CN111218601B - High-strength-toughness low-activation FeCrVO multi-principal-element alloy and preparation method thereof - Google Patents
High-strength-toughness low-activation FeCrVO multi-principal-element alloy and preparation method thereof Download PDFInfo
- Publication number
- CN111218601B CN111218601B CN202010013308.5A CN202010013308A CN111218601B CN 111218601 B CN111218601 B CN 111218601B CN 202010013308 A CN202010013308 A CN 202010013308A CN 111218601 B CN111218601 B CN 111218601B
- Authority
- CN
- China
- Prior art keywords
- alloy
- activation
- principal
- fecrvo
- raw materials
- 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.)
- Active
Links
Images
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
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/001—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacture And Refinement Of Metals (AREA)
Abstract
The invention relates to the field of nuclear energy structural materials and preparation, and provides a high-strength-toughness low-activation FeCrVO multi-principal-element alloy and a preparation method thereof, wherein the alloy has an atomic percentage expression of FeaCrbVcOd，20≤a≤35，20≤b≤35，20≤c≤35，0<d is less than or equal to 3, and a + b + c + d is 100. The preparation process comprises the following steps: removing surface oxide skin from raw materials Fe, Cr and V, accurately weighing according to molar ratio, and using low-melting-point V as O element2O5Is added in the form of (1); smelting the target alloy in a non-consumable vacuum arc furnace or a vacuum magnetic suspension smelting furnace, and obtaining the alloy by a vacuum suction casting or casting method. The strength and the compressive plasticity of the low-activation FeCrV multi-principal-element alloy are improved by adding O element innovatively, and the comprehensive tensile property is obviously superior to that of the existing low-activation multi-principal-element alloy; the alloy has high strength, high toughness, high thermal stability and excellent radiation resistance, and has application prospect in the field of nuclear energy structural materials.
Description
Technical Field
The invention relates to the technical field of nuclear energy structural materials and preparation, in particular to a high-strength-toughness low-activation FeCrVO multi-principal-element alloy and a preparation method thereof.
Background
The development of safe and efficient advanced nuclear energy systems is a major strategic requirement of the country, wherein the radiation resistance of nuclear structural materials is one of the key factors influencing the safety and the economy of nuclear energy reactors, particularly, the operating environments of fourth generation reactors and fusion reactors are complex and severe, high neutron irradiation dose and high-temperature service environments exist, and more severe performance requirements are provided for the nuclear energy structural materials. Therefore, the material is required to have low activation characteristic, difficult activation after neutron irradiation, low residual radioactivity, convenient post-treatment and recycling, and better high-temperature strength and radiation resistance under the conditions of strong neutron irradiation and high temperature.
The multi-principal element solid solution alloy is mainly characterized in that different elements have random occupation in the structure, and according to the Miracle point of view, when the number of the principal elements of the alloy is more than or equal to 3, atoms in the alloy have the possibility of random occupation of lattice sites. Meanwhile, when the atomic fraction of the alloy element exceeds 50%, the effect of high disorder degree of the multi-principal element cannot be sufficiently exerted. The multi-principal-element alloy or the high-entropy alloy renovates the design concept of the traditional alloy, improves the freedom degree of alloy design without the basis of equal atomic ratio during alloy design, and simultaneously can add trace alloy elements to regulate and control the organization structure of the alloy, thereby optimizing the performance. Because of this, the multi-principal element alloy produces many unusual new phenomena, such as breaking the design limit of the traditional material with low-temperature brittleness and high-temperature softening, and shows the engineering application prospect of wide-temperature-range application. Meanwhile, the existing research reports find that the multi-principal-element alloy shows excellent radiation resistance and has wide application prospect in the field of nuclear energy structural materials.
In the aspect of improving the radiation resistance of the nuclear energy structure material, an effective strategy is to introduce high-density defect potential wells to promote the compounding of defects and improve the radiation resistance of the material, and the other strategy is to modulate the formation and migration processes of the defects by optimizing the structure, components and the like of the material and inhibit the formation of large-size defect clusters. The BCC (body centered cubic solid solution) multi-principal element alloy is a representative of a second strategy, and in recent years, regarding the radiation resistance of the multi-principal element alloy, the multi-principal element alloy has obvious advantages in the aspects of inhibiting defect formation and promoting defect recombination compared with the traditional alloy, and simultaneously, the multi-principal element alloy is shown from the theoretical simulation angle to have shorter electron and phonon mean free path and longer energy dissipation process, and is beneficial to the recombination of irradiation shifted atoms and vacancies in the cascade evolution process. In addition, recent research shows that the multi-principal-element alloy with larger lattice distortion has higher radiation resistance in the aspect of inhibiting the radiation defect evolution. Unfortunately, recent studies have been directed mainly to FCC (face centered cubic solid solution) -structured multi-host alloys, or FCC-structured high-entropy alloys, which on the one hand have lattice distortions to a lesser extent than BCC structures; on the other hand, the multi-principal alloy with the FCC structure generally contains high-activation elements such as Co, Ni and the like, and the refractory multi-principal alloy mostly contains high-activation elements such as Nb and the like.
Disclosure of Invention
The invention aims to overcome the defects of the prior art, provides a multi-principal-element high-entropy alloy with a single-phase BCC structure by selecting low-activation alloy aiming at the service environment of structural materials for an advanced reactor and a fusion reactor and the advantage of the multi-principal-element alloy in the capability of resisting irradiation defects, and also aims at the problem of poor toughness of the multi-principal-element alloy with the BCC structure, and innovatively strengthens a low-activation FeCrV multi-principal-element alloy system with the BCC structure by using O element.
The invention adopts the following technical scheme:
a high-strength and high-toughness low-activation FeCrVO multi-principal-element alloy comprises the following alloy components in atomic percentage expression of FeaCrbVcOdWherein a is more than or equal to 20 and less than or equal to 35, b is more than or equal to 20 and less than or equal to 35, c is more than or equal to 20 and less than or equal to 35, and c is more than or equal to 0<d≤3，a+b+c+d＝100。
Further, the atomic percent expression of the alloy component is FeaCrbVcOdWhere a, b, c, 33.3 and d 0.1.
Further, the atomic percent expression of the alloy component is FeaCrbVcOdWhere a, b, c, 33.167 and d 0.5.
Further, the atomic percent expression of the alloy component is FeaCrbVcOdWhere a, b, c, and d are 33.0 and 1.0, respectively.
Further, the atomic percent expression of the alloy component is FeaCrbVcOdWhere a, b, c, 32.833 and d 1.5.
Further, the atomic percent expression of the alloy component is FeaCrbVcOdWhere a, b, c, 32.667 and d 2.0.
Further, the atomic percent expression of the alloy component is FeaCrbVcOdWhere a, b, c, 32.50 and d 2.5.
Further, the atomic percent expression of the alloy component is FeaCrbVcOdWhere a, b, c, 32.333 and d 3.0.
Further, the alloy has a simple body-centered cubic structure, the yield strength of the alloy is not lower than 1.1GPa, and the compression plasticity exceeds 55%.
The invention also provides a preparation method of the high-strength-toughness low-activation FeCrVO multi-principal-element alloy, which comprises the following steps:
s1, smelting the raw materials Fe, Cr, V and V for alloy2O5Converting the metal oxide into the corresponding mass of each raw material according to the mass of the required target melting alloy according to an atomic percentage expression; o element as metal oxide V2O5Adding in the form of powder;
s2, removing the surface film of the raw material by a mechanical method, weighing the raw material, and placing the raw material in absolute ethyl alcohol for ultrasonic oscillation to remove impurities remained on the surface;
s3, configuring V2O5Placing the raw materials at the bottom of a crucible, stacking the raw materials in a non-consumable vacuum electric arc furnace according to the sequence of the melting point, placing Fe at the bottom, placing Cr in the middle, and placing V at the topmost part when the melting point is highest; after the raw materials are placed, a mechanical pump and a molecular pump are started in sequence for vacuumizing, and when the vacuum degree is not higher than 5 multiplied by 10-3After Pa, the chamber is filled with argon to a certain pressure (e.g. half atmospheric pressure), and then the chamber is evacuated again to a vacuum of not higher than 5X 10-3Pa, filling argon into the furnace chamber to a certain pressure (for example, half atmospheric pressure), striking an arc, and further regulating the current in a stepped manner until the alloy is melted; after the alloy is melted, cooling and turning over, and repeatedly melting 4 in such a way to cover the whole range;
and S4, after the target alloy is fully and uniformly smelted, carrying out suction casting on the target alloy into a water-cooling copper mold by using vacuum suction casting equipment to obtain the O-reinforced high-strength-toughness low-activation FeCrVO multi-principal-element alloy.
The preparation method of the high-strength-toughness low-activation FeCrVO multi-principal-element alloy comprises the following steps:
s1, smelting the raw materials Fe, Cr, V and V for alloy2O5Converting the metal oxide into the corresponding mass of each raw material according to the mass of the required target melting alloy according to an atomic percentage expression; o element as metal oxide V2O5Adding in the form of powder;
s2, removing the surface film of the raw material by a mechanical method, weighing the raw material, and placing the raw material in absolute ethyl alcohol for ultrasonic oscillation to remove impurities remained on the surface;
s3, putting the raw materials into a water-cooled copper crucible from the upper cavity of the magnetic suspension smelting furnace, and V2O5The metal oxide is arranged at the preset position of the cavity, the sample chamber of the vacuum magnetic suspension smelting furnace is vacuumized, and when the vacuum degree is not higher than 5 multiplied by 10-3After Pa, filling high-purity argon until the pressure in the furnace reaches a certain pressure (for example, half atmospheric pressure), performing stepped power induction heating (for example, the steps are 40kw, 80kw and 120kw, and the heating time is 2-3 mins, 4-5 mins and 7-8 mins in sequence), and melting the metal raw materials of Fe, Cr and V; at this time, V to be placed at the preset position of the cavity2O5Adding the raw materials into the alloy in a molten state, and performing stepped power induction heating again; inverting the cast ingot, and repeatedly smelting for 2-3 times after all the raw materials are added;
and S4, cooling to obtain an alloy ingot after the smelting is finished, wherein the alloy ingot has a single-phase body-centered cubic solid solution structure.
The invention has the beneficial effects that: the invention innovatively and obviously improves the strength and the compression plasticity of the low-activation FeCrV multi-principal-element alloy by adding O element, wherein (FeCrV)98O2The compressive yield strength of the multi-principal-element alloy exceeds 1.1GPa, and meanwhile, when the compressive plasticity is more than 55%, the multi-principal-element alloy does not have fracture behavior, and the comprehensive tensile property is obviously superior to that of the existing low-activation multi-principal-element alloy system; designing components and preparing method according to alloyThe low-activation multi-principal-element alloy material obtained by the method has the characteristics of high strength, high toughness, high thermal stability and excellent irradiation resistance, and has an application prospect in the aspect of nuclear energy structural materials.
Drawings
Fig. 1 illustrates the XRD pattern of FeCrVO system (FCV in the figure both represent FeCrV).
FIG. 2 illustrates an EBSD map of a FeCrVO multi-principal element alloy containing oxygen at 2.0 at.%.
FIG. 3 illustrates the room temperature compressive stress-strain curve of FCVO-2.0 multi-principal alloy containing 2.0 at.% oxygen versus FCV-Base.
FIG. 4 illustrates HRTEM images of FCV with FCVO-2.0 multi-principal alloy containing 2.0 at.% oxygen;
wherein (a) the FCV alloy is shown to have a simple single phase disordered BCC structure; (b) the FCVO-2.0 alloy was shown to have nanometer second phase particles present at-20 nm.
Detailed Description
Specific embodiments of the present invention will be described in detail below with reference to the accompanying drawings. It should be noted that technical features or combinations of technical features described in the following embodiments should not be considered as being isolated, and they may be combined with each other to achieve better technical effects. In the drawings of the embodiments described below, the same reference numerals appearing in the respective drawings denote the same features or components, and may be applied to different embodiments.
Example 1
A high-strength and high-toughness low-activation FeCrVO multi-principal-element alloy comprises the following alloy components in atomic percentage expression of FeaCrbVcOdWherein a is more than or equal to 20 and less than or equal to 35, b is more than or equal to 20 and less than or equal to 35, c is more than or equal to 20 and less than or equal to 35, and c is more than or equal to 0<d≤3，a+b+c+d＝100。
Example 2
In the high-toughness low-activation FeCrVO multi-principal-element alloy of the embodiment, the atomic percent expression of the alloy components is FeaCrbVcOdWhere a, b, c, 33.167 and d 0.5. The alloy has a simple body-centered cubic structure, the yield strength of the alloy is not less than 1.1GPa, and the compression plasticity exceeds 55%.
Example 3
In the high-toughness low-activation FeCrVO multi-principal-element alloy of the embodiment, the atomic percent expression of the alloy components is FeaCrbVcOdWhere a, b, c, and d are 33.0 and 1.0, respectively. The alloy has a simple body-centered cubic structure, the yield strength of the alloy is not less than 1.1GPa, and the compression plasticity exceeds 55%.
Example 4
In the high-toughness low-activation FeCrVO multi-principal-element alloy of the embodiment, the atomic percent expression of the alloy components is FeaCrbVcOdWhere a, b, c, 32.833 and d 1.5. The alloy has a simple body-centered cubic structure, the yield strength of the alloy is not less than 1.1GPa, and the compression plasticity exceeds 55%.
Example 5
In the high-toughness low-activation FeCrVO multi-principal-element alloy of the embodiment, the atomic percent expression of the alloy components is FeaCrbVcOdWhere a, b, c, 32.667 and d 2.0. The alloy has a simple body-centered cubic structure, the yield strength of the alloy is not less than 1.1GPa, and the compression plasticity exceeds 55%. FIG. 2 illustrates an EBSD map of a FeCrVO multi-principal element alloy containing oxygen at 2.0 at.%; FIG. 3 illustrates the room temperature compressive stress-strain curve of FCVO-2.0 multi-principal alloy containing 2.0 at.% oxygen versus FCV-Base; FIG. 4 illustrates HRTEM images of FCV with FCVO-2.0 multi-host alloy containing 2.0 at.% oxygen.
Example 6
In the high-toughness low-activation FeCrVO multi-principal-element alloy of the embodiment, the atomic percent expression of the alloy components is FeaCrbVcOdWhere a, b, c, 32.50 and d 2.5. The alloy has a simple body-centered cubic structure, the yield strength of the alloy is not less than 1.1GPa, and the compression plasticity exceeds 55%.
Example 7
In the high-toughness low-activation FeCrVO multi-principal-element alloy of the embodiment, the atomic percent expression of the alloy components is FeaCrbVcOdWhere a, b, c, 32.333 and d 3.0. The alloy has a simple body-centered cubic structure, the yield strength of the alloy is not less than 1.1GPa, and the compression plasticity exceeds 55%.
In all of the above embodiments, a ═ b ═ c is used, and good yield strength and compression plasticity can be achieved even when a, b, and c are different.
Example 8
This embodiment is a method for preparing a high-toughness low-activation FeCrVO multi-principal-element alloy.
In the examples, the purity of the metallic materials Fe, Cr and V is not less than 99.9 wt.%, and the purity of the non-metallic material V2O5The purity of the product is more than or equal to 99.9 wt.%.
O-enhanced high toughness Low activation (FeCrV) of this example98O2The multi-principal component alloy comprises 2.0% of O atomic percent and 2.0% of symbol FCVO. In order to reflect the influence of O addition on the FeCrV low-activation mid-entropy alloy, the inventor also designs and prepares the FeCrV mid-entropy alloy as a reference alloy under the same preparation condition, and the symbol is FCV-Base.
Preparing raw materials: removing surface oxide skin of metal raw materials Fe, Cr and V by using grinding wheels, sand paper and other methods, accurately weighing according to a set molar ratio, washing the metal raw materials in alcohol by using ultrasonic oscillation, and naturally airing the metal raw materials for subsequent alloy smelting. The element O is in the form of block or powder V2O5Form of direct addition of, V2O5The block or powder of (A) needs to be dried.
Smelting a small sample: the target alloy has a mass of 50g, and the mass ratios of the constituent elements in FCVO-2.0 are respectively Fe17.4780g, Cr16.2727g, V15.5522g and V2O50.6971 g. The mass of each raw material was accurately weighed using an electronic balance with an accuracy of 0.0001g (within an error of. + -. 0.0002 g). Will weigh the good V2O5The method is characterized in that the method is placed at the bottom of a crucible, and the metal raw materials are sequentially placed in the crucible of a non-consumable vacuum arc furnace according to the sequence of the melting point, namely Fe is placed at the bottom, Cr is placed in the middle, and V has the highest melting point and is placed at the top. After the raw materials are placed, a mechanical pump and a molecular pump are started in sequence for vacuumizing, and when the vacuum degree reaches 5 multiplied by 10-3After PaFilling high-purity argon into the furnace chamber to half atmospheric pressure, and then vacuumizing again to 5X 10-3Pa, filling argon into the furnace chamber to half atmospheric pressure, striking an arc, and further regulating current in a stepped manner until the alloy is melted; after the alloy is melted, the alloy is turned over after being cooled, and the alloy is repeatedly melted for more than 4 times. And after the target alloy is fully and uniformly smelted, carrying out suction casting on the target alloy into a water-cooling copper mold by using vacuum suction casting equipment to obtain the O-reinforced low-activation multi-principal-element alloy material.
Example 9
This example uses the same starting materials as example 8.
O-enhanced high toughness Low activation (FeCrV) of this example98O2The multi-principal component alloy comprises 2.0% of O atomic percent and 2.0% of symbol FCVO.
Preparing raw materials: removing surface oxide skin of metal raw materials Fe, Cr and V by using grinding wheels, sand paper and other methods, accurately weighing according to a set molar ratio, washing the metal raw materials in alcohol by using ultrasonic oscillation, and naturally airing the metal raw materials for subsequent alloy smelting. The element O is in the form of block or powder V2O5Form of direct addition of, V2O5The block or powder of (A) needs to be dried.
Smelting a kg-grade sample: the target alloy is 5kg, and the mass ratios of all the components in FCVO-2.0 are respectively Fe 1747.800g, Cr1627.275g, V1555.227g and V2O569.698 g. Accurately weighing the mass of each raw material (within +/-0.002 g of error requirement) by using an electronic balance with the precision of 0.001g, and weighing the weighed V2O5Placing the rest of Fe, Cr and V metal raw materials at the preset position of the cavity into the bottom of a water-cooled copper crucible in a magnetic suspension smelting furnace, vacuumizing a sample chamber of the vacuum magnetic suspension smelting furnace, and when the vacuum degree reaches 5 multiplied by 10-3After Pa, filling high-purity argon until the pressure in the furnace reaches half atmospheric pressure, performing stepped power induction heating at 40kw, 80kw and 120kw for 2-3 mins, 4-5 mins and 7-8 mins in sequence, and melting the metal raw materials of Fe, Cr and V; at this time, V to be placed at the preset position of the cavity2O5Adding the raw materials into the molten alloy, and performing stepped power induction heating again(ii) a And (3) inverting the ingot, repeatedly smelting for 2-3 times after all the raw materials are added, and smelting and cooling to obtain the alloy ingot, wherein the alloy ingot has a single-phase body-centered cubic solid solution structure.
It should be noted that, the small sample preparation and the Kg sample preparation in example 8 and example 9 are only used for illustrating the preparation process of the alloy of the present invention, and the same method can be extended to the industrial grade preparation. The scope of the present invention should not be limited by examples 8 or 9.
The invention removes surface oxide skin from metal materials Fe, Cr and V by mechanical method, then accurately weighs them according to molar ratio, and O element is V2O5Is added in the form of (1); smelting the target alloy in a non-consumable vacuum arc furnace or a vacuum magnetic suspension smelting furnace, and further obtaining the alloy by a vacuum suction casting or casting method. The invention innovatively and obviously improves the strength and the compression plasticity of the low-activation FeCrV multi-principal-element alloy by adding O element, wherein (FeCrV)98O2The compressive yield strength of the multi-principal-element alloy exceeds 1.1GPa, and meanwhile, when the compressive plasticity is more than 55%, the multi-principal-element alloy does not have fracture behavior, and the comprehensive tensile property is obviously superior to that of the existing low-activation multi-principal-element alloy system. The low-activation multi-principal-element alloy material obtained according to the alloy design components and the preparation method has the characteristics of high strength, high toughness, high thermal stability and excellent irradiation resistance, and has an application prospect in the aspect of nuclear energy structural materials.
While several embodiments of the present invention have been presented herein, it will be appreciated by those skilled in the art that changes may be made to the embodiments herein without departing from the spirit of the invention. The above examples are merely illustrative and should not be taken as limiting the scope of the invention.
Claims (9)
1. The high-strength low-activation FeCrVO multi-principal-element alloy is characterized in that the atomic percent expression of the alloy components is FeaCrbVcOdWherein a is more than or equal to 20 and less than or equal to 35, b is more than or equal to 20 and less than or equal to 35, c is more than or equal to 20 and less than or equal to 35, and c is more than or equal to 0<d is less than or equal to 3, and a + b + c + d is 100; the alloy has a simple body-centered cubic structure, and the yield strength of the alloyNot less than 1.1GPa, and the compression plasticity of more than 55%.
2. The high strength and toughness low activation FeCrVO multi-element alloy as recited in claim 1, wherein the atomic percent expression of the alloy component is FeaCrbVcOdWhere a, b, c, 33.167 and d 0.5.
3. The high strength and toughness low activation FeCrVO multi-element alloy as recited in claim 1, wherein the atomic percent expression of the alloy component is FeaCrbVcOdWhere a, b, c, and d are 33.0 and 1.0, respectively.
4. The high strength and toughness low activation FeCrVO multi-element alloy as recited in claim 1, wherein the atomic percent expression of the alloy component is FeaCrbVcOdWhere a, b, c, 32.833 and d 1.5.
5. The high strength and toughness low activation FeCrVO multi-element alloy as recited in claim 1, wherein the atomic percent expression of the alloy component is FeaCrbVcOdWhere a, b, c, 32.667 and d 2.0.
6. The high strength and toughness low activation FeCrVO multi-element alloy as recited in claim 1, wherein the atomic percent expression of the alloy component is FeaCrbVcOdWhere a, b, c, 32.50 and d 2.5.
7. The high strength and toughness low activation FeCrVO multi-element alloy as recited in claim 1, wherein the atomic percent expression of the alloy component is FeaCrbVcOdWhere a, b, c, 32.333 and d 3.0.
8. A method for preparing the high-toughness low-activation FeCrVO multi-principal-element alloy according to any one of claims 1 to 7, which comprises the following steps:
s1, smelting the raw materials Fe, Cr, V and V for alloy2O5Converting the metal oxide into the corresponding mass of each raw material according to the mass of the required target melting alloy according to an atomic percentage expression; o element as metal oxide V2O5Adding in the form of powder;
s2, removing the surface film of the raw material by a mechanical method, weighing the raw material, and placing the raw material in absolute ethyl alcohol for ultrasonic oscillation to remove impurities remained on the surface;
s3, configuring V2O5Placing the raw materials at the bottom of a crucible, stacking the raw materials in a non-consumable vacuum electric arc furnace according to the sequence of the melting point, placing Fe at the bottom, placing Cr in the middle, and placing V at the topmost part when the melting point is highest; after the raw materials are placed, a mechanical pump and a molecular pump are started in sequence for vacuumizing, and when the vacuum degree is not higher than 5 multiplied by 10-3After Pa, filling argon into the furnace chamber to a certain pressure, and then vacuumizing again to not higher than 5 multiplied by 10-3Pa, filling argon into the furnace chamber to a certain pressure, striking an arc, and further regulating the current in a stepped manner until the alloy is melted; after the alloy is melted, cooling and turning over, and repeatedly melting 4 in such a way to cover the whole range;
and S4, after the target alloy is fully and uniformly smelted, carrying out suction casting on the target alloy into a water-cooling copper mold by using vacuum suction casting equipment to obtain the O-reinforced high-strength-toughness low-activation FeCrVO multi-principal-element alloy.
9. A method for preparing the high-toughness low-activation FeCrVO multi-principal-element alloy according to any one of claims 1 to 7, which comprises the following steps:
s1, smelting the raw materials Fe, Cr, V and V for alloy2O5Converting the metal oxide into the corresponding mass of each raw material according to the mass of the required target melting alloy according to an atomic percentage expression; o element as metal oxide V2O5Adding in the form of powder;
s2, removing the surface film of the raw material by a mechanical method, weighing the raw material, and placing the raw material in absolute ethyl alcohol for ultrasonic oscillation to remove impurities remained on the surface;
s3, putting the raw materials into a water-cooled copper crucible from the upper cavity of the magnetic suspension smelting furnace, and V2O5The metal oxide is arranged at the preset position of the cavity, the sample chamber of the vacuum magnetic suspension smelting furnace is vacuumized, and when the vacuum degree is not higher than 5 multiplied by 10-3After Pa, filling high-purity argon until the pressure in the furnace reaches a certain pressure, and performing stepped power induction heating to melt the metal raw materials of Fe, Cr and V; at this time, V to be placed at the preset position of the cavity2O5Adding the raw materials into the alloy in a molten state, and performing stepped power induction heating again; inverting the cast ingot, and repeatedly smelting for 2-3 times after all the raw materials are added;
and S4, cooling to obtain an alloy ingot after the smelting is finished, wherein the alloy ingot has a single-phase body-centered cubic solid solution structure.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010013308.5A CN111218601B (en) | 2020-01-07 | 2020-01-07 | High-strength-toughness low-activation FeCrVO multi-principal-element alloy and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010013308.5A CN111218601B (en) | 2020-01-07 | 2020-01-07 | High-strength-toughness low-activation FeCrVO multi-principal-element alloy and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN111218601A CN111218601A (en) | 2020-06-02 |
| CN111218601B true CN111218601B (en) | 2021-06-01 |
Family
ID=70806476
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202010013308.5A Active CN111218601B (en) | 2020-01-07 | 2020-01-07 | High-strength-toughness low-activation FeCrVO multi-principal-element alloy and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN111218601B (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN112981210B (en) * | 2021-02-09 | 2022-04-26 | 中国科学院近代物理研究所 | Nuclear medium-entropy alloy system and preparation method and application thereof |
| CN116240442B (en) * | 2023-02-28 | 2023-10-27 | 中南大学 | Low-activation high-strength multicomponent alloy and preparation method thereof |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103710607A (en) * | 2013-12-16 | 2014-04-09 | 北京科技大学 | Oxygen-strengthened TiZrNbHfO high-entropy alloy and preparation method thereof |
| CN104630596A (en) * | 2015-01-15 | 2015-05-20 | 北京科技大学 | High-toughness radiation-proof multi-element alloy and preparation method thereof |
| KR20170110018A (en) * | 2016-03-21 | 2017-10-10 | 포항공과대학교 산학협력단 | Cryogenic High Entropy Alloy |
| WO2019039743A1 (en) * | 2017-08-21 | 2019-02-28 | 포항공과대학교 산학협력단 | V-cr-fe-ni based high-strength high-entropy alloy |
| CN109957700A (en) * | 2019-04-12 | 2019-07-02 | 苏州大学 | Laser melting deposition manufacturing FeCrCuTiV high-entropy alloy powder and preparation method thereof |
| CN110205506A (en) * | 2019-06-24 | 2019-09-06 | 北京理工大学 | A kind of low activation multi-principal elements alloy and preparation method thereof |
| CN110306094A (en) * | 2018-03-20 | 2019-10-08 | 斯沃奇集团研究和开发有限公司 | High-entropy alloy for external module |
-
2020
- 2020-01-07 CN CN202010013308.5A patent/CN111218601B/en active Active
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103710607A (en) * | 2013-12-16 | 2014-04-09 | 北京科技大学 | Oxygen-strengthened TiZrNbHfO high-entropy alloy and preparation method thereof |
| CN104630596A (en) * | 2015-01-15 | 2015-05-20 | 北京科技大学 | High-toughness radiation-proof multi-element alloy and preparation method thereof |
| KR20170110018A (en) * | 2016-03-21 | 2017-10-10 | 포항공과대학교 산학협력단 | Cryogenic High Entropy Alloy |
| WO2019039743A1 (en) * | 2017-08-21 | 2019-02-28 | 포항공과대학교 산학협력단 | V-cr-fe-ni based high-strength high-entropy alloy |
| CN110306094A (en) * | 2018-03-20 | 2019-10-08 | 斯沃奇集团研究和开发有限公司 | High-entropy alloy for external module |
| CN109957700A (en) * | 2019-04-12 | 2019-07-02 | 苏州大学 | Laser melting deposition manufacturing FeCrCuTiV high-entropy alloy powder and preparation method thereof |
| CN110205506A (en) * | 2019-06-24 | 2019-09-06 | 北京理工大学 | A kind of low activation multi-principal elements alloy and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN111218601A (en) | 2020-06-02 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN111074133A (en) | Low-activation multi-principal-element solid solution alloy and preparation method thereof | |
| CN103122431B (en) | Preparation method for magnesium-lithium alloy with enhanced long-period structure phase | |
| CN111187962B (en) | High thermal stability AlxFeCrV multi-principal-element solid solution alloy, preparation and application | |
| CN114457270B (en) | L1 2 Medium-entropy alloy with strong particle plasticization and preparation method thereof | |
| CN111218601B (en) | High-strength-toughness low-activation FeCrVO multi-principal-element alloy and preparation method thereof | |
| CN111876647A (en) | Co-free eutectic medium-entropy alloy and preparation method thereof | |
| CN107841672B (en) | Re-containing high-density ReWTaMoNbxHigh-entropy alloy material and preparation method thereof | |
| CN114058888B (en) | Smelting method of FeCrCoNiAl high-entropy alloy | |
| WO2014059769A1 (en) | Zirconium-based amorphous alloy | |
| CN109023004B (en) | Plasma tungsten-containing single-phase refractory high-entropy alloy and preparation method thereof | |
| CN114525451B (en) | Shielding type non-equal atomic ratio high-entropy alloy steel and preparation method thereof | |
| CN114134385A (en) | Refractory medium-entropy alloy and preparation method thereof | |
| CN114799155B (en) | Preparation method of ceramic particle reinforced refractory high-entropy alloy | |
| CN114657439A (en) | Refractory high-entropy alloy with good room-temperature plasticity and preparation method thereof | |
| CN112267055B (en) | ZrTi-based eutectic high-entropy alloy and preparation method thereof | |
| CN114318067B (en) | Multi-carbide particle reinforced aluminum matrix composite and preparation method thereof | |
| CN114672716B (en) | CoCrNi with high strength and toughness in heat treatment state2(V2B)xEutectic high-entropy alloy and preparation method thereof | |
| CN115595490A (en) | Bimodal eutectic high-entropy alloy and preparation method thereof | |
| CN102108473B (en) | Iron-based amorphous alloy and preparation method thereof | |
| CN110923482B (en) | High-quality high-tungsten high-cobalt-nickel alloy material and preparation method thereof | |
| CN115216677B (en) | High-entropy alloy material with second phases uniformly distributed and reinforced and preparation method thereof | |
| CN109536817B (en) | Tungsten high-entropy alloy with armor-piercing self-sharpening effect and preparation method thereof | |
| CN116043090B (en) | Ti-Zr-Nb-Mo-V series high-strength high-entropy alloy and preparation method thereof | |
| CN115323244B (en) | High-entropy alloy material and preparation method thereof | |
| CN117431449A (en) | Precipitation phase reinforced multi-principal element 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 | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |