Cobalt-rich multi-component alloy with amorphous induced plasticity effect and preparation method thereof

Abstract

The invention discloses a cobalt-rich multi-component alloy with an amorphous induced plasticity effect and a preparation method of the cobalt-rich multi-component alloy, and belongs to the technical field of metal materials. The cobalt-rich multi-component alloy is composed of the following components of, by atomic percent, 14%-16% of Fe, 14%-16% of Ni, 14%-16% of Cr, 3%-7% of Al and the balance Co. The prepared multi-component alloy forms a uniform face-centered cubic structure after being annealed, a plastic deformation mechanism of transformation from a crystal to an amorphous state can be activated in the later stage of room-temperature static tensile deformation, and good ductility and machinability are kept.

Description

Technical Field

[0001] This invention belongs to the field of metallic materials technology, specifically relating to a cobalt-rich multicomponent alloy with amorphous induced plasticity effect and its preparation method. Background Technology

[0002] The mechanical properties of metallic materials are closely related to their plastic deformation mechanisms, with strength and plasticity being important performance indicators for evaluating metallic structural materials. Therefore, the key to designing high-strength and high-toughness metallic materials lies in activating different plastic deformation mechanisms through reasonable composition design and microstructure control, thereby simultaneously improving the material's strength and plasticity.

[0003] In recent years, multi-component alloys have provided a new research direction for the development of high-strength and high-toughness metallic materials. The high-entropy effect caused by their multi-component characteristics not only helps to stabilize single solid solution structures, but also provides a broad design space for systematically controlling plastic deformation mechanisms (dislocation slip, twinning, and phase transformation) through their huge tunable composition. For example, through composition control, the main plastic deformation mechanism can be transformed from dislocation slip in equiatomic FeMnCoCrNi multi-component alloys [cited in Acta Materialia: F. Otto, A. Dlouhý, C. Somsen, et al, Acta Materialia 61 (2013) 5743–5755] to non-equiatomic Fe... 50 Mn 30 Co 10 Cr 10 Phase transformation induced plasticity of multicomponent alloys [Cited in Nature: Z. Li, KGPradeep, Y. Deng, et al, Nature 534 (2016) 227–230].

[0004] Therefore, it is necessary to find a new plastic deformation mechanism to develop alloys with higher strength and toughness. Summary of the Invention

[0005] The purpose of this section is to outline some aspects of embodiments of the present invention and to briefly describe some preferred embodiments. Simplifications or omissions may be made in this section, as well as in the abstract and title of this application, to avoid obscuring the purpose of these documents; however, such simplifications or omissions should not be construed as limiting the scope of the invention.

[0006] In view of the problems existing in the above and / or prior art, the present invention is proposed.

[0007] One objective of this invention is to provide a cobalt-rich multicomponent alloy with an amorphous induced plasticity effect, which exhibits an amorphous transformation plastic deformation mechanism during quasi-static tensile testing at room temperature and thus possesses higher strength and toughness.

[0008] To solve the above-mentioned technical problems, the present invention provides the following technical solution: a cobalt-rich multi-component alloy with amorphous induced plasticity effect, which is composed of the following components by atomic percentage: Fe 14~16%, Ni 14~16%, Cr 14~16%, Al 3~7%, with the balance being Co.

[0009] As a preferred embodiment of the cobalt-rich multicomponent alloy with amorphous induced plasticity effect of the present invention, the alloy has the following characteristics:

[0010] (i) After annealing, it has a single-phase face-centered cubic structure;

[0011] (ii) In the later stages of plastic deformation, amorphous induced plasticity can be induced;

[0012] (iii) Yield strength is 240~460 MPa;

[0013] (iv) Tensile strength is 740~880 MPa;

[0014] (v) Elongation after fracture is 60-80%.

[0015] Another object of the present invention is to provide a method for preparing a cobalt-rich multicomponent alloy with amorphous induced plasticity effect as described above, comprising,

[0016] Each component is prepared according to the atomic ratio of the alloy components as described above, melted under vacuum or inert gas protection, and cast into a billet. After hot rolling, homogenization, cold rolling and annealing, a cobalt-rich multi-component alloy with amorphous induced plasticity effect is obtained.

[0017] As a preferred embodiment of the preparation method of the cobalt-rich multi-component alloy with amorphous induced plasticity effect of the present invention, the melting includes melting in an induction furnace, an electric arc furnace or a suspension furnace, at a temperature of 1450~2200℃, and holding at that temperature for 0.01~1 hours.

[0018] As a preferred embodiment of the preparation method of the cobalt-rich multi-component alloy with amorphous induced plasticity effect of the present invention, wherein: the melting process maintains the vacuum degree in the furnace at 1~0.0001 Pa or maintains the inert gas pressure in the furnace at 0.000001~100 MPa.

[0019] As a preferred embodiment of the preparation method of the cobalt-rich multi-component alloy with amorphous induced plasticity effect of the present invention, wherein: the hot rolling adopts multi-pass hot rolling, the hot rolling temperature is 800~1250℃, the single-pass rolling reduction is ≤25%, and the total rolling reduction is 30~90%.

[0020] As a preferred embodiment of the preparation method of the cobalt-rich multi-component alloy with amorphous induced plasticity effect of the present invention, wherein: the homogenization process is carried out at a temperature of 1100~1300℃ for a time of 30~600 min.

[0021] As a preferred embodiment of the preparation method of the cobalt-rich multi-component alloy with amorphous induced plasticity effect of the present invention, the homogenization treatment is carried out under vacuum or a protective atmosphere, wherein the protective atmosphere is selected from argon, nitrogen or helium.

[0022] As a preferred embodiment of the preparation method of the cobalt-rich multi-component alloy with amorphous induced plasticity effect of the present invention, wherein: the cold rolling adopts multi-pass cold rolling, the rolling reduction per pass is ≤25%, and the total rolling reduction is 40~90%.

[0023] As a preferred embodiment of the preparation method of the cobalt-rich multi-component alloy with amorphous induced plasticity effect of the present invention, wherein: the annealing is performed at a temperature of 800~1000℃ and a holding time of 5~300 min; the annealing is carried out under vacuum or a protective atmosphere, wherein the protective atmosphere is selected from argon, nitrogen or helium.

[0024] Compared with the prior art, the present invention has the following beneficial effects:

[0025] The multi-component alloy prepared by this invention forms a uniform face-centered cubic structure after annealing. In the later stage of plastic deformation under quasi-static tension at room temperature, it can undergo a transformation from crystalline to amorphous, maintaining good elongation and machinability. This provides new design ideas and technical approaches for developing alloys with higher strength and toughness. Attached Figure Description

[0026] To more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings used in the description of the embodiments will be briefly introduced below. Obviously, the drawings described below are only some embodiments of the present invention. For those skilled in the art, other drawings can be obtained based on these drawings without creative effort. Wherein:

[0027] Figure 1 The XRD pattern of the multi-component alloy material with amorphous induced plasticity effect provided in Example 1 of the present invention;

[0028] Figure 2This is a scanning electron backscattering morphology image of a multi-component alloy material with amorphous induced plasticity effect provided in Embodiment 1 of the present invention;

[0029] Figure 3 The room temperature quasi-static tensile mechanical property curves of the multi-component alloy material with amorphous induced plasticity effect provided in Example 1 of the present invention;

[0030] Figure 4 This is a scanning transmission electron micrograph of a multi-component alloy material with amorphous induced plasticity effect in the later stage of tensile deformation, provided in Embodiment 1 of the present invention.

[0031] Figure 5 This is a high-resolution transmission image of a multi-component alloy material with amorphous induced plasticity effect in the later stage of tensile deformation, provided in Embodiment 1 of the present invention.

[0032] Figure 6 The XRD pattern of the multi-component alloy material with amorphous induced plasticity effect provided in Example 2 of the present invention;

[0033] Figure 7 This is a scanning electron backscattering morphology image of a multi-component alloy material with amorphous induced plasticity effect provided in Embodiment 2 of the present invention;

[0034] Figure 8 The room temperature quasi-static tensile mechanical property curves of the multi-component alloy material with amorphous induced plasticity effect provided in Example 2 of the present invention;

[0035] Figure 9 This is a scanning transmission microstructure image of a multi-component alloy material with amorphous induced plasticity effect in the later stage of tensile deformation, provided in Embodiment 2 of the present invention.

[0036] Figure 10 The XRD pattern of the multi-component alloy material with amorphous induced plasticity effect provided in Example 3 of the present invention;

[0037] Figure 11 This is a scanning electron backscattering morphology image of a multi-component alloy material with amorphous induced plasticity effect provided in Embodiment 3 of the present invention;

[0038] Figure 12 The room temperature quasi-static tensile mechanical property curves of the multi-component alloy material with amorphous induced plasticity effect provided in Example 3 of the present invention;

[0039] Figure 13 This is a scanning transmission electron micrograph of a multi-component alloy material with amorphous induced plasticity effect in the later stage of tensile deformation, provided in Example 3 of the present invention.

[0040] Figure 14 This is a scanning electron backscattering topography image provided in Comparative Example 1 of the present invention;

[0041] Figure 15 The room temperature quasi-static tensile mechanical property curves provided in Embodiment 1 of the present invention. Detailed Implementation

[0042] To make the above-mentioned objects, features and advantages of the present invention more apparent and understandable, the specific embodiments of the present invention will be described in detail below with reference to the examples in the specification.

[0043] Many specific details are set forth in the following description in order to provide a full understanding of the invention. However, the invention may also be practiced in other ways different from those described herein, and those skilled in the art can make similar extensions without departing from the spirit of the invention. Therefore, the invention is not limited to the specific embodiments disclosed below.

[0044] Secondly, the term "one embodiment" or "embodiment" as used herein refers to a specific feature, structure, or characteristic that may be included in at least one implementation of the present invention. The phrase "in one embodiment" appearing in different places in this specification does not necessarily refer to the same embodiment, nor is it a single or selective embodiment that is mutually exclusive with other embodiments.

[0045] Unless otherwise specified, all raw materials used in the examples are commercially available.

[0046] Example 1

[0047] (1) According to the chemical formula Co 50 Fe 15 Ni 15 Cr 15 Al5 (atomic percentage) is used for ingredient mixing, and the raw materials use blocks corresponding to each pure element with a purity greater than 99.9%;

[0048] (2) Place the prepared raw materials in a copper crucible and melt them in an electric arc furnace. First, introduce high-purity argon gas into the crucible for gas washing, then evacuate to a low vacuum of less than 5 Pa, and then evacuate to a high vacuum of 5 × 10 Pa. -3 Below 1600°C, 5 MPa high-purity argon gas was introduced as a protective gas, the melting temperature was 1600°C, the holding time was 10 min, and the melting was repeated 4 times to obtain the molten alloy ingot.

[0049] (3) The alloy ingot is subjected to multi-pass hot rolling at a temperature of 900°C, with a single rolling reduction of 10% and a total rolling reduction of 50%.

[0050] (4) The hot-rolled alloy block is subjected to high-temperature homogenization treatment under vacuum (vacuum degree is 10). -2 The temperature was 1200℃, the homogenization time was 2 hours, and then water quenching was performed.

[0051] (5) The alloy block after high temperature homogenization is subjected to multi-pass room temperature rolling, with a single pass reduction of 10% and a total reduction of 70%;

[0052] (6) Anneal the cold-rolled alloy sheet under vacuum (vacuum degree is 10). -2 The annealing temperature was 900℃ and the annealing time was 30 min, resulting in a multi-component alloy material with amorphous induced plasticity effect.

[0053] The morphology of the obtained multi-component alloy material exhibiting amorphous induced plasticity was observed, such as... Figure 1 and 2 As shown. Figure 1 The XRD pattern of a multi-component alloy material exhibiting amorphous induced plasticity effect. Figure 2 This is a scanning electron backscattering (SPR) image of a multi-component alloy exhibiting amorphous-induced plasticity. A room-temperature quasi-static tensile test was performed on the obtained multi-component alloy exhibiting amorphous-induced plasticity, and the microstructure after deformation was analyzed, such as... Figures 3-5 As shown. Figure 3 The Schneider-Schneider-Static Mechanical Property Curves for Multicomponent Alloys Exhibiting Amorphous Induced Plasticity Figure 4 and Figure 5 This is a scanning transmission electron micrograph of a multi-component alloy material exhibiting amorphous induced plasticity during the later stages of plastic deformation.

[0054] Depend on Figure 1 It is evident that the obtained multi-component alloy material exhibiting amorphous induced plasticity has a single face-centered cubic microstructure, composed of... Figure 2 As can be seen, the alloy grains are uniform after annealing, with an average grain size of 18.2 μm. Figure 3 As can be seen, the yield strength of the multi-component alloy material with amorphous induced plasticity effect obtained in this embodiment is approximately 303 MPa, the tensile strength is approximately 770 MPa, and the elongation after fracture is approximately 78%. Figure 4 It is evident that deformed amorphous bands appeared in the alloy after deformation, indicating that the amorphous-induced plasticity effect was activated in the later stages of deformation. Figure 5 The high-resolution transmission images further confirm the presence of deformed amorphous zones.

[0055] Example 2

[0056] (1) According to the chemical formula Co 50 Fe 15 Ni 15 Cr 15 Al5 (atomic percentage) is used for ingredient mixing, and the raw materials use blocks corresponding to each pure element with a purity greater than 99.9%;

[0057] (2) Place the prepared raw materials in a copper crucible and melt them in an electric arc furnace. First, introduce high-purity argon gas into the crucible for gas washing, then evacuate to a low vacuum of less than 5 Pa, and then evacuate to a high vacuum of 5 × 10 Pa. -3 Below 1600°C, 5 MPa high-purity argon gas was introduced as a protective gas, the melting temperature was 1600°C, the holding time was 5 min, and the melting was repeated 5 times to obtain the molten alloy ingot.

[0058] (3) The smelted alloy ingot is subjected to multiple hot rolling processes at a temperature of 950°C, with a single rolling reduction of 10% and a total rolling reduction of 50%.

[0059] (4) The hot-rolled alloy block is subjected to high-temperature homogenization treatment under vacuum (vacuum degree is 10). -2 The temperature was 1200℃, the homogenization time was 3 hours, and then water quenching was performed.

[0060] (5) Anneal the cold-rolled alloy sheet under vacuum (vacuum degree is 10). -2 The alloy block, homogenized at high temperature, is subjected to multi-pass room temperature cold rolling, with a single-pass reduction of 20% and a total reduction of 70%.

[0061] (6) The cold-rolled alloy sheet is annealed under vacuum (vacuum degree is 10). -2 The annealing temperature was 1000℃, and the annealing time was 30 min. A multi-component alloy material with amorphous induced plasticity effect was obtained.

[0062] The morphology of the obtained multi-component alloy material exhibiting amorphous induced plasticity was observed, such as... Figure 6-9 As shown. Figure 6 The XRD pattern of a multi-component alloy material exhibiting amorphous induced plasticity effect. Figure 7 This is a scanning electron backscattering morphology image of a multi-component alloy material exhibiting amorphous induced plasticity. Figure 8 The room temperature quasi-static tensile mechanical property curves of multi-component alloys exhibiting amorphous induced plasticity effects are shown. Figure 9 This is a scanning transmission electron micrograph of a multi-component alloy material exhibiting amorphous induced plasticity after plastic deformation.

[0063] Depend on Figure 6 It is evident that the obtained multi-component alloy material exhibiting amorphous induced plasticity has a single face-centered cubic structure. Figure 7 It can be seen that the alloy grains are uniform after annealing, with an average grain size of 51.0 μm.

[0064] The room temperature quasi-static mechanical properties of the obtained multi-component alloy material with amorphous induced plasticity effect were tested. Figure 8As can be seen, the yield strength of the multi-component alloy material with amorphous induced plasticity effect obtained in this embodiment is approximately 246 MPa, the tensile strength is approximately 745 MPa, and the elongation after fracture is approximately 71%. Figure 9 It can be seen that an amorphous induced plastic effect can occur after plastic deformation.

[0065] Example 3

[0066] (1) According to the chemical formula Co 50 Fe 15 Ni 15 Cr 15 Al5 (atomic percentage) is used for ingredient mixing, and the raw materials use blocks corresponding to each pure element with a purity greater than 99.9%;

[0067] (2) Place the prepared raw materials in a copper crucible and melt them in an electric arc furnace. First, introduce high-purity argon gas into the crucible for gas washing, then evacuate to a low vacuum of less than 5 Pa, and then evacuate to a high vacuum of 5 × 10 Pa. -3 Below 100 MPa, 5 MPa high-purity argon gas was introduced as a protective gas. The melting temperature was 1700℃, and the temperature was held for 3 minutes. The melting was carried out under vacuum conditions, and the melting was repeated 3 times to obtain the melted alloy ingot.

[0068] (3) The smelted alloy ingot is subjected to multiple hot rolling processes at a temperature of 1000℃, with a single rolling reduction of 15% and a total rolling reduction of 60%.

[0069] (4) The hot-rolled alloy block is subjected to high-temperature homogenization treatment under vacuum (vacuum degree is 10). -2 The temperature was 1200℃, the homogenization time was 4 hours, and then water quenching was performed.

[0070] (5) The alloy block after high temperature homogenization is subjected to multi-pass room temperature rolling, with a single pass reduction of 15% and a total reduction of 60%;

[0071] (6) The cold-rolled alloy sheet is annealed under vacuum (vacuum degree is 10). -2 The annealing temperature was 800℃ and the annealing time was 30 min, resulting in a multi-component alloy material with amorphous induced plasticity effect.

[0072] The morphology of the obtained multi-component alloy material exhibiting amorphous induced plasticity was observed, such as... Figure 10 , 11 As shown. Figure 10 The XRD pattern of a multi-component alloy material exhibiting amorphous induced plasticity effect. Figure 11 This is a scanning electron backscattering morphology image of a multi-component alloy material exhibiting amorphous induced plasticity.

[0073] Depend on Figure 10 It is evident that the obtained multi-component alloy material exhibiting amorphous induced plasticity has a single face-centered cubic structure. Figure 11 It can be seen that the alloy completely recrystallizes after annealing, with an average grain size of 5.1 μm.

[0074] The mechanical properties of the obtained multi-component alloy material exhibiting amorphous induced plasticity were tested. The room temperature quasi-static stress-strain curve of the multi-component alloy material with amorphous induced plasticity obtained in Example 3 is shown below. Figure 12 As shown. Figure 12 As can be seen, the yield strength of the multi-component alloy material with amorphous induced plasticity effect obtained in this embodiment is about 456 MPa, the tensile strength is about 872 MPa, and the elongation after fracture is about 60%.

[0075] Comparative Example 1

[0076] (1) According to the chemical formula Co 50 Fe 15 Ni 15 Cr 15 Al5 (atomic percentage) is used for ingredient mixing, and the raw materials use blocks corresponding to each pure element with a purity greater than 99.9%;

[0077] (2) Place the prepared raw materials in a copper crucible and melt them in an electric arc furnace. First, introduce high-purity argon gas into the crucible for gas washing, then evacuate to a low vacuum of less than 5 Pa, and then evacuate to a high vacuum of 5 × 10 Pa. -3 Below 1800°C, 5 MPa high-purity argon gas was introduced as a protective gas. The melting temperature was 1800°C, and the temperature was held for 10 minutes. The melting was carried out under vacuum conditions, and the melting was repeated 3 times to obtain the melted alloy ingot.

[0078] (3) The smelted alloy ingot is subjected to multiple hot rolling processes at a temperature of 950°C, with a single rolling reduction of 15% and a total rolling reduction of 55%.

[0079] (4) The hot-rolled alloy block is subjected to high-temperature homogenization treatment under vacuum (vacuum degree is 10). -2 The temperature was 1200℃, the homogenization time was 1.5 hours, and then water quenching was performed.

[0080] (5) The alloy block after high temperature homogenization is subjected to multi-pass room temperature rolling, with a single pass reduction of 15% and a total reduction of 70%;

[0081] (6) The cold-rolled alloy sheet is annealed under vacuum (vacuum degree is 10). -2 The annealing temperature was 600℃ and the annealing time was 30 min, resulting in the comparative alloy material 1.

[0082] The morphology of the obtained comparative alloy material 1 was observed, such as... Figure 14 As shown. Mechanical properties of the obtained comparative alloy material 1 were tested. (As shown...) Figure 15 As shown.

[0083] Depend on Figure 14 It is evident that comparative material 1 exhibits a partially recrystallized structure. Figure 15 As can be seen, the yield strength of the multi-component alloy material with amorphous induced plasticity effect obtained in this embodiment is about 1652 MPa, the tensile strength is about 1700 MPa, and the elongation after fracture is about 7.3%.

[0084] Comparative Example 2

[0085] (1) According to the chemical formula Co 25 Fe 75 The ingredients are prepared according to (atomic percentage), using bulk materials corresponding to each pure element, with a purity greater than 99.9%;

[0086] (2) Place the prepared raw materials in a copper crucible and melt them in an electric arc furnace. First, introduce high-purity argon gas into the crucible for gas washing, then evacuate to a low vacuum of less than 5 Pa, and then evacuate to a high vacuum of 5 × 10 Pa. -3 Below 1650°C, 5 MPa high-purity argon gas was introduced as a protective gas. The melting temperature was 1650°C, and the temperature was held for 15 minutes. The melting was carried out under vacuum conditions, and the melting was repeated 3 times to obtain the melted alloy ingot.

[0087] (3) The smelted alloy ingot is subjected to multiple hot rolling processes at a temperature of 950°C, with a single rolling reduction of 15% and a total rolling reduction of 55%.

[0088] (4) The hot-rolled alloy block is subjected to high-temperature homogenization treatment under vacuum (vacuum degree is 10). -1 The temperature was 1150℃, the homogenization time was 1.5 hours, and then water quenching was performed.

[0089] (5) The alloy block after high temperature homogenization is subjected to multi-pass room temperature rolling, with a single pass reduction of 10% and a total reduction of 65%;

[0090] (6) The cold-rolled alloy sheet is annealed under vacuum (vacuum degree is 10). -2 The comparative alloy material was obtained by annealing at 900℃ for 30 min (Pa). Mechanical properties of the obtained comparative alloy material were tested, and the elongation was 38%.

[0091] Comparative Example 3

[0092] (1) According to the chemical formula Co 50 Fe 50The ingredients are prepared according to (atomic percentage), using bulk materials corresponding to each pure element, with a purity greater than 99.9%;

[0093] (2) Place the prepared raw materials in a copper crucible and melt them in an electric arc furnace. First, introduce high-purity argon gas into the crucible for gas washing, then evacuate to a low vacuum of less than 5 Pa, and then evacuate to a high vacuum of 5 × 10 Pa. -3 Below 1650°C, 5 MPa high-purity argon gas was introduced as a protective gas. The melting temperature was 1650°C, and the temperature was held for 15 minutes. The melting was carried out under vacuum conditions, and the melting was repeated 3 times to obtain the melted alloy ingot.

[0094] (3) The smelted alloy ingot is subjected to multiple hot rolling processes at a temperature of 950°C, with a single rolling reduction of 15% and a total rolling reduction of 55%.

[0095] (4) The hot-rolled alloy block is subjected to high-temperature homogenization treatment under vacuum (vacuum degree is 10). -1 The temperature was 1150℃, the homogenization time was 1.5 hours, and then water quenching was performed.

[0096] (5) The alloy block after high temperature homogenization is subjected to multi-pass room temperature rolling, with a single pass reduction of 10% and a total reduction of 65%;

[0097] (6) The cold-rolled alloy sheet is annealed under vacuum (vacuum degree is 10). -2 The comparative alloy material was obtained by annealing at 900℃ for 30 min (Pa). Mechanical properties of the obtained comparative alloy material were tested, and the elongation was 12%.

[0098] In the multi-component alloy material with amorphous induced plasticity effect prepared by the present invention, the alloy billet is hot rolled to effectively eliminate defects (such as micropores and microcracks) generated in the alloy during melting and casting; then homogenization treatment can further promote the uniform distribution of each component in the alloy; and through subsequent cold rolling and annealing, a fully recrystallized microstructure can be formed.

[0099] It should be noted that the above embodiments are only used to illustrate the technical solutions of the present invention and are not intended to limit it. Although the present invention has been described in detail with reference to preferred embodiments, those skilled in the art should understand that modifications or equivalent substitutions can be made to the technical solutions of the present invention without departing from the spirit and scope of the technical solutions of the present invention, and all such modifications or substitutions should be covered within the scope of the claims of the present invention.

Claims

1. A cobalt-rich multicomponent alloy exhibiting amorphous induced plasticity, characterized in that: Based on atomic percentage, it consists of the following components: Fe 14~16%, Ni 14~16%, Cr 14~16%, Al 3~7%, with the balance being Co.

2. The cobalt-rich multicomponent alloy with amorphous induced plasticity effect as described in claim 1, characterized in that: The alloy has the following properties: (i) After annealing, it has a single-phase face-centered cubic structure; (ii) In the later stages of plastic deformation, amorphous induced plasticity can be induced; (iii) Yield strength is 240~460 MPa; (iv) Tensile strength is 740~880 MPa; (v) Elongation after fracture is 60-80%.

3. The method for preparing the cobalt-rich multi-component alloy with amorphous induced plasticity effect as described in claim 1 or 2, characterized in that: include, According to the atomic ratio of the alloy components described in claim 1, each component is prepared, melted under vacuum or inert gas protection conditions, and cast into a billet. After hot rolling, homogenization, cold rolling and annealing, a cobalt-rich multi-component alloy with amorphous induced plasticity effect is obtained.

4. The method for preparing the cobalt-rich multicomponent alloy with amorphous induced plasticity effect as described in claim 3, characterized in that: The smelting process includes smelting in an induction furnace, electric arc furnace, or suspension furnace at a temperature of 1450~2200℃ and holding at that temperature for 0.01~1 hour.

5. The method for preparing the cobalt-rich multicomponent alloy with amorphous induced plasticity effect as described in claim 4, characterized in that: The smelting process maintains a vacuum level of 1 to 0.0001 Pa or an inert gas pressure of 0.000001 to 100 MPa in the furnace.

6. The method for preparing the cobalt-rich multicomponent alloy with amorphous induced plasticity effect as described in any one of claims 3 to 5, characterized in that: The hot rolling process employs multi-pass hot rolling, with a hot rolling temperature of 800~1250℃, a single pass reduction of ≤25%, and a total reduction of 30~90%.

7. The method for preparing the cobalt-rich multicomponent alloy with amorphous induced plasticity effect as described in any one of claims 3 to 5, characterized in that: The homogenization process is carried out at a temperature of 1100~1300℃ for a time of 30~600 min.

8. The method for preparing the cobalt-rich multicomponent alloy with amorphous induced plasticity effect as described in claim 7, characterized in that: The homogenization process is carried out under a vacuum or a protective atmosphere, the protective atmosphere being selected from argon, nitrogen or helium.

9. The method for preparing the cobalt-rich multicomponent alloy with amorphous induced plasticity effect as described in any one of claims 3 to 5 and 8, characterized in that: The cold rolling process employs multi-pass cold rolling, with each pass having a reduction of ≤25% and a total reduction of 40~90%.

10. The method for preparing the cobalt-rich multicomponent alloy with amorphous induced plasticity effect as described in any one of claims 3 to 5 and 8, characterized in that: The annealing is performed at a temperature of 800~1000℃ for a holding time of 5~300 min. The annealing is carried out under vacuum or a protective atmosphere, the protective atmosphere being selected from argon, nitrogen or helium.

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