WO2022139277A1 - 공구용 강재 및 그 제조방법 - Google Patents

공구용 강재 및 그 제조방법 Download PDF

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Publication number
WO2022139277A1
WO2022139277A1 PCT/KR2021/018722 KR2021018722W WO2022139277A1 WO 2022139277 A1 WO2022139277 A1 WO 2022139277A1 KR 2021018722 W KR2021018722 W KR 2021018722W WO 2022139277 A1 WO2022139277 A1 WO 2022139277A1
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Prior art keywords
steel
less
tools
present
annealing
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PCT/KR2021/018722
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English (en)
French (fr)
Korean (ko)
Inventor
손창영
최재훈
Original Assignee
주식회사 포스코
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Priority to CN202180086543.8A priority Critical patent/CN116745443A/zh
Publication of WO2022139277A1 publication Critical patent/WO2022139277A1/ko

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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
    • 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
    • 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
    • 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
    • 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
    • C21D2211/009—Pearlite

Definitions

  • the present invention relates to a steel material for a tool and a method for manufacturing the same, and more particularly, to a steel material for a tool having improved heat treatment properties and a method for manufacturing the same.
  • hardness and workability are widely known as incompatible properties. This is because an increase in the strength of the steel causes an increase in hardness, whereas when the strength of the steel increases, the workability of the steel deteriorates.
  • Spheroidizing annealing is a heat treatment in which plate-shaped cementite in lamellar pearlite is heated at a high temperature to make it spherical, and it takes a long time to secure a desired level of workability.
  • a method of maintaining a temperature below A1 for a long time is mainly used, but heat treatment at a high temperature for a long time inevitably entails a decrease in economic efficiency and productivity.
  • Patent Document 1 proposes a method of accelerating the spheroidization of cementite in a steel sheet having a lamellar pearlite structure through cold rolling without annealing, but the steel sheet of Patent Document 1 has a carbon (C) content of 0.6% by weight or less. Therefore, it is not possible to provide hardness suitable as a steel material for tools.
  • Patent Document 2 proposes a method of performing a secondary annealing heat treatment at a temperature of about 650° C. after performing a primary annealing heat treatment at a temperature directly above A1 to control the spheroidized carbide structure, but such a heating condition is a typical heating furnace There are aspects that are difficult to implement in
  • Patent Document 1 Japanese Patent Application Laid-Open No. 2005-133199 A (published on May 26, 2005)
  • Patent Document 2 Japanese Patent Application Laid-Open No. 2006-257449 A (published on September 28, 2006)
  • a steel material suitable for tools and a method for manufacturing the same can be provided by improving the heat treatment properties of the spheroidizing annealing while securing high hardness characteristics including 0.8% by weight or more of carbon (C).
  • the average pole density of the ⁇ 011> to ⁇ 223 ⁇ 110> crystal orientation groups may be 1.8 or more, and the ⁇ 332 ⁇ 113> crystal orientation may have a pole density of 2.0 or more.
  • the thickness center means a region within the range of 3/8t to 5/8t with respect to the thickness (t, mm) of the steel material when the cross-section of the steel material is observed.
  • the average long/short axis ratio of (block) may be 1.41:1 or more.
  • the method of manufacturing a steel material for a tool by weight, carbon (C): 0.8 to 1.0%, silicon (Si): 0.1 to 0.3%, manganese (Mn): 0.3 to 0.5%, chromium (Cr): 0.1 to 0.3%, phosphorus (P): 0.03% or less, sulfur (S): 0.005% or less, reheating the slab containing the remaining iron (Fe) and unavoidable impurities in a temperature range of 1000 to 1300 °C step; hot rolling the reheated slab in a temperature range of 850 to 1150 °C; and cold-rolling the hot-rolled steel at a reduction ratio of 30-50% without annealing.
  • FIG. 1 is a photograph of a cross-section of a non-annealed cold-rolled specimen 1 observed with a scanning electron microscope.
  • the present invention relates to a steel material for a tool and a method for manufacturing the same, and preferred embodiments of the present invention will be described below. Embodiments of the present invention may be modified in various forms, and the scope of the present invention should not be construed as being limited to the embodiments described below. The present embodiments are provided in order to further detailed the present invention to those of ordinary skill in the art to which the present invention pertains.
  • the steel material for tools of the present invention is, by weight, carbon (C): 0.8 to 1.0%, silicon (Si): 0.1 to 0.3%, manganese (Mn): 0.3 to 0.5%, chromium (Cr): 0.1 to 0.3 %, phosphorus (P): 0.03% or less, sulfur (S): 0.005% or less, the remaining iron (Fe) and unavoidable impurities, and pearlite as a matrix, in the center of the thickness, ⁇ 100 ⁇ 011> to ⁇ 223 ⁇ 110> crystal orientation groups may have an average pole density of 1.8 or more, and ⁇ 332 ⁇ 113> crystal orientations may have a pole density of 2.5 or more.
  • the thickness center means a region within the range of 3/8t to 5/8t with respect to the thickness (t, mm) of the steel material when the cross-section of the steel material is observed.
  • % described in relation to the alloy composition means % by weight.
  • Carbon (C) is a representative hardenability improving element, and in the present invention, it is an element essential to secure hardness after quenching. Therefore, the present invention may contain 0.8% or more of carbon (C) for this effect.
  • a preferred carbon (C) content may be greater than 0.8%, and a more preferred carbon (C) content may be 0.82% or more.
  • the carbon (C) content in the steel exceeds a certain range, the cementite fraction in the steel is too high to promote brittle fracture, so the present invention limits the upper limit of the carbon (C) content to 1.0%.
  • a preferred carbon (C) content may be less than 1.0%, and a more preferred carbon (C) content may be 0.98% or less.
  • the present invention may include 0.1% or more of silicon (Si) to achieve such an effect.
  • a preferable lower limit of the silicon (Si) content may be 0.12%, and a more preferable lower limit of the silicon (Si) content may be 0.15%.
  • the silicon (Si) content in the steel exceeds a certain range, not only the cold rolling is inferior, but also the possibility of decarburization during heat treatment increases, and since it may cause an increase in scale defects on the surface of the steel, the present invention provides silicon ( The upper limit of the Si) content may be limited to 0.3%.
  • a preferable upper limit of the silicon (Si) content may be 0.28%, and a more preferable upper limit of the silicon (Si) content may be 0.25%.
  • Manganese (Mn) is not only an element contributing to the improvement of hardenability, but also an element that effectively contributes to the improvement of the strength of the material by solid solution strengthening.
  • manganese (Mn) is combined with sulfur (S) in steel to precipitate as MnS, it is possible to effectively prevent red hot brittleness caused by sulfur (S).
  • the present invention may contain 0.3% or more of manganese (Mn) to achieve such an effect.
  • a preferred lower limit of the manganese (Mn) content may be 0.32%, and a more preferred lower limit of the manganese (Mn) content may be 0.35%.
  • the present invention sets the upper limit of the manganese (Mn) content It can be limited to 0.5%.
  • a preferable upper limit of the manganese (Mn) content may be 0.48%, and a more preferable upper limit of the manganese (Mn) content may be 0.45%.
  • Chromium (Cr) is an element that effectively contributes to improvement of hardenability, like manganese (Mn). Therefore, the present invention may contain 0.1% or more of chromium (Cr) for this effect.
  • a preferable lower limit of the chromium (Cr) content may be 0.13%, and a more preferable lower limit of the chromium (Cr) content may be 0.16%.
  • the chromium (Cr) content in the steel exceeds a certain range, not only the cold rolling ductility may decrease, but also the decomposition of cementite by heat treatment is delayed, so that the spheroidization of the carbide is not completed even by spheroidizing annealing. Possibility exists.
  • the present invention may limit the upper limit of the chromium (Cr) content to 0.3%.
  • a preferable upper limit of the chromium (Cr) content may be 0.28%, and a more preferable upper limit of the chromium (Cr) content may be 0.25%.
  • Phosphorus (P) in steel is a typical impurity element, but it is also the most advantageous element for securing strength without significantly impairing formability.
  • the present invention may limit the upper limit of the phosphorus (P) content to 0.03%.
  • Sulfur (S) is an impurity element that is unavoidably introduced into steel, and it is desirable to manage its content as low as possible.
  • sulfur (S) in steel may cause red hot brittleness
  • the present invention may limit the upper limit of the sulfur (S) content to 0.005%.
  • the steel material for tools of the present invention may include the remaining Fe and other unavoidable impurities in addition to the above-described components.
  • unintended impurities from raw materials or the surrounding environment may inevitably be mixed in the normal manufacturing process, it cannot be entirely excluded. Since these impurities are known to those of ordinary skill in the art, all contents thereof are not specifically mentioned in the present specification.
  • additional addition of effective ingredients other than the above-mentioned ingredients is not entirely excluded.
  • the steel material for a tool according to an aspect of the present invention may have a microstructure including a pearlite matrix and other residual structures.
  • Pearlite is an essential structure for securing the desired physical properties of the present invention, and the preferred fraction of pearlite may be 90% by area or more.
  • Other residual structures may include low-temperature structures such as proeutectoid ferrite and bainite and martensite.
  • proeutectoid ferrite When proeutectoid ferrite is excessive, not only hardness is lowered, but also workability may be deteriorated by promoting grain boundary fracture, so the fraction of proeutectoid ferrite may be limited to 10 area% or less (including 0%). Since hard bainite and martensite are not preferable in terms of workability, the fraction of hard structures such as bainite and martensite may be limited to less than 3 area% (including 0%).
  • the average value of the pole density of the ⁇ 100 ⁇ 011> to ⁇ 223 ⁇ ⁇ 110> crystal orientation groups measured at the center of the thickness of the steel is 1.8 or more, and it is measured at the center of the thickness of the steel.
  • the pole density of the crystal orientation may be 2.5 or more.
  • the pole density average value of the ⁇ 100 ⁇ 011> to ⁇ 223 ⁇ 110> crystal orientation groups measured at the center of the thickness of the steel may be 1.9 or more, and the ⁇ 332 ⁇ 113> crystals measured at the center of the thickness of the steel.
  • the pole density of the orientation may be 2.7 or more.
  • the average values of the pole densities of the ⁇ 100 ⁇ 011> to ⁇ 223 ⁇ 110> crystal orientation groups are ⁇ 100 ⁇ 011>, ⁇ 116 ⁇ 110>, ⁇ 114 ⁇ 110>, ⁇ 113 ⁇ 110>, ⁇ 112 ⁇ 110>, ⁇ 335 ⁇ 110>, and ⁇ 223 ⁇ 110> mean the pole density average value of the crystal orientation, and the thickness center of the steel material is 3/8t to 5/ with respect to the steel material thickness (t, mm) It means an area within the range of 8t.
  • Each crystal orientation pole density can be measured using a backscattered electron diffraction pattern (EBSD) of a scanning electron microscope, and a person skilled in the art can determine the present invention without difficulty without adding special technical means.
  • the azimuth pole density can be measured.
  • the plate-shaped lamellar pearlite structure is deformed by cold rolling without annealing, and the growth of a specific crystal orientation can be controlled according to the non-annealing reduction method.
  • the pole density average value of the ⁇ 100 ⁇ 011> to ⁇ 223 ⁇ 110> crystal orientation groups of the thickness center of the steel material is controlled to be 1.8 or more, and measured at the thickness center of the steel material.
  • the pole density of the crystal orientation can be controlled to be 2.5 or more.
  • the average long-short axis ratio of the pearlite block in the longitudinal section of the steel is also a factor affecting the spheroidization rate of cementite. Since the longitudinal elongation of pearlite occurs by non-annealing cold rolling, the average long-short axis ratio of the pearlite block in the longitudinal section of the steel is also a factor controlled by non-annealing cold rolling.
  • the average long-short axis ratio of the pearlite block observed in the longitudinal section of the steel can be controlled to 1.41:1 or more in order to promote a sufficient rate of spheroidization of cementite. . More preferably, the average long-short axis ratio of the pearlite block may be 1.43:1 or more.
  • the steel material for a tool according to an aspect of the present invention may have a surface hardness of HRB 104 to HRB 115.
  • a more preferable surface hardness may be HRB 108 or more or HRB 112 or less.
  • the spheroidization speed of the steel material for tools according to an aspect of the present invention is accelerated, so that spheroidization of carbides can be effectively completed even when the spheroidization annealing is performed in a temperature range of 650 to 700°C.
  • a preferred spheroidizing annealing time may be 10 hours to 30 hours.
  • the spheroidization completion condition of the carbide means that the number of spherical carbides having a long/short axis ratio of 1.2 or less of the carbide is 90% or more of the total number of carbides, and more preferably 95% or more.
  • the workability may be significantly reduced by the needle-shaped carbide that has not been spheroidized.
  • the spheroidization annealing temperature is less than 650° C., it is not easy to spheroidize the carbide due to the low temperature, and it may take an excessively long time for the spheroidization of the carbide.
  • the spheroidizing annealing temperature exceeds 700 °C, the size of the carbide becomes coarse and cracks easily occur at the interphase boundary, so that the workability may be poor.
  • the method of manufacturing a steel material for a tool by weight, carbon (C): 0.8 to 1.0%, silicon (Si): 0.1 to 0.3%, manganese (Mn): 0.3 to 0.5%, chromium (Cr): 0.1 ⁇ 0.3%, phosphorus (P): 0.03% or less, sulfur (S): 0.005% or less, reheating the slab containing the remaining iron (Fe) and unavoidable impurities and then hot rolling to provide hot-rolled steel sheet to do; and mechanically segmenting pearlite cementite included in the hot-rolled steel sheet by cold-rolling the hot-rolled steel sheet without annealing at a reduction ratio of 30-50%.
  • reheating of the slab may be performed. Since the slab alloy composition of the present invention corresponds to the alloy composition of the above-described steel, the description of the slab alloy composition of the present invention is replaced with a description of the alloy composition of the above-described steel.
  • the slab reheating temperature of the present invention may be applied to the conditions applied to normal slab reheating, as a non-limiting example, the slab reheating temperature of the present invention may be in the range of 1000 to 1300 °C.
  • the present invention can limit the upper limit of the hot rolling temperature range to 1150°C.
  • the present invention may limit the lower limit of the hot rolling temperature to 850 °C.
  • Hot-rolled steel can be wound in the temperature range of 600 ⁇ 650 °C.
  • the coiling temperature is excessively high, not only the thickness of the cementite in the pearlite structure becomes thick, but also shape defects may occur due to the phase transformation after coiling.
  • the present invention may limit the lower limit of the coiling temperature to 600°C.
  • the temperature deviation in the longitudinal direction of the hot-rolled coil may be controlled to 20° C. or less.
  • the pickling process can be selectively applied according to the surface quality of the uncoiled steel, and then the carbide (plate-like cementite) can be mechanically segmented by applying a mechanical external force to the steel.
  • the method of applying a mechanical external force to the steel material may be any method as long as it is a method capable of segmenting plate-shaped cementite, but preferably cold rolling may be applied.
  • cold rolling for mechanical segmentation of carbides is referred to as non-annealing cold rolling in order to distinguish it from conventional cold rolling for manufacturing a cold rolled steel sheet.
  • the plate-shaped cementite is segmented by applying a mechanical external force to the hot-rolled steel, it is possible to effectively improve the spheroidizing efficiency in the spheroidizing annealing performed later. That is, in the present invention, since the spheroidizing annealing is initiated in a state in which a large amount of finely segmented carbide is distributed, the carbide can be effectively spheroidized within a relatively short time.
  • the final specimen was prepared by performing cold rolling without annealing under the conditions shown in Table 2, and the rollability during cold rolling without annealing was evaluated according to the following criteria and described together in Table 2.
  • the polar density of the crystal azimuth group in the thickness center (3/8t to 5/8t region) of each non-annealed cold-rolled specimen was measured using a scanning electron microscope, and the values are also described in Table 2.
  • pole density 1 means the average pole density of the ⁇ 100 ⁇ 011> to ⁇ 223 ⁇ 110> crystal orientation groups
  • pole density 2 means the pole density of the ⁇ 332 ⁇ 113> crystal orientations.
  • the pearlite block was observed in the longitudinal section of each specimen using a scanning electron microscope, and the average long-short axis ratio of the pearlite block calculated through this was also described in Table 2.
  • the surface hardness of each specimen was measured according to ISO6508, and the Rockwell hardness (HRB) measured using this was also described in Table 2.
  • edge cracks of 10 mm or more occur, or 5 or more edge cracks of less than 10 mm occur
  • Spheroidizing annealing was performed under the conditions of Table 3 for each specimen. At this time, the spheroidization annealing time was commonly applied to 15 hours. After completion of the spheroidization annealing, carbides were observed in the cross section of each specimen using a scanning electron microscope, and the spheroidization rate was determined using the number ratio of carbides having a long/short axis ratio of 1.2 or less to the total number of carbides. Vickers hardness was measured by pressing the surface of the specimen with a load of 1 kg and a holding time of 10 seconds for the specimen after spheroidization annealing, and the values are described together in Table 3.
  • the height of the bur on the punching surface is measured through a stereoscopic optical microscope, and the specimen of thickness t is rotated at 90 degrees in the vertical direction of the rolling direction using a jig having a radius of curvature R.
  • the occurrence of cracks on the surface was judged, and the minimum radius of curvature at which cracks did not occur was measured to evaluate bending at 90 degrees, and the values are also listed in Table 3.
  • the specimens satisfying the alloy composition and process conditions of the present invention have excellent hardness properties and workability at the same time, whereas the specimens that do not satisfy any one of the alloy composition or process conditions of the present invention are It can be seen that both excellent hardness properties and workability are not compatible at the same time.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Steel (AREA)
PCT/KR2021/018722 2020-12-21 2021-12-10 공구용 강재 및 그 제조방법 WO2022139277A1 (ko)

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Citations (6)

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JPS4119283B1 (zh) * 1964-11-21 1966-11-09
JPH0987805A (ja) * 1995-09-26 1997-03-31 Sumitomo Metal Ind Ltd 高炭素薄鋼板およびその製造方法
JP3215891B2 (ja) * 1991-06-14 2001-10-09 新日本製鐵株式会社 冷間加工用棒鋼線材の製造方法
KR20080097121A (ko) * 2007-04-30 2008-11-04 한양대학교 산학협력단 강소성 가공을 이용한 중·고탄소강의 구상화 방법, 강소성장치 및 이로써 얻어진 구상화 중·고탄소강
KR20130068402A (ko) * 2011-12-15 2013-06-26 주식회사 포스코 고탄소 열연강판, 냉연강판 및 그 제조방법
KR20130120345A (ko) * 2012-04-25 2013-11-04 현대제철 주식회사 강판 및 그 제조 방법

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JPH0625379B2 (ja) * 1987-10-12 1994-04-06 住友金属工業株式会社 熱処理後靭性に優れた高炭素冷延鋼板の製造法
JP4412094B2 (ja) 2003-10-10 2010-02-10 Ｊｆｅスチール株式会社 高炭素冷延鋼板およびその製造方法
JP4738028B2 (ja) 2005-03-15 2011-08-03 日新製鋼株式会社 被削性に優れた中・高炭素鋼板の製造方法
KR101630951B1 (ko) * 2014-10-21 2016-06-16 주식회사 포스코 고상 접합성이 우수한 고탄소 열연강판 및 그 제조방법

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS4119283B1 (zh) * 1964-11-21 1966-11-09
JP3215891B2 (ja) * 1991-06-14 2001-10-09 新日本製鐵株式会社 冷間加工用棒鋼線材の製造方法
JPH0987805A (ja) * 1995-09-26 1997-03-31 Sumitomo Metal Ind Ltd 高炭素薄鋼板およびその製造方法
KR20080097121A (ko) * 2007-04-30 2008-11-04 한양대학교 산학협력단 강소성 가공을 이용한 중·고탄소강의 구상화 방법, 강소성장치 및 이로써 얻어진 구상화 중·고탄소강
KR20130068402A (ko) * 2011-12-15 2013-06-26 주식회사 포스코 고탄소 열연강판, 냉연강판 및 그 제조방법
KR20130120345A (ko) * 2012-04-25 2013-11-04 현대제철 주식회사 강판 및 그 제조 방법

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