6 μm.
Using the metallic element composition of detection method analysis high-entropy alloy same as Example 1, as a result with 1 phase of embodiment
Together.
Comparative example 1
A kind of high-entropy alloy is prepared by the element for including following atomic percentage content：Fe 50.0%, Co
10.0%, Mn 30.0% and Cr 10%.
The preparation method of above-mentioned high-entropy alloy, includes the following steps：
(1) above-mentioned raw metal is smelted 5 times in vaccum sensitive stove in 1800 DEG C, obtains smelting liquid alloy water；
(2) the smelting liquid alloy water for obtaining the step (1) is successively through being cast into the ingot casting of cylindrical body, by cylindrical body
Ingot casting makes cylindrical body ingot casting become cross section and is square (80 × 80mm in 1200 DEG C of forged 10min2) rectangular solid ingot,
Then by rectangular solid ingot in 900 DEG C of progress hot rollings, the opposite volume under pressure of hot rolling is 50%, before obtaining the alloy that plate thickness is 40mm
Body；
(3) the alloy precursor for obtaining the step (2) obtains solid solution state in 1200 DEG C of solid solution 2h, water cooling to room temperature
Then high-entropy alloy carries out 5 passage cold-rolling treatments to solid solution state high-entropy alloy, cold rolling overall reduction is 60%, and alloy is finally thick
Degree is 16mm；By cold rolling alloy in salt bath furnace 900 DEG C of heat preservation 3min, be then air-cooled to room temperature, obtain high-entropy alloy.
Using X-ray diffraction studies high-entropy alloy microstructure, as a result as shown in Figure 5.Packet in alloy as can be seen from Figure 5
Contain austenite grain and a small amount of martensitic crystal grains.
Mechanical property of the high-entropy alloy at 298K and 173K is detected using GB/T 228.1-2010 respectively, result is：?
The yield strength of high-entropy alloy is 310MPa, tensile strength 710MPa, extensibility 74% when 298K；In 173K, high entropy
The yield strength of alloy is 382MPa, tensile strength 980MPa, extensibility 51%.
Using the composition of the energy spectrum analysis method analysis high-entropy alloy of scanning electron microscope, the results are shown in Table 2.
The element composition of high-entropy alloy prepared by comparative example 1
| Element | Content (%) |
| Fe | 49.17 |
| Co | 9.83 |
| Mn | 30.92 |
| Cr | 10.08 |
The stacking fault energy value that high-entropy alloy is obtained using theoretical calculation is about 20mJ/mol.It is observed using electron backscatter diffraction
The microstructure of high-entropy alloy, as a result as shown in Figure 6；In Fig. 6, solid black lines are crystal boundary, and solid white line is 3 type annealing twin of ∑
Boundary, black crystal grain are austenite grain, and white crystal grain is martensitic crystal grains.As can be seen from Figure 6：The high entropy that the comparative example obtains
Alloy is austenite and martensite duplex structure, and average grain size is about 5 μm.
Comparative example 2
A kind of high-entropy alloy is prepared by the element for including following atomic percentage content：Fe 50.0%, Co10.0%,
Mn 30.0% and Cr10.0%.
The preparation method of above-mentioned high-entropy alloy, includes the following steps：
(1) above-mentioned raw metal is smelted 5 times in vaccum sensitive stove in 1800 DEG C, obtains smelting liquid alloy water；
(2) the smelting liquid alloy water for obtaining the step (1) is successively through being cast into the ingot casting of cylindrical body, by cylindrical body
Ingot casting makes cylindrical body ingot casting become cross section and is square (80 × 80mm in 1200 DEG C of forged 10min2) rectangular solid ingot,
Then by rectangular solid ingot in 900 DEG C of progress hot rollings, the opposite volume under pressure of hot rolling is 50%, before obtaining the alloy that plate thickness is 40mm
Body；
(3) the alloy precursor for obtaining the step (2) obtains solid solution state in 1200 DEG C of solid solution 2h, water cooling to room temperature
Then high-entropy alloy carries out 8 passage cold-rolling treatments to solid solution state high-entropy alloy, cold rolling overall reduction is 90%, and alloy sheets are final
With a thickness of 4mm；By cold rolling alloy in salt bath furnace 900 DEG C of heat preservation 3min, be then air-cooled to room temperature, obtain high-entropy alloy.
Using mechanical property of the detection method test high-entropy alloy of embodiment 1 at 298K and 173K, result is：?
When 298K, the yield strength of high-entropy alloy is 325MPa, tensile strength 722MPa, extensibility 75%；In 173K, high entropy
The yield strength of alloy is 550MPa, tensile strength 1026MPa, extensibility 43%.
Using the microstructure of the method observation high-entropy alloy of embodiment 1, result is：High-entropy alloy manufactured in the present embodiment
For the alloy sheets of austenite and martensite duplex structure, average grain size is about 3 μm.
It is as a result identical as comparative example 1 using the metallic element composition of the method analysis high-entropy alloy of embodiment 1.
Comparative example 3
A kind of high-entropy alloy is prepared by the element for including following atomic percentage content：Fe 50.0%, Co10.0%,
Mn 30.0% and Cr10.0%.
The preparation method of above-mentioned high-entropy alloy, includes the following steps：
(1) above-mentioned raw metal is smelted 5 times in vaccum sensitive stove in 1800 DEG C, obtains smelting liquid alloy water；
(2) the smelting liquid alloy water for obtaining the step (1) is successively through being cast into the ingot casting of cylindrical body, by cylindrical body
Ingot casting makes cylindrical body ingot casting become cross section and is square (80 × 80mm in 1200 DEG C of forged 10min2) rectangular solid ingot,
Then by rectangular solid ingot in 900 DEG C of progress hot rollings, the opposite volume under pressure of hot rolling is 50%, before obtaining the alloy that plate thickness is 40mm
Body；
(3) the alloy precursor for obtaining the step (2) obtains solid solution state in 1200 DEG C of solid solution 2h, water cooling to room temperature
Then high-entropy alloy carries out 5 passage cold-rolling treatments to solid solution state high-entropy alloy, cold rolling overall reduction is 60%, and alloy sheets are final
With a thickness of 16mm；By cold rolling alloy in salt bath furnace 900 DEG C of heat preservation 2min, be then air-cooled to room temperature, obtain high-entropy alloy.
Using mechanical property of the detection method test high-entropy alloy of embodiment 1 at 298K and 173K, result is：?
When 298K, the yield strength of high-entropy alloy is 355MPa, tensile strength 780MPa, extensibility 63%；In 173K, high entropy
The yield strength of alloy is 425MPa, tensile strength 1030MPa, extensibility 42%.
Using the microstructure of the method observation high-entropy alloy of embodiment 1, result is high-entropy alloy manufactured in the present embodiment
For the alloy of austenite and martensite duplex structure, average grain size is about 4 μm.
It is as a result identical as comparative example 1 using the metallic element composition of the method analysis high-entropy alloy in embodiment 1.
From embodiment as can be seen that it is fine grain austenite that high-entropy alloy of the invention, which is high-entropy alloy, have at low temperature
Excellent mechanical property, for high-entropy alloy of the invention when 173K is deformed, for uniform elongation up to 62%, intensity reaches 750MPa；Modeling
Property with intensity be higher than the mechanical property of cryogenic steel product prepared with conventional method.
The above is only a preferred embodiment of the present invention, it is noted that for the ordinary skill people of the art
For member, various improvements and modifications may be made without departing from the principle of the present invention, these improvements and modifications are also answered
It is considered as protection scope of the present invention.
Claims (10)
1. a kind of high-entropy alloy is prepared by the element for including following atomic percentage content：Fe 39.0~41.0%, Co
9.0~11.0%, Mn 39.0~41.0%, Cr 9.0~11.0%.
2. high-entropy alloy according to claim 1, which is characterized in that in 173K, yield strength is the high-entropy alloy
670M, for extensibility up to 62%, tensile strength reaches 750MPa.
3. the preparation method of high-entropy alloy as claimed in claim 1 or 2, includes the following steps：
(1) raw metal is smelted, obtains smelting liquid alloy water；
(2) the smelting liquid alloy water for obtaining the step (1) is successively through casting ingot, forged and hot rolling, before obtaining alloy
Body；
(3) the alloy precursor for obtaining the step (2) obtains high-entropy alloy successively through solid solution, cold rolling and calcining.
4. preparation method according to claim 3, which is characterized in that the temperature smelted in the step (1) is 1700~
1900℃。
5. preparation method according to claim 3, which is characterized in that the temperature being hot-forged in the step (2) is 1150~
1250℃。
6. preparation method according to claim 3, which is characterized in that in the step (2) temperature of hot rolling be 850~
900℃。
7. preparation method according to claim 6, which is characterized in that the opposite volume under pressure of hot rolling is in the step (2)
40~60%.
8. preparation method according to claim 3, which is characterized in that the temperature being dissolved in the step (3) is 1150~
1250℃。
9. preparation method according to claim 8, which is characterized in that the soaking time being dissolved in the step (3) is 1.5
~2h.
10. preparation method according to claim 3, which is characterized in that the temperature calcined in the step (3) is 850~
900℃。
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810752440.0A CN108823481A (en) | 2018-07-10 | 2018-07-10 | A kind of high-entropy alloy and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201810752440.0A CN108823481A (en) | 2018-07-10 | 2018-07-10 | A kind of high-entropy alloy and preparation method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN108823481A true CN108823481A (en) | 2018-11-16 |
Family
ID=64136757
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201810752440.0A Pending CN108823481A (en) | 2018-07-10 | 2018-07-10 | A kind of high-entropy alloy and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN108823481A (en) |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109371309A (en) * | 2018-11-23 | 2019-02-22 | 西安工业大学 | A kind of more pivot graded alloy of high-strength and high-plasticity and preparation method thereof |
| CN110923538A (en) * | 2019-12-12 | 2020-03-27 | 燕山大学 | High-entropy alloy with multidirectional annealing twin crystals and preparation method thereof |
| CN111172417A (en) * | 2020-01-20 | 2020-05-19 | 西安交通大学 | Powder metallurgy material of endogenetic oxide strengthened alloy and preparation method thereof |
| CN111893362A (en) * | 2020-07-24 | 2020-11-06 | 北京航空航天大学 | Three-dimensional network structure high-entropy alloy and preparation method thereof |
| CN112522634A (en) * | 2019-09-17 | 2021-03-19 | 东北大学 | High-strength high-entropy alloy and preparation method thereof |
| CN112575236A (en) * | 2019-09-27 | 2021-03-30 | 沈阳航空航天大学 | High-nitrogen high-entropy alloy and preparation method thereof |
| CN112626364A (en) * | 2020-10-29 | 2021-04-09 | 西安福莱电工合金有限公司 | Method for preparing high-entropy alloy with non-uniform layered structure by powder metallurgy method |
| CN116043126A (en) * | 2023-01-09 | 2023-05-02 | 鞍钢股份有限公司 | High-strength high-toughness high-entropy steel and manufacturing method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103290404A (en) * | 2013-05-06 | 2013-09-11 | 浙江工业大学 | Laser-cladding high-entropy alloy powder and preparation method of high-entropy alloy coating |
| CN107338385A (en) * | 2017-06-27 | 2017-11-10 | 北京科技大学 | A kind of hydrogen storage high-entropy alloy based on body-centered cubic structure and preparation method thereof |
-
2018
- 2018-07-10 CN CN201810752440.0A patent/CN108823481A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103290404A (en) * | 2013-05-06 | 2013-09-11 | 浙江工业大学 | Laser-cladding high-entropy alloy powder and preparation method of high-entropy alloy coating |
| CN107338385A (en) * | 2017-06-27 | 2017-11-10 | 北京科技大学 | A kind of hydrogen storage high-entropy alloy based on body-centered cubic structure and preparation method thereof |
Non-Patent Citations (1)
| Title |
|---|
| ZHIMING LI ET AL.: "Metastable high-entropy dual-phase alloys overcome the strength-ductility trade-off", 《NATURE》 * |
Cited By (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109371309A (en) * | 2018-11-23 | 2019-02-22 | 西安工业大学 | A kind of more pivot graded alloy of high-strength and high-plasticity and preparation method thereof |
| CN112522634B (en) * | 2019-09-17 | 2021-11-09 | 东北大学 | High-strength high-entropy alloy and preparation method thereof |
| CN112522634A (en) * | 2019-09-17 | 2021-03-19 | 东北大学 | High-strength high-entropy alloy and preparation method thereof |
| CN112575236A (en) * | 2019-09-27 | 2021-03-30 | 沈阳航空航天大学 | High-nitrogen high-entropy alloy and preparation method thereof |
| CN112575236B (en) * | 2019-09-27 | 2022-02-18 | 沈阳航空航天大学 | High-nitrogen high-entropy alloy and preparation method thereof |
| CN110923538A (en) * | 2019-12-12 | 2020-03-27 | 燕山大学 | High-entropy alloy with multidirectional annealing twin crystals and preparation method thereof |
| CN110923538B (en) * | 2019-12-12 | 2021-06-29 | 燕山大学 | High-entropy alloy with multidirectional annealing twin crystals and preparation method thereof |
| CN111172417A (en) * | 2020-01-20 | 2020-05-19 | 西安交通大学 | Powder metallurgy material of endogenetic oxide strengthened alloy and preparation method thereof |
| CN111893362A (en) * | 2020-07-24 | 2020-11-06 | 北京航空航天大学 | Three-dimensional network structure high-entropy alloy and preparation method thereof |
| CN111893362B (en) * | 2020-07-24 | 2021-11-09 | 北京航空航天大学 | Three-dimensional network structure high-entropy alloy and preparation method thereof |
| CN112626364A (en) * | 2020-10-29 | 2021-04-09 | 西安福莱电工合金有限公司 | Method for preparing high-entropy alloy with non-uniform layered structure by powder metallurgy method |
| CN112626364B (en) * | 2020-10-29 | 2022-02-18 | 西安福莱电工合金有限公司 | Method for preparing high-entropy alloy with non-uniform layered structure by powder metallurgy method |
| CN116043126A (en) * | 2023-01-09 | 2023-05-02 | 鞍钢股份有限公司 | High-strength high-toughness high-entropy steel and manufacturing method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN108823481A (en) | A kind of high-entropy alloy and preparation method thereof | |
| US10364487B2 (en) | High entropy alloy having TWIP/TRIP property and manufacturing method for the same | |
| CN107267838B (en) | A method of there is high tough fine grain high-entropy alloy using pyromagnetic coupling preparation | |
| WO2021254028A1 (en) | B2 nanoparticle coherent precipitation strengthened ultrahigh-strength maraging stainless steel and preparation method therefor | |
| US20080031769A1 (en) | High-temperature resistant alloy with low contents of cobalt and nickel | |
| Fang et al. | Effects of cobalt on the structure and mechanical behavior of non-equal molar CoxFe50− xCr25Ni25 high entropy alloys | |
| Ondicho et al. | Experimental investigation and phase diagram of CoCrMnNi–Fe system bridging high-entropy alloys and high-alloyed steels | |
| CN105568151A (en) | Aluminum-strengthened maraging steel and preparing method thereof | |
| CN110408861B (en) | Cold-rolled high-strength-ductility medium manganese steel with lower Mn content and preparation method thereof | |
| CN113718152A (en) | High-temperature-resistant low-density Ni-Co-Cr-Fe-Al-Ti high-entropy alloy and preparation method thereof | |
| Padilha et al. | Microstructures and mechanical properties of Fe–15% Cr–15% Ni austenitic stainless steels containing different levels of niobium additions submitted to various processing stages | |
| Wang et al. | Evolution of microstructure and tensile properties of Fe–18Ni–12Cr based AFA steel during aging at 700° C | |
| CN106167877B (en) | Maraging steel | |
| CN112322957B (en) | Corrosion-resistant high-strength-and-toughness Fe-rich multi-component alloy and preparation method thereof | |
| Moon et al. | The negative effect of Zr addition on the high temperature strength in alumina-forming austenitic stainless steels | |
| JP2012057200A (en) | Titanium plate excelling in rigidity in rolling width direction, and method of manufacturing the same | |
| CN110343970A (en) | A kind of hot rolling high strength and ductility medium managese steel and preparation method thereof having lower Mn content | |
| CN107587080B (en) | A kind of precipitation strength heat resisting steel and its preparation process | |
| CN112522634B (en) | High-strength high-entropy alloy and preparation method thereof | |
| Ren et al. | Effect of Mo addition on the microstructural evolution and mechanical properties of Fe–Ni–Cr–Mn–Al–Ti high entropy alloys | |
| CN108624820B (en) | Automobile high-strength ductile steel with strength-elongation product of more than 45 GPa% and preparation method thereof | |
| Zhou et al. | Excellent strength-ductility in Ti-alloyed Fe35Ni35Cr20Mn10 high-entropy alloy | |
| Han et al. | The effects of thermo-mechanical treatments on superplasticity of Fe-24Cr-7Ni-3Mo-0.14 N duplex stainless steel | |
| CN112760565B (en) | Fe-Ni-Mo alloy for buzzer and preparation method thereof | |
| CN111218600A (en) | Nano-sheet multi-phase high-entropy alloy and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| RJ01 | Rejection of invention patent application after publication | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20181116 |