CN113621860B - Fe-Ni-Co-Al-Dy super-elastic alloy and preparation method thereof - Google Patents
Fe-Ni-Co-Al-Dy super-elastic alloy and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a Fe-Ni-Co-Al-Dy super-elastic alloy and a preparation method thereof, wherein the expression of the super-elastic alloy is Fe a Ni b Co c Al d Dy e Wherein a, b, c, d, e respectively represent the atomic number percentage (at.%) of each corresponding element, a = 35-60, b = 18-38, c = 7-25, d = 5-18, e = 0.01-10, a +, b +, c + e =100. The preparation method of the alloy comprises the steps of smelting, rolling, solid solution and aging treatment. The super-elastic alloy of the invention regulates and controls the size and volume fraction of precipitated phases by adding rare earth elements and controlling the heat treatment mode and time. The precipitated phase can make the matrix parent phase ordered, and can pin dislocation, inhibit the plastic deformation of the alloy, thereby obtaining excellent superelasticity. The super-elastic alloy has the strength of over 1300MPa and the recoverable strain of 1.1 percent.
Description
Technical Field
The invention relates to a Fe-Ni-Co-Al-Dy super-elastic alloy and a preparation method thereof, belonging to the technical field of super-elastic alloy materials.
Background
The super-elastic alloy can show reversible large strain, nonlinearity and other rules in the stress loading and unloading process. Superelasticity refers to the phenomenon that after limited plastic deformation (nonlinear elastic deformation) of an alloy occurs under the action of stress, the stress can be directly released, so that the alloy returns to the original shape. Decades of development in superelastic alloysIn the above, the super-elastic alloys are classified into Ni-Ti-based super-elastic alloys, cu-based super-elastic alloys, and Fe-based super-elastic alloys according to their component classification. NiTi-based super-elastic alloy is most widely applied at present because the NiTi-based super-elastic alloy has the advantages of super-elastic strain up to 8%, good mechanical property, strong corrosion resistance, good biocompatibility and the like, but also has the defects of high material cost, difficult processing and the like. The Cu-based super-elastic alloy has smaller resistivity which is about one order of magnitude smaller than that of the NiTi-based alloy, is not suitable for occasions of power-on heating, has poorer mechanical property and is sensitive to temperature change, and the application of the Cu-based super-elastic alloy is limited. The Fe-based super-elastic alloy has the advantages of low price, good plasticity, high strength, easy processing, weldability and the like, so that the Fe-based super-elastic alloy can be used as a substitute of the NiTi-based super-elastic alloy and becomes a hot spot of the current research. However, the martensite phase transformation of the Fe-based superelastic alloy is almost all non-thermo-elastic and does not exhibit significant superelasticity. The Fe-Ni-Co-Al series super elastic alloy has large phase change thermal hysteresis, disordered parent phase, difficult thermoelastic martensite transformation and L1 precipitation through aging strengthening 2 And phase transformation, namely changing the parent phase into order, improving the coherent degree of the martensite phase and the parent phase, and transforming the martensite phase from non-thermal elasticity to thermal elasticity so as to obtain super elasticity.
In 2007, liyongqing and the like research the influence of rare earth Tb doping on the phase change and the performance of the shape memory alloy Ni-Mn-Ga. It was found that Tb did not form a solid solution with Ni-Mn-Ga. After Tb is added, the martensite phase transformation point of the alloy is slightly raised, and the comprehensive mechanical property is obviously improved. In 2020, zhang Ming et Al selects four rare earth elements Nd, sm, Y and La to be added into the Cu-Al-Ni shape memory alloy. After the rare earth elements are added, crystal grains are obviously refined, and the addition of the four rare earth elements reduces the phase transition temperature of the alloy. Meanwhile, the rare earth elements are added to have the functions of fine grain strengthening and second phase strengthening, so that the mechanical property of the alloy is obviously improved. However, the effect of rare earth elements on the super elastic properties of the alloy is not reported. Therefore, the rare earth element Dy is selected and added, and the influence of the rare earth element Dy on the microstructure evolution and the super-elastic performance is researched.
In 2010, tanaka et Al reported that Fe-28Ni-17Co-11.5Al-2.5Ta-0.05B (at%) alloy could transform the non-thermoelastic martensitic phase transformation into a thermoelastic martensitic phase transformation with high superelastic strain, high hardness, high strength and good cold workability with a maximum recoverable strain as high as 13.5%. In 2015, tanaka et al concluded the design basis for the FeNiCoAlTaB alloy and gave the optimum alloy composition design ratio. The invention patent of publication No. CN 103509988A relates to a polycrystalline Fe-Ni-Co-Al-Nb-B shape memory alloy with super elasticity and a preparation method thereof. The alloy comprises the following atomic percentage: 30-50% of Fe, 8-40% of Ni2, 10-30% of Co, 8-15% of Al, 1-4% of Nb and 0.1-3% of B. The shape memory alloy obtained by the invention has obviously improved recoverable strain, the maximum recoverable strain can reach 10.5 percent, and excellent super elasticity is embodied. According to the invention, rare earth elements are innovatively added into the Fe-Ni-Co-Al series super-elastic alloy to pin dislocation and inhibit the slippage of dislocation, so that large recoverable strain is obtained under a proper heat treatment process, and further, the super-elasticity is realized by stress-induced martensite phase transformation in the alloy loading process.
Disclosure of Invention
The first technical problem to be solved by the invention is as follows: provides a composition design of Fe-based super-elastic alloy with excellent super-elasticity.
The second technical problem to be solved by the invention is: provides a preparation method of Fe-based super-elastic alloy with excellent super-elasticity.
In order to solve the first technical problem, the invention provides a Fe-based super-elastic alloy with excellent super-elasticity, and the component is Fe a Ni b Co c Al d Dy e Wherein a, b, c, d, e respectively represent the atomic number percentage (at.%) of each corresponding element, and the following conditions are satisfied: a = 35-60, b = 18-38, c = 7-25, d = 5-18, e = 0.01-2, a + b + c + d + e =100.
In order to solve the second technical problem, the invention provides a method for preparing the Fe-based superelastic alloy, and the preparation method comprises the processes of smelting, rolling, solid solution and aging treatment.
The preparation method of the Fe-Ni-Co-Al-Dy super-elastic alloy is characterized by comprising the following preparation processes:
(1) The method comprises the following steps of selecting and proportioning industrially used metallic iron particles, metallic nickel particles, metallic cobalt blocks, metallic aluminum particles and metallic dysprosium particles according to the atomic percentage of each element in the super-elastic alloy, and then smelting in vacuum or under the protection of inert gases such as argon. The metal solution needs to be thoroughly mixed during the smelting process to ensure that the composition is sufficiently uniform.
(2) Heating the casting to 1100-1300 ℃, preserving heat for 1-3 h to homogenize the casting, eliminating segregation, then carrying out hot rolling with small deformation of 0-60% at 1100-1300 ℃, and carrying out cold rolling with large deformation of more than or equal to 85% after water cooling to room temperature.
(3) The rolled material is subjected to solution treatment for 0 to 5 hours at the temperature of 1000 to 1300 ℃, and is subjected to aging treatment for 1 to 120 hours at the temperature of 400 to 700 ℃ after being cooled to room temperature by water.
Has the advantages that: the invention carries out reasonable component proportion on each alloy element, so that the alloy parent phase has a face-centered cubic structure, precipitates and precipitated phases are promoted to be precipitated in the alloy parent phase, and the precipitated phases can change the matrix parent phase into order, thus being beneficial to generating thermoelastic martensite phase transformation, effectively pinning dislocation and inhibiting dislocation slip. The strength and super-elasticity of the alloy are increased by controlling the rolling process to obtain strong texture. The strength of an austenite parent phase is improved by regulating and controlling solid solution and aging treatment, the content of a precipitated phase is increased, and the critical stress of stress-induced martensite phase transformation is reduced, so that the Fe-based super-elastic alloy with super elasticity, high strength and high hardness is obtained.
Drawings
FIG. 1 is a stress-strain curve of Fe-Ni-Co-Al-Dy superelasticity alloy of the present invention after aging for 24h, loaded-unloaded at room temperature;
FIG. 2 is a Fe-Ni-Co-Al-Dy super elastic alloy microstructure after aging of the inventive Fe-Ni-Co-Al-Dy super elastic alloy for 24h.
Detailed Description
The invention is described in further detail below with reference to the drawings and the detailed description.
Example 1
The method comprises the steps of selecting industrially used pure metal raw materials of iron, nickel, cobalt, aluminum and dysprosium, mixing the raw materials according to the atomic percentage content of Fe 43.45%, ni 28%, co 17%, al 11.5% and Dy 0.05%, smelting by using a vacuum arc smelting furnace under the protection of argon, uniformly mixing metal solutions by using a magnetic stirring technology in the smelting process, repeatedly smelting the alloy for 4 times in the smelting process, and finally performing suction casting to form a columnar part. The casting was homogenized for 2h at 1200 ℃ in a heat treatment and hot rolled from 20mm to 12mm at 1200 ℃. The hot rolled samples were water cooled to room temperature, cold rolled from 12mm to 1mm at room temperature and then aged at 600 ℃ for 24h.
The stress-strain curve obtained by loading and unloading the polycrystalline Fe-Ni-Co-Al-Dy super-elastic alloy prepared in the example at room temperature is shown in the attached drawing 1. As can be seen from the stress-strain curve shown in FIG. 1, the polycrystalline Fe-Ni-Co-Al-Dy superelastic alloy of this composition has a recoverable strain of 1.1% at room temperature.
The invention discloses a Fe-Ni-Co-Al-Dy super-elastic alloy and a preparation method thereof, wherein the expression of the super-elastic alloy is Fe a Ni b Co c Al d Dy e Wherein a, b, c, d, e respectively represent the atomic number percentage (at.%) of each corresponding element, and the following conditions are satisfied: a = 35-60, b = 18-38, c = 7-25, d = 5-18, e = 0.01-10, a + b + c + d + e =100. The preparation method of the alloy comprises smelting, rolling, solid solution and aging treatment. The super-elastic alloy of the invention regulates and controls the size and volume fraction of precipitated phases by adding rare earth elements and controlling the heat treatment mode and time. The precipitated phase can make the matrix parent phase ordered, is beneficial to generating thermoelastic martensite phase transformation, can pin dislocation and inhibit the plastic deformation of the alloy, thereby obtaining excellent superelasticity. The super-elastic alloy has the strength of over 1300MPa and the recoverable strain of 1.1 percent.
Claims (2)
1. A Fe-Ni-Co-Al-Dy super-elastic alloy is characterized by comprising the following components: feaNibCoAlddye, wherein a, b, c, d and e respectively represent atomic percent at.% of each corresponding element, and the following conditions are met: a =43.45,b =28,c =17,d =11.5,e =0.05,a + b + c + d + e =100, and the preparation method of the superelastic alloy comprises the following steps:
(1) According to the atomic percentage of each element in the super-elastic alloy, selecting metal iron particles, metal nickel particles, metal cobalt blocks, metal aluminum particles and metal dysprosium particles, and smelting and casting the metal iron particles, the metal nickel particles, the metal cobalt blocks, the metal aluminum particles and the metal dysprosium particles to form a casting; the smelting and forming process is carried out under the vacuum condition or under the protection of inert gas; in the smelting process, the metal solution needs to be fully stirred and mixed to ensure the uniformity of alloy components;
(2) Homogenizing the casting at 1200 ℃ for 2h in a heat treatment, and hot rolling from 20mm to 12mm at 1200 ℃;
(3) The hot rolled samples were water cooled to room temperature, cold rolled from 12mm to 1mm at room temperature, and then aged at 600 ℃ for 24h.
2. A method of producing the Fe-Ni-Co-Al-Dy superelastic alloy of claim 1, comprising the steps of:
(1) According to the atomic percentage of each element in the super-elastic alloy, selecting metal iron particles, metal nickel particles, metal cobalt blocks, metal aluminum particles and metal dysprosium particles, and smelting and casting the metal iron particles, the metal nickel particles, the metal cobalt blocks, the metal aluminum particles and the metal dysprosium particles to form a casting; the smelting and forming process is carried out under the vacuum condition or under the protection of inert gas; in the smelting process, the metal solution needs to be fully stirred and mixed to ensure the uniformity of alloy components;
(2) Homogenizing the casting at 1200 ℃ for 2h in a heat treatment, and hot rolling from 20mm to 12mm at 1200 ℃;
(3) The hot rolled samples were water cooled to room temperature, cold rolled from 12mm to 1mm at room temperature and then aged at 600 ℃ for 24h.
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| JPS61552A (en) * | 1984-06-11 | 1986-01-06 | Seiko Electronic Components Ltd | High elasticity alloy having high hardness |
| DE69129098T2 (en) * | 1990-12-18 | 1998-09-17 | Advanced Cardiovascular System | Process for producing a super-elastic guide part |
| JP5065904B2 (en) * | 2005-11-09 | 2012-11-07 | 独立行政法人科学技術振興機構 | Iron-based alloy having shape memory and superelasticity and method for producing the same |
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