Non-magnetic austenitic stainless steel

Abstract

A non-magnetic austenitic stainless steel is provided. [Solution] The non-magnetic austenitic stainless steel of the present invention is characterized by comprising, by weight, C: 0.01-0.1%, Si: 1.5% or less (excluding 0), Mn: 0.5-3.5%, Cr: 16-22%, Ni: 7-15%, Mo: 3% or less, N: 0.01-0.3%, and the balance being Fe and other unavoidable impurities, and by having a negative value for the following formula (1): Formula (1): 3*(Cr+Mo)+5*Si-65*(C+N)-2*(Ni+Mn)-28 In the above formula (1), Cr, Mo, Si, C, N, Ni, and Mn represent the content (wt %) of each alloy element.

Description

[Technical Field]

[0001] The present invention relates to a non-magnetic austenitic stainless steel, and more particularly to a non-magnetic austenitic stainless steel that can be used as a material for various electronic devices. [Background technology]

[0002] Recently, with the increasing use of smart devices with diverse functions, there has been an increasing demand for steel with reduced magnetic properties to reduce power loss and prevent malfunctions. 300 series stainless steel, which has a predominant austenite phase and is normally non-magnetic, is widely used as a material for electronic devices.

[0003] However, in typical STS304 or STS316 austenitic stainless steel, δ-ferrite is formed at a fraction of 1-5% during steelmaking / continuous casting. The formed δ-ferrite is a structure that induces magnetism, which can cause the final product to exhibit magnetism. Therefore, typical STS304 and STS316 austenitic stainless steels have the problem of not being able to maintain non-magnetic properties due to the inclusion of δ-ferrite. δ-ferrite can be decomposed by heat treatment in the temperature range of 1,300 to 1,400° C. However, the δ-ferrite may not be completely removed in the rolling and annealing processes and may remain in the structure, which causes a problem that the residual ferrite generates magnetism and makes it impossible to ensure non-magnetic properties. [Prior art documents] [Patent documents]

[0004] [Patent Document 1] Korean Patent Publication No. 10-2018-0068542 Summary of the Invention [Problem to be solved by the invention]

[0005] The present invention has been made to solve the above problems, and its object is to provide a non-magnetic austenitic stainless steel that can be used as a material for various electronic devices. [Means for solving the problem]

[0006] In order to achieve the above object, the non-magnetic austenitic stainless steel of the present invention is characterized by comprising, by weight percent, 0.01 to 0.1% C, 1.5% or less Si (excluding 0), 0.5 to 3.5% Mn, 16 to 22% Cr, 7 to 15% Ni, 3% or less Mo, 0.01 to 0.3% N, with the balance being Fe and other unavoidable impurities, and by the value of the following formula (1) being a negative value: Formula (1): 3*(Cr+Mo)+5*Si-65*(C+N)-2*(Ni+Mn)-28 In the above formula (1), Cr, Mo, Si, C, N, Ni, and Mn represent the content (wt %) of each alloy element.

[0007] The non-magnetic austenitic stainless steel of the present invention may further contain, by weight %, Cu: 2.5% or less.

[0008] Another non-magnetic austenitic stainless steel that can achieve the above object is characterized by containing, by weight, 0.01 to 0.1% C, 1.5% or less Si (excluding 0), 0.5 to 3.5% Mn, 16 to 22% Cr, 7 to 15% Ni, 3% or less Mo, 0.01 to 0.3% N, and the balance being Fe and other unavoidable impurities, and having a value of 70 or more for the following formula (2): Formula (2):ΣA5 / ΣA×100 In the above formula (2), ΣA5 is the area of ​​5 μm 2 is the sum of the areas of the ferrite particles below, and ΣA is the sum of the areas of all ferrite particles.

[0009] The non-magnetic austenitic stainless steel of the present invention may further contain, by weight %, Cu: 2.5% or less. The non-magnetic austenitic stainless steel of the present invention preferably has a thickness of 1 mm or less and a magnetic permeability of 1.02 or less. [Effects of the Invention]

[0010] According to the present invention, it is possible to provide a non-magnetic austenitic stainless steel that can be used as a material for various electronic devices by controlling the fraction of the ferrite phase that induces magnetism to a low level. According to the present invention, the fraction of the ferrite phase can be reduced by controlling the alloying elements to suppress the formation of ferrite or by accelerating the decomposition of ferrite through control of the microstructure. [Brief explanation of the drawings]

[0011] [Figure 1] 1 is a graph showing the change in ferrite fraction depending on the value of formula (1) in Table 1. [Figure 2] 10 is a graph showing the change in magnetic permeability depending on the value of formula (2) in Table 2. DETAILED DESCRIPTION OF THE INVENTION

[0012] A non-magnetic austenitic stainless steel according to one example of the present invention contains, by weight, 0.01 to 0.1% C, 1.5% or less Si (excluding 0), 0.5 to 3.5% Mn, 16 to 22% Cr, 7 to 15% Ni, 3% or less Mo, 0.01 to 0.3% N, and the remainder being Fe and other unavoidable impurities, and the value of the following formula (1) is a negative value. Formula (1): 3*(Cr+Mo)+5*Si-65*(C+N)-2*(Ni+Mn)-28 In the above formula (1), Cr, Mo, Si, C, N, Ni, and Mn represent the content (wt %) of each alloy element.

[0013] The following describes preferred embodiments of the present invention. However, the embodiments of the present invention can be modified into various other forms, and the technical concept of the present invention is not limited to the embodiments described below. Furthermore, the embodiments of the present invention are provided to more completely explain the present invention to those having average knowledge in the art. The terms used in the present invention are merely used to describe specific examples. Therefore, singular expressions include plural expressions unless the context clearly requires otherwise. Furthermore, it should be noted that the terms "comprise" or "have" used in the present invention are used to clearly indicate the presence of features, steps, functions, components, or combinations thereof described in the specification, and are not used to preliminarily exclude the presence of other features, steps, functions, components, or combinations thereof.

[0014] Unless otherwise defined, all terms used herein should be considered to have the same meaning as commonly understood by a person of ordinary skill in the art to which the present invention pertains. Therefore, unless clearly defined herein, specific terms should not be construed as having an overly ideal or formal meaning. For example, in this specification, the singular expression includes the plural expression unless there is a clear exception in the context. Furthermore, in this specification, the terms "about," "substantially," and the like are used to mean a numerical value or a value close to the numerical value when manufacturing and material tolerances inherent in the stated meaning are given, and are used to prevent unscrupulous infringers from unfairly exploiting the disclosure in which precise or absolute numerical values ​​are stated to aid in the understanding of the present invention.

[0015] A non-magnetic austenitic stainless steel according to one embodiment of the present invention contains, by weight, 0.01-0.1% C, 1.5% or less (excluding 0) Si, 0.5-3.5% Mn, 16-22% Cr, 7-15% Ni, 3% or less Mo, 0.01-0.3% N, and the balance being Fe and other unavoidable impurities. It may also contain 2.5% or less Cu. The reasons for limiting the alloy composition to the above will be specifically explained below. Unless otherwise specified, all of the following component compositions are in weight percent.

[0016] Carbon (C): 0.01~0.1% by weight C is a strong austenite phase stabilizing element that suppresses the increase in magnetism during solidification. In the present invention, C is preferably added in an amount of 0.01 wt% or more to achieve the austenite phase stabilizing effect. However, if the C content is excessive, it may combine with Cr to form carbides at the grain boundaries, which may locally reduce the Cr content around the grain boundaries and reduce corrosion resistance. Therefore, in order to ensure sufficient corrosion resistance, the upper limit of the C content in the present invention is preferably limited to 0.1 wt%.

[0017] Silicon (Si): 1.5% by weight or less (excluding 0%) Si is an element that improves corrosion resistance. However, Si is a ferrite phase stabilizing element that induces magnetism, and excessive Si content may promote the precipitation of intermetallic compounds such as the σ phase, which may degrade mechanical properties and corrosion resistance. Therefore, in the present invention, the upper limit of the Si content is preferably set to 1.5 wt %.

[0018] Manganese (Mn): 0.5 to 3.5% by weight Mn, like C and Ni, is an austenite phase stabilizer and is effective in strengthening non-magnetic properties. Therefore, in the present invention, it is preferable to add 0.5 wt% or more of Mn. However, excessive Mn content may form inclusions such as MnS, which may reduce corrosion resistance and surface gloss. Therefore, in the present invention, it is preferable to limit the upper limit of the Mn content to 3.5 wt%.

[0019] Chromium (Cr): 16 to 22% by weight Cr is a typical element that improves the corrosion resistance of stainless steels. In the present invention, Cr is added in an amount of 16 wt.% or more to ensure sufficient corrosion resistance. However, Cr is also a ferrite phase stabilizer that induces magnetism. Furthermore, excessive Cr content requires the inclusion of a large amount of Ni to achieve non-magnetic properties, which increases costs and promotes the formation of σ phase, resulting in reduced mechanical properties and corrosion resistance. For this reason, the upper limit of the Cr content is preferably set to 22 wt.%.

[0020] Nickel (Ni): 7 to 15% by weight Ni is the most powerful austenite phase stabilizing element, and in the present invention, Ni is preferably added in an amount of 7 wt% or more to obtain non-magnetic properties. However, since an increase in Ni content increases raw material costs, the upper limit of the Ni content is preferably limited to 15 wt%.

[0021] Molybdenum (Mo): 3% by weight or less Mo is an element that improves corrosion resistance. However, Mo is a ferrite phase stabilizing element, and if the Mo content is excessive, the formation of the σ phase is promoted, which may deteriorate the mechanical properties and corrosion resistance. Therefore, in the present invention, the upper limit of the Mo content is preferably limited to 3 wt %.

[0022] Nitrogen (N): 0.01 to 0.3% by weight N is an austenite phase stabilizing element, and in order to obtain non-magnetic properties in the present invention, it is preferable to add 0.01% by weight or more of N. However, an excessive N content reduces the hot workability of the steel and deteriorates the surface quality, so the upper limit of the N content is preferably limited to 0.3% by weight.

[0023] The non-magnetic austenitic stainless steel according to one embodiment of the present invention may further contain 2.5 wt % or less of Cu. The reasons for limiting the Cu content will be specifically explained below. Copper (Cu): 2.5% by weight or less Cu is an austenite-phase stabilizing element and can be used in place of expensive Ni. However, excessive Cu content forms a low-melting-point phase, which reduces hot workability and surface quality. Therefore, in the present invention, the upper limit of the Cu content is preferably limited to 2.5 wt% or less.

[0024] Typically, STS304 or 316 stainless steel has a microstructure primarily composed of austenite and a residual ferrite phase formed during steelmaking / continuous casting. The austenite phase has a face-centered cubic structure and is nonmagnetic, while ferrite has a body-centered cubic structure and is magnetic. Therefore, the fraction of the remaining ferrite phase makes it difficult to achieve the nonmagnetic properties desired by the present invention. Therefore, to achieve the nonmagnetic properties, the fraction of the ferrite phase, which induces magnetism, must be minimized. Specific technical means for achieving the nonmagnetic properties desired by the present invention will be described in detail below.

[0025] Control of alloy components The alloy composition has a significant effect on the fraction of the ferrite phase that is initially formed. For example, austenite-stabilizing elements such as Ni, Mn, C, and N decrease the fraction of the ferrite phase when added, while elements such as Cr and Mo increase the fraction of the ferrite phase. Taking this into consideration, the inventors have derived the following equation (1), which can control the fraction of the ferrite phase. Formula (1): 3*(Cr+Mo)+5*Si-65*(C+N)-2*(Ni+Mn)-28 In the above formula (1), Cr, Mo, Si, C, N, Ni, and Mn represent the content (wt %) of each alloy element. According to the present invention, when the value of formula (1) has a negative value, the fraction of the ferrite phase initially formed can be 0%.

[0026] Microstructure control Meanwhile, the ferrite phase remaining during steelmaking / continuous casting can be decomposed by a subsequent heat treatment process. The inventors have found that even when the value of Equation (1) is positive, the ferrite phase remains, resulting in the steel exhibiting magnetic properties, but the decomposition of the ferrite phase during the heat treatment process can be accelerated by controlling the microstructure. The accelerated decomposition of the ferrite phase is related to the size and distribution of the remaining ferrite phase through analysis, and the following Equation (2) was derived: Formula (2):ΣA5 / ΣA×100 In the above formula (2), ΣA5 is the area of ​​5 μm 2 where ΣA is the sum of the areas of the ferrite particles below, and ΣA is the sum of the areas of the entire ferrite particles. That is, equation (2) is the ratio of 5 μm to the sum of the areas of the entire ferrite particles. 2 This means the percentage of the sum of the areas of the following fine ferrite particles. According to one example of the present invention, it is preferable to control the value of the above formula (2) to be 70 or more. As described above, the present invention can accelerate the decomposition of the ferrite phase in the heat treatment process by controlling the sum of the areas of the fine ferrite particles to be high. As a result, the magnetic permeability after heat treatment can be reduced to 1.02 or less, and in particular, the magnetic permeability of a steel sheet having a thickness of 1 mm or less can be reduced to 1.02 or less.

[0027] The size distribution of the ferrite phase can be controlled by various processes, as long as the value of the above formula (2) is 70 or more. For example, it can be controlled through a forging or rolling process, and can be controlled by variously adjusting the reduction ratio, the number of rolling passes, etc. However, it should be noted that the above examples are merely listed to facilitate understanding of the present invention, and are not intended to limit the technical concept of the present invention. According to the present invention, as described above, the proportion of magnetic ferrite phase can be minimized by controlling the alloy composition, the microstructure, or both the alloy composition and the microstructure. As a result, the present invention can provide a non-magnetic austenitic stainless steel that can be used as a material for various electronic devices. The present invention will be described in more detail below with reference to examples. However, it should be noted that the following examples are intended to illustrate and explain the present invention in more detail, and are not intended to limit the scope of the present invention, as the scope of the present invention is determined by the matters described in the claims and matters that can be reasonably inferred therefrom.

[0028] {Example} First, the cast slab was reheated at a temperature of 1,250°C for 2 hours, and then the reheated slab was hot rolled to a thickness of 6 mm and annealed at a temperature of 1,150°C. The values ​​of formula (1) in Table 1 are values ​​derived by substituting the weight percentages of the alloying elements in Table 1 into the following formula (1). Formula (1): 3*(Cr+Mo)+5*Si-65*(C+N)-2*(Ni+Mn)-28 The ferrite fractions in Table 1 were determined by measuring the ferrite fraction of annealed hot-rolled coils using a contact ferrite scope. If no value was displayed upon contact, the ferrite fraction was determined to be 0%.

[0029] [Table 1]

[0030] As shown in Table 1, steel types 17 to 30 satisfied the alloy composition range defined in the present invention, and the value of formula (1) was negative, so the ferrite fraction was 0%. On the other hand, steel types 1 to 16, although each alloy component was within the composition range defined in the present invention, had a positive value for formula (1), so ferrite remained even after heat treatment.

[0031] Figure 1 is a graph showing the change in ferrite fraction depending on the value of formula (1) in Table 1. As shown in Figure 1, it can be seen that the ferrite fraction tends to increase when the value of formula (1) changes from 0 to a positive value. In other words, Figure 1 shows that the ferrite fraction tends to become 0% as a result of controlling the value of formula (1) to have a negative value in the present invention. From the above results, it can be seen that in the present invention, by controlling the value of formula (1) to have a negative value, the ferrite fraction can be controlled to 0%, and as a result, the desired non-magnetic properties can be ensured. Meanwhile, for steel types 1 to 16, in which the ferrite fraction exceeds 0.0%, the decomposition of ferrite can be accelerated through control of the microstructure, thereby controlling the magnetic permeability to a low level. The evaluation results in Table 2 below are for steel types 1 to 16 in Table 1, in which the ferrite fraction exceeds 0.0% and the ferrite phase remains. The results are for steel sheets in which steel types 1 to 16 were obtained by cold rolling a 6 mm thick hot-rolled coil to a thickness of 1 mm or less and then annealing.

[0032] The values ​​of equation (2) in Table 2 were derived through image analysis using an optical microscope after cold rolling. The ferrite fractions in Table 2 were determined by measuring the ferrite fraction of annealed cold-rolled coils using a contact ferrite scope. If no value was displayed upon contact, the ferrite phase fraction was determined to be 0%. The magnetic permeability μ in Table 2 was measured using a contact type magnetic permeability measuring instrument, Ferromaster. Steel types 1 to 16 were cold rolled to a thickness of 1 mm or less using various reduction ratios.

[0033] [Table 2]

[0034] As shown in Table 2, when the microstructure is controlled so that the value of formula (2) is 70 or more, all of the residual ferrite is decomposed during annealing after rolling, resulting in a ferrite fraction of 0.0%, and as a result, a magnetic permeability of 1.02 or less can be ensured. On the other hand, when the value of formula (2) is less than 70, the residual ferrite is not completely decomposed during annealing after rolling, resulting in a magnetic permeability value exceeding 1.02.

[0035] Figure 2 is a graph showing the change in magnetic permeability depending on the value of formula (2) in Table 2. As shown in Figure 2, it can be seen that the magnetic permeability tends to decrease from 1.02 when the value of formula (2) changes from 70 or more. In other words, it can be seen from Figure 2 that as a result of controlling the value of formula (2) to 70 or more in the present invention, a magnetic permeability of 1.02 or less tends to be ensured. From the above results, it can be seen that the present invention can accelerate the decomposition of residual ferrite during annealing after cold rolling and ensure the desired nonmagnetic properties by controlling the value of formula (2) to be 70 or more, even when residual ferrite remains after hot rolling and annealing.

[0036] Although the preferred embodiments of the present invention have been described above, the present invention is not limited thereto, and a person having ordinary skill in the art will understand that various changes and modifications can be made without departing from the concept and scope of the claims set forth below. [Industrial Applicability]

[0037] The non-magnetic austenitic stainless steel according to the present invention can be used as a material for various electronic devices.

Claims

1. A non-magnetic austenitic stainless steel sheet produced by cold rolling a steel sheet consisting of, by weight percent, C: 0.01 to 0.1%, Si: 1.5% or less (excluding 0), Mn: 0.5 to 3.5%, Cr: 16 to 22%, Ni: 7 to 15%, Mo: 3% or less, N: 0.01 to 0.3%, and the balance being Fe and other unavoidable impurities, and then annealing the steel sheet; In the state before the annealing heat treatment after the cold rolling, the value of the following formula (2) is 70 or more, A non-magnetic austenitic stainless steel sheet characterized in that after the annealing heat treatment, the sheet has a thickness of 1 mm or less and a magnetic permeability of 1.02 or less. Formula (2): ΣA ５ / ΣA × 100 (In the above formula (2), ΣA ５ has an area of ​​5 μm ２ where ΣA is the sum of the areas of the ferrite particles below, and ΣA is the sum of the areas of all the ferrite particles).

2. 2. The non-magnetic austenitic stainless steel sheet according to claim 1, further comprising, by weight percent, Cu: 2.5% or less.

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