Tensile magnetostrictive functional alloy and preparation method thereof

Abstract

The invention provides a functional alloy capable of obtaining permanent magnet performance (stretching induced magnetic effect) through stretching and a preparation method of the functional alloy. The expression of the functional alloy is FeaNibCocAld, a, b, c and d respectively represent the atomic percentage (at.%) of corresponding elements, a = 40-50, b = 25-35, c = 10-20, d = 5-15, and a + b + c + d = 100. The preparation method of the functional alloy comprises the steps of smelting, rolling and heat treatment. The BCC magnetic particles are precipitated and separated out through rolling and heat treatment processes, so that the BCC magnetic particles have the special performance of generating magnetic force under the action of tensile strain. And the number of BCC magnetic particle precipitates can be controlled by adjusting the heat treatment temperature, so that the magnetic field intensity of the alloy after breaking is regulated and controlled. The maximum magnetic induction intensity of the functional alloy after tensile fracture is increased to 122 Gs from 2Gs of an original alloy through rolling and heat treatment processes, and the maximum magnetic induction intensity of the functional alloy after tensile fracture can be regulated and controlled within a certain range by adjusting the heat treatment temperature. The effect of obtaining the permanent magnet performance through stretching is found for the first time, a method for regulating and controlling the magnetic induction intensity is found, stress changes and magnetic signal changes can correspond to each other through the phenomenon, and therefore the method is expected to be applied to some specific equipment.

Description

Technical Field

[0001] The present invention relates to a stretch-induced magnetic functional alloy and a preparation method thereof, belonging to the technical field of the interdisciplinary of force and magnetism. Background Art

[0002] As is well known, except for natural permanent magnet stones, ferromagnetic materials must be magnetized by applying an external magnetic field to obtain permanent magnetic properties. The magnetic domain theory points out that in order to obtain the permanent magnetic properties of ferromagnetic materials, an external magnetic field must be applied to make the magnetic moments in the ferromagnetic materials rotate, the magnetic domain walls move, and the magnetic domains rotate in the same direction as the external magnetic field. So far, there has been no report on obtaining permanent magnetic properties through tensile strain. In the present invention, we report the experimental results of obtaining permanent magnets only through tensile strain without applying an external magnetic field. The present invention promotes the precipitation of a large number of BCC magnetic particles through a large deformation rolling and heat treatment process, providing a prerequisite for the stretch-induced magnetic effect. The prepared alloy can convert mechanical energy (or mechanical displacement information) into magnetic force (or magnetic information), and is a mechanical force and magnetic information conversion functional material. Moreover, the functional material can adjust its maximum magnetic induction intensity after fracture within a certain range through changes in the heat treatment process, which not only provides a new direction for us to explore the correlation between force and magnetism, but also is expected to have broad application prospects in high-tech fields such as ocean exploration and development technologies, micro-displacement drive, vibration reduction and anti-vibration, noise reduction and anti-noise systems, automation technologies, valves, pumps, etc. Summary of the Invention

[0003] The present invention provides a stretch-induced magnetic functional alloy and a preparation method thereof. The alloy can obtain a significant increase in magnetic induction intensity after fracture through a large deformation rolling and heat treatment process.

[0004] To achieve the above object, the present invention is realized through the following technical solutions:

[0005] An Fe-Ni-Co-Al stretch-induced magnetic alloy, the composition of the stretch-induced magnetic alloy is Fe a Ni b Co c Al d , where a, b, c, and d respectively represent the atomic percentages (at.%) of the corresponding elements, a = 40 - 50, b = 25 - 35, c = 10 - 20, d = 5 - 15, and a + b + c + d = 100.

[0006] The molecular formula of the Fe-Ni-Co-Al stretch-induced magnetic alloy is preferably Fe (40～50) Ni (25～35) Co (10～20) Al (5～15) , and more preferably Fe (41～43) Ni(30～33) Co (15～20) Al (9～12) Most preferably Fe 43 Ni 30 Co 16 Al 11 。

[0007] A preparation method of an Fe-Ni-Co-Al tensile magnetostrictive alloy, comprising the following steps:

[0008] (1) Alloy melting. Weigh iron, nickel, cobalt, and aluminum in proportion, and perform arc melting in a non-consumable vacuum arc furnace to obtain a metal ingot for standby.

[0009] (2) Rolling. Cut the metal ingot into appropriate sizes and then perform cold rolling with a large deformation amount of ≥50%.

[0010] (3) Heat treatment. Keep the cold-rolled sample at a specific temperature for a specific duration and then rapidly cool it.

[0011] Preferably, the metals iron, nickel, cobalt, and aluminum are metal elements, and the purity of the metals iron, nickel, cobalt, and aluminum is preferably greater than 99.9%.

[0012] Preferably, the vacuum degree during melting is less than 3×10 -3 Pa, and the melting process is carried out under argon protection.

[0013] Preferably, the metal ingot during melting is flipped and remelted more than 3 times to ensure uniform alloy composition.

[0014] Preferably, the rolling process is preferably 50% - 99%, more preferably 80% - 95%.

[0015] The temperature of the solution treatment is preferably 300°C - 1200°C, more preferably 500°C - 800°C, and most preferably 700°C.

[0016] The heat preservation duration is preferably 30 Min - 120 Min, more preferably 30 Min - 60 Min, and most preferably 47 Min.

[0017] The present invention provides an Fe-Ni-Co-Al tensile magnetostrictive alloy and a preparation method thereof. Compared with the prior art, the advantages are as follows:

[0018] (1) The alloy prepared by the present invention is subjected to rolling + heat treatment with a large deformation amount of ≥50%, so that the Fe-Ni-Co-Al functional alloy gradually precipitates nano- to micron-sized BCC magnetic precipitate particles, enabling it to obtain permanent magnetic properties only by stretching without the need for an external magnetic field. This phenomenon provides a new idea for our research field of exploring the relationship between force and magnetism.

[0019] (2) By adjusting the heat treatment temperature to control the number and size of the precipitated BCC particles, the magnetic induction intensity of the magnetostrictive alloy can be regulated, enabling this functional material to be applied to certain specific fields where mechanical information is associated with magnetic information. Description of the Drawings

[0020] Figure 1 X-ray diffraction patterns of the tensile magneto-functional alloys prepared in Example 1, Example 2, Example 3, Example 4, Example 5, Example 6 and Comparative Example 1 of the present invention;

[0021] Figure 2 Microstructure morphology of the tensile magneto-functional alloy prepared in Comparative Example 1 of the present invention;

[0022] Figure 3 Microstructure morphology of the tensile magneto-functional alloys prepared in Example 1, Example 2, Example 3, Example 4, Example 5 and Example 6 of the present invention before stretching (where Figures a, b, c, d, e, f correspond to Example 1, Example 2, Example 3, Example 4, Example 5 and Example 6 respectively);

[0023] Figure 4 Histogram of the maximum magnetic induction intensity of the tensile magneto-functional alloys prepared in Comparative Example 1, Example 1, Example 2, Example 3, Example 4, Example 5 and Example 6 of the present invention before stretching and after tensile fracture. Detailed Description of the Invention

[0024] To make the objectives, technical solutions and advantages of the embodiments of the present invention clearer, the technical solutions in the embodiments of the present invention will be clearly and completely described below in conjunction with the embodiments of the present invention. Obviously, the described embodiments are some, but not all, of the embodiments of the present invention. All other embodiments obtained by those of ordinary skill in the art based on the embodiments of the present invention without creative efforts shall fall within the protection scope of the present invention.

[0025] Example 1:

[0026] (1) According to the molecular formula Fe 43 Ni 30 Co 16 Al 11 Weigh 133.3722 g of metallic iron with a purity of 99.9%, 97.7820 g of nickel, 52.3637 g of cobalt and 16.4819 g of aluminum, and put them into a non-consumable vacuum melting furnace for melting. When the furnace chamber vacuum reaches 3.0×10 -3 Pa, argon is filled for protection, and the melting is repeated more than 5 times to obtain an alloy sample.

[0027] (2) The cast alloy was cold rolled at room temperature using a two-roll rolling mill of laboratory scale model YS-S-W100 with a deformation of 95%.

[0028] (3) The rolled specimens were kept at 500°C for 47 min and then water quenched.

[0029] (4) The heat-treated sample was cut into a size of 1 mm × 3 mm × 10 mm (dog bone shape).

[0030] Embodiment 2:

[0031] (1) According to the molecular formula Fe 43 Ni 30 Co 16 Al 11 Weigh 133.3722g of 99.9% pure iron, 97.7820g of nickel, 52.3637g of cobalt and 16.4819g of aluminum and place them in a non-consumable vacuum melting furnace for melting. When the furnace vacuum reaches 3.0×10 -3 After Pa, argon gas was filled in for protection and the melting was repeated for more than 5 times to obtain the alloy sample.

[0032] (2) The cast alloy was cold rolled at room temperature using a two-roll rolling mill of laboratory scale model YS-S-W100 with a deformation of 95%.

[0033] (3) The rolled specimens were kept at 600°C for 47 min and then water quenched.

[0034] (4) The heat-treated sample was cut into a size of 1 mm × 3 mm × 10 mm (dog bone shape).

[0035] Embodiment 3:

[0036] (1) According to the molecular formula Fe 43 Ni 30 Co 16 Al 11 Weigh 133.3722g of 99.9% pure iron, 97.7820g of nickel, 52.3637g of cobalt and 16.4819g of aluminum and place them in a non-consumable vacuum melting furnace for melting. When the furnace vacuum reaches 3.0×10 -3 After Pa, argon gas was filled in for protection and the melting was repeated for more than 5 times to obtain the alloy sample.

[0037] (2) The cast alloy was cold rolled at room temperature using a two-roll rolling mill of laboratory scale model YS-S-W100 with a deformation of 95%.

[0038] (3) The rolled specimens were kept at 700°C for 47 min and then water quenched.

[0039] (4) Cut the heat-treated specimen into a size of 1 mm × 3 mm × 10 mm (dog-bone shape).

[0040] Example 4:

[0041] (1) According to the molecular formula Fe 43 Ni 30 Co 16 Al 11 Weigh 133.3722 g of metallic iron with a purity of 99.9%, 97.7820 g of nickel, 52.3637 g of cobalt, and 16.4819 g of aluminum. Put them into a non-consumable vacuum melting furnace for melting. When the furnace chamber vacuum reaches 3.0×10 -3 Pa, then charge argon for protection and melt repeatedly for more than 5 times to obtain an alloy sample.

[0042] (2) At room temperature, cold-roll the as-cast alloy of the specimen with a two-roll rolling mill of laboratory scale model YS-S-W100, and the deformation amount is 95%.

[0043] (3) Keep the rolled specimen at a temperature of 1000 °C for 47 min, and then water quench.

[0044] (4) Cut the heat-treated specimen into a size of 1 mm × 3 mm × 10 mm (dog-bone shape).

[0045] Example 5:

[0046] (1) According to the molecular formula Fe 43 Ni 30 Co 16 Al 11 Weigh 133.3722 g of metallic iron with a purity of 99.9%, 97.7820 g of nickel, 52.3637 g of cobalt, and 16.4819 g of aluminum. Put them into a non-consumable vacuum melting furnace for melting. When the furnace chamber vacuum reaches 3.0×10 -3 Pa, then charge argon for protection and melt repeatedly for more than 5 times to obtain an alloy sample.

[0047] (2) At room temperature, cold-roll the as-cast alloy of the specimen with a two-roll rolling mill of laboratory scale model YS-S-W100, and the deformation amount is 95%.

[0048] (3) Keep the rolled specimen at a temperature of 1100 °C for 47 min, and then water quench.

[0049] (4) Cut the heat-treated specimen into a size of 1 mm × 3 mm × 10 mm (dog-bone shape).

[0050] Example 6:

[0051] (1) According to the molecular formula Fe 43 Ni 30 Co 16 Al 11 Weigh 133.3722 g of metallic iron with a purity of 99.9%, 97.7820 g of nickel, 52.3637 g of cobalt, and 16.4819 g of aluminum. Put them into a non-consumable vacuum melting furnace for melting. After the furnace chamber vacuum reaches 3.0×10 -3 Pa, fill it with argon for protection and melt it repeatedly for more than 5 times to obtain an alloy sample.

[0052] (2) At room temperature, cold roll the as-cast alloy with a two-roll rolling mill of model YS-S-W100 on a laboratory scale, and the deformation amount is 95%.

[0053] (3) Keep the rolled sample at a temperature of 1200 °C for 47 Min, and then water quench it.

[0054] (4) Cut the heat-treated sample into a specification of 1 mm×3 mm×10 mm (dog bone shape).

[0055] Comparative Example 1:

[0056] (1) According to the molecular formula Fe 43 Ni 30 Co 16 Al 11 Weigh 133.3722 g of metallic iron with a purity of 99.9%, 97.7820 g of nickel, 52.3637 g of cobalt, and 16.4819 g of aluminum. Put them into a non-consumable vacuum melting furnace for melting. After the furnace chamber vacuum reaches 3.0×10 -3 Pa, fill it with argon for protection and melt it repeatedly for more than 5 times to obtain an alloy sample.

[0057] (2) Cut the heat-treated sample into a specification of 1 mm×3 mm×10 mm (dog bone shape).

[0058] Microstructure morphology characterization and magnetic induction intensity test

[0059] 1. Determine the crystal structure of the stretch-induced magnetic functional alloy of Fe 43 Ni 30 Co 16 Al 11 prepared in Examples 1-6 of the present invention and Comparative Example 1.

[0060] Determination method: Use an X-ray diffractometer to characterize the crystal structure of the sample. The sample to be characterized is the debris filed by a file and ground into powder with a mortar, and data is collected with a step size of 0.02 degrees.

[0061] A. For the alloys prepared in Examples 1-6 and Comparative Example 1, their crystal structures were tested, and the test results are as follows Figure 1 shown. The as-cast alloy exhibited diffraction peaks of a single FCC phase. After the preparation process of large deformation + heat treatment, obvious BCC phase diffraction peaks were observed in Examples 1, 2, 3, and 4.

[0062] 2. Characterize the microstructural morphologies of the Fe 43 Ni 30 Co 16 Al 11 tensile magnetic functional alloys prepared in Examples 1-6 and Comparative Example 1:

[0063] Determination method: Use an optical microscope to characterize the microstructural morphologies of the specimens of the Fe 43 Ni 30 Co 16 Al 11 functional alloys prepared in Comparative Example 1 and Examples 1-6. Before specimen characterization, first grind the specimens with 400-mesh sandpaper along the same direction. After the scratches are completely consistent, replace with 1000-mesh sandpaper and grind at a 90° rotation. Then, successively replace with 1500, 2000, and 3000-mesh sandpaper and grind according to the above steps. Finally, polish with diamond polishing paste of model W1.5 until the surface is smooth and scratch-free. Finally, etch with Keller's reagent with a composition of 1 ml HF + 2.5 ml HNO3 + 1.5 ml HCl + 95 ml H2O for 5 minutes.

[0064] B. For the alloys prepared in Comparative Example 1 and Examples 1-6, their metallographic microstructural morphologies were characterized, as shown in Figure 2 and Figure 3 respectively. It can be seen that through the large deformation heat treatment process, the BCC formed in the original specimens of the specimens shows a tendency to dissolve, and a large number of new fine precipitate particles are precipitated.

[0065] 3. Determine the maximum magnetic induction intensities of the Fe 43 Ni 30 Co 16 Al 11 tensile magnetic functional alloys prepared in Examples 1-6 of the present invention and Comparative Example 1 before and after tensile fracture:

[0066] Determination method: Use a gaussmeter (model KANETEC, TM-901EXP) to test the maximum magnetic induction intensities of the Fe 43 Ni 30 Co 16 Al 11 functional alloys prepared in Examples 1-6 and Comparative Example 1 before and after tensile fracture.

[0067] C. For the Fe 43 Ni 30 Co 16 Al 11 functional alloys prepared in Examples 1-6 and Comparative Example 1, the maximum magnetic induction intensity before and after tensile fracture was tested, and the test results are as Figure 4 shown. It can be seen from the figure that: the maximum magnetic induction intensity of Example 1 before tensile was 2 Gs, and the maximum magnetic induction intensity increased to 25 Gs after tensile fracture; the maximum magnetic induction intensity of Example 2 before tensile was 2 Gs, and the maximum magnetic induction intensity increased to 65 Gs after tensile fracture; the maximum magnetic induction intensity of Example 3 before tensile was 4 Gs, and the maximum magnetic induction intensity increased to 122 Gs after tensile fracture; the maximum magnetic induction intensity of Example 4 before tensile was 3 Gs, and the maximum magnetic induction intensity increased to 21 Gs after tensile fracture; the maximum magnetic induction intensity of Example 5 before tensile was 3 Gs, and the maximum magnetic induction intensity increased to 9 Gs after tensile fracture; the maximum magnetic induction intensity of Example 6 before tensile was 3 Gs, and the maximum magnetic induction intensity increased to 5 Gs after tensile fracture; the maximum magnetic induction intensity of Comparative Example 1 before tensile was 2 Gs, and the maximum magnetic induction intensity remained 2 Gs after tensile fracture. By comparing Examples 1-6, it can be seen that: with the increase of the heat treatment temperature, the maximum magnetic induction intensity of the Fe 43 Ni 30 Co 16 Al 11 functional alloy after tensile fracture showed a trend of first increasing and then decreasing.

[0068] D. According to Examples 1-6 and Comparative Example 1, it can be known that the maximum magnetic induction intensity of the Fe 43 Ni 30 Co 16 Al 11 functional alloy of the present invention before tensile was relatively low, being 2 Gs - 4 Gs. The maximum magnetic induction intensity of the as-cast specimen did not change after being pulled apart, while after cold rolling and heat treatment processes with a large deformation amount, the maximum magnetic induction intensity of this functional alloy increased more or less after tensile fracture. Especially for the Fe 43 Ni 30 Co 16 Al 11 functional alloy in Example 3, after cold rolling with a large deformation amount of 95% and heat treatment at 700 °C for 47 min, its maximum magnetic induction intensity increased from 4 Gs before tensile to 122 Gs after being pulled apart. The maximum magnetic induction intensity before and after tensile fracture of the functional alloys prepared in Examples 1-6 and Comparative Example 1 under different processing techniques is shown in Table 1.

[0069] Table 1. Preparation processes of each group of specimens and maximum magnetic induction intensity before and after tensile fracture

[0070]

[0071] As can be seen from the above embodiments, the present invention provides a stretchable magneto-functional alloy. After undergoing large deformation rolling and heat treatment processes, the maximum magnetic induction intensity after tensile fracture of this functional alloy has increased significantly. By adjusting the heat treatment temperature, the control of the maximum magnetic induction intensity of the functional alloy after tensile fracture within a certain range is achieved. Among them, for the Fe 43 Ni 30 Co 16 Al 11 magneto-functional alloy, the maximum magnetic induction intensity increases sharply from 4 Gs before tensile fracture to 122 Gs after tensile fracture. The present invention provides a preparation method for the said Fe 43 Ni 30 Co 16 Al 11 magneto-functional alloy. Through melting, rolling, and heat treatment, a stretchable magneto-functional alloy can be obtained. The unique functionality of this alloy and its adjustable maximum magnetic induction intensity within a certain range have opened up new ideas for the future combination of force and magnetism.

[0072] It should be noted that in this article, relational terms such as first and second are only used to distinguish one entity or operation from another entity or operation, and do not necessarily require or imply any actual relationship or order between these entities or operations. Moreover, the term "comprising", "including" or any other variant thereof is intended to cover non-exclusive inclusion, so that a process, method, article or device including a series of elements not only includes those elements, but also includes other elements not expressly listed, or also includes elements inherent to such process, method, article or device. Without further limitation, an element defined by the statement "including a..." does not exclude the existence of additional identical elements in the process, method, article or device including the said element.

[0073] The above embodiments are only used to illustrate the technical solutions of the present invention, rather than to limit them; although the present invention has been described in detail with reference to the foregoing embodiments, those of ordinary skill in the art should understand that they can still modify the technical solutions recorded in the foregoing embodiments, or perform equivalent replacements for some of the technical features; and these modifications or replacements do not cause the essence of the corresponding technical solutions to deviate from the technical solutions of the various embodiments of the present invention.

Claims

1. A stretchable magnetofunctional alloy, characterized in that: The composition of this functional alloy is Fe a Ni b Co c Al d , where a, b, c, and d represent the atomic percentage (at.%) of the corresponding element, a=40-50, b=25-35, c=10-20, d=5-15, and a+b+c+d=100.

2. The Fe-Ni-Co-Al functional alloy according to claim 1, wherein the preparation method comprises the following steps: (1) Melting. Metal iron, nickel, cobalt and aluminum are weighed in proportion and arc-melted in a non-consumable vacuum arc furnace to obtain metal ingots for use. (2) Rolling. (3) Heat treatment.

3. The method for preparing a Fe-Ni-Co-Al tensile magnetometallic alloy according to claim 2, characterized in that: The purity of the metal iron, nickel, cobalt and aluminum is equal to or greater than 99.9%.

4. The method for preparing a Fe-Ni-Co-Al tensile magnetometallic alloy according to claim 2, characterized in that: The vacuum degree of arc melting in step (1) is less than 3×10 -3 Pa, and the smelting process is carried out under argon protection.

5. The method for preparing a Fe-Ni-Co-Al tensile magnetometallic alloy according to claim 2, characterized in that: The metal ingot subjected to arc melting in step (1) is repeatedly melted more than three times to ensure uniform alloy composition.

6. The method for preparing a Fe-Ni-Co-Al tensile magnetometallic alloy according to claim 2, characterized in that: The rolling process in step (2) is: a large deformation of ≥50%.

7. The method for preparing a Fe-Ni-Co-Al tensile magnetometallic alloy according to claim 2, characterized in that: The heat treatment process in step (2) is: heat treatment at 300-1200° C. for 30 minutes to 120 minutes.

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