KR101379076B1 - Lean duplex stainless steel and manufacturing method using the same - Google Patents

Abstract

The present invention relates to a high ductility, high strength lean duplex stainless steel and a method for producing the same. Lean duplex stainless steel according to the present invention is in weight%, C: greater than 0 to 0.08 or less, Si: greater than 0 to 0.5 or less, Mn: 4 to 6, Cr: 19 to 23, Ni: greater than 0 to 0.3 or less, N : 0.18 to 0.40, balance Fe and other unavoidable impurities, the chromium equivalent (Cr _eq ) value defined by the following formula is in the range of 19.0 to 23.75, the nickel equivalent (Ni _eq ) value is in the range of 3.48 to 10.14.
Cr _eq =% Cr + 1.5% Si
Ni _eq =% Ni + 30% C + 18% N + 0.1% Mn-0.01 (% Mn) ²

Description

BACKGROUND OF THE INVENTION 1. Field of the Invention [0001] The present invention relates to a stainless steel duplex stainless steel,

The present invention relates to a lean duplex stainless steel and a method of manufacturing the same, and more particularly to a high strength, high-ductility lean duplex stainless steel and a method of manufacturing the same.

In general, austenitic stainless steel having good workability and corrosion resistance contains iron (Fe) as a base metal and contains Cr and Ni as main raw materials. In addition, austenitic stainless steels have been developed into various steel types suitable for various applications by adding other elements such as Mo and Cu.

These austenitic stainless steels are steel grades excellent in corrosion resistance and corrosion resistance, and contain 8% or more of Ni component by weight in terms of low carbon. For this reason, there is a problem in that the price is unstable due to the large fluctuation in cost caused by the rise in Ni price, resulting in inferior competitiveness. Therefore, in order to compensate for this, it is necessary to develop a new steel grade that can secure corrosion resistance equal to or higher than that of the austenitic stainless steel grade while lowering the Ni content.

Accordingly, the duplex stainless steel, which is a stainless steel having a microstructure composed of a mixture of an austenite phase and a ferrite phase, exhibits both the austenitic and ferritic characteristics. Various duplex stainless steels have been proposed to date, and examples thereof include US Pat. Nos. 5,624,504 and 61,641. One of the duplex stainless steels used in high corrosion resistance environments is Allegheny Ludlum's Al2205 (UNS S 31803 or S32205) consisting of 22% Cr, 5.5% Ni, 3% Mo and 0.16% N components.

In the case of the duplex stainless steel, it provides excellent corrosion resistance in various corrosive environments, and exhibits superior corrosion resistance than that of the austenitic stainless steel such as AISI's 304 and 316. In the case of such a duplex stainless steel, not only the manufacturing cost is increased by expensive elements such as Ni and Mo, but also the Ni and Mo are consumed, which leads to a decrease in price competitiveness with other steel grades.

Accordingly, in recent years, lean duplex stainless steel, which has eliminated expensive alloying elements such as Ni and Mo and added low-cost alloying elements in place of these elements, has been further increased. Interest in the trend is increasing.

An object of the present invention is to provide a lean duplex stainless steel and its manufacturing method that can reduce the cost by adjusting the content of components such as Ni, Si, Mo, and Cu so as to ensure a proper corrosion resistance or more than austenitic stainless steel It is done.

In addition, the present invention, by controlling the phase ratio of austenite and ferrite, Cr equivalent and Ni equivalent during annealing heat treatment to secure a high ductility of 50% or more and a high tensile strength of 800MPa or more at the same time, significantly improve the workability An object of the present invention is to provide a lean duplex stainless steel and a method of manufacturing the same.

Lean duplex stainless steel according to the present invention is in weight%, C: greater than 0 to 0.08 or less, Si: greater than 0 to 0.5 or less, Mn: 4 to 6, Cr: 19 to 23, Ni: greater than 0 to 0.3 or less, N : 0.18 to 0.40, balance Fe and other unavoidable impurities, the chromium equivalent (Cr _eq ) value defined by the following formula is in the range of 19.0 to 23.75, the nickel equivalent (Ni _eq ) value is in the range of 3.48 to 10.14.

Cr _eq =% Cr + 1.5% Si

Ni _eq =% Ni + 30% C + 18% N + 0.1% Mn-0.01 (% Mn) ²

In this case, the stainless steel may be composed of a ferrite phase of 20 to 65% and an austenite phase of 35 to 80% by volume fraction.

In addition, the stainless steel may have an elongation of 50% or more.

In addition, the stainless steel may have a tensile strength of 800MPa or more.

The manufacturing method of lean duplex stainless steel according to the present invention is in weight%, C: greater than 0 to 0.08 or less, Si: greater than 0 to 0.5 or less, Mn: 4 to 6, Cr: 19 to 23, Ni: greater than 0 to 0.3 or less , N: 0.18 to 0.40, balance Fe and other unavoidable impurities, and the chromium equivalent (Cr _eq ) value defined by the following formula is in the range of 19.0 to 23.75, the nickel equivalent (Ni _eq ) in the range of 3.48 to 10.14 Annealing heat treatment of the phosphorus duplex stainless steel slab in the range of 1030 to 1220 ° C.

Cr _eq =% Cr + 1.5% Si

Ni _eq =% Ni + 30% C + 18% N + 0.1% Mn-0.01 (% Mn) ²

Here, the annealing heat treatment may be performed for 2 to 40 minutes.

According to the present invention, by controlling the content of Ni, Si, Cu, and Mo alloy components of expensive elements, it is possible to remarkably improve resource savings and raw material costs. In addition, by controlling the process conditions such as the phase fraction and annealing heat treatment to secure an elongation of 50% or more, the workability can be improved to be used for forming and bending purposes. In addition, by securing a high strength of 800MPa or more, it is possible to reduce the weight specific gravity by manufacturing the material in a thin material can be produced in a lightweight material.

1 is a graph showing the nominal strain and nominal stress of the material according to the present invention heat-treated at 1100 ℃.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS Reference will now be made in detail to embodiments of the present invention and other details necessary for those skilled in the art to understand the present invention with reference to the accompanying drawings. However, the present invention may be embodied in various different forms within the scope of the claims, and thus the embodiments described below are merely exemplary, regardless of expression.

In the following description of the present invention, a detailed description of known functions and configurations incorporated herein will be omitted when it may make the subject matter of the present invention rather unclear.

The present invention is a lean duplex stainless steel in which the content of expensive alloying elements such as Ni, Mo, Si, Cu and the like is reduced among duplex stainless steel having two phases of austenite phase and ferrite phase. Lean duplex stainless steel can maintain corrosion resistance more than equivalent to that of 304 stainless steel and 316 steel, which are common austenitic stainless steels. In addition, it is possible to secure an elongation of at least austenitic stainless steel and to secure high strength compared to 304 and 316. The high strength, high ductile lean duplex stainless steel of the present invention can be used, for example, in corrosive environments or in general products for forming, and can be used in strips, bars, plates, sheets, pipes. It can be manufactured and used as a product, such as a pipe or a tube.

The lean duplex stainless steel is economical because it has a low Ni content while ensuring corrosion resistance equivalent to 304 steel and 316 steel, which are austenitic stainless steels. In addition, it has been spotlighted as a steel material for industrial facilities such as freshwater, pulp, paper, and chemical facilities requiring high strength and easy corrosion resistance. Such lean duplex stainless steels are disclosed in Japanese Patent Laid-Open Nos. 61-056267, WO 02/027056 and WO 96/18751. Among them, lean duplex stainless steel disclosed in Japanese Patent Application Laid-Open No. 61-56267 and WO 02/027056 is standardized by ASTM A240, the former is S32304 (representative component 23Cr-4Ni-0.13N), and the latter is S32101 (representative component 21Cr-1.5Ni-5Mn-0.22N).

S32205 duplex stainless steel, one of the representative steel grades of duplex stainless steel having a mixed structure of austenite phase and ferrite phase at room temperature, contains a large amount of Cr, Mo, and N components to secure high corrosion resistance. In order to secure the phase ratio, the Ni component contains 5% or more by weight. In addition, disclosed in Korean Patent Laid-Open Publication No. 2006-0074400, S81921 steel, which is standardized by ASTM A240, contains expensive alloying elements such as 2.5% and 2.4% by weight of Ni and Mo, respectively.

These duplex stainless steels are designed for cold workability, i.e., strengthening of corrosion resistance rather than formability, providing superior corrosion resistance than that required in certain applications. In addition, the stress corrosion resistance is also superior to the design requirements to provide a technical solution, but ductility, which is a factor related to workability, is inferior to that of austenitic stainless steel. This causes a lot of restrictions on applications in various industrial fields that require molding, bending, and the like, and there are aspects that are not economically feasible. Therefore, the development of industrial equipment and various duplex stainless steels for forming and processing, which ensures corrosion resistance equivalent to or higher than that of 304, 304L and 316 steels while reducing manufacturing costs by eliminating these expensive elements, in particular, ensures workability, that is, ductility equal to 304. This is necessary.

In addition, in the case of austenitic stainless steel having excellent moldability or elongation, expensive Ni is 4% or more, and in the case of 316 series steel, Mo is about 2%. For this reason, the material cost is very high when manufacturing stainless steel, and Ni, Mo, etc. are consumed in large quantities. Accordingly, in order to reduce the Ni, Mo and the like, the duplex stainless steel in which the ferrite phase and the austenitic phase coexist as a method of securing elongation and corrosion resistance equivalent to that of the austenitic stainless steel.

In Japanese Patent Laid-Open No. 11-071643, an austenitic and ferritic stainless steel having excellent elongation is controlled by limiting the amount of Ni added to less than 0.1 to 1% and controlling the stability index of austenite in the two-phase structure steel in the range of 40 to 115. The steel sheet manufacturing method is presented. In order to ensure excellent workability of the austenitic and ferritic stainless steels, Korean Laid-Open Patent Publication No. 2010-0097741 discloses essentially containing 0.5 to 5% of Ni, 0.01 to 2% of Si, and 0.5 to 5% of Cu. Steel is disclosed, and Korean Patent Laid-Open Publication No. 2006-0127107 discloses a steel essentially containing Si of 4% or less and Ni of 3% or less.

Hereinafter, the lean duplex stainless steel which consists of an austenite phase and a ferrite phase of this invention is demonstrated in detail.

According to the present invention, it is possible to secure a high elongation of not less than 50% and a tensile strength of not less than 800 MPa while providing excellent general properties of the duplex stainless steel made of austenitic ferrite. That is, the present invention is a low-carbon chromium stainless steel, containing high nitrogen, and while controlling the alloy components to increase the content of Mn and to exclude expensive alloying elements such as Ni, Si, Mo, Cu, etc. to the residual level . In addition, by optimizing the process conditions such as annealing heat treatment conditions, by adjusting the phase ratio of austenite and ferrite during annealing heat treatment, it is possible to produce a high ductility high austenite ferrite two-phase steel. Lean duplex stainless steel according to the present invention can significantly reduce the raw material cost in the manufacturing cost, greatly improve the price competitiveness, improve the elongation can be used for a variety of applications, such as molding, complex bending processing other than simple bending.

In the following, the reasons for limiting the components of the present invention will be described. (Hereinafter, weight% is simply expressed as%.)

C is an austenite forming element and is an element effective for increasing the material strength by solid solution strengthening. However, when excessively added, it easily bonds with carbide-forming elements such as Cr, which is effective for corrosion resistance at the ferrite-austenite phase boundary, thereby lowering the Cr content around the grain boundary and reducing corrosion resistance. It is preferable to add in the range of%.

Si acts as a deoxidation effect and a ferrite stabilizing element, so some is added. However, if excessive, deteriorates the mechanical properties related to corrosion resistance and impact toughness and is limited to the range of 0 to 0.5%.

N is an element that greatly contributes to stabilization of the austenite phase together with Ni in duplex stainless steel, and is one of the elements that thicken on the austenite phase during annealing heat treatment. Therefore, the increase in N content may result in increased corrosion resistance and higher strength. However, when the N content exceeds 0.4% or more, it is difficult to stably manufacture the steel due to surface defects caused by the occurrence of blow holes, pin holes, and the like during casting. In addition, it is economically disadvantageous to use means such as pressure dissolution. On the other hand, when the amount of nitrogen is added less than 0.18%, the concentration of nitrogen on the austenite phase is too low, which increases the stability of the austenite phase. In addition, if the N content is too low, it is difficult to secure an appropriate phase ratio, and it is difficult to secure strength due to a lack of solid solution strengthening by N. Therefore, the N content is preferably limited to 0.18 to 0.40%.

Mn is an element that increases the deoxidizer and nitrogen solubility, and is an austenite forming element, and when used for replacing expensive Ni, its content should be increased to 4% or more. If the content of Mn is too low, it is difficult to control the phase fraction, and the solubility of N added is low, and sufficient solid solution of N cannot be obtained at normal pressure. In addition, the addition of a large amount of Mn is effective in the solid solubility of nitrogen, but combines with S in steel to form MnS, not only lowers the corrosion resistance but also worsens the hot workability, limiting the Mn content to 6% or less. Therefore, the Mn content is preferably limited to 4-6%.

Cr is a ferrite stabilizing element together with Si, which plays a major role in securing ferrite phase of two-phase stainless steel and is an essential element for securing corrosion resistance. Increasing the content increases the corrosion resistance, but the content of expensive Ni or other austenite forming elements should be increased to maintain the phase ratio. Accordingly, the content of Cr is limited to 19 to 23% to ensure corrosion resistance of STS304 or more while maintaining the phase ratio of the two-phase stainless steel.

Ni, together with Mn and N, is an austenite stabilizing element and plays a major role in securing the austenite phase of duplex stainless steel. Instead of reducing the costly Ni content as much as possible to reduce cost, the austenitic phase forming elements Mn and N may be increased to sufficiently maintain the balance of phase fraction due to the reduction of Ni. In particular, Ni can be managed in the range of more than 0 to 0.3% in scrap used in steelmaking, unless intentionally added.

At this time, it is preferable that the austenitic ferrite duplex stainless steel according to the present invention satisfies the constitution with a 20 to 65 ferrite phase and an 80 to 35% austenite phase by volume fraction. This is because when the austenite phase fraction is less than 35%, the amount of deformed organic martensite transformation occurring during deformation of the austenite phase is small, so that the ductility and tensile strength contributions are small, so that the desired elongation and strength cannot be sufficiently obtained. From the viewpoint of high ductility, the austenite phase fraction is preferably 80% or less. However, when the austenite fraction exceeds 80%, surface cracks, etc., occur during hot rolling, resulting in deterioration of hot workability, and lack of austenite phase thickening of N and Mn, which contributes to the stability of austenite, during deformation. Metamorphic organic martensite does not occur.

On the other hand, it is also characterized by having a range of Cr equivalent (Cr _eq ) and Ni equivalent (Ni _eq ) calculated by the following equation.

Cr _eq : 19.0 ≤% Cr + 1.5% Si ≤ 23.75

Ni _eq : 3.48 ≤% Ni + 30% C + 18% N + 0.1% Mn-0.01 (% Mn) ² ≤ 10.14

When the Cr _eq value and the Ni _eq value are within the above ranges, the phase ratio of the duplex steel, that is, the two-phase steel composed of austenite and ferrite, and the austenite present in the two-phase steel are metastabilized to transform organic martensite during processing. Occurs.

In addition, the annealing heat treatment temperature should be maintained for 2 to 40 minutes at 1030 ~ 1220 ℃. When the annealing heat treatment temperature is less than 1030 ° C., defects occur during the rolling of the two-phase ferrite and austenite, and the recovery and recrystallization of the heat treatment ferrite and austenite are insufficient, which tends to lower the elongation. In addition, when the annealing heat treatment temperature exceeds 1220 ° C, the grains of ferrite and austenite are so coarse that it is difficult to obtain a tensile strength of 800 Mpa or more.

In addition, in the case of annealing heat treatment time, in a short time, that is, less than 2 minutes, the diffusion that the distribution of alloying elements occurs during heat treatment is not sufficient. As a result, the thickening of the alloying elements on austenite does not occur sufficiently, and therefore, it is difficult to control the rate of transformation organic martensite formation during cold working. In addition, when the heat treatment time exceeds 40 minutes, sagging of the plate occurs during heat treatment by the two-phase structure of ferrite and austenite, resulting in a decrease in productivity and loss of heat source units. Therefore, the optimum annealing heat treatment conditions are preferably maintained for 10 to 1220 ℃ for 2 to 40 minutes.

EMBODIMENT OF THE INVENTION Hereinafter, the high strength high ductility austenite ferrite lean duplex stainless steel and its manufacturing method are demonstrated in detail. Specimens of lean duplex stainless steels for the composition range of the component according to the present invention were prepared and subjected to hot rolling, hot rolling annealing, cold rolling followed by cold rolling annealing to measure the phase fraction, elongation and tensile strength of the material. Table 1 below shows the alloy composition (wt%) for the experimental steel.

Steel grade Cr Mn Ni Si C N Mo Cu Comparative River 1 18.14 1.37 8.06 0.45 0.065 0.042 0.1 0.2 Comparative River 2 21.84 1.76 2.51 0.54 0.025 0.19 0.58 0.47 Comparative Steel 3 20.30 5.05 0.198 0.217 0.021 0.102 - - Inventive Steel 1 20.19 5.15 0.203 0.185 0.018 0.188 - - Invention river 2 20.08 5.06 0.230 0.190 0.020 0.283 - - Invention steel 3 20.25 4.81 0.232 0.209 0.018 0.360 - -

Table 2 shows the phase fractions of ferrite and austenite according to the heat treatment temperature of some of the experimental steels of Table 1 above.

Steel grade Heat treatment temperature (캜) Ferrite fraction (%) Austenitic fraction (%)
Comparative Steel 3 950 71 29 1050 78 22 1100 83 17 1200 86 14
Inventive Steel 1 950 48 52 1050 52 48 1100 56 44 1200 61 39
Invention river 2 950 40 60 1050 41 59 1100 43 57 1200 46 54
Invention steel 3 950 22 78 1050 23 77 1100 25 75 1200 27 73

In the case of duplex stainless steel, the phase fraction changes depending on the alloy composition and the heat treatment temperature. Accordingly, Table 2 shows the ferrite and austenite phase fractions of Comparative Steel 3, Invented Steel 1, Invented Steel 2, and Invented Steel 3 having different alloying components, respectively, when heat treated at 950 ° C, 1050 ° C, 1100 ° C, and 1200 ° C. It is shown. Inventive steel 1, invention steel 2 and invention steel 3 it can be seen that the phase fraction of ferrite is in the range of about 20 to 65%, the austenite phase fraction is in the range of 80 to 35%. And, Comparative steel 3, unlike the invention steels can be seen that the ferrite phase fraction is 71 ~ 86%, the austenite phase fraction is 29 ~ 14% range.

1 is a representative nominal strain-nominal stress comparison curve obtained in the present invention.

Referring to FIG. 1, as a result of a tensile test after heat treatment of each material at 1100 ° C., the comparative steel 3 had a tensile strength of about 680 MPa and an elongation of 48%.

However, in the case of lean duplex stainless steel obtained in the present invention, in particular, inventive steel 1 exhibited a characteristic of the minimum tensile strength of 857 MPa and elongation of 50.3% under the present heat treatment conditions. In addition, both the inventive steels 2 and 3 exhibited an elongation of 50% or more and a tensile strength of 800 MPa or more, showing excellent physical properties compared to 304 steel.

Steel grade Heat treatment temperature (캜) Yield strength (MPa) Tensile Strength (MPa) Elongation (%) Comparative River 1 1040 282 653 58 Comparative River 2 1050 601 765 31.2

Comparative Steel 3 950 413 766 33 1000 416 776 36 1050 420 712 39 1100 427 682 48 1150 402 642 45 1200 453 705 50

Inventive Steel 1 950 500 973 39 1000 505 968 40 1050 465 900 51 1100 470 857 50.3 1150 470 811 43 1200 486 808 53

Invention river 2 950 538 1103 49 1000 541 1084 44 1050 510 1060 50 1100 486 1007 51 1150 500 993 53 1200 505 917 47
Invention steel 3 950 563 1128 57 1050 506 1067 52 1100 516 1038 61

Table 3 shows the yield strength, tensile strength, and elongation after heat-treating the comparative steel and the inventive steel used in the present invention at various heat treatment temperatures for 5 minutes. In the case of Comparative Steel 1, that is, 304 steel, the elongation is very good at 58%, but the tensile strength is 653 MPa, which is lower than that of Comparative Steels 2 and 3. In the case of Comparative Steels 2 and 3, the tensile strength is about 600 to 700 MPa, but the elongation is less than 50, which is lower than that of Comparative Steel 1 (304 steel).

In the case of the inventive steels 1, 2, and 3, the temperature varies depending on the heat treatment temperature and the ferrite and austenite phase fraction. However, when the heat treatment temperature is 1050 ° C or higher, tensile strength of 800 MPa or more and elongation of 50% or more can be secured in most invention steels. have. In particular, it can be seen that in the case of the inventive steel 3, even when the heat treatment temperature is 950 ° C., it exhibits about 57% of excellent elongation.

Steel grade Annealing time (min) Tensile Strength (MPa) Elongation (%)
Comparative Steel 3 5 680 50 10 662 49 15 662 48 30 671 49
Inventive Steel 1 5 857 50.3 10 837 51 15 839 51 30 838 51
Invention river 2 5 1013 51 10 1043 54 15 1040 53 30 1013 55

Table 4 shows the tensile strength and elongation of the steel used in the present invention according to the heat treatment time at 1100 ℃. For Comparative Steel 3, the tensile strength was 700 MPa or less at the heat treatment time of 5 minutes, 10 minutes, 15 minutes, and 30 minutes, respectively, and the elongation was also 50% or less. When the annealing steel 1 was annealed for 5 minutes, the elongation was 50%, but the tensile strength was 680 MPa.

However, both the inventive steels 1 and 2 simultaneously exhibit a tensile strength of 800 MPa or more and an elongation of 50% or more at a heat treatment time of 5 minutes, 10 minutes, 15 minutes, and 30 minutes, respectively. For example, when the invention steel 1 is annealed for 10 minutes, the tensile strength is 837MPa, it can be seen that the elongation is 51%.

As described above, according to the present invention, an elongation of 50% or more can be secured by controlling process conditions such as phase fraction and annealing heat treatment, and high strength of 800 MPa or more can be ensured.

While the present invention has been particularly shown and described with reference to exemplary embodiments thereof, it is to be understood that the invention is not limited to the disclosed exemplary embodiments. It will be apparent to those skilled in the art that various modifications may be made without departing from the scope of the present invention.

The scope of the present invention is defined by the following claims. The scope of the present invention is not limited to the description of the specification, and all variations and modifications falling within the scope of the claims are included in the scope of the present invention.

Claims (7)

By weight%, C: greater than 0 to 0.08 or less, Si: greater than 0 to 0.5 or less, Mn: 4 to 6, Cr: 19 to 23, Ni: greater than 0 to 0.3 or less, N: 0.18 to 0.40, balance Fe and others It contains an unavoidable impurity, 20 to 65% ferrite phase and 35 to 80% austenite phase by volume fraction, the chromium equivalent (Cr _eq ) value defined by the following formula is in the range of 19.0 to 23.75, Lean duplex stainless steel with a nickel equivalent (Ni _eq ) value ranging from 3.48 to 10.14.
Cr _eq =% Cr + 1.5% Si
Ni _eq =% Ni + 30% C + 18% N + 0.1% Mn-0.01 (% Mn) ² delete The method of claim 1,
The stainless steel is a lean duplex stainless steel having an elongation of 50% or more. The method of claim 1,
The stainless steel is lean duplex stainless steel having a tensile strength of 800MPa or more. By weight%, C: greater than 0 to 0.08 or less, Si: greater than 0 to 0.5 or less, Mn: 4 to 6, Cr: 19 to 23, Ni: greater than 0 to 0.3 or less, N: 0.18 to 0.40, balance Fe and others It contains unavoidable impurities, and the chromium equivalent (Cr _eq ) value defined by the following formula is in the range of 19.0 to 23.75, the nickel equivalent (Ni _eq ) value is in the range of 3.48 to 10.14, and the volume fraction is 20 to 65% of ferrite A method of manufacturing a lean duplex stainless steel comprising annealing and heat-treating a lean duplex stainless steel slab composed of a phase and a 35 to 80% austenite phase in a range of 1030 to 1220 ° C.
Cr _eq =% Cr + 1.5% Si
Ni _eq =% Ni + 30% C + 18% N + 0.1% Mn-0.01 (% Mn) ² 6. The method of claim 5,
The annealing heat treatment is a manufacturing method of lean duplex stainless steel made for 2 to 40 minutes. delete

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