WO2014098301A1 - 경도와 저온 충격특성이 우수한 스테인리스 열연강판 - Google Patents
경도와 저온 충격특성이 우수한 스테인리스 열연강판 Download PDFInfo
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- WO2014098301A1 WO2014098301A1 PCT/KR2012/011651 KR2012011651W WO2014098301A1 WO 2014098301 A1 WO2014098301 A1 WO 2014098301A1 KR 2012011651 W KR2012011651 W KR 2012011651W WO 2014098301 A1 WO2014098301 A1 WO 2014098301A1
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Definitions
- the present invention relates to a stainless steel hot rolled steel sheet excellent in hardness and low temperature impact characteristics, and more particularly, to a stainless steel hot rolled steel sheet excellent in hardness and low temperature impact characteristics in which ferrite is formed by a matrix structure.
- stainless steel is classified according to chemical composition or metal structure. According to the metal structure, stainless steel is classified into austenite series (300 series), ferrite series (400 series), martensite series, and ideal system.
- ferritic (400) stainless steels have excellent workability and corrosion resistance
- 410 series steels are mainly composed of 0.15 wt% or less carbon and 11 to 13 wt% chromium.
- the 410 series steel has a disadvantage in that the low temperature impact characteristics of the base metal and the weld are poor.
- a stabilizing element such as Ti or Nb in order to secure a high hardness, there is a disadvantage that is very vulnerable to grain boundary corrosion of the weld.
- 3Cr12 steel is a steel with a small amount of Ni and Mn added at approximately 0.025% C-11.5% Cr, and the weld heat affected zone structure is composed of two phases of ferrite-martensite, which improves the impact characteristics of the weld.
- Patent Document 1 US Patent No. 4,608,099 (Patent Document 1) is characterized in that in order to further improve the impact properties of the base material of the 3Cr12 steel, Ti is removed from the components of the 3Cr12 steel, Mo is added 0.2 ⁇ 0.5%.
- Inventive steel described in Patent Document 1 is used by heat treatment at an annealing temperature of 670 ⁇ 730 °C, yield strength of 303 ⁇ 450MPa, tensile strength of 455 ⁇ 600MPa level is higher than the general ferritic stainless steel.
- the softness is low to be used for abrasion resistance.
- the hardness of these steels is mostly Brinell hardness of 140 ⁇ 180HB is not suitable for wear resistance.
- corrosion resistance is lowered due to Cr-carbide precipitation in the weld heat affected zone due to the absence of C and N stabilization elements.
- Patent Document 1 US Patent No. 4,608,099 (August 26, 1986)
- the present invention provides a stainless steel hot rolled steel sheet having high hardness of 250HB or more, containing stabilizing elements, having excellent corrosion resistance and excellent low temperature impact characteristics, and which can be used for wear-resistant equipment.
- the present invention provides a stainless steel hot rolled steel sheet capable of securing low-temperature impact characteristics by controlling an alloy component having a high ferrite fraction and anisotropic control of ferrite.
- Stainless steel hot rolled steel sheet excellent in hardness and low temperature impact characteristics is a stainless steel hot rolled steel sheet produced by performing a steelmaking, playing and hot rolling process, C: 0.01 ⁇ 0.03wt%, Cr: 11 ⁇ 14wt% , Ti: 0.1-0.2wt%, Nb: 0.1-0.2wt%, N: 0.01-0.03wt%, Si: 0.2-0.5wt%, Mn: 0.2-2.0wt%, Ni: 1.0-2.0wt%, Mo : 0.1 to 0.5 wt%, the sum of the contents of C and N is 0.02 to 0.05wt%, the sum of the contents of Ti and Nb is 0.2 to 0.3wt%, and the ferrite stability index represented by the following [Formula 1] ( Ferrite Stability (FS) is 5 to 50, characterized in that the ferrite is formed by the martensite base structure.
- FS Ferrite Stability
- Each component described in [Equation 1] means the content (wt%) of the corresponding component.
- the stainless steel hot rolled steel sheet is characterized in that the hardness in the hot rolled state is more than 250HB Brinell hardness.
- the stainless steel hot-rolled steel sheet has an impact value (0 ° C.) measured in the longitudinal direction L parallel to the rolling direction RD and an impact value measured in the width direction T perpendicular to the horizontal plane of the rolling direction RD (0).
- °C is characterized in that all 20J or more.
- the stainless steel hot rolled steel sheet is characterized in that the impact value (0 °C) measured in the longitudinal direction (L) is 5J or more higher than the impact value (0 °C) measured in the width direction (T).
- the stainless steel hot rolled steel sheet has a microstructure bending degree ( ⁇ 12 ) of a TS surface formed in a height direction (S) perpendicular to a width direction (T) and a vertical direction of the width direction (T) of 0.60 to 0.80 based on ASTM E1268-01. It is characterized by that.
- the ferrite is characterized in that formed in the reticular.
- the ferrite stability index (F) in an appropriate range so that the ferrite fraction is increased while having the martensite structure as a base structure, it is possible to secure low-temperature impact characteristics while maintaining sufficient hardness. It has an effect.
- Figure 1a is a view showing the impact test piece for each direction
- Figure 1b is a view showing a plane (plane) for each direction of the plate
- FIG. 6 is a graph showing the impact toughness of each impact specimen as a function of the ferrite stability index and the degree of microstructure bending.
- the present invention is C: 0.01 ⁇ 0.03wt%, N: 0.01 ⁇ 0.03wt%, Si: 0.2 ⁇ 0.5wt%, Mn: 0.2 ⁇ 2.0wt%, Cr: 11 ⁇ 14wt%, Ni: 1.0 ⁇ 2.0wt%, A stainless steel hot rolled steel sheet containing 0.1 to 0.2 wt% of Ti, 0.1 to 0.2 wt% of Nb, and 0.1 to 0.5 wt% of Mo, and consisting of the remaining Fe and other unavoidable impurities to form martensite as a base structure. It is targeted.
- the sum of the contents of C and N is 0.02 to 0.05 wt%, and the sum of the contents of Ti and Nb is adjusted to 0.2 to 0.3 wt%.
- each upper limit 0.01 to 0.03 wt% or less (hereinafter, also simply referred to as "%") because the impact properties of the weld cannot be secured. .
- the reason for adjusting C + N, which is the sum of two elements, to be 0.05% or less is that when the sum of the two elements exceeds 0.05%, the low-temperature impact property of the material is sharply lowered, and the toughness of martensite formed in the weld part is drastically reduced. This is because it is degraded.
- Si is usually added at least 0.2% as deoxidizer to reduce inclusions in the steel, and in particular, it is preferable to keep the content at 0.5% or less in order to prevent the deterioration of the toughness of the welded portion.
- Mn is an austenite forming element, the content of which is less than 0.2%, the effect of improving the toughness of the weld is weak, and when the content is more than 2.0%, the toughness of the steel sharply decreases. Therefore, the content of Mn is preferably maintained at 0.2 ⁇ 2.0%.
- the Cr content is preferably maintained at 11.0 to 14.0%.
- Ni is an austenite forming element that contributes to the toughness of the base material, and is an element that improves the weld toughness during welding. Accordingly, in order to improve low-temperature impact toughness, the Ni content was limited to 1% or more, and the excessive addition of expensive Ni leads to an increase in cost, and therefore, the upper limit is preferably maintained at 2.0% or less.
- Ti and Nb are carbonitride-forming elements, and particularly effective for improving weld strength and corrosion resistance when used as a welding structural material.
- Ti and Nb are added excessively or excessively, the toughness and ductility of the material will be reduced.
- excessive addition of 0.2% or more in the case of Ti causes large surface defects due to oxide during casting.
- the low temperature impact toughness is greatly deteriorated. Therefore, in order to secure the corrosion resistance of the welded part and to prevent the sudden drop in the low temperature impact toughness of the base material, Ti and Nb should be maintained at 0.1 to 0.2%, respectively, and the sum of Ti + Nb, the sum of the two elements, to be 0.2 to 0.3%. desirable.
- Mo is an element which improves the formal resistance of a material and increases corrosion resistance.
- Mn is a very expensive element, and it is preferable to keep the content at more than 0.01 to 0.5%.
- the present invention adjusts the alloy components to secure the low-temperature laminar characteristics by predicting the ferrite (1200 °C) fraction.
- the stainless steel hot-rolled steel sheet according to the present invention is to adjust the composition range of the alloy components so that the Ferrite Stability Index (FS) represented by the following [Equation 1] as a function of the composition range of the alloy components is 5 to 50 It is preferable.
- FS Ferrite Stability Index
- Each component described in [Equation 1] means content (wt%) of the said component.
- the ferrite stability index (FS) means that the larger the value, the higher the volume fraction of the ferrite tissue.
- the ferrite stability index (FS) is adjusted to 5 to 50 while securing high hardness at low temperature while maintaining high hardness. The reason for limiting the ferrite stability index (FS) to 5 to 50 as described above will be described later based on examples.
- the present invention is prepared by adjusting the molten steel having the composition as described above in order to produce a stainless steel hot rolled steel sheet excellent in hardness and low temperature impact characteristics and then playing in a conventional manner and then air-cooled after the hot rolling process.
- the twelve component steels shown in Table 1 were each cast in the form of a 50 kg ingot of about 140 mm thickness in a vacuum induction melting furnace. Then, the cast ingot was hot rolled to a thickness of 12 mm after a three-hour aging process in a heating furnace of 1240 °C. At this time, the hot rolling was all finished at a temperature of 900 °C or more, and air-cooled after hot rolling.
- Figure 1a is a view showing the impact test piece for each direction
- Figure 1b is a view showing a plane (plane) for each direction of the plate
- longitudinal direction (L) impact specimen is the notched surface of the impact specimen
- the width direction T impact specimen means a case where the notched surface of the impact specimen is parallel to the rolling direction.
- the direction perpendicular to the vertical plane of the width direction T is the height direction S (Short Transverse), and the surface having the length direction L and the width direction T as sides in the stainless steel plate.
- the LT surface, the surface having the longitudinal direction L and the height direction S as the sides is referred to as the LS surface
- the surface having the width direction T and the height direction S as the sides is referred to as the TS surface.
- Figure 2 is a photograph showing the fracture surface of the low-temperature (0 °C) impact specimens of the Examples and Comparative Examples according to the present invention, in the case of Comparative Example (# 10) steel having a low ferrite stability index (FS), the impact fracture surface is very smooth It is easy to identify the low energy wavefront.
- FS ferrite stability index
- the steels of Examples # 11 and # 12 having a high ferrite stability index FS a fracture surface with deep bends formed during the fracture process is observed. Accordingly, as the ferrite stability index FS increases, the change in brittle fracture to soft fracture increases the impact energy, as shown by the increase in the curvature on the fracture surface, indicating that the impact toughness increases as a result. Accordingly, as can be seen from [Table 2] and FIG. 2, it was confirmed that the ferrite stability index (FS) should be controlled to a predetermined level or more, that is, 5 or more in order to secure low temperature impact toughness of 20J or more.
- Figure 3 is a photograph showing the microstructure of the Example and Comparative Example according to the present invention
- Figure 4 is a graph showing the correlation between the ferrite stability index and the ferrite fraction
- Figure 5 is a ferrite volume fraction and low temperature (0 °C) This graph shows the correlation with impact toughness.
- the black image in the microstructure of FIG. 3 is a ferrite phase, and the matrix surrounding the ferrite phase is a high hardness martensite phase.
- the ferrite fractions of the steels of Examples (# 11, # 12) are relatively high in comparison with those of Comparative Example (# 10) steels of Table 1 having low impact toughness. 12)
- the ferrite fraction is high, the ferrite phase forms a reticular shape, and in particular, the ferrite phase of the TS surface becomes more reticular than the LS surface. Therefore, it can be inferred that the impact toughness of the embodiment steel is larger than that of the comparative steel, and in particular, it can be inferred that the impact toughness of the TS surface is greater than that of the LS surface among the same steels.
- the ferrite stability index (FS) is an important factor for controlling the low temperature impact toughness. Therefore, the correlation between the difference in the L-direction shock value and the T-direction shock value, which is one of the obvious differences between the comparative example and the embodiment, will be described below.
- the present invention has been confirmed that it is possible to add higher impact toughness by controlling the anisotropy of the tissue in the wear-resistant structural steel having a high hardness martensite having a very low impact toughness. In addition, to provide a method of controlling the microstructure to secure.
- microstructural banding of the ferrite phase which is the second phase drawn in the rolling direction, is controlled, and the degree of anisotropy is expressed by using ⁇ 12 specified in ASTM E1268-01.
- a defined ⁇ 12 has a value of zero for fully random distribution tissue and a value of 1 for fully oriented tissue.
- Microstructure banding degree ( ⁇ 12 ) is calculated by the following formula (2).
- N ⁇ number of feature interceptions with test lines perpendicular to the deformation direction
- N ll number of feature interceptions with test lines perpendicular to the deformation direction
- the bending degree of the microstructure is almost similar to that of the LS plane and the TS plane, whereas in the steels (# 11, # 12), the microstructure banding of the TS plane is higher than that of the LS plane. That is, the TS surface is a surface parallel to the notch surface of the longitudinal impact (L) specimen, and the longitudinal (L) impact value and the width (T) impact value when the microstructure bending degree of the TS surface is controlled in a disordered direction.
- Impact toughness can be controlled so that the difference of.
- the microstructure bending degree of the TS surface is 0.60 to 0.80 so that the low temperature (0 ° C) impact value in the longitudinal direction L is higher than 5J higher than the low temperature (0 ° C) impact value in the width direction T. It is preferable to control in the range of.
- ferrite phase change is controlled by controlling various factors such as ferrite volume fraction, reheating temperature and reduction rate of hot rolling process. It is preferable.
- Figure 6 is a graph showing the impact toughness by the direction of the impact specimen as a function of the ferrite stability index and the degree of microstructure bending, the higher the ferrite volume fraction, the lower the degree of banding of the microstructure, It can be seen that a material having excellent low temperature (0 ° C.) impact toughness can be manufactured.
- the high hardness wear resistant steel composed of the martensite matrix and the ferrite phase was controlled by controlling the ferrite volume fraction and the degree of banding of the microstructure.
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Abstract
Description
# | 합금원소 | FS | 비고 | ||||||||
C | Mn | Cr | Ni | Mo | Ti | Nb | N | Si | |||
1 | 0.031 | 1.8 | 11.5 | 0.8 | 0.25 | - | - | 0.035 | 0.40 | -12 | 비교예 |
2 | 0.027 | 1.4 | 11.6 | 1.2 | 0.25 | 0.05 | - | 0.015 | 0.38 | -6 | 비교예 |
3 | 0.019 | 1.4 | 11.4 | 1.2 | - | 0.22 | - | 0.016 | 0.39 | 0 | 비교예 |
4 | 0.019 | 1.4 | 11.5 | 1.2 | - | - | 0.31 | 0.015 | 0.38 | 2 | 비교예 |
5 | 0.025 | 1.4 | 11.5 | 1.8 | 0.25 | 0.11 | 0.05 | 0.016 | 0.40 | -20 | 비교예 |
6 | 0.027 | 1.4 | 11.7 | 1.2 | 0.26 | 0.16 | 0.11 | 0.016 | 0.39 | 15 | 실시예 |
7 | 0.012 | 1.4 | 11.9 | 1.3 | - | 0.13 | 0.13 | 0.011 | 0.39 | 14 | 실시예 |
8 | 0.011 | 1.9 | 12.0 | 1.4 | - | 0.13 | 0.15 | 0.011 | 0.40 | 6 | 실시예 |
9 | 0.013 | 1.2 | 12.4 | 1.7 | - | 0.11 | 0.17 | 0.013 | 0.38 | 14 | 실시예 |
10 | 0.028 | 0.3 | 11.5 | 1.8 | - | 0.17 | 0.10 | 0.015 | 0.39 | -5 | 비교예 |
11 | 0.025 | 0.3 | 12.5 | 1.7 | - | 0.15 | 0.10 | 0.016 | 0.41 | 23 | 실시예 |
12 | 0.028 | 0.3 | 13.6 | 1.7 | - | 0.16 | 0.10 | 0.015 | 0.39 | 48 | 실시예 |
# | 0 충격(J) | 경도 | 비고 | |
T | L | HB | ||
1 | 3 | 3 | 382 | 비교예 |
2 | 9 | 11 | 312 | 비교예 |
3 | 3 | 5 | 293 | 비교예 |
4 | 6 | 9 | 298 | 비교예 |
5 | 9 | 9 | 294 | 비교예 |
6 | 21 | 30 | 293 | 실시예 |
7 | 21 | 26 | 257 | 실시예 |
8 | 20 | 25 | 260 | 실시예 |
9 | 30 | 51 | 278 | 실시예 |
10 | 6 | 7 | 312 | 비교예 |
11 | 20 | 30 | 286 | 실시예 |
12 | 27 | 46 | 279 | 실시예 |
시료 [표 1] | 구분 | 미세조직의 밴딩정도(O12) | |
LS면 | TS면 | ||
#10 | 비교예 | 0.88 | 0.86 |
#11 | 실시예 | 0.85 | 0.74 |
#12 | 실시예 | 0.78 | 0.65 |
Claims (6)
- 제강, 연주 및 열간압연 공정을 실시하여 제조되는 스테인리스 열연강판으로서,C: 0.01 ~ 0.03wt%, Cr: 11 ~ 14wt%, Ti: 0.1 ~ 0.2wt%, Nb: 0.1 ~ 0.2wt%, N: 0.01 ~ 0.03wt%, Si: 0.2 ~ 0.5wt%, Mn: 0.2 ~ 2.0wt%, Ni: 1.0 ~ 2.0wt%, Mo: 0.1 ~ 0.5wt%를 함유하고,C와 N의 함량 합이 0.02 ~ 0.05wt%이고, Ti와 Nb의 함량 합이 0.2 ~ 0.3wt%이며,하기 [식 1]로 표현되는 페라이트 안정도 지수(Ferrite Stability; FS)가 5 ~ 50이고,마르텐사이트를 기지조직으로 페라이트가 형성된 경도와 저온 충격특성이 우수한 스테인리스 열연강판.[식 1]FS = -215-619C-16.6Mn+23.7Cr-36.8Ni+42.2Mo+96.2Ti+67Nb-237N+17.2Si[식 1]에 기재된 각 성분은 해당 성분의 함량(wt%)을 의미함.
- 청구항 1에 있어서,상기 스테인리스 열연강판은 열간압연 된 상태에서의 경도가 브리넬 경도로 250HB 이상인 경도와 저온 충격특성이 우수한 스테인리스 열연강판.
- 청구항 1에 있어서,상기 스테인리스 열연강판은 압연방향(RD)과 평행한 길이방향(L)에서 측정된 충격값(0℃) 및 압연방향(RD)의 수평면상에서 직각인 폭방향(T)에서 측정된 충격값(0℃)이 모두 20J 이상인 경도와 저온 충격특성이 우수한 스테인리스 열연강판.
- 청구항 3에 있어서,상기 스테인리스 열연강판은 길이방향(L)에서 측정된 충격값(0℃)이 폭방향(T)에서 측정된 충격값(0℃) 보다 5J 이상 높은 경도와 저온 충격특성이 우수한 스테인리스 열연강판.
- 청구항 4에 있어서,상기 스테인리스 열연강판은 폭방향(T)와 상기 폭방향(T)의 수직면상에서 직각인 높이방향(S)으로 이루어지는 TS면의 미세조직 밴딩정도(Ω12)가 ASTM E1268-01 기준으로 0.60 ~ 0.80인 높은 경도와 저온 충격특성이 우수한 스테인리스 열연강판.
- 청구항 1에 있어서,상기 페라이트는 망상으로 형성되는 경도와 저온 충격특성이 우수한 스테인리스 열연강판.
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CA2895971A CA2895971C (en) | 2012-12-21 | 2012-12-27 | Hot-rolled stainless steel sheet having excellent hardness and low-temperature impact properties |
US14/653,944 US9790565B2 (en) | 2012-12-21 | 2012-12-27 | Hot-rolled stainless steel sheet having excellent hardness and low-temperature impact properties |
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KR101987665B1 (ko) * | 2017-12-22 | 2019-06-11 | 주식회사 포스코 | 열간가공성이 우수한 유틸리티 페라이트계 스테인리스강 및 그 제조방법 |
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KR20050107595A (ko) * | 2003-04-28 | 2005-11-14 | 제이에프이 스틸 가부시키가이샤 | 디스크브레이크용 마르텐사이트계 스테인레스강 |
US20070170226A1 (en) * | 2004-12-22 | 2007-07-26 | Naoto Ono | Ferritic stainless steel welded pipe superior in expandability |
KR20100058852A (ko) * | 2008-11-25 | 2010-06-04 | 주식회사 포스코 | 가공성이 우수한 페라이트계 스테인리스강 및 그의 제조방법 |
KR20100073825A (ko) * | 2008-12-23 | 2010-07-01 | 주식회사 포스코 | 용접부의 가공성이 우수한 페라이트계 스테인리스강 |
KR20120126112A (ko) * | 2010-03-29 | 2012-11-20 | 닛폰 스틸 앤드 스미킨 스테인레스 스틸 코포레이션 | 복상 조직 스테인리스 강판 및 강대 및 그들의 제조 방법 |
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US4608099A (en) | 1984-10-10 | 1986-08-26 | Amax Inc. | General purpose maintenance-free constructional steel of superior processability |
BRPI0904608A2 (pt) | 2009-11-17 | 2013-07-02 | Villares Metals Sa | aÇo inoxidÁvel para moldes com menor quantidade de ferrita delta |
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KR20050107595A (ko) * | 2003-04-28 | 2005-11-14 | 제이에프이 스틸 가부시키가이샤 | 디스크브레이크용 마르텐사이트계 스테인레스강 |
US20070170226A1 (en) * | 2004-12-22 | 2007-07-26 | Naoto Ono | Ferritic stainless steel welded pipe superior in expandability |
KR20100058852A (ko) * | 2008-11-25 | 2010-06-04 | 주식회사 포스코 | 가공성이 우수한 페라이트계 스테인리스강 및 그의 제조방법 |
KR20100073825A (ko) * | 2008-12-23 | 2010-07-01 | 주식회사 포스코 | 용접부의 가공성이 우수한 페라이트계 스테인리스강 |
KR20120126112A (ko) * | 2010-03-29 | 2012-11-20 | 닛폰 스틸 앤드 스미킨 스테인레스 스틸 코포레이션 | 복상 조직 스테인리스 강판 및 강대 및 그들의 제조 방법 |
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US20150315686A1 (en) | 2015-11-05 |
KR20140081478A (ko) | 2014-07-01 |
CA2895971C (en) | 2017-12-05 |
KR101463315B1 (ko) | 2014-11-18 |
US9790565B2 (en) | 2017-10-17 |
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