WO2023008413A1 - Acier d'outil de travail à chaud doté de résistance et de ténacité excellentes à haute température - Google Patents

Acier d'outil de travail à chaud doté de résistance et de ténacité excellentes à haute température Download PDF

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Publication number
WO2023008413A1
WO2023008413A1 PCT/JP2022/028733 JP2022028733W WO2023008413A1 WO 2023008413 A1 WO2023008413 A1 WO 2023008413A1 JP 2022028733 W JP2022028733 W JP 2022028733W WO 2023008413 A1 WO2023008413 A1 WO 2023008413A1
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work tool
tool steel
hot work
less
max
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PCT/JP2022/028733
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English (en)
Japanese (ja)
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剛士 難波
章生 美谷
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山陽特殊製鋼株式会社
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Priority to KR1020247004389A priority Critical patent/KR20240041334A/ko
Priority to CN202280045221.3A priority patent/CN117561345A/zh
Publication of WO2023008413A1 publication Critical patent/WO2023008413A1/fr

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Classifications

    • 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
    • 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
    • C21D9/22—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for drills; for milling cutters; for machine cutting tools
    • 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
    • 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
    • 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
    • C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Definitions

  • the present invention relates to hot work tool steel excellent in high-temperature strength and toughness, which is used as hot tools such as hot forging dies.
  • Hot tools for example, molds for hot press forging, hot extrusion or die casting are generally made of Japanese Industrial Standard (JIS) SKD61 steel, and molds for hot hammer forging are made of JIS SKT4 steel is commonly used.
  • JIS SKD61 steel is a mold steel that has both strength and toughness at a relatively high level.
  • the toughness of JIS SKD61 steel is insufficient to suppress the extension of thermal fatigue cracks.
  • JIS SKT4 steel emphasizes toughness so that it can withstand a large impact from hammer forging, but it lacks wear resistance due to its low softening resistance.
  • the hardenability is low, causing a decrease in hardness at the center, and cracks and settling occur due to lack of strength. Furthermore, due to its low applicable hardness, it lacks wear resistance and strength, and is not suitable for hot press forging and hot extrusion applications.
  • Patent Document 1 does not consider the carbide precipitation state before the hot work tool steel is used as a hot work tool in hot (high temperature) conditions (hereinafter sometimes referred to as "before high temperature use”). , the high temperature strength was insufficient.
  • Patent Document 2 in mass%, C: 0.10 to 0.70%, Si: 0.10 to 2.00%, Mn ⁇ 2.00%, Cr ⁇ 7.00%, W and Mo (1/2 W + Mo): 0.20 to 12.00%, V ⁇ 3.00%, S: less than 0.005%, O is less than 30 ppm, and the balance is substantially Fe
  • a hot working tool having a composition of
  • Patent Document 2 neither the range of component fluctuations nor the state of carbide precipitation before high-temperature use was considered, and the toughness was insufficient.
  • Hot work tool steel exhibits softening resistance, that is, high-temperature strength, due to the precipitation of carbides (e.g., MC-based carbides, M 2 C-based carbides, etc., where M represents a metal element) and carbonitrides when used at high temperatures. can get.
  • carbides e.g., MC-based carbides, M 2 C-based carbides, etc.
  • M represents a metal element
  • the amount of carbides (e.g., MC-based carbides, M 2 C-based carbides, etc.) and carbonitrides during high-temperature use decreases, and high-temperature No strength.
  • the toughness is lowered.
  • the problem to be solved by the present invention is to limit the quenching conditions so that the M 23 C 6 -based carbides, which may remain after pressing and have a small contribution to high-temperature strength, are dissolved in the quenching process. At the same time, it is to obtain excellent toughness by controlling the width of component variation. Then, the solid solution of M 23 C 6 carbides in the quenching process increases the carbon content in the matrix, and fine carbides (such as MC It is to obtain excellent high -temperature strength by precipitating fine carbonitrides and fine carbonitrides. That is, the problem to be solved by the present invention is to provide a hot work tool steel having toughness and high temperature strength.
  • the present inventors have made intensive development, and as a result, by specifying the alloy composition, quenching conditions, carbide state and the range of composition fluctuation, heat It has been found that a tool steel can be obtained.
  • the present invention provides the following hot work tool steel.
  • Hot work tool steel wherein the number of carbides having an equivalent circle diameter of 1 ⁇ m or more per 10000 ⁇ m 2 in the hot work tool steel before use is 150 or less.
  • the hot work tool steel is represented by the following formulas 1-4: ([C] max- [C] min )/[C] ⁇ 1.0 (1) ([Cr] max-[Cr]min ) /[Cr] ⁇ 0.5 (2) ([Mo]max-[Mo] min )/[Mo] ⁇ 1.5 (3) ([V]max-[V] min )/[V] ⁇ 1.5 (4) [In the formula, [C] max and [C] min represent the maximum and minimum concentrations of C determined by concentration mapping of hot work tool steel by the electron probe microanalysis method, [Cr] max and [ Cr] min represent the maximum and minimum Cr concentrations, respectively, determined in concentration mapping of hot work tool steel by the electron probe microanalysis method, and [Mo] max and [Mo] min , respectively, [V] max and [V] min represent the highest and lowest concentrations of Mo determined in the hot work tool steel concentration mapping by the analysis method, and [V] max and [V] min are respectively the hot work tool steel concentration mapping by the electron probe microanalysis
  • a hot work tool steel having both high-temperature strength and toughness, such as a reduction in hardness from the initial hardness of 14 HRC or less, and an impact value of 70 J/cm 2 or more in a Charpy impact test. .
  • hot work tool steel before being used in hot as hot work tools such as hot forging dies
  • hot work tool steel before use The hot tool is, for example, for the purpose of improving workability, or for the purpose of structure control for obtaining desired properties after hot working.
  • the vicinity of the surface is exposed to a considerable temperature (for example, 180 to 1300° C.) due to heat transfer from the surface.
  • C 0.20% or more and 0.60% or less
  • C is a component for ensuring sufficient hardenability and for obtaining high-temperature strength, hardness and wear resistance by forming carbides and carbonitrides. If C is less than 0.20%, sufficient high-temperature strength cannot be obtained. On the other hand, when C exceeds 0.60%, solidification segregation is promoted, coarse carbides and carbonitrides are formed, and toughness is lowered. In addition, the resulting carbides remain undissolved during quenching, reducing the amount of precipitated carbides and carbonitrides when used as a hot work tool steel at high temperatures, and an improvement in high-temperature strength cannot be expected. Therefore, C should be 0.20% or more and 0.60% or less. Preferably, C is 0.40% or more and 0.60% or less.
  • Si 0.10% or more and less than 0.30%
  • Si is a component necessary for securing the deoxidizing effect and hardenability in steelmaking. If the Si content is less than 0.10%, sufficient effects are not exhibited. On the other hand, when Si is 0.30% or more, the toughness is lowered. Therefore, Si should be 0.10% or more and less than 0.30%. Preferably, Si is 0.10% or more and 0.20% or less.
  • Mn 0.50% or more and 2.00% or less
  • Mn is a component necessary for securing the deoxidizing effect and hardenability in steelmaking. If Mn is less than 0.50%, sufficient effects are not exhibited. If the Mn content is more than 2.00%, workability is lowered. Therefore, Mn should be 0.50% or more and 2.00% or less. Preferably, Mn is 0.50% or more and 1.40% or less.
  • Ni 0.50% or more and 2.50% or less
  • Ni is a component necessary for ensuring hardenability and improving toughness. If Ni is less than 0.50%, sufficient effects are not exhibited. Above 2.50% Ni, the cost becomes too high. Therefore, Ni should be 0.50% or more and 2.50% or less. Preferably, Ni is 1.10% or more and 2.30% or less.
  • Cr 1.6% or more and 2.6% or less Cr is a component necessary for ensuring sufficient hardenability. If Cr is less than 1.6%, sufficient hardenability cannot be obtained. On the other hand, when Cr is added in an amount of more than 2.6%, M 23 C 6 -based carbides mainly composed of Cr and Fe are excessively formed during quenching and tempering, deteriorating high-temperature strength, softening resistance and toughness. Therefore, Cr should be 1.6% or more and 2.6% or less. Preferably, Cr is 1.6% or more and 2.4% or less.
  • Mo 0.3% to 2.0% Mo is a useful component for obtaining precipitated carbides that contribute to hardenability, secondary hardening and high-temperature strength. If Mo is less than 0.3%, sufficient effects cannot be obtained. When Mo is more than 2.0%, not only does the effect saturate even if it is excessively added, but also the toughness is reduced due to coarse aggregation of carbides. Moreover, it becomes costly. Therefore, Mo should be 0.3% or more and 2.0% or less. Preferably, Mo is 0.3% or more and 1.7% or less.
  • V 0.05% or more and 0.80% or less V precipitates fine, hard carbides and fine, hard carbonitrides during tempering or when used as hot work tool steel at high temperatures, resulting in strength and wear resistance. It is a component that contributes to If V is less than 0.05%, these effects cannot be sufficiently obtained. If V is more than 0.80%, coarse carbides and carbonitrides crystallize during solidification, impairing toughness. Therefore, V is set to 0.05% or more and 0.80% or less. Preferably, V is 0.05% or more and 0.20% or less.
  • Value A 27.4 or more and 29.3 or less
  • the hot work tool steel before use has been quenched and tempered so that the value A is 27.4 or more and 29.3 or less.
  • Value A is calculated based on Equation A below.
  • Value A ([T] + 273) (log 10 [t] + 24) / 1000 (A)
  • [T] represents the quenching temperature (°C)
  • [t] represents the quenching temperature holding time (h). That is, when obtaining the value A, the numerical value of the quenching temperature (°C) is substituted for [T] in Formula A, and the numerical value of the quenching temperature holding time (h) is substituted for [t] in Formula A. do.
  • the value A is an index for ensuring the solid solubility of carbide by specifying the quenching temperature and holding time. If the value A is less than 27.4, solid solution of carbides due to quenching of the steel of the composition of the present invention becomes insufficient, resulting in insufficient toughness and high-temperature strength when used as a hot tool at high temperatures. On the other hand, if the value A exceeds 29.3, the prior austenite crystal grains become coarse, resulting in a decrease in toughness. Therefore, the value A is set to 27.4 or more and 29.3 or less.
  • Carbides e.g., MC-based carbides, M 2 C-based carbides, etc.
  • carbonitrides contribute to the improvement of high-temperature strength by precipitating during high-temperature use as hot work tool steel, so these are reduced. As a result, sufficient high-temperature strength cannot be obtained.
  • the number of carbides having an equivalent circle diameter of 1 ⁇ m or more per 10000 ⁇ m 2 is 150 or less.
  • the number of carbides having an equivalent circle diameter of 1 ⁇ m or more per 10,000 ⁇ m 2 is measured using a steel material after quenching and tempering, as described in the Examples.
  • the carbides to be measured are, for example, MC-based carbides, M2C-based carbides, M3C - based carbides , M7C3 - based carbides, M23C6 - based carbides, and the like.
  • M represents a metal element.
  • the number of carbides having an equivalent circle diameter of 1 ⁇ m or more per 10000 ⁇ m 2 is measured according to the method described in the Examples.
  • the hot work tool steel prior to use has the following formulas 1-4: ([C] max- [C] min )/[C] ⁇ 1.0 (1) ([Cr] max-[Cr]min ) /[Cr] ⁇ 0.5 (2) ([Mo]max-[Mo] min )/[Mo] ⁇ 1.5 (3) ([V]max-[V] min )/[V] ⁇ 1.5 (4) is preferably satisfied.
  • [C] max and [C] min are the highest concentration (% by mass) and lowest concentration (% by mass) of C determined by concentration mapping of hot work tool steel by the electron probe microanalysis method, respectively.
  • [Cr] max and [Cr] min are respectively the maximum Cr concentration (% by mass) and the minimum concentration (% by mass) determined by concentration mapping of hot work tool steel by the electron probe microanalysis method.
  • [Mo] max and [Mo] min represent the highest concentration (% by mass) and the lowest concentration (% by mass) of Mo determined by concentration mapping of hot work tool steel by the electron probe microanalysis method, respectively
  • [V] max and [V] min respectively represent the highest concentration (% by mass) and lowest concentration (% by mass) of V determined by concentration mapping of hot work tool steel by the electron probe microanalysis method
  • [C ] represents the C content (% by mass) determined by the composition analysis of the hot work tool steel by the infrared absorption method
  • [Cr], [Mo] and [V] are each determined by the fluorescent X-ray analysis method. The contents of Cr, Mo and V (% by mass) determined by composition analysis of hot work tool steel are shown.
  • the value of ([X] max - [X] min )/[X] is an index of the variation in composition due to internal segregation of each alloying element.
  • the value of ([X] max - [X] min )/[X] may be referred to as "the width of the component variation of the alloying element X". If the variation in composition due to internal segregation of each alloying element is large (that is, the value of ([X] max - [X] min )/[X] is large), the difference in distribution of carbides and carbonitrides and the difference in deformability Since it becomes large, it will reduce toughness. Therefore, it is preferable to regulate the range of component variation for C, Cr, Mo and V. That is, the hot work tool steel before use preferably satisfies all of formulas 1 to 4.
  • composition analysis of the steel material by the infrared absorption method analysis of the content of C
  • composition analysis of the steel material by the fluorescent X-ray analysis method analysis of the content of Cr, Mo and V
  • C determined by the infrared absorption method [C] is the content (% by mass) of Cr
  • [Cr] and [Mo] and [V] are the contents (% by mass) of Cr, Mo and V determined by fluorescent X-ray analysis, respectively.
  • Concentration mapping by the electron probe microanalysis method, composition analysis by the infrared absorption method and fluorescent X-ray analysis method are performed according to the methods described in Examples.
  • the application of the soaking treatment in which the center of the steel ingot is soaked for 10 to 40 hours in the range of 1225°C to 1300°C makes it possible to effectively reduce the value of component fluctuation.
  • Invention Examples Nos. 1 to 28 and Comparative Examples Nos. 29 to 40 are steels each having the chemical composition shown in Table 1 and the balance being Fe and inevitable impurities. 100 kg of each steel was melted in a vacuum induction melting furnace (VIM) and cast into ingots. Invention Steel No. For Nos. 1 to 20, soaking treatment was performed under the above conditions (that is, soaking treatment in which the center of the steel ingot was soaked at 1225° C. to 1300° C. for 10 to 40 hours). After that, these ingots were heated to 1220° C. and forged into square bars of 15 mm square (15 mm ⁇ 15 mm).
  • EPMA was performed under the following conditions.
  • Analyzer EPMA1600 manufactured by Shimadzu Corporation Accelerating voltage: 15 kV Beam diameter: 2 ⁇ m
  • Scan mode Stage scan Step size (measured area once): 2.5 ⁇ m ⁇ 2.5 ⁇ m Number of steps (number of measurement points): 200 x 200 Measurement time (1 step): 50ms Analysis crystal: C LS12L Mo PET Cr, V LIF
  • composition analysis analysis of C content
  • composition analysis analysis of Cr, Mo and V content
  • composition analysis by the infrared absorption method was carried out based on the "infrared absorption method" of JIS Z 2615: 2015 “general rules for carbon determination method of metal materials” using Horiba's carbon sulfur analyzer EMIA-Expert.
  • Composition analysis by X-ray fluorescence spectroscopy was performed based on JIS G 1256:2013 "Iron and steel - X-ray fluorescence analysis method" using MXF-2400 manufactured by Shimadzu Corporation.
  • the highest concentration (% by mass) and the lowest concentration (% by mass) of the alloying element X determined by concentration mapping are set to [X] max and [X] min , respectively, and the content of C (% by mass) determined by the infrared absorption method ) is [C], the contents of Cr, Mo and V (% by mass) determined by fluorescent X-ray analysis are respectively [Cr], [Mo] and [V], and ([X] max - [ The value of X] min )/[X] was calculated as the width of component variation.
  • Tables 3A to 3D show the evaluation results of the width of component variation.
  • Comparative example no. No. 29 had a low high-temperature strength due to a small amount of C. Comparative example no. In No. 30, the amount of C was large, the number of carbides having an equivalent circle diameter of 1 ⁇ m or more was large, and the range of component fluctuation was large, so the toughness and high-temperature strength were low. Comparative example no. In No. 31, the amount of Si was large and the toughness was low. Comparative example no. In No. 32, the amount of Ni was small and the toughness was low. Comparative example no. In No. 33, the Cr content was large, the number of carbides having an equivalent circle diameter of 1 ⁇ m or more was large, and the range of component fluctuation was large, so the toughness and high-temperature strength were low.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
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Abstract

La présente invention a pour but de fournir un acier d'outil de travail à chaud présentant une résistance et une ténacité excellentes à haute température. À cet effet, la présente invention concerne un acier d'outil de travail à chaud comprenant, en % en masse : 0,20 % à 0,60 % de C ; au moins 0,10 % mais moins de 0,30 % de Si ; 0,50 % à 2,00 % de Mn ; 0,50 % à 2,50 % de Ni ; 1,6 % à 2,6 % de Cr ; 0,3 % à 2,0 % de Mo ; 0,05 % à 0,80 % de V ; le reste étant du Fe et des impuretés inévitables. L'acier d'outil de travail à chaud se trouve dans un état ayant été trempé et revenu, de sorte qu'une valeur A de la formule A, calculée sur la base de la formule A : valeur A = ([T]+273)(log10[t]+24)/1000 (où [T] représente la température de trempe (°C) et [t] représente le temps (h) de rétention de température de trempe), soit comprise entre 27,4 et 29,3 ; et que le nombre de carbures présentant un diamètre circulaire équivalent égal ou supérieur à 1 µm pour 10 000 μm2 de l'acier d'outil de travail à chaud avant l'utilisation soit égal ou inférieur à 150.
PCT/JP2022/028733 2021-07-27 2022-07-26 Acier d'outil de travail à chaud doté de résistance et de ténacité excellentes à haute température WO2023008413A1 (fr)

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KR1020247004389A KR20240041334A (ko) 2021-07-27 2022-07-26 고온 강도 및 인성이 우수한 열간 공구강
CN202280045221.3A CN117561345A (zh) 2021-07-27 2022-07-26 高温强度和韧性优异的热作工具钢

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JP2021122796A JP7220750B1 (ja) 2021-07-27 2021-07-27 高温強度と靭性に優れた熱間工具鋼
JP2021-122796 2021-07-27

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Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH11106868A (ja) * 1998-07-24 1999-04-20 Hitachi Metals Ltd 熱間加工用工具鋼
JP2013213255A (ja) * 2012-04-02 2013-10-17 Sanyo Special Steel Co Ltd 熱間金型鋼
CN104928586A (zh) * 2015-06-30 2015-09-23 宝山钢铁股份有限公司 一种热冲压模具钢及其生产方法
JP2019019397A (ja) * 2017-07-20 2019-02-07 山陽特殊製鋼株式会社 被削性に優れたプリハードン熱間工具鋼
JP2019116678A (ja) * 2017-04-19 2019-07-18 大同特殊鋼株式会社 プレハードン鋼材、並びに、金型及び金型部品
JP2021080492A (ja) * 2019-11-14 2021-05-27 山陽特殊製鋼株式会社 高温強度と靭性に優れた熱間工具鋼

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP6903507B2 (ja) 2017-07-15 2021-07-14 山陽特殊製鋼株式会社 焼入れ性および靱性に優れた熱間工具鋼

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH11106868A (ja) * 1998-07-24 1999-04-20 Hitachi Metals Ltd 熱間加工用工具鋼
JP2013213255A (ja) * 2012-04-02 2013-10-17 Sanyo Special Steel Co Ltd 熱間金型鋼
CN104928586A (zh) * 2015-06-30 2015-09-23 宝山钢铁股份有限公司 一种热冲压模具钢及其生产方法
JP2019116678A (ja) * 2017-04-19 2019-07-18 大同特殊鋼株式会社 プレハードン鋼材、並びに、金型及び金型部品
JP2019019397A (ja) * 2017-07-20 2019-02-07 山陽特殊製鋼株式会社 被削性に優れたプリハードン熱間工具鋼
JP2021080492A (ja) * 2019-11-14 2021-05-27 山陽特殊製鋼株式会社 高温強度と靭性に優れた熱間工具鋼

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TW202321480A (zh) 2023-06-01

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