CN107326246A - A kind of high-performance high-entropy alloy and its processing method - Google Patents

A kind of high-performance high-entropy alloy and its processing method Download PDF

Info

Publication number
CN107326246A
CN107326246A CN201710583007.4A CN201710583007A CN107326246A CN 107326246 A CN107326246 A CN 107326246A CN 201710583007 A CN201710583007 A CN 201710583007A CN 107326246 A CN107326246 A CN 107326246A
Authority
CN
China
Prior art keywords
alloy
melting
plasticity
intensity
temperature
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.)
Granted
Application number
CN201710583007.4A
Other languages
Chinese (zh)
Other versions
CN107326246B (en
Inventor
江峰
陈良斌
唐可
杨中岳
吴亚科
孙军
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Shenzhen Biest Precision Co ltd
Original Assignee
Xian Jiaotong University
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Xian Jiaotong University filed Critical Xian Jiaotong University
Priority to CN201710583007.4A priority Critical patent/CN107326246B/en
Publication of CN107326246A publication Critical patent/CN107326246A/en
Application granted granted Critical
Publication of CN107326246B publication Critical patent/CN107326246B/en
Active legal-status Critical Current
Anticipated expiration legal-status Critical

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
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • 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
    • C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon

Abstract

The invention discloses a kind of high-performance high-entropy alloy and its processing method, by Fe40Mn40Co10Cr10The carbon of certain content is introduced in alloy, with matrix formation interstitial solid solution, on the one hand the stacking fault energy of material can effectively be reduced so that can just induce twin at ambient temperature, another aspect carbon can provide extra intensity increment by solid solution and carbide precipitate for matrix.Carbon of the present invention is used as effective precipitation strength phase as good interstitial atom and carbide, by being incubated in final step in the higher temperature long period, as-forged microstructure is partially or completely eliminated, part separates out phased soln and formed after nearly phase structure, alloy can possess larger performance controllable space again on the basis of higher performance level, the combination by other schedule of reinforcements such as working hardening and precipitation strength is conducive to further to be strengthened, obtain more rational intensity and plasticity collocation, and the content of overall alloy element is reasonable, cost is low, possesses stronger economy.

Description

A kind of high-performance high-entropy alloy and its processing method
【Technical field】
The invention belongs to the composition design of high performance alloys and handling process field, design a kind of high-performance high-entropy alloy and Its processing method.
【Background technology】
High-entropy alloy is the class alloy based on new alloy design concept proposed by Ye Junwei in 2004, this kind of Alloy typically contains the alloying element (being also made up of now four kinds of elements) of five kinds and the above, and every kind of constituent content is 5% More than, no clear superiority element, also there is mixed structure sometimes in FCC or BCC generally single-phase in structure.High-entropy alloy Because of its strong solid solution effect, with higher intensity, heat endurance, wearability and decay resistance, obtain since the proposition Extensive concern and research, it is considered to be a kind of potential structural material.
But part high-entropy alloy system, such as Fe40Mn40Co10Cr10, but show that cryogenic property is excellent, room temperature strength has The characteristics of limit, limit the actual use of such alloy；In addition, by introducing traditional material reinforcement means, such as precipitation strength And dislocation strengthening, although the room temperature strength of the part high-entropy alloy can be improved, but causes significantly reducing for its plasticity, therefore Usually need to be balanced in intensity and plasticity in practical application, significantly limit the expansion of high-entropy alloy application.Interface Reinforcing, including intercrystalline strengthening and twinning strengthening, it is considered to be can preferably coordinate a kind of means of intensity and plasticity, it is especially twin Crystalline substance reinforcing, the intensity and plasticity of material can be increased substantially simultaneously, but inducing twin then needs to meet some requirements.Grind Study carefully and show, by the doping of alloying element, the stacking fault energy of reduction material is a kind of feasible method.Pass through rational composition and work Skill is designed, it is possible to the room-temperature property of larger lift portion high-entropy alloy, promotes its practical application.
【The content of the invention】
It is an object of the invention to solve Fe40Mn40Co10Cr10The problems such as room temperature strength that alloy faces is not enough, and coordinate There is provided a kind of high-performance high-entropy alloy and its processing method for relation between eager to do well in everything degree and plasticity.The present invention by Fe40Mn40Co10Cr10The carbon of certain content is introduced in alloy, with matrix formation interstitial solid solution, on the one hand can effectively be dropped The stacking fault energy of low material so that can just induce twin at ambient temperature, another aspect carbon can pass through solid solution and analysis Go out carbide and extra intensity increment is provided for matrix, effectively improve the room-temperature property of material.
To reach above-mentioned purpose, the present invention is achieved using following technical scheme：
A kind of high-performance high-entropy alloy, according to foundry alloy (Fe40Mn40Co10Cr10)100-xCxNominal composition dispensing and carry out Melting, wherein alloy substrate Fe40Mn40Co10Cr10Middle each element atomic percentage conc is：Fe：35-45%；Mn：35-45%； Co：5-15%；Cr：5-15%；
The ＜ x of content 0≤10at% of doping carbon.
Further improve of the invention is：
The crystallite dimension for the high-performance high-entropy alloy that melting is obtained is 100-300 μm.
A kind of processing method of high-performance high-entropy alloy, comprises the following steps：
1) according to foundry alloy (Fe40Mn40Co10Cr10)100-xCxNominal composition dispensing and carry out melting, obtain crystallite dimension Cast alloy between about 100-300 μm；Wherein, 0 ＜ x≤10at%；
If 2) equal when the quality of master alloy melting and the method for smelting of selection sample reference alloy GB/T 13298-2015 Even property and consistency meet GB/T 11352-2009 and GB/T 7233 regulation, then perform step 3)；Otherwise step 4 is performed)；
3) by adjusting the phosphorus content of cast alloy, if the tensile strength of alloy and actual be on active service of plasticity satisfaction will after regulation Ask, then adopt using；Otherwise step 4 is performed)；Wherein, actual service demand be tensile strength between 500~2000MPa and Intensity-plasticity collocation of the plasticity between 10~100% is required；
4) in vacuum annealing furnace, to step 1) obtain cast alloy between 1000-1300 DEG C homogenizing annealing 8- 24h；
5) upsetting pull processing, 1000-1100 DEG C of initial forging temperature, final forging temperature 950-1000 are carried out to the alloy after homogenization ℃；
6) alloy after upsetting pull is further forged in lower temperature, 900-1000 DEG C of initial forging temperature, final forging temperature 850- 900℃；
7) if the intensity and plasticity of the material after the completion of forging meet actual service demand, adopt and use；Otherwise perform Step 8)；
8) alloy after the completion of forging is heat-treated at a temperature of 850~1100 DEG C in vacuum drying oven, time 10- 60min；
9) if the intensity of alloy and plasticity meet actual service demand, adopt and use；Otherwise executive termination condition judgment, Processing is terminated if end condition is met, alloy is discarded, otherwise returns and performs step 3)；
The end condition is：If the carbon content of alloy is in x=0,5,10, the intensity and plasticity of alloy pass through step 3) after processing -8), actual service demand still can not be met, then terminates processing, alloy is discarded.
Compared with prior art, the invention has the advantages that：
The present invention effectively reduces the stacking fault energy of material, and inducing twin becomes more easy, meanwhile, carbon is as good Interstitial atom and carbide as effective precipitation strength phase, can greatly improve performance of the material in room temperature, fit When doping and handling process it is reasonably combined can provide compared with horn of plenty performance regulate and control suites of measure, especially by most It is incubated afterwards in step in the higher temperature long period, as-forged microstructure is partially or completely eliminated, part separates out phased soln and formed closely After phase structure, alloy can possess larger performance controllable space again on the basis of higher performance level, be conducive to Further strengthened by the combination of other schedule of reinforcements such as working hardening and precipitation strength, obtain more rational intensity Arranged in pairs or groups with plasticity, and the content of overall alloy element is reasonable, and cost is low, possesses stronger economy.
【Brief description of the drawings】
Fig. 1 is the different carbon content as cast condition Fe using the small quality melting of vacuum arc furnace ignition40Mn40Co10Cr10The metallographic of alloy Tissue；
Fig. 2 is the different carbon content as cast condition Fe using the small quality melting of vacuum arc furnace ignition40Mn40Co10Cr10The stretching of alloy Performance curve；
Fig. 3 is the tissue of the ingot casting obtained using suspension smelting furnace melting；
Fig. 4 is to use suspension smelting furnace melting and the (Fe Jing Guo different post processings40Mn40Co10Cr10)96.7C3.3Alloy Tensile property curve.
【Embodiment】
The present invention is described in further detail below in conjunction with the accompanying drawings：
The processing method of high-performance high-entropy alloy of the present invention, comprises the following steps：
1) according to foundry alloy (Fe40Mn40Co10Cr10)100-xCxNominal composition dispensing and carry out melting, obtain crystallite dimension Cast alloy between about 100-300 μm；Wherein, 0 ＜ x≤10at%；
If 2) equal when the quality of master alloy melting and the method for smelting of selection sample reference alloy GB/T 13298-2015 Even property and consistency meet GB/T 11352-2009 and GB/T 7233 regulation, then perform step 3)；Otherwise step 4 is performed)；
3) by adjusting the phosphorus content of cast alloy, if the tensile strength of alloy and actual be on active service of plasticity satisfaction will after regulation Ask, then adopt using；Otherwise step 4 is performed)；Wherein, actual service demand be tensile strength between 500~2000MPa and Intensity-plasticity collocation of the plasticity between 10~100% is required；
4) in vacuum annealing furnace, to step 1) obtain cast alloy between 1000-1300 DEG C homogenizing annealing 8- 24h；
5) upsetting pull processing, 1000-1100 DEG C of initial forging temperature, final forging temperature 950-1000 are carried out to the alloy after homogenization ℃；
6) alloy after upsetting pull is further forged in lower temperature, 900-1000 DEG C of initial forging temperature, final forging temperature 850- 900℃；
7) if the intensity and plasticity of the material after the completion of forging meet actual service demand, adopt and use；Otherwise perform Step 8)；
8) alloy after the completion of forging is heat-treated at a temperature of 850~1100 DEG C in vacuum drying oven, time 10- 60min；
9) if the intensity of alloy and plasticity meet actual service demand, adopt and use；Otherwise executive termination condition judgment, Processing is terminated if end condition is met, alloy is discarded, otherwise returns and performs step 3)；
The end condition is：If the carbon content of alloy is in x=0,5,10, the intensity and plasticity of alloy pass through step 3) after processing -8), actual service demand still can not be met, then terminates processing, alloy is discarded.
(the Fe of embodiment 140Mn40Co10Cr10)
1) it is (Fe according to nominal composition40Mn40Co10Cr10)97.8C2.2Composition carry out dispensing, gross mass 200g or so, Melting is carried out under vacuum arc furnace ignition, melting four times obtains cast alloy of the crystallite dimension at 100 μm or so；
2) under this kind of method, single 200g, which carries out melting, can ensure composition and structural homogenity, and Tensile strength About 650MPa, meets service demand, without subsequent treatment, can be used directly；
Ingot structure after the alloy melting of the composition is as shown in figure 1, about 100 μm of average grain size, the casting of the composition The stress strain curve of ingot is as shown in C2.2 in Fig. 2, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and its intensity and plasticity will be more excellent, and especially tensile strength less carbon containing (471MPa) improves about 38%；
(the Fe of embodiment 240Mn40Co10Cr10)
1) it is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out dispensing, gross mass 200g or so, Melting is carried out under vacuum arc furnace ignition, melting four times obtains cast alloy of the crystallite dimension at 100 μm or so；
2) under this kind of method, single 200g, which carries out melting, can ensure composition and structural homogenity, and Tensile strength About 787MPa, meets service demand, without subsequent treatment, can be used directly；
Ingot structure after the alloy melting of the composition is as shown in figure 1, about 100 μm of average grain size, the casting of the composition The stress strain curve of ingot is as shown in C3.3 in Fig. 2, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and its intensity and plasticity will be more excellent, and especially tensile strength less carbon containing (471MPa) improves about 67%；
(the Fe of embodiment 340Mn40Co10Cr10)
1) it is (Fe according to nominal composition40Mn40Co10Cr10)95.6C4.4Composition carry out dispensing, gross mass 200g or so, Melting is carried out under vacuum arc furnace ignition, melting four times obtains cast alloy of the crystallite dimension at 100 μm or so；
2) under this kind of method, single 200g, which carries out melting, can ensure composition and structural homogenity, and Tensile strength About 836MPa, meets service demand, without subsequent treatment, can be used directly；
Ingot structure after the alloy melting of the composition is as shown in figure 1, about 100 μm of average grain size, the casting of the composition The stress strain curve of ingot is as shown in C4.4 in Fig. 2, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and its intensity and plasticity will be more excellent, and especially tensile strength less carbon containing (471MPa) improves about 77%；
(the Fe of embodiment 440Mn40Co10Cr10)
1) it is (Fe according to nominal composition40Mn40Co10Cr10)93.4C6.6Composition carry out dispensing, gross mass 200g or so, Melting is carried out under vacuum arc furnace ignition, melting four times obtains cast alloy of the crystallite dimension at 100 μm or so；
2) under this kind of method, single 200g, which carries out melting, can ensure composition and structural homogenity, and Tensile strength About 960MPa, meets service demand, without subsequent treatment, can be used directly；
Ingot structure after the alloy melting of the composition is as shown in figure 1, about 100 μm of average grain size, the casting of the composition The stress strain curve of ingot is as shown in C6.6 in Fig. 2, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and its intensity and plasticity will be more excellent, and especially tensile strength less carbon containing (471MPa) is improved about 104%；
(the Fe of embodiment 540Mn40Co10Cr10)
1) it is (Fe according to nominal composition40Mn40Co10Cr10)91.1C8.9Composition carry out dispensing, gross mass 200g or so, Melting is carried out under vacuum arc furnace ignition, melting four times obtains cast alloy of the crystallite dimension at 100 μm or so；
2) under this kind of method, single 200g, which carries out melting, can ensure composition and structural homogenity, and Tensile strength About 1080MPa, meets service demand, without subsequent treatment, can be used directly；
Ingot structure after the alloy melting of the composition is as shown in figure 1, about 100 μm of average grain size, the casting of the composition The stress strain curve of ingot is as shown in C8.9 in Fig. 2, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and its intensity and plasticity will be more excellent, and especially tensile strength less carbon containing (471MPa) is improved about 129%；
From small quality, the Fe of arc melting is used40Mn40Co10Cr10The organization chart 1 and stress strain curve Fig. 2 of alloy casting state As can be seen that under preparation method of the same race, compared with the alloy of not carbon elements, the tissue change of the alloy after doping is not obvious, But with the raising of phosphorus content, intensity is also corresponding therewith to be improved, and plasticity then shows the variation characteristic fallen after rising, containing Plasticity is optimal when carbon amounts is 3.3at%.
(the Fe of embodiment 640Mn40Co10Cr10)
1) it is (Fe according to nominal composition40Mn40Co10Cr10)90C10Composition carry out dispensing, gross mass 200g or so, true Melting is carried out under empty electric arc furnaces, melting four times obtains cast alloy of the crystallite dimension at 100 μm or so；
2) under this kind of method, single 200g, which carries out melting, can ensure composition and structural homogenity, and Tensile strength About 1160MPa, meets service demand, without subsequent treatment, can be used directly；
(the Fe of embodiment 740Mn40Co10Cr10)
1) it is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out dispensing, gross mass 8kg or so, Melting is carried out under vacuum levitation melting stove, melting four times obtains the most of as cast condition between 200-300 μm of crystallite dimension and closed Gold；
2) under this kind of method single melting 8kg it cannot be guaranteed that composition and structural homogenity are, it is necessary to subsequent treatment；
3) in vacuum annealing furnace, the ingot casting obtained to smelting in suspension is incubated 24h at 1000 DEG C；
4) three upsettings three are carried out to the alloy after homogenization and pulls out processing, 1050 DEG C of initial forging temperature, 970 DEG C of final forging temperature,；
5) alloy after upsetting pull is further forged in lower temperature, 950 DEG C of initial forging temperature, 870 DEG C of final forging temperature；
6) performance detection is carried out to the material after the completion of forging, tensile strength reaches 1100MPa, and elongation percentage about 20% is full Sufficient use requirement, without post processing, can directly be used；
The tissue of ingot casting by being obtained after suspension smelting furnace melting is as shown in Figure 3, it is seen that the size of most of crystal grain is equal Between 200-300 μm.In stress strain curve such as Fig. 4 of the alloy of the composition after above handling process shown in " Forging ", It can be seen that with carbon-free Fe for preparing under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and its tensile strength is relatively free of Carbon (600MPa) improves about 83%；
(the Fe of embodiment 840Mn40Co10Cr10)
1) it is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out dispensing, gross mass 8kg or so, Melting is carried out under vacuum levitation melting stove, melting four times obtains the most of as cast condition between 200-300 μm of crystallite dimension and closed Gold；
2) under this kind of method single melting 8kg it cannot be guaranteed that composition and structural homogenity are, it is necessary to subsequent treatment；
3) in vacuum annealing furnace, the ingot casting obtained to smelting in suspension is incubated 24h at 1000 DEG C；
4) three upsettings three are carried out to the alloy after homogenization and pulls out processing, 1050 DEG C of initial forging temperature, 970 DEG C of final forging temperature,；
5) alloy after upsetting pull is further forged in lower temperature, 950 DEG C of initial forging temperature, 870 DEG C of final forging temperature；
6) performance detection is carried out to the material after the completion of forging, tensile strength reaches 1100MPa, elongation percentage about 20%, modeling Property is poor, it is necessary to post-process；
7) alloy after the completion of forging is heat-treated in vacuum drying oven, 850 DEG C of temperature, time 10min；
The tissue of ingot casting by being obtained after suspension smelting furnace melting is as shown in Figure 3, it is seen that the size of most of crystal grain is equal Between 200-300 μm." 850-10min " institute in stress strain curve such as Fig. 4 of the alloy of the composition after above handling process Show, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and its intensity and plasticity are all More excellent, especially tensile strength less carbon containing (600MPa) improves about 66%；
(the Fe of embodiment 940Mn40Co10Cr10)
1) it is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out dispensing, gross mass 8kg or so, Melting is carried out under vacuum levitation melting stove, melting four times obtains the most of as cast condition between 200-300 μm of crystallite dimension and closed Gold；
2) under this kind of method single melting 8kg it cannot be guaranteed that composition and structural homogenity are, it is necessary to subsequent treatment；
3) in vacuum annealing furnace, the ingot casting obtained to smelting in suspension is incubated 24h at 1000 DEG C；
4) three upsettings three are carried out to the alloy after homogenization and pulls out processing, 1050 DEG C of initial forging temperature, 970 DEG C of final forging temperature,；
5) alloy after upsetting pull is further forged in lower temperature, 950 DEG C of initial forging temperature, 870 DEG C of final forging temperature；
6) performance detection is carried out to the material after the completion of forging, tensile strength reaches 1100MPa, elongation percentage about 20%, modeling Property is poor, it is necessary to post-process；
7) alloy after the completion of forging is heat-treated in vacuum drying oven, 950 DEG C of temperature, time 10min；
The tissue of ingot casting by being obtained after suspension smelting furnace melting is as shown in Figure 3, it is seen that the size of most of crystal grain is equal Between 200-300 μm." 950-10min " institute in stress strain curve such as Fig. 4 of the alloy of the composition after above handling process Show, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and its intensity and plasticity are all More excellent, especially tensile strength less carbon containing (600MPa) improves about 66%；
(the Fe of embodiment 1040Mn40Co10Cr10)
1) it is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out dispensing, gross mass 8kg or so, Melting is carried out under vacuum levitation melting stove, melting four times obtains the most of as cast condition between 200-300 μm of crystallite dimension and closed Gold；
2) under this kind of method single melting 8kg it cannot be guaranteed that composition and structural homogenity are, it is necessary to subsequent treatment；
3) in vacuum annealing furnace, the ingot casting obtained to smelting in suspension is incubated 24h at 1000 DEG C；
4) three upsettings three are carried out to the alloy after homogenization and pulls out processing, 1050 DEG C of initial forging temperature, 970 DEG C of final forging temperature,；
5) alloy after upsetting pull is further forged in lower temperature, 950 DEG C of initial forging temperature, 870 DEG C of final forging temperature；
6) performance detection is carried out to the material after the completion of forging, tensile strength reaches 1100MPa, elongation percentage about 20%, modeling Property is poor, it is necessary to post-process；
7) alloy after the completion of forging is heat-treated in vacuum drying oven, 1050 DEG C of temperature, time 10min；
The tissue of ingot casting by being obtained after suspension smelting furnace melting is as shown in Figure 3, it is seen that the size of most of crystal grain is equal Between 200-300 μm.1050-10min institutes in stress strain curve such as Fig. 4 of the alloy of the composition after above handling process Show, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and its intensity and plasticity are all More excellent, tensile strength less carbon containing (600MPa) improves about 62%, and plastic strain more carbon containing (600MPa) is improved about 71%；
(the Fe of embodiment 1140Mn40Co10Cr10)
1) it is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out dispensing, gross mass 8kg or so, Melting is carried out under vacuum levitation melting stove, melting four times obtains the most of as cast condition between 200-300 μm of crystallite dimension and closed Gold；
2) under this kind of method single melting 8kg it cannot be guaranteed that composition and structural homogenity are, it is necessary to subsequent treatment；
3) in vacuum annealing furnace, the ingot casting obtained to smelting in suspension is incubated 24h at 1000 DEG C；
4) three upsettings three are carried out to the alloy after homogenization and pulls out processing, 1050 DEG C of initial forging temperature, 970 DEG C of final forging temperature,；
5) alloy after upsetting pull is further forged in lower temperature, 950 DEG C of initial forging temperature, 870 DEG C of final forging temperature；
6) performance detection is carried out to the material after the completion of forging, tensile strength reaches 1100MPa, elongation percentage about 20%, modeling Property is poor, it is necessary to post-process；
7) alloy after the completion of forging is heat-treated in vacuum drying oven, 1100 DEG C of temperature, time 10min；
The tissue of ingot casting by being obtained after suspension smelting furnace melting is as shown in Figure 3, it is seen that the size of most of crystal grain is equal Between 200-300 μm." 1100-10min " institute in stress strain curve such as Fig. 4 of the alloy of the composition after above handling process Show, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and its intensity and plasticity are all More excellent, tensile strength less carbon containing (600MPa) improves about 50%, and plastic strain more carbon containing (600MPa) is improved about 114%；
(the Fe of embodiment 1240Mn40Co10Cr10)
1) it is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out dispensing, gross mass 8kg or so, Melting is carried out under vacuum levitation melting stove, melting four times obtains the most of as cast condition between 200-300 μm of crystallite dimension and closed Gold；
2) under this kind of method single melting 8kg it cannot be guaranteed that composition and structural homogenity are, it is necessary to subsequent treatment；
3) in vacuum annealing furnace, the ingot casting obtained to smelting in suspension is incubated 24h at 1000 DEG C；
4) three upsettings three are carried out to the alloy after homogenization and pulls out processing, 1050 DEG C of initial forging temperature, 970 DEG C of final forging temperature,；
5) alloy after upsetting pull is further forged in lower temperature, 950 DEG C of initial forging temperature, 870 DEG C of final forging temperature；
6) performance detection is carried out to the material after the completion of forging, tensile strength reaches 1100MPa, elongation percentage about 20%, modeling Property is poor, it is necessary to post-process；
7) alloy after the completion of forging is heat-treated in vacuum drying oven, 1100 DEG C of temperature, time 30min；
The tissue of ingot casting by being obtained after suspension smelting furnace melting is as shown in Figure 3, it is seen that the size of most of crystal grain is equal Between 200-300 μm." 1100-30min " institute in stress strain curve such as Fig. 4 of the alloy of the composition after above handling process Show, it is seen that with the carbon-free Fe prepared under method of the same race40Mn40Co10Cr10Alloy (curve C0) is compared, and its intensity and plasticity are all More excellent, tensile strength less carbon containing (600MPa) improves about 50%, and plastic strain more carbon containing (600MPa) is improved about 143%；
From big quality, (the Fe of suspension smelting furnace melting is used40Mn40Co10Cr10)96.7C3.3By different heat treatment systems Alloy tensile curve map 4 can be seen that under preparation method of the same race after degree, compared with the alloy of not carbon elements, the conjunction after doping Gold example in lower temperature heat treatment can obtain higher intensity, such as Fig. 4, maximum intensity can be obtained about after the completion of forging 1100MPa, and with the raising of heat treatment temperature, the intensity decreases of material, and plasticity is improved, but generally speaking, compare not The alloy of carbon doping is carried out, its intensity and plasticity are obviously improved, should selected in practical application according to actual service demand Select suitable processing technology and heat treating regime.
(the Fe of embodiment 1340Mn40Co10Cr10)
1) it is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out dispensing, gross mass 8kg or so, Melting is carried out under vacuum levitation melting stove, melting four times obtains cast alloy of the crystallite dimension at 300 μm or so；
2) under this kind of method single melting 8kg it cannot be guaranteed that composition and structural homogenity are, it is necessary to subsequent treatment；
3) in vacuum annealing furnace, the ingot casting obtained to smelting in suspension is incubated 8h at 1300 DEG C；
4) three upsettings three are carried out to the alloy after homogenization and pulls out processing, 1100 DEG C of initial forging temperature, 1000 DEG C of final forging temperature,；
5) alloy after upsetting pull is further forged in lower temperature, 1000 DEG C of initial forging temperature, 900 DEG C of final forging temperature；
6) performance detection is carried out to the material after the completion of forging, tensile strength reaches 1000MPa, elongation percentage about 25%, modeling Property is poor, it is necessary to post-process；
7) alloy after the completion of forging is heat-treated in vacuum drying oven, 1100 DEG C of temperature, time 30min；
(the Fe of embodiment 1440Mn40Co10Cr10)
1) it is (Fe according to nominal composition40Mn40Co10Cr10)96.7C3.3Composition carry out dispensing, gross mass 8kg or so, Melting is carried out under vacuum levitation melting stove, melting four times obtains cast alloy of the crystallite dimension at 300 μm or so；
2) under this kind of method single melting 8kg it cannot be guaranteed that composition and structural homogenity are, it is necessary to subsequent treatment；
3) in vacuum annealing furnace, the ingot casting obtained to smelting in suspension is incubated 15h at 1200 DEG C；
4) three upsettings three are carried out to the alloy after homogenization and pulls out processing, 1000 DEG C of initial forging temperature, 950 DEG C of final forging temperature,；
5) alloy after upsetting pull is further forged in lower temperature, 900 DEG C of initial forging temperature, 850 DEG C of final forging temperature；
6) performance detection is carried out to the material after the completion of forging, tensile strength reaches 900MPa, elongation percentage about 25%, plasticity It is poor, it is necessary to post-process；
7) alloy after the completion of forging is heat-treated in vacuum drying oven, 1000 DEG C of temperature, time 1h；
The principle of the present invention：
By in Fe40Mn40Co10Cr10Middle introducing interstitial element carbon, reduces the stacking fault energy of material, and reduction induces twin formation Required condition, meanwhile, by the introducing of appropriate carbon, can outside twinning strengthening, introduce solution strengthening and/or Precipitation strength, further improve material room-temperature property, especially by final step the higher temperature long period be incubated, As-forged microstructure is partially or completely eliminated, and part separates out phased soln and formed after nearly phase structure, and alloy can be in higher performance water Possess larger performance controllable space again on the basis of flat, be conducive to by other schedule of reinforcements such as working hardening and precipitation The combination of reinforcing is further strengthened, and obtains more rational intensity and plasticity collocation.

Claims (3)

1. a kind of high-performance high-entropy alloy, it is characterised in that according to foundry alloy (Fe40Mn40Co10Cr10)100-xCxNominal composition Dispensing simultaneously carries out melting, wherein alloy substrate Fe40Mn40Co10Cr10Middle each element atomic percentage conc is：Fe：35-45%；Mn： 35-45%；Co：5-15%；Cr：5-15%；
The ＜ x of content 0≤10at% of doping carbon.
2. high-performance high-entropy alloy according to claim 1, it is characterised in that the high-performance high-entropy alloy that melting is obtained Crystallite dimension is 100-300 μm.
3. the processing method of high-performance high-entropy alloy described in a kind of claim 1 or 2, it is characterised in that comprise the following steps：
1) according to foundry alloy (Fe40Mn40Co10Cr10)100-xCxNominal composition dispensing and carry out melting, obtain crystallite dimension about Cast alloy between 100-300 μm；Wherein, 0 ＜ x≤10at%；
If 2) quality of master alloy melting and selection method of smelting make reference alloy GB/T 13298-2015 sample when uniformity Meet GB/T 11352-2009 and GB/T 7233 regulation with consistency, then perform step 3)；Otherwise step 4 is performed)；
3) by adjusting the phosphorus content of cast alloy, if the tensile strength and plasticity of alloy meet actual service demand after regulation, Then adopt and use；Otherwise step 4 is performed)；Wherein, actual service demand is tensile strength between 500~2000MPa and plasticity Intensity-plasticity collocation between 10~100% is required；
4) in vacuum annealing furnace, to step 1) obtain cast alloy between 1000-1300 DEG C homogenizing annealing 8-24h；
5) upsetting pull processing, 1000-1100 DEG C of initial forging temperature, 950-1000 DEG C of final forging temperature are carried out to the alloy after homogenization；
6) alloy after upsetting pull is further forged in lower temperature, 900-1000 DEG C of initial forging temperature, final forging temperature 850-900 ℃；
7) if the intensity and plasticity of the material after the completion of forging meet actual service demand, adopt and use；Otherwise step is performed 8)；
8) alloy after the completion of forging is heat-treated at a temperature of 850~1100 DEG C in vacuum drying oven, time 10- 60min；
9) if the intensity of alloy and plasticity meet actual service demand, adopt and use；Otherwise executive termination condition judgment, if symbol Close end condition and then terminate processing, discard alloy, otherwise return and perform step 3)；
The end condition is：If the carbon content of alloy is in x=0,5,10, the intensity and plasticity of alloy pass through step 3) -8) Processing after, still can not meet actual service demand, then terminate processing, discard alloy.
CN201710583007.4A 2017-07-17 2017-07-17 A kind of high-performance high-entropy alloy and its processing method Active CN107326246B (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
CN201710583007.4A CN107326246B (en) 2017-07-17 2017-07-17 A kind of high-performance high-entropy alloy and its processing method

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN201710583007.4A CN107326246B (en) 2017-07-17 2017-07-17 A kind of high-performance high-entropy alloy and its processing method

Publications (2)

Publication Number Publication Date
CN107326246A true CN107326246A (en) 2017-11-07
CN107326246B CN107326246B (en) 2019-02-05

Family

ID=60227248

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201710583007.4A Active CN107326246B (en) 2017-07-17 2017-07-17 A kind of high-performance high-entropy alloy and its processing method

Country Status (1)

Country Link
CN (1) CN107326246B (en)

Cited By (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108048724A (en) * 2017-12-19 2018-05-18 郑州大学 A kind of high-performance high-entropy alloy and its processing method
CN108213422A (en) * 2017-12-20 2018-06-29 中南大学 A kind of preparation method of carbon containing high-entropy alloy composite material
CN108220837A (en) * 2018-01-19 2018-06-29 北京理工大学 High-entropy alloy mismatch, which is cut, pulls out processing technology
CN108411132A (en) * 2018-05-04 2018-08-17 广西大学 A kind of preparation method of magnetic levitation vacuum melting FeMnNiCoCr high-entropy alloys
CN108439986A (en) * 2018-05-09 2018-08-24 西北工业大学 (HfTaZrTiNb) preparation method of C high entropys ceramic powder and high entropy ceramic powder and high entropy ceramic block
CN109182877A (en) * 2018-11-07 2019-01-11 北京科技大学 (NbMoTaW)100-xMxIt is infusibility high-entropy alloy and preparation method thereof
CN110129731A (en) * 2019-05-22 2019-08-16 江苏理工学院 A kind of antifatigue high-entropy alloy film and preparation method thereof
CN110484796A (en) * 2019-09-20 2019-11-22 吉林大学 A kind of high entropy ceramic particle of transition metal carbide 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
CN111636036A (en) * 2020-06-12 2020-09-08 中国矿业大学 High-manganese-iron alloy and strengthening and toughening method for regulating metastable phase thereof
CN112522634A (en) * 2019-09-17 2021-03-19 东北大学 High-strength high-entropy alloy and preparation method thereof
CN112522563A (en) * 2020-10-30 2021-03-19 西安福莱电工合金有限公司 Low-temperature high-strength high-toughness high-entropy alloy and processing method thereof
CN112725681A (en) * 2020-12-29 2021-04-30 中国矿业大学 Iron-cobalt-nickel-manganese-copper high-entropy cast iron and preparation method and application thereof
CN115354241A (en) * 2022-09-01 2022-11-18 西北工业大学 Low-temperature wear-resistant alloy with synergistically improved strong plasticity and preparation method thereof
CN115491560A (en) * 2021-06-17 2022-12-20 西北工业大学 Method for improving low-temperature wear resistance of alloy

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002173732A (en) * 2000-11-29 2002-06-21 Univ Qinghua High entropy multicomponent alloy
CN104694808A (en) * 2015-03-26 2015-06-10 北京科技大学 High-entropy alloy with dispersion nano-sized precipitate strengthening effect and preparing method thereof
JP2016023364A (en) * 2014-07-25 2016-02-08 株式会社日立製作所 Alloy structure
CN106756407A (en) * 2016-12-07 2017-05-31 徐轶 A kind of CrMnFeCoNiZr high-entropy alloys and preparation method thereof

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2002173732A (en) * 2000-11-29 2002-06-21 Univ Qinghua High entropy multicomponent alloy
JP2016023364A (en) * 2014-07-25 2016-02-08 株式会社日立製作所 Alloy structure
CN104694808A (en) * 2015-03-26 2015-06-10 北京科技大学 High-entropy alloy with dispersion nano-sized precipitate strengthening effect and preparing method thereof
CN106756407A (en) * 2016-12-07 2017-05-31 徐轶 A kind of CrMnFeCoNiZr high-entropy alloys and preparation method thereof

Non-Patent Citations (2)

* Cited by examiner, † Cited by third party
Title
N.D.STEPANOV ET AL.: "Effect of carbon content and annealing on structure and hardness of the CoCrFeNiMn-based high entropy alloys", 《JOURNAL OF ALLOYS AND COMPOUNDS》 *
Y.DENG ET AL.: "Design of a twinning-induced plasticity high entropy alloy", 《ACTA MATERIALIA》 *

Cited By (19)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108048724A (en) * 2017-12-19 2018-05-18 郑州大学 A kind of high-performance high-entropy alloy and its processing method
CN108213422A (en) * 2017-12-20 2018-06-29 中南大学 A kind of preparation method of carbon containing high-entropy alloy composite material
CN108220837A (en) * 2018-01-19 2018-06-29 北京理工大学 High-entropy alloy mismatch, which is cut, pulls out processing technology
CN108411132A (en) * 2018-05-04 2018-08-17 广西大学 A kind of preparation method of magnetic levitation vacuum melting FeMnNiCoCr high-entropy alloys
CN108439986A (en) * 2018-05-09 2018-08-24 西北工业大学 (HfTaZrTiNb) preparation method of C high entropys ceramic powder and high entropy ceramic powder and high entropy ceramic block
CN109182877A (en) * 2018-11-07 2019-01-11 北京科技大学 (NbMoTaW)100-xMxIt is infusibility high-entropy alloy and preparation method thereof
CN110129731B (en) * 2019-05-22 2021-01-19 江苏理工学院 Anti-fatigue high-entropy alloy film and preparation method thereof
CN110129731A (en) * 2019-05-22 2019-08-16 江苏理工学院 A kind of antifatigue high-entropy alloy film 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
CN112522634B (en) * 2019-09-17 2021-11-09 东北大学 High-strength high-entropy alloy and preparation method thereof
CN110484796B (en) * 2019-09-20 2020-11-10 吉林大学 Transition metal carbide high-entropy ceramic particles and preparation method thereof
CN110484796A (en) * 2019-09-20 2019-11-22 吉林大学 A kind of high entropy ceramic particle of transition metal carbide 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
CN111636036A (en) * 2020-06-12 2020-09-08 中国矿业大学 High-manganese-iron alloy and strengthening and toughening method for regulating metastable phase thereof
CN112522563A (en) * 2020-10-30 2021-03-19 西安福莱电工合金有限公司 Low-temperature high-strength high-toughness high-entropy alloy and processing method thereof
CN112725681A (en) * 2020-12-29 2021-04-30 中国矿业大学 Iron-cobalt-nickel-manganese-copper high-entropy cast iron and preparation method and application thereof
CN115491560A (en) * 2021-06-17 2022-12-20 西北工业大学 Method for improving low-temperature wear resistance of alloy
CN115354241A (en) * 2022-09-01 2022-11-18 西北工业大学 Low-temperature wear-resistant alloy with synergistically improved strong plasticity and preparation method thereof

Also Published As

Publication number Publication date
CN107326246B (en) 2019-02-05

Similar Documents

Publication Publication Date Title
CN107326246B (en) A kind of high-performance high-entropy alloy and its processing method
CN105568151B (en) A kind of aluminium enhancing Maraging steel and preparation method thereof
CN101538686B (en) Martensite precipitation hardening stainless steel for structural member and manufacturing method thereof
CN109338160A (en) The castable forging solid solution tungsten alloy of one kind and preparation method
CN104745879B (en) High-density ultra-strength Co strengthens Ni-based high tungsten heat-resisting alloy and preparation method
CN105112728B (en) Heat-resisting alloy for 700-DEG C ultra-supercritical steam turbine rotor and preparation method thereof
CN107937831A (en) Pressure vessel 12Cr2Mo1V steel alloys and its forging heat treatment process
CN107557667A (en) A kind of large die-casting mould high performance hot-work die steel and its manufacturing process
CN106244927A (en) A kind of low-density unimach and preparation method thereof
CN106399858B (en) A kind of low-density Ti3Al enhancing unimach and preparation method thereof
CN105821250A (en) High-strength nickel-base superalloy and manufacturing method thereof
CN105088017B (en) A kind of castable forging kinetic energy tungsten nickel cobalt (alloy) and preparation method of two-phase high density
CN104745880B (en) A kind of high density kinetic energy superhigh intensity tungsten nickel heat-resisting alloy and preparation method
CN104630597A (en) Iron-nickel-chromium-based superalloy and manufacturing method thereof
CN109112425B (en) Ultra-high strength and high toughness maraging steel and preparation method and application thereof
CN108220807A (en) A kind of low-density high alumina superelevation carbon bearing steel and preparation method thereof
CN114150238B (en) Ti-Al-Nb-based composite material and preparation method thereof
CN105734234B (en) It is a kind of to improve low activation ferrite/martensite steel elevated temperature strength and the method for antioxygenic property
CN106702241A (en) Boron strengthened high-density and high-strength tungsten, nickel and cobalt alloy and preparation method
CN110257689A (en) A kind of high polishing pre-hardening plastic mould steel and its preparation process
CN113832401B (en) Rare earth die steel and preparation method thereof
CN114351058B (en) Alloy steel with yield strength of 2000MPa and preparation method thereof
CN107746993A (en) A kind of high-strength high-plasticity alpha and beta type titan alloy and preparation method thereof
CN104711459A (en) High-density ultrahigh-strength tungsten-cobalt heat-resistant alloy and preparation method thereof
CN107937756A (en) Ni Cr based precipitation hardening type wrought superalloy materials 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
GR01 Patent grant
GR01 Patent grant
TR01 Transfer of patent right

Effective date of registration: 20230608

Address after: 518127, 2nd Floor A, No. 116 Xiangshan Avenue, Luotian Community, Yanluo Street, Bao'an District, Shenzhen City, Guangdong Province

Patentee after: SHENZHEN KADAM TECHNOLOGY CO.,LTD.

Address before: Beilin District Xianning West Road 710049, Shaanxi city of Xi'an province No. 28

Patentee before: XI'AN JIAOTONG University

TR01 Transfer of patent right
TR01 Transfer of patent right

Effective date of registration: 20240312

Address after: 518000 201 Xiangshan Avenue, Luotian community, Yanluo street, Bao'an District, Shenzhen City, Guangdong Province

Patentee after: SHENZHEN BIEST PRECISION Co.,Ltd.

Country or region after: China

Address before: 518127, 2nd Floor A, No. 116 Xiangshan Avenue, Luotian Community, Yanluo Street, Bao'an District, Shenzhen City, Guangdong Province

Patentee before: SHENZHEN KADAM TECHNOLOGY CO.,LTD.

Country or region before: China

TR01 Transfer of patent right