WO2012091394A2 - 고내식 마르텐사이트 스테인리스강 및 그 제조방법 - Google Patents
고내식 마르텐사이트 스테인리스강 및 그 제조방법 Download PDFInfo
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- WO2012091394A2 WO2012091394A2 PCT/KR2011/010123 KR2011010123W WO2012091394A2 WO 2012091394 A2 WO2012091394 A2 WO 2012091394A2 KR 2011010123 W KR2011010123 W KR 2011010123W WO 2012091394 A2 WO2012091394 A2 WO 2012091394A2
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- stainless steel
- martensitic stainless
- high corrosion
- steel
- corrosion resistance
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/06—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars
- B22D11/0622—Continuous casting of metals, i.e. casting in indefinite lengths into moulds with travelling walls, e.g. with rolls, plates, belts, caterpillars formed by two casting wheels
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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
- C21D8/021—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular fabrication or treatment of ingot or slab
- C21D8/0215—Rapid solidification; Thin strip casting
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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
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following 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
- C21D9/18—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for knives, scythes, scissors, or like hand cutting tools
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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
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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
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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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
Definitions
- the present invention relates to martensitic stainless steel, and more particularly to a high corrosion-resistant martensitic stainless steel used in the production of razor blades and a method for producing the same.
- high hardness stainless steel is used in the manufacture of razor blades to secure corrosion resistance and machinability.
- These steels are mainly steels containing more than 12% chromium and more than 0.6% carbon, which secures high hardness through solid solution of carbon after the final heat treatment and corrosion resistance in the wet environment due to the influence of chromium contained in the base material.
- a method of manufacturing steel for blades is known by adding carbon to 0.65 to 0.7% and chromium to 12.7 to 13.7%.
- the carbide formed inside the material is difficult to be completely employed in the heat treatment process, forming a chromium-deficient layer, which lowers the corrosion resistance of the material. I have a problem.
- the carbon content is limited to 0.45 to 55 and molybdenum may be added to suppress residual carbide in the final heat treatment material and to improve the corrosion resistance of the base material.
- these steels are characterized by containing high silicon in order to prevent the hardness decrease due to carbon degradation.
- Steels containing high silicon have a problem in that the hardness of the hot rolled annealing material is increased, so that it is not easy to manufacture using a conventional stainless steel manufacturing process.
- An object of the present invention is to provide a high-grade martensitic stainless steel with excellent corrosion resistance, which is devised to solve the above problems.
- the present invention comprises, by weight, carbon: 0.45-0.60%, nitrogen: 0.02-0.08%, silicon: 0.2-0.4%, manganese: 0.3-0.6%, chromium: 12-15%, and molybdenum 0.1-1.5 % And the remainder provide a high corrosion-resistant martensitic stainless steel containing iron and other unavoidable impurities.
- Another embodiment of the present invention by weight, carbon: 0.45-0.60%, nitrogen: 0.02-0.08%, silicon: 0.2-0.4%, manganese: 0.3-0.6%, chromium: 12-15%, It provides a high corrosion-resistant martensitic stainless steel containing 0.1 to 1.5% of tungsten and the remainder containing iron and other unavoidable impurities.
- Another embodiment of the present invention by weight, carbon: 0.45-0.60%, nitrogen: 0.02-0.08%, silicon: 0.2-0.4%, manganese: 0.3-0.6%, chromium: 12-15%, It provides a high corrosion-resistant martensitic stainless steel containing molybdenum: 0.1-1.5% and tungsten: 0.1-1.5%, the remainder containing iron and other unavoidable impurities.
- Final heat treatment hardness of the stainless steel in the present invention is in the range of 500 ⁇ 750 Hv.
- the pitting corrosion index of the stainless steel in the present invention has a value of 15 or more by the following formula (1).
- the Charpy impact energy of the hot rolled material may be 6J or more (thickness 4mm or more) through batch annealing.
- a pair of rolls rotating in opposite directions, an edge dam installed to form molten steel pools on both sides thereof, and a meniscus shield for supplying inert nitrogen gas to the upper surface of the molten steel pool are provided.
- a stripping apparatus comprising, in weight percent, carbon: 0.45-0.60%, nitrogen: 0.02-0.08%, silicon: 0.2-0.4%, manganese: 0.3-0.6%, chromium: 12-15%
- molybdenum Stainless steel sheet is cast by supplying at least one of 0.1 to 1.5% or tungsten to 0.1 to 1.5%, and the remainder containing iron and other unavoidable impurities from a tundish to the molten steel pool through a nozzle. It provides a high corrosion resistance martensitic stainless steel manufacturing method for producing a hot-rolled strip by using the cast stainless steel sheet in-line roller.
- FIG. 1 is a schematic diagram of a stripcasting process for applying the present invention.
- Figure 2 is a photograph showing a comparison of the microstructure of the martensitic steel of the present invention produced by ingot casting and the martensite steel of the present invention cast using strip casting.
- Figure 3 is a graph showing the hardness according to the silicon content of the hot rolled annealing material in the present invention.
- Figure 4 is a graph showing the hardness of the final heat treatment material in the present invention.
- Fig. 6 is a photograph showing the edge portion of a plate rolled at 80% reduction ratio for the inventive steel and the specific u steel.
- FIG. 7 is a graph showing that the pitting resistance index due to the composite addition of molybdenum and tungsten according to the present invention is improved.
- Martensitic stainless steel for high corrosion resistance blades is a weight%, carbon: 0.45 ⁇ 0.60%, nitrogen: 0.02 ⁇ 0.08% or less, silicon: 0.2 ⁇ 0.4%, manganese: 0.3 ⁇ 0.6%, chromium: 12 15% and Fe and other unavoidable impurities, the stainless steel may be added at least one of molybdenum: 0.1-1.5%, tungsten: 0.1-1.5%.
- the characteristics of the alloy composition are designed from three viewpoints.
- the first is improvement of operability
- the second is improvement of corrosion resistance
- the third is securing desirable hardness.
- the silicon content is designed to ensure the ductility without sacrificing hardness.
- the inventors have confirmed through various experiments that limiting the content of silicon in martensitic steel containing high carbon has significant advantages in the manufacturing process by securing the ductility of the hot-rolled annealing material.
- silicon is known to be added to improve the hardness, but it has been found to contribute greatly to the hardness improvement of hot-rolled and annealed materials, but not to increase the hardness of the final heat treatment material.
- molybdenum and tungsten are added, so that the solid-solution strengthening effect and tempering resistance during the heat treatment process are secured. Therefore, the hardness using silicon may be negligible.
- molybdenum and tungsten can be added in combination to improve corrosion resistance. It was confirmed that the effect of molybdenum added to improve the corrosion resistance in the martensitic steel can be replaced by tungsten.
- the carbon content was optimized to obtain carbide solidification effect while suppressing carbide production.
- a final heat treatment hardness of 500 to 750 Hv can be obtained.
- the present invention is based on the above alloy design, characterized in that the application of the strip casting process rather than the usual continuous casting method.
- the carbon content is low, the hardness of martensite decreases, so that it is impossible to secure the machinability. Therefore, 0.45% or more is added. However, if the content is excessively high, the corrosion resistance of the material is reduced through carbide formation, so the upper limit is limited to 0.6%. Preferably, however, the carbon is added at least 0.5%.
- nitrogen contributes to strength and corrosion resistance, it should be added more than 0.02%. However, if excessively added, there is a risk of pore caused by nitrogen during casting, so the upper limit is limited to 0.08%.
- Silicon is one of the important elements in the alloy design of the present invention. 0.2% or more is added since it is an essential element for silicon deoxidation. However, the addition of a high content of silicon increases the hardness of the annealing material after hot rolling, thereby inhibiting manufacturability, thereby limiting the upper limit to 0.4%.
- the content of silicon greatly contributes to the hardness improvement of the annealing material, but the contribution is not large to the hardness improvement of the final heat treatment material.
- the annealing material most of the solid solution carbon precipitates in the form of carbide, and the hardness is increased by silicon, which is a representative reinforcing element.
- silicon which is a representative reinforcing element.
- the final heat treatment material most of the carbon is dissolved in the base material to cause the increase in hardness. Has the characteristic of being extinct.
- FIGS. 3 and 4 are graph showing the hardness according to the silicon content of the hot rolled annealing material in the present invention
- Figure 4 is a graph showing the hardness of the final heat treatment material in the present invention.
- the hardness in the final heat treatment material is silicon content 0.3%, 0.5%. In the case of 1%, the change in hardness is not large.
- the silicon content is reduced to 0.2% or more and 0.4% or less.
- chromium is a basic element to ensure corrosion resistance, it is added at least 12%. However, the excessive limit increases the manufacturing cost and limits the upper limit to 15% because carbides can lower the dissolved carbon in the final heat treatment material.
- Molybdenum is added at least 0.1% because it has an excellent effect on corrosion resistance.
- excessive addition limits the upper limit to 1.5%, which leads to an increase in manufacturing cost.
- Tungsten is added at least 0.1% to improve the corrosion resistance.
- excessive addition impedes the increase in manufacturing costs and the operability, so the upper limit is limited to 1.5%.
- the molybdenum and tungsten may be contained one or two.
- molybdenum and tungsten are added in combination to improve corrosion resistance.
- the present invention can obtain a high pitting index by slightly increasing the composite addition of molybdenum and tungsten and chromium slightly.
- the pitting index PREN can be obtained by the following formula (1), and the preferred pitting index in the present invention is 15 or more.
- the martensitic stainless steel is manufactured by the strip casting process shown in FIG. 1, and undergoes a heat treatment process of a unique method to obtain proper physical properties for use.
- the strip casting process for applying the present invention is a process for producing a hot rolled strip of the thin directly from the molten stainless steel made of the above composition to omit the hot rolling process, manufacturing cost, equipment investment cost, energy It is a new steel processing process that can drastically reduce consumption and pollution gas emissions.
- a twin roll sheet caster used in a general strip casting process receives molten steel in a ladle 1, flows into a tundish 2 along a nozzle, and flows into a tundish 2.
- the silver is supplied through the molten steel injection nozzle 3 between the edge dams 5 provided at both ends of the casting roll 6, that is, between the casting rolls 6 to start solidification. At this time, the molten portion between the rolls to protect the molten surface with the meniscus shield (4) in order to prevent oxidation and inject the appropriate gas to properly control the atmosphere.
- the thin plate 8 is manufactured and drawn while rolling out the roll nip 7 where both rolls meet, and then rolled through the rolling mill 9 and then wound up in the winding facility 10 through a cooling process.
- the molten steel is supplied through the injection nozzle between the internal water-cooled twin rolls rotating in the opposite direction at a high speed to provide a thin plate of the desired thickness It is manufactured so that there is no crack and the error rate is improved.
- hot-rolled annealing material was manufactured by BAF process simulation which maintains 20 hours at 850 °C for annealing of hot-rolled sheet. After blasting, the scale formed during the hot rolling process was removed, and it was pickled in a mixed solution of nitric acid and hydrofluoric acid. The final cold rolled material was fabricated by cold rolling at% rolling rate.
- martensitic stainless steel containing high carbon is characterized by being manufactured by the ingot casting method.
- the solidification time of the ingot is maintained for a long time, so that carbides may be segregated in the center part during solidification. Once the segregation is formed, it is difficult to remove the segregation in the post-process, which is a factor that inhibits the corrosion resistance or blade tip quality.
- FIG. 2 is a photograph comparing the microstructure of the martensitic steel of the present invention manufactured by ingot casting and the martensitic steel of the present invention cast using strip casting. As shown in FIG. 2, ingot casting has severe carbide segregation in the center, and strip casting has little segregation. Through this, when the present invention is manufactured by applying the strip casting method, it can be seen that it is possible to manufacture martensitic steel having a uniform microstructure compared to the ingot manufacturing method.
- the stainless steel having the composition of the present invention limiting the content of silicon in the martensitic steel containing high carbon has significant advantages in the manufacturing process using strip casting by securing the ductility of the hot-annealed material. It is known that silicon is added to improve the hardness, but it contributes greatly to the hardness improvement of hot-rolled and annealed materials, but it is confirmed that the degree is not large enough to improve the hardness of the final heat treatment material. In the case of high corrosion resistant steels, molybdenum and tungsten are added, so that the solid-solution strengthening effect and tempering resistance during the heat treatment process are secured. Therefore, the hardness using silicon may be negligible. This is as described with reference to FIGS. 3 and 4.
- a test piece was prepared by performing a reinforcing heat treatment at 1100 ° C for 20 seconds.
- razor blades are used in tap water at room temperature, but the experiment was conducted by immersing in 0.05% NaCl environment at 85 °C for accelerated experiment.
- FIG. 5 is a photograph showing the presence of surface rust after the corrosion test for the invention steel 1 and comparative steel 1
- Figure 6 shows the edge portion of the plate rolled at 80% reduction rate for the invention steel 1 and comparative steel 2. It is a photograph.
- the comparative steel 1 has a very high degree of rust generation compared to the inventive steel 1. This can be seen that when the corrosion test is carried out as described above, in the case of the comparative steel outside the composition range of the present invention, a lot of rust occurs and the corrosion resistance is poor. However, in the case of the present invention steel rust hardly occurs, it is excellent in corrosion resistance compared to Comparative steel 1.
- the invention steel which added molybdenum and tungsten concerning this invention can obtain high corrosion resistance compared with the steel which does not add these in chlorine atmosphere.
- Figure 7 shows that the pitting resistance index due to the composite addition of molybdenum and tungsten according to the present invention is improved.
- the present invention can obtain a high pitting index by slightly increasing the composite addition of molybdenum and tungsten and chromium slightly.
- a higher pitting index of 17.8 can be obtained than the pitting index of 13.6.
- the pitting index PREN can be obtained by the following formula (1), and the preferred pitting index in the present invention is 15 or more.
- martensitic materials with a high carbon content have high hardness of the base material and a large amount of carbides, so that defects such as edge cracks or fracture of the material are more likely to occur during cold rolling and pickling processes. In other words, operability is a very important factor in the mass production process.
- Table 3 shows the physical properties obtained through the above experiment.
- the steel produced through the present invention which controls the content of silicon while lowering the content of carbon, shows that the Charpy impact energy property is superior to that of the comparative steel with high carbon content or high silicon content. Can be.
- the present impact energy characteristics may vary depending on the thickness of the material and the reduction ratio, but in the present embodiment, a value of 6J or more may be obtained based on 4 mm thickness or 4 mm thickness or more.
- Figure 8 is a graph showing that the elongation of the hot-rolled annealing material is improved when the content of silicon in the martensitic steel containing high carbon is limited.
- the comparative steel 2 contained excessively more silicon than the inventive steel 1. Therefore, the present invention can be seen that the elongation is significantly improved compared to the comparative steel 2. Accordingly, it can be seen from the Table 3 and FIG. 8 that the inventive steel of the present invention does not generate edge cracks due to an improvement in elongation and impact toughness and thus greatly improves operability.
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Abstract
Description
강종 | C | Si | Mn | Cr | Mo | W | N |
발명강1 | 0.50 | 0.2 | 0.3 | 12.8 | 0.2 | 0.8 | 0.062 |
발명강2 | 0.59 | 0.3 | 0.4 | 14.3 | 0.5 | 1.3 | 0.038 |
발명강3 | 0.56 | 0.4 | 0.3 | 14.2 | 1.2 | 0.4 | 0.040 |
발명강4 | 0.55 | 0.4 | 0.4 | 14.6 | 0.3 | 0.6 | 0.044 |
발명강5 | 0.51 | 0.3 | 0.5 | 13.7 | 0.4 | 0.6 | 0.033 |
발명강6 | 0.47 | 0.3 | 0.4 | 13.2 | 0.4 | 0.7 | 0.045 |
비교강1 | 0.71 | 0.3 | 0.7 | 13.2 | - | - | 0.032 |
비교강2 | 0.50 | 0.8 | 0.7 | 12.5 | 1.3 | - | 0.031 |
강종 | 녹발생 유무 |
발명강1 | X |
발명강2 | X |
발명강3 | X |
발명강4 | X |
발명강5 | X |
발명강6 | X |
비교강1 | O |
비교강2 | X |
강종 | Charpy 충격에너지(J) (4mm기준) | 상소둔시의 경도(Hv) |
발명강1 | 6.6 | 208 |
발명강2 | 6.5 | 205 |
발명강3 | 6.3 | 206 |
발명강4 | 6.5 | 205 |
발명강5 | 7.1 | 202 |
발명강6 | 7.3 | 203 |
비교강1 | 2.8 | 213 |
비교강2 | 4.4 | 230 |
Claims (12)
- 중량%로, 탄소: 0.45~0.60%, 질소: 0.02~0.08%, 실리콘: 0.2~0.4%, 망간: 0.3~0.6%, 크롬: 12~15%을 포함하고, 몰리브덴을 0.1~1.5% 함유하고, 나머지는 철 및 기타 불가피한 불순물을 포함하는 고내식 마르텐사이트계 스테인리스강.
- 중량%로, 탄소: 0.45~0.60%, 질소: 0.02~0.08%, 실리콘: 0.2~0.4%, 망간: 0.3~0.6%, 크롬: 12~15%을 포함하고, 텅스텐을 0.1~1.5% 함유하고, 나머지는 철 및 기타 불가피한 불순물을 포함하는 고내식 마르텐사이트계 스테인리스강.
- 중량%로, 탄소: 0.45~0.60%, 질소: 0.02~0.08%, 실리콘: 0.2~0.4%, 망간: 0.3~0.6%, 크롬: 12~15%을 포함하고, 몰리브덴 : 0.1~1.5% 및 텅스텐 : 0.1~1.5% 함유하고, 나머지는 철 및 기타 불가피한 불순물을 포함하는 고내식 마르텐사이트계 스테인리스강.
- 제1항 내지 제3항 중 어느 한 항에 있어서,상기 스테인리스강의 최종 열처리 경도는 500~750Hv 범위내에 있는 고내식 마르텐사이트 스테인리스강.
- 제1항 내지 제3항 중 어느 한 항에 있어서,상기 스테인리스강의 내공식지수는 하기 식(1)에 의하여 15이상의 값을 갖는 고내식 마르텐사이트 스테인리스강.식(1) : PREN = %Cr+3.3(%Mo + 0.5%W) + 16%N
- 제1항 내지 제3항 중 어느 한 항에 있어서,상기 스테인리스강은 중량%로 탄소가 0.5~0.60%를 함유하는 고내식 마르텐사이트계 스테인리스강.
- 제1항 내지 제3항 중 어느 한 항에 있어서,상기 스테인리스강은 상소둔(batch annealing)을 통하여 열연 소재의 챠르피 충격에너지가 6J이상(두께 4mm 이상)인 고내식 마르텐사이트계 스테인리스강.
- 서로 반대방향으로 회전하는 한쌍의 롤과 그 양측면에 용강풀을 형성하도록 설치되는 에지댐과 상기 용강풀 상부면으로 불활성 질소가스를 공급하는 매니스커스 쉴드를 포함하는 스트립캐스팅 장치에서, 중량%로, 탄소: 0.45~0.60%, 질소: 0.02~0.08%, 실리콘: 0.2~0.4%, 망간: 0.3~0.6%, 크롬: 12~15%을 포함하고, 몰리브덴 : 0.1~1.5% 또는 텅스텐 : 0.1~1.5% 의 1종 이상을 함유하고, 나머지는 철 및 기타 불가피한 불순물을 포함하는 스테인리스 용강을 턴디쉬로부터 노즐을 통하여 상기 용강풀로 공급하여 스테인리스 박판을 주조하고, 상기 주조된 스테인리스 박판을 인라인롤러를 이용하여 열연스트립을 제조하는 고내식 마르텐사이트계 스테인리스강 제조방법.
- 제8항에 있어서,상기 스테인리스강은 중량%로 탄소가 0.5~0.60%를 함유하는 고내식 마르텐사이트계 스테인리스강 제조방법.
- 제8항에 있어서,상기 스테인리스강은 상소둔(batch annealing)을 통하여 열연 소재의 챠르피 충격에너지가 6J이상(두께 4mm 이상) 확보되는 것을 특징으로 하는 고내식 마르텐사이트계 스테인리스강 제조방법.
- 제8항에 있어서,상기 스테인리스강의 최종 열처리 경도는 500~750Hv 범위내에 있는 고내식 마르텐사이트 스테인리스강 제조방법.
- 제8항에 있어서,상기 스테인리스강의 내공식지수는 하기 식(1)에 의하여 15이상의 값을 갖도록 제어하는 고내식 마르텐사이트 스테인리스강 제조방법.식(1) : PREN = %Cr+3.3(%Mo + 0.5%W) + 16%N
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JP2013543113A JP5696225B2 (ja) | 2010-12-27 | 2011-12-26 | 高耐食マルテンサイト系ステンレス鋼およびその製造方法 |
US13/823,502 US9731345B2 (en) | 2010-12-27 | 2011-12-26 | Martensitic stainless steel highly resistant to corrosion, and method for manufacturing same |
DE112011104603.0T DE112011104603T5 (de) | 2010-12-27 | 2011-12-26 | Hochkorrosionsbeständiger martensitischer rostfreier Stahl und Verfahren zu dessen Herstellung |
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KR101439607B1 (ko) * | 2012-07-16 | 2014-09-11 | 주식회사 포스코 | 쌍롤식 박판 주조공정에 의해 제조된 마르텐사이트계 스테인리스강 및 그 제조방법 |
JP6002114B2 (ja) * | 2013-11-13 | 2016-10-05 | 日本精工株式会社 | マルテンサイト系ステンレス鋼による機構部品の製造方法および転がり軸受の製造方法 |
CN103866193A (zh) * | 2014-03-24 | 2014-06-18 | 无锡宝顺不锈钢有限公司 | 8Cr15不锈钢带钢及其制造方法 |
KR101648271B1 (ko) * | 2014-11-26 | 2016-08-12 | 주식회사 포스코 | 항균성이 우수한 고경도 마르텐사이트계 스테인리스강 및 이의 제조방법 |
WO2016174500A1 (fr) * | 2015-04-30 | 2016-11-03 | Aperam | Acier inoxydable martensitique, procédé de fabrication d'un demi-produit en cet acier et outil de coupe réalisé à partir de ce demi-produit |
CN107699815B (zh) * | 2017-11-27 | 2019-08-30 | 上海大学 | 高硬度高韧性刀具用不锈钢及其制备方法 |
CN108642391A (zh) * | 2018-06-07 | 2018-10-12 | 成都先进金属材料产业技术研究院有限公司 | 马氏体不锈钢及其制备方法 |
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KR101239589B1 (ko) | 2013-03-05 |
CN103298964B (zh) | 2016-01-06 |
JP2014504332A (ja) | 2014-02-20 |
JP5696225B2 (ja) | 2015-04-08 |
US9731345B2 (en) | 2017-08-15 |
WO2012091394A9 (ko) | 2012-08-09 |
DE112011104603T5 (de) | 2014-01-02 |
WO2012091394A3 (ko) | 2012-09-27 |
CN103298964A (zh) | 2013-09-11 |
KR20120073649A (ko) | 2012-07-05 |
US20130309126A1 (en) | 2013-11-21 |
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