CN112853230B - Low-layer-dislocation-energy face-centered cubic structure high-entropy shape memory alloy and preparation method thereof - Google Patents
Low-layer-dislocation-energy face-centered cubic structure high-entropy shape memory alloy and preparation method thereof Download PDFInfo
- Publication number
- CN112853230B CN112853230B CN202110023664.XA CN202110023664A CN112853230B CN 112853230 B CN112853230 B CN 112853230B CN 202110023664 A CN202110023664 A CN 202110023664A CN 112853230 B CN112853230 B CN 112853230B
- Authority
- CN
- China
- Prior art keywords
- shape memory
- alloy
- low
- centered cubic
- cubic structure
- 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
- 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
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C5/00—Manufacture of carbon-steel, e.g. plain mild steel, medium carbon steel or cast steel or stainless steel
- C21C5/52—Manufacture of steel in electric furnaces
- C21C5/5241—Manufacture of steel in electric furnaces in an inductively heated furnace
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C5/00—Manufacture of carbon-steel, e.g. plain mild steel, medium carbon steel or cast steel or stainless steel
- C21C5/52—Manufacture of steel in electric furnaces
- C21C5/5264—Manufacture of alloyed steels including ferro-alloys
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
-
- 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
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2201/00—Treatment for obtaining particular effects
- C21D2201/01—Shape memory effect
Abstract
The application relates to a low-layer fault energy face-centered cubic structure high-entropy shape memory alloy and a preparation method thereof, wherein the alloy comprises the following components in percentage by atom: 28-32% of Mn, 8-12% of Cr, 9-12% of Si, and the balance of Fe and inevitable impurity elements; wherein the total atomic percent of Mn, Cr and Si in the alloy is not less than 50 percent; the atomic percentage ratio of Fe to Mn in the alloy is not lower than 1.5; the preparation method comprises the steps of induction melting, homogenizing annealing treatment, hot rolling treatment and solution treatment, wherein the solution treatment process is water-cooling quenching after heat preservation at 1000-1100 ℃ for 1-2 hours under the protection of argon. The high-entropy shape memory alloy provided by the application has the advantages of low raw material cost, easiness in preparation and processing, high strength, high plasticity and good shape memory effect, and has wide application prospects in the fields of self-repairing skins of naval vessels, large-scale pipeline sleeve joints, intelligent concrete structures and the like.
Description
Technical Field
The application belongs to the technical field of high-entropy alloy materials, and particularly relates to a low-layer fault energy face-centered cubic structure high-entropy shape memory alloy and a preparation method thereof.
Background
The high-entropy alloy generally has high stability and high solid solution strengthening effect because the high-entropy alloy contains a plurality of composition elements with high solubility and has high composition entropy. Such alloys were initially considered to be expected to find wide application in areas where corrosion resistance and high temperature mechanical properties are highly required. Research in recent years shows that the high-entropy alloy with the face-centered cubic structure can obtain various plastic deformation mechanisms by regulating and controlling the stacking fault energy, and comprises {111} <112> deformation twin crystals and stress-induced fcc → hcp martensite phase transformation, so that the alloy can generate twin crystals and the effect of transformation-induced plasticity in the plastic deformation process, thereby presenting high work hardening rate, high tensile strength and high plasticity. Meanwhile, the alloy is easy to prepare and process, so the high-entropy alloy with the face-centered cubic structure is regarded as a high-performance room-temperature structural material with important application potential. It is noted that when the stacking fault energy is low, such alloys produce a large amount of stress-induced hcp martensite during plastic deformation, and such martensite rapidly reverts to the original fcc matrix phase at high temperatures. Considering that the generation of the stress-induced martensite phase during the deformation and the reverse transformation thereof during the heating annealing are sources of the shape memory effect, it can be concluded that the low-stacking fault energy face-centered cubic structure high-entropy alloy has the shape memory effect.
A variety of alloy systems have been found to have shape memory effects over the past several decades, with NiTi-based and Cu-based shape memory alloys being the primary ones that have gained widespread attention. However, Cu-based shape memory alloys have been rarely used commercially to date due to their low strength, poor shape memory stability, and the like. Of the various types of shape memory alloys, only the NiTi-based shape memory alloys have been widely commercially used today to make sleeve joints, actuators, bone plates, vascular stents, springs, smart phone antennas, eyeglass frames, vibration dampers, and the like. However, it is worth noting that the raw materials of the NiTi-based shape memory alloy are expensive, and the main composition phase thereof is an intermetallic compound, so that the preparation and processing are difficult, and the manufacturing of large-sized parts is difficult, thereby greatly limiting the wider application thereof. High-entropy alloys developed based on the NiTi-based alloy system and having a solid solution with a body-centered cubic structure as a main constituent phase, such as the alloy system disclosed in the invention patent with the application number of 201510788841.8, have been proved to have a shape memory effect, but on one hand, the shape memory performance of the alloys is much lower than that of the NiTi-based alloys, on the other hand, the raw material cost of the alloys is still high, and the content of intermetallic compounds in the constituent phases is high, so that the alloys can be expected to hardly meet the production requirements of large parts in the aspects of shape memory performance, raw material cost, processability, and the like.
Disclosure of Invention
Considering that the low-stacking fault energy face-centered cubic structure high-entropy alloy can be prepared from low-cost elements such as Fe, Mn, Cr, Si and the like, and the alloy has good mechanical properties on one hand and is easy to prepare and process on the other hand, the development of the low-stacking fault energy face-centered cubic structure high-entropy alloy with the shape memory effect is the key to solve the application limitation of the existing shape memory alloy. The alloy material can be widely applied to the manufacturing and assembling field of large parts such as self-repairing skins of naval vessels, large-scale pipeline sleeve joints and the like and the manufacturing field of intelligent concrete structures.
Based on the consideration, the application aims at the problems that the existing commercial shape memory alloy is high in cost, difficult to prepare and process and difficult to manufacture large parts, and provides the low-stacking fault energy face-centered cubic structure high-entropy shape memory alloy which is low in cost and easy to prepare and process and the preparation method thereof.
Specifically, in a first aspect of the present application, there is provided a low-stacking fault energy face-centered cubic structure high-entropy shape memory alloy, wherein the alloy comprises the following constituent elements in atomic percentage: 28-32% of Mn, 8-12% of Cr, 9-12% of Si, and the balance of Fe and inevitable impurity elements;
wherein, the total atomic percentage of Mn, Cr and Si in the alloy is not less than 50 percent, so as to ensure that the alloy has high component entropy and can obtain 100 percent of face-centered cubic structure phase after solution quenching;
the atomic percentage ratio of Fe to Mn in the alloy is not less than 1.5, so that the alloy has low stacking fault energy and can generate a large amount of stress-induced martensite in the plastic deformation process.
In a second aspect, the present application provides a method for preparing the low-stacking fault energy face-centered-cubic structure high-entropy shape memory alloy, which comprises the steps of induction melting, homogenizing annealing treatment, hot rolling treatment and solution treatment.
Wherein the solution treatment process is water-cooling quenching after heat preservation at 1000-1100 ℃ for 1-2 h under the protection of argon.
As further illustration of the application, pure Fe, pure Mn, pure Cr and pure Si with the purity higher than 99.5 percent are taken as raw materials in the preparation method.
As further illustrated in the present application, the induction melting is performed in a vacuum intermediate frequency induction melting furnace, and argon is used as a protective atmosphere.
As a further illustration of the present application, the argon pressure is 0.8X 105Pa, 380V voltage, and 2500Hz frequency of the induction current.
As a further explanation of the present application, the induction melting is repeated 3 to 5 times, wherein the alloy ingot is turned over after each melting is completed to perform the next melting, so as to improve the component uniformity of the final obtained finished product ingot.
As further illustration of the application, the homogenizing annealing treatment process is water-cooling quenching after heat preservation at 1000-1100 ℃ for 10-12 h under the protection of argon.
As a further explanation of the application, the hot rolling treatment is that a double-roller plate strip rolling mill is adopted for multi-pass rolling after the heat preservation and the thorough heat penetration at 900 ℃, the deformation rate of each pass is 15-25%, the furnace is returned to the furnace after the rolling of each pass before the last pass is finished and the heat preservation is carried out at 900 ℃ for 5-10 min, and the total hot rolling deformation rate is 60-70%.
Compared with the prior art, the method has the following beneficial technical effects:
the low-stacking fault energy face-centered cubic structure high-entropy shape memory alloy provided by the application has the advantages of low raw material cost, easiness in preparation and processing, high tensile strength, high elongation after fracture and high recovery strain, under the conditions of optimal component proportion and optimal solution treatment, the tensile strength reaches 669MPa, the elongation after fracture reaches 69.8%, and the recovery strain reaches more than 2.25%, and is particularly suitable for manufacturing large structure-function integrated components with high requirements on strength, plasticity and shape memory effect.
Drawings
FIG. 1 is an XRD spectrum of a high-entropy alloy prepared in examples 1 to 4 of the present application;
FIG. 2 is a scanning electron microscope picture of the high-entropy alloy prepared in embodiments 1 to 4 of the present application;
FIG. 3 is an exemplary graph of the determination of the recovery strain in combination with the bending deformation and recovery annealing tests;
FIG. 4 shows the recovery strain of the high-entropy alloy prepared in embodiments 1 to 4 of the present application under different pre-strain amounts.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present application clearer, the technical solutions in the embodiments of the present application will be clearly and completely described below with reference to the drawings in the embodiments of the present application, and it is obvious that the described embodiments are some embodiments of the present application, but not all embodiments. The alloy structure and properties of the embodiments of the present application, generally described and illustrated in the figures herein, can be tailored and designed in a variety of different compositional configurations.
Thus, the following detailed description of the embodiments of the present application, presented in the accompanying drawings, is not intended to limit the scope of the claimed application, but is merely representative of selected embodiments of the application. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present application.
The technical solution of the present application will be explained with reference to specific embodiments.
Example 1
The low-stacking fault energy face-centered cubic structure high-entropy shape memory alloy of the embodiment comprises the following main components in atomic percentage: 50% of Fe, 30% of Mn, 10% of Cr and 10% of Si. The alloy has a stacking fault energy of 12.79mJ/m2。
The preparation method of the alloy comprises the following steps:
s1, taking pure Fe, pure Mn, pure Cr and pure Si with the purity higher than 99.5% as raw materials, adopting argon as protective atmosphere, smelting in a vacuum medium frequency induction smelting furnace, wherein the pressure of the argon is 0.8 multiplied by 105Pa, 380V of voltage and 2500Hz of induced current;
s2, turning over the ingot obtained by the previous smelting step, and adopting the same parameters to carry out re-smelting, and repeatedly smelting for 3 times in such a way to improve the component uniformity of the final obtained finished ingot;
s3, placing the finished product ingot in a heat treatment furnace with argon protection, heating the ingot to 1100 ℃ along with the furnace, firstly carrying out homogenization annealing for 10 hours, and then carrying out water-cooling quenching;
s4, cutting the ingot subjected to the homogenizing annealing treatment into plates by using a wire cut electric discharge machine, heating the plates to 900 ℃, preserving heat, carrying out thorough heat rolling, and then carrying out multi-pass rolling by using a double-roller plate and strip rolling mill, wherein the deformation rate of each pass is 15-20%, and the ingot is returned to the furnace after each pass before the last pass is rolled and preserved at 900 ℃ for 5-7 min, and the total hot rolling deformation rate is 65%;
s5, placing the plate after the hot rolling treatment in a heat treatment furnace with argon protection, carrying out solution treatment at 1100 ℃ for 1h, and then carrying out water cooling quenching.
XRD and scanning electron microscopy were used to characterize the initial structure of the alloy prepared in this example, and the results are shown in fig. 1 and fig. 2, respectively. From these two figures, it can be seen that the alloy prepared in this example consists of 100% of the face-centered cubic phase.
The shape memory effect of the alloy prepared in this example was measured in combination with the bending deformation and the recovery annealing (as shown in FIG. 3), and the result is shown in FIG. 4. As can be seen in FIG. 4, the alloy exhibited a recovery strain that increased with increasing bending pre-strain, with a maximum recovery strain of 2.25% over the illustrated bending pre-strain range, exhibiting a good shape memory effect.
According to GB/T228.1-2010 part 1 of the tensile test of metallic materials: the mechanical properties of the alloy prepared in this example were measured by room temperature test method, and the results showed that the tensile strength was 669MPa and the elongation after fracture was 69.8%.
Example 2
The low-stacking fault energy face-centered cubic structure high-entropy shape memory alloy of the embodiment comprises the following main components in atomic percentage: 48% of Fe, 32% of Mn, 8% of Cr and 12% of Si. The alloy has a stacking fault energy of 8.70mJ/m2。
The preparation method of the alloy comprises the following steps:
s1, taking pure Fe, pure Mn, pure Cr and pure Si with the purity higher than 99.5% as raw materials, adopting argon as protective atmosphere, smelting in a vacuum medium frequency induction smelting furnace, wherein the pressure of the argon is 0.8 multiplied by 105Pa, 380V of voltage and 2500Hz of induced current;
s2, turning over the ingot obtained by the previous smelting step, and adopting the same parameters to carry out re-smelting, and repeatedly smelting for 4 times in such a way to improve the component uniformity of the final finished ingot;
s3, placing the finished product ingot in a heat treatment furnace with argon protection, heating the ingot to 1000 ℃ along with the furnace, firstly carrying out homogenization annealing treatment for 12 hours, and then carrying out water-cooling quenching;
s4, cutting the ingot subjected to the homogenizing annealing treatment into plates by using a wire cut electric discharge machine, heating the plates to 900 ℃, preserving heat, carrying out thorough heat rolling, and then carrying out multi-pass rolling by using a double-roller plate and strip rolling mill, wherein the deformation rate of each pass is 20-25%, and the ingot is returned to the furnace after each pass before the last pass is rolled and preserved at 900 ℃ for 8-10 min, and the total hot rolling deformation rate is 60%;
s5, placing the plate after the hot rolling treatment in a heat treatment furnace with argon protection, carrying out solution treatment at 1000 ℃ for 2h, and then carrying out water cooling quenching.
XRD and scanning electron microscopy were used to characterize the initial structure of the alloy prepared in this example, and the results are shown in fig. 1 and fig. 2, respectively. From these two figures, it can be seen that the alloy prepared in this example consists of 100% of the face-centered cubic phase.
The shape memory effect of the alloy prepared in this example was measured in combination with the bending deformation and the recovery annealing (as shown in FIG. 3), and the result is shown in FIG. 4. As can be seen in FIG. 4, the alloy exhibited a recovery strain that increased with increasing bending pre-strain, with a maximum recovery strain of 2.15% over the illustrated bending pre-strain range, exhibiting a good shape memory effect.
According to GB/T228.1-2010 part 1 of the tensile test of metallic materials: the mechanical properties of the alloy prepared in this example were measured by room temperature test method, and the results showed that the tensile strength was 658MPa and the elongation after fracture was 67.5%.
Example 3
The low-stacking fault energy face-centered cubic structure high-entropy shape memory alloy of the embodiment comprises the following main components in atomic percentage: 48% of Fe, 28% of Mn, 12% of Cr and 12% of Si. The alloy has a stacking fault energy of 11.81mJ/m2。
The preparation method of the alloy comprises the following steps:
s1, taking pure Fe, pure Mn, pure Cr and pure Si with the purity higher than 99.5% as raw materials, adopting argon as protective atmosphere, smelting in a vacuum medium frequency induction smelting furnace, wherein the pressure of the argon is 0.8 multiplied by 105Pa, 380V of voltage and 2500Hz of induced current;
s2, turning over the ingot obtained by the previous smelting step, and adopting the same parameters to carry out re-smelting, and repeatedly smelting for 5 times in such a way to improve the component uniformity of the final finished ingot;
s3, placing the finished product ingot in a heat treatment furnace with argon protection, heating the ingot to 1050 ℃ along with the furnace, firstly carrying out homogenization annealing for 12 hours, and then carrying out water-cooling quenching;
s4, cutting the ingot subjected to the homogenizing annealing treatment into plates by using a wire cut electric discharge machine, heating the plates to 900 ℃, preserving heat, carrying out thorough heat rolling, and then carrying out multi-pass rolling by using a double-roller plate and strip rolling mill, wherein the deformation rate of each pass is 15-18%, and the ingot is returned to the furnace after each pass before the last pass is rolled and preserved at 900 ℃ for 8-10 min, and the total hot rolling deformation rate is 70%;
and S5, placing the plate after the hot rolling treatment in a heat treatment furnace with argon protection, carrying out solution treatment at 1050 ℃ for 2h, and then carrying out water cooling quenching.
XRD and scanning electron microscopy were used to characterize the initial structure of the alloy prepared in this example, and the results are shown in fig. 1 and fig. 2, respectively. From these two figures, it can be seen that the alloy prepared in this example consists of 100% of the face-centered cubic phase.
The shape memory effect of the alloy prepared in this example was measured in combination with the bending deformation and the recovery annealing (as shown in FIG. 3), and the result is shown in FIG. 4. As can be seen in FIG. 4, the alloy exhibited a recovery strain that increased with increasing bending pre-strain, with a maximum recovery strain of 2.34% over the illustrated bending pre-strain range, exhibiting a good shape memory effect.
According to GB/T228.1-2010 part 1 of the tensile test of metallic materials: the mechanical properties of the alloy prepared in this example were measured by room temperature test method, and the results showed that the tensile strength was 663MPa, and the elongation after fracture was 65.8%.
Example 4
The low-stacking fault energy face-centered cubic structure high-entropy shape memory alloy of the embodiment comprises the following main components in atomic percentage: 50% of Fe, 31% of Mn, 10% of Cr and 9% of Si. The alloy has a stacking fault energy of 14.43mJ/m2。
The preparation method of the alloy comprises the following steps:
s1, taking pure Fe, pure Mn, pure Cr and pure Si with the purity higher than 99.5% as raw materials, adopting argon as protective atmosphere, smelting in a vacuum medium frequency induction smelting furnace, wherein the pressure of the argon is 0.8 multiplied by 105Pa, 380V of voltage and 2500Hz of induced current;
s2, turning over the ingot obtained by the previous smelting step, and adopting the same parameters to carry out re-smelting, and repeatedly smelting for 3 times in such a way to improve the component uniformity of the final obtained finished ingot;
s3, placing the finished product ingot in a heat treatment furnace with argon protection, heating the ingot to 1050 ℃ along with the furnace, firstly carrying out homogenization annealing treatment for 11 hours, and then carrying out water-cooling quenching;
s4, cutting the ingot subjected to the homogenizing annealing treatment into plates by using a wire cut electric discharge machine, heating the plates to 900 ℃, preserving heat, carrying out thorough heat rolling by using a double-roller plate and strip rolling mill for multiple passes, wherein the deformation rate of each pass is 20-25%, and the ingot is returned to the furnace after each pass before the last pass is rolled, preserved at 900 ℃ for 6-9 min, and the total hot rolling deformation rate is 67%;
s5, placing the plate after hot rolling treatment in a heat treatment furnace with argon protection, carrying out solution treatment at 1100 ℃ for 1.5h, and then carrying out water cooling quenching.
XRD and scanning electron microscopy were used to characterize the initial structure of the alloy prepared in this example, and the results are shown in fig. 1 and fig. 2, respectively. From these two figures, it can be seen that the alloy prepared in this example consists of 100% of the face-centered cubic phase.
The shape memory effect of the alloy prepared in this example was measured in combination with the bending deformation and the recovery annealing (as shown in FIG. 3), and the result is shown in FIG. 4. As can be seen in FIG. 4, the recovery strain of the alloy increased with increasing bending pre-strain, with a maximum recovery strain of 2.31% over the illustrated bending pre-strain range, exhibiting good shape memory.
According to GB/T228.1-2010 part 1 of the tensile test of metallic materials: the mechanical properties of the alloy prepared in this example were measured by room temperature test method, and the results showed that the tensile strength was 655MPa and the elongation after fracture was 68.1%.
The embodiments given above are preferable examples for implementing the present application, and the present application is not limited to the above-described embodiments. Any non-essential addition or replacement made by a person skilled in the art according to the technical features of the technical solution of the present application falls within the scope of the present application.
Claims (8)
1. The high-entropy shape memory alloy with the low-stacking fault energy face-centered cubic structure is characterized by comprising the following components in percentage by atom: 28-32% of Mn, 8-12% of Cr, 9-12% of Si, and the balance of Fe and inevitable impurity elements; wherein the total atomic percent of Mn, Cr and Si in the alloy is not less than 50 percent; the atomic percentage ratio of Fe to Mn in the alloy is not lower than 1.5; the alloy consists of 100% face centered cubic phase.
2. A method for preparing a high-entropy shape memory alloy with a low-stacking fault energy face-centered cubic structure according to claim 1, which is characterized in that: the preparation method comprises the steps of induction melting, homogenizing annealing treatment, hot rolling treatment and solution treatment,
wherein the solution treatment process is water-cooling quenching after heat preservation at 1000-1100 ℃ for 1-2 h under the protection of argon.
3. A method for preparing a high entropy shape memory alloy with low stacking fault energy face-centered-cubic structure according to claim 2, wherein the method uses pure Fe, pure Mn, pure Cr, and pure Si with purity higher than 99.5% as raw materials.
4. The method for preparing a high-entropy shape memory alloy with a low-stacking fault energy face-centered cubic structure according to claim 2, wherein the method comprises the following steps: the induction melting is carried out in a vacuum medium-frequency induction melting furnace, and argon is used as a protective atmosphere.
5. The method for preparing a high-entropy shape memory alloy with a low-stacking fault energy face-centered cubic structure according to claim 4, wherein the method comprises the following steps: the argon pressure is 0.8 multiplied by 105Pa, 380V voltage, and 2500Hz frequency of the induction current.
6. The method for preparing a high-entropy shape memory alloy with a low-stacking fault energy face-centered cubic structure according to claim 2, wherein the method comprises the following steps: and the induction melting is repeatedly carried out for 3-5 times, wherein the alloy ingot is turned over after each time of melting is finished so as to carry out the next melting.
7. The method for preparing a high-entropy shape memory alloy with a low-stacking fault energy face-centered cubic structure according to claim 2, wherein the method comprises the following steps: the homogenizing annealing treatment process is water-cooling quenching after heat preservation for 10-12 hours at 1000-1100 ℃ under the protection of argon.
8. The method for preparing a high-entropy shape memory alloy with a low-stacking fault energy face-centered cubic structure according to claim 2, wherein the method comprises the following steps: the hot rolling treatment is that a double-roller plate strip rolling mill is adopted for multi-pass rolling after the heat preservation and thorough heating at 900 ℃, the deformation rate of each pass is 15-25%, the furnace is returned after each pass before the last pass is finished, the heat preservation is carried out for 5-10 min at 900 ℃, and the total hot rolling deformation rate is 60-70%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110023664.XA CN112853230B (en) | 2021-01-08 | 2021-01-08 | Low-layer-dislocation-energy face-centered cubic structure high-entropy shape memory alloy and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202110023664.XA CN112853230B (en) | 2021-01-08 | 2021-01-08 | Low-layer-dislocation-energy face-centered cubic structure high-entropy shape memory alloy and preparation method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN112853230A CN112853230A (en) | 2021-05-28 |
| CN112853230B true CN112853230B (en) | 2022-03-18 |
Family
ID=76005439
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202110023664.XA Active CN112853230B (en) | 2021-01-08 | 2021-01-08 | Low-layer-dislocation-energy face-centered cubic structure high-entropy shape memory alloy and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN112853230B (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN116356190A (en) * | 2023-04-14 | 2023-06-30 | 西北工业大学 | High-strength high-plasticity Gao Liewen capacity-limit high-entropy alloy and preparation method thereof |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101215678A (en) * | 2008-01-17 | 2008-07-09 | 四川大学 | Training-free casting iron-base shape memory alloy containing high temperature ferrite |
-
2021
- 2021-01-08 CN CN202110023664.XA patent/CN112853230B/en active Active
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101215678A (en) * | 2008-01-17 | 2008-07-09 | 四川大学 | Training-free casting iron-base shape memory alloy containing high temperature ferrite |
Also Published As
| Publication number | Publication date |
|---|---|
| CN112853230A (en) | 2021-05-28 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN115141984B (en) | High-entropy austenitic stainless steel and preparation method thereof | |
| CN108642362B (en) | High-entropy alloy and preparation method thereof | |
| CN110952041B (en) | Fe-Mn-Ni-Cr four-component high-entropy alloy | |
| CN114657417B (en) | High-strength plastic titanium alloy suitable for cold deformation processing and preparation method thereof | |
| CN113637885B (en) | Multicomponent FeNiCoAlTiZr super elastic alloy and preparation method thereof | |
| WO2023050860A1 (en) | Multi-component precision high-resistance alloy with high strength and toughness, and preparation method therefor | |
| CN114990382B (en) | Ultra-low-gap phase transition induced plasticity metastable beta titanium alloy and preparation method thereof | |
| CN112853149A (en) | Copper-nickel-silicon-aluminum alloy and preparation method thereof | |
| JP4756974B2 (en) | Ni3 (Si, Ti) -based foil and method for producing the same | |
| CN112853230B (en) | Low-layer-dislocation-energy face-centered cubic structure high-entropy shape memory alloy and preparation method thereof | |
| JP5512145B2 (en) | Shape memory alloy | |
| CN109457091B (en) | Method for preparing coarse-grain Fe-Mn-Si-based shape memory alloy | |
| CN116287931A (en) | Method for remarkably improving strength and hardness of entropy alloy in VCoNi | |
| CN113930693B (en) | Fe-Mn-Al-Ni-Cu super-elastic alloy and preparation method thereof | |
| JP3749589B2 (en) | Hot-rolled strip, hot-rolled sheet or hot-rolled strip made of Ti-Fe-O-N-based titanium alloy and method for producing them | |
| CN115478201A (en) | CoNiV-based medium-entropy alloy containing dual ordered phases and preparation method thereof | |
| CN113564441A (en) | Fe-Ni-Co-Al-W alloy with super elasticity and preparation method thereof | |
| CN111235491B (en) | High-strength high-plasticity shape memory steel and preparation method thereof | |
| JPWO2018061530A1 (en) | Method of manufacturing Fe-Ni based alloy sheet and Fe-Ni based alloy sheet | |
| CN113637921A (en) | Fe-Ni-Co-Al-Mo hyperelastic alloy and preparation method thereof | |
| CN109504871A (en) | It is applicable in the high strength titanium copper alloy silk material and manufacturing method of electrically conductive elastic component | |
| JP2016023315A (en) | Titanium plate and manufacturing method therefor | |
| CN113621891B (en) | Polycrystalline FeNiCoAlNbV hyperelastic alloy and preparation method thereof | |
| CN116855814A (en) | Wide temperature range superelasticity Ti 46 Ni 50-x Nb 4 Cu x Shape memory alloy and preparation method thereof | |
| CN116356190A (en) | High-strength high-plasticity Gao Liewen capacity-limit 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 | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |