US20100193089A1 - Hot-working tool steel having excellent toughness and high-temperature strength and method for production thereof - Google Patents

Hot-working tool steel having excellent toughness and high-temperature strength and method for production thereof Download PDF

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US20100193089A1
US20100193089A1 US12/440,406 US44040607A US2010193089A1 US 20100193089 A1 US20100193089 A1 US 20100193089A1 US 44040607 A US44040607 A US 44040607A US 2010193089 A1 US2010193089 A1 US 2010193089A1
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hot
steel
working tool
tool steel
steel according
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US12/440,406
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Kouta Kataoka
Hideshi Nakatsu
Yasushi Tamura
Masayuki Nagasawa
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Proterial Ltd
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Hitachi Metals Ltd
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Assigned to HITACHI METALS, LTD. reassignment HITACHI METALS, LTD. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: NAGASAWA, MASAYUKI, NAKATSU, HIDESHI, TAMURA, YASUSHI, KATAOKA, KOUTA
Publication of US20100193089A1 publication Critical patent/US20100193089A1/en
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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
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • 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
    • C21D6/002—Heat treatment of ferrous alloys containing Cr
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium 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
    • C22C38/44—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
    • 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
    • C21D2211/001—Austenite
    • 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
    • C21D2211/002—Bainite
    • 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
    • C21D2211/004—Dispersions; Precipitations
    • 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
    • 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
    • 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
    • C21D6/02—Hardening by precipitation

Definitions

  • the invention relates to a hot-working tool steel having improved toughness and high-temperature strength, which is suitable for many kinds of hot-working tools such as press dies, forging dies, die-casting dies, and extruding tools, and a method for producing the hot-working tool steel.
  • a hot-working tool contacts a high-temperature workpiece or a hard workpiece during use, it is required to have both strength and toughness to be resistant to thermal fatigue and impact. Therefore, in the field of hot-working tool, an alloy tool steel, such as SKD 61 of JIS steel grade, has been conventionally employed. Recently, the workpiece is processed at higher temperature due to shortening of the production time of the product by using the hot-working tool and to work an intricate shaped product.
  • the hot-working tool such as a die, has become larger in order to work simultaneously a plurality of products. Therefore, the material for hot-working tool is required to ensure a further improved high-temperature strength and a toughness even in the interior of a large-size tool.
  • An object of the invention is to provide a hot-working tool steel surely having improved toughness and high-temperature strength and a method for production thereof.
  • the inventors found that the structure after quenching exerts a great influence on the toughness and high-temperature strength, and identified a structure after quenching that is suitable for providing both of excellent toughness and high-temperature strength.
  • the inventors found that there exists a very narrow preferred composition range where the suitable structure after quenching can be obtained by controlling the each element so as to be in an optimum range, and finally arrived at the invention.
  • the invention provides a hot-working tool steel having excellent toughness and high-temperature strength, consisting essentially of, by mass percent, 0.34 to 0.40% of carbon, 0.3 to 0.5% of Si, 0.45 to 0.75% of Mn, 0 to less than 0.5% of Ni, 4.9 to 5.5% of Cr, total amount of Mo and half of tungsten (Mo+1/2W) of 2.5 to 2.9% wherein Mo and W may be contained singly or in combination, and 0.5 to 0.7% of V, the balance being Fe and unavoidable impurities.
  • the hot-working tool steel according to the invention may be tempered to have a hardness of not lower than 40HRC. Especially, the steel has an effect of providing both of excellent toughness and high-temperature strength in a high hardness of not lower than 43HRC, particularly not lower than 45HRC.
  • the steel preferably has a hardness of not higher than 49HRC.
  • one or more kinds of elements of C, Si, Mn, Ni, Cr, Mo, W and V constituting this steel meet the conditions of the following narrow composition ranges. Needless to say, it is desirable that all elements meet the conditions.
  • the invention also provides the hot-working tool steel having the above-described composition, and the cross-sectional structure thereof after quenching contains a granular structure and an acicular structure, wherein the area percentage of the granular structure (A %) is not more than 45%; the area percentage of the acicular structure (B %) is not more than 40%; and the volume percentage of retained austenite (C %) is 5 to 20%.
  • the invention provides a method of production of a hot-working tool steel having excellent toughness and high-temperature strength, wherein the hot-working tool steel is tempered so that a value X determined by the following relational expression between tempered hardness (HRC) and the percentages of the structures is not less than 40.
  • the tempered hardness is set at 40 to 49HRC, preferably 43 to 49HRC, and further preferably 45 to 49HRC.
  • both of the toughness and high-temperature strength of a hot-working tool steel can be provided at a very high level.
  • This effect is achieved to the maximum when the steel is tempered so as to have hardness of not lower than 40HRC, for example, not lower than 43HRC, more preferably not lower than 45HRC, and still further preferably not lower than 46HRC. Therefore, the invention provides a technique that is effective for practical use of a hot-working tool steel capable of being applied to many kinds of high-temperature applications and environments.
  • one important aspect of the invention is to define the contents of elements controlled in the optimum range.
  • the aspect of the invention is to find the existence of a narrow composition range which is capable of providing both toughness and high-temperature strength at a high level even by any quenching method, for example, in addition to a quench cooling rate in a wide range in the conventional production method, by controlling the contents of elements into a limited range, further desirably, by recognizing the later-described quenched structure.
  • Carbon (C) is an essential and important element for hot-working tool steel, some of which solid-solute in a matrix to provide strength and some of which form carbide to enhance wear resistance and seizure resistance. Also, in the case where carbon is an interstitial atom forming a solid solution, and is added together with a substitutional atom having a high affinity with carbon, such as Cr, is expected an I (interstitial atom)—S (substitutional atom) effect, that is an effect that carbon acts as drag resistance of solute atom to enhance strength. However, if the carbon content is not more than 0.34 mass %, hardness and wear resistance sufficient for a tool element cannot be secured. On the other hand, since the excessive addition of carbon leads to a decrease in toughness and hot strength, the upper limit of carbon content is defined to be 0.40 mass %. The carbon content is preferably 0.35 to 0.39%, further preferably 0.36 to 0.38%.
  • Si is a deoxidizing agent in the steel making process and is also an element for enhancing the machinability. To achieve these effects, not less than 0.3 mass % of Si should be added. If the addition is too much, however, the later-described acicular structure develops, thereby decreasing the toughness. Also, much addition of Si restrains the precipitation of cementite-based carbide in the bainite structure at quenching so that the precipitation, coagulation, and coarsening of alloy carbide during tempering are promoted indirectly, thereby decreasing the high-temperature strength. Therefore, the Si content is limited to not more than 0.5 mass %, preferably 0.35 to 0.45%.
  • Manganese (Mn) has effects of enhancing the hardenability and restraining the production of ferrite to obtain a proper quenched/tempered hardness. If Mn is present in the structure as a nonmetallic inclusion MnS, it has a great effect of improving the machinability. To achieve these effects, not less than 0.45 mass % of Mn is added. If the addition is too much, the viscosity of matrix is increased, thereby decreasing the machinability. Therefore, the Mn content is limited to not more than 0.75 mass %, preferably 0.5 to 0.7%.
  • Nickel (Ni) is an element for restraining the production of ferrite. Also, Ni is an additional element that is important for providing excellent hardenability together with C, Cr, Mn, Mo, W, etc., achieving an effect of restraining the production of the later-described acicular structure even in the case where the cooling rate of quenching is low, forming a structure mainly composed of martensite, and preventing the toughness from decreasing. Furthermore, Ni has an effect of improving toughness essentially in the matrix. Therefore, for example, not less than 0.01% of Ni is preferably added. It is most important in the invention to regulate strictly the upper limit of Ni, even if Ni is added.
  • the Ni content is limited to not more than 0.5 mass %.
  • the Ni content is regulated to not more than 0.3 mass %.
  • Chromium (Cr) is an element having effects of enhancing the hardenability and of strengthening the matrix and improving the wear resistance by forming carbide, and also is an element essential for the hot-working tool steel according to the invention, which contributes to the improvement in resistance to softening in temper and high-temperature strength.
  • Cr Chromium
  • the Cr content is preferably 5.0 to 5.4%, further preferably 5.1 to 5.3%.
  • Molybdenum (Mo) and tungsten (W) can be added singly or in combination to enhance the hardenability, to provide strength by precipitating fine carbide by means of tempering, and to improve the softening resistance. Since W has an atomic weight about two times that of Mo, the content can be specified by Mo+1/2W (naturally, either one may be added, or both of the two may be added). To achieve the above-mentioned effects, not less than 2.5 mass % of (Mo+1/2W) should be added. Since the excessive addition thereof leads to a decrease in machinability and a decrease in toughness caused by the development of the later-described acicular structure, the content of (Mo+1/2W) is not more than 2.9 mass %. Preferably, the content of (Mo+1/2W) is 2.6 to 2.8%.
  • Vanadium (V) forms carbide having effects of strengthening the matrix and improving the wear resistance. Also, it enhances the resistance to softening in temper and restrains the coarsening of crystal grains. It also contributes to the improvement in toughness. To achieve these effects, not less than 0.5 mass % of V should be added. Since the excessive addition of V leads to a decrease in machinability and toughness, the content of V is not more than 0.7 mass %. Preferably, the content of V is 0.55 to 0.65%.
  • the main elements that possibly remain as unavoidable impurities are P, S, Co, Cu, Al, Ca, Mg, O, N, and the like. In order to attain the effects of the invention to the maximum, it is desirable that the contents of these elements be as low as possible. On the other hand, for the purpose of achieving additional effects such as the mode control of inclusion and the improvement in mechanical properties or manufacturing efficiency, a minute amount of these elements can be also contained and/or added.
  • the invention preferably define a feature from an approach in term of the structure. Specifically, by studying the “structural factors” having an influence on the mechanical properties of alloy tool steel, the optimum structure is also defined in addition to the optimum composition range, which is the very narrow range of the invention. That is to say, the hot-working tool steel in accordance with the invention having the above-described composition contains a granular structure and an acicular structure each having the following area percentage in the cross-sectional structure after quenched.
  • a “quenched structure” means a structure mainly composed of martensite and/or bainite, which is obtained by cooling from an austenite temperature region, as is defined ordinarily.
  • the quenched structure of the invention is essentially composed of the above-mentioned martensite and/or bainite and a small amount of retained austenite, and each of the above-mentioned granular structure and acicular structure is composed of a part of the martensite and/or bainite.
  • the granular structure and acicular structure defined in the quenched structure according to the invention is different from those specified by the definition of feather-like bainite (upper bainite) and needle-like bainite (lower bainite), which are used for ordinary classification of bainite.
  • the granular structure according to the invention is a structure in which many fine carbides grow in several directions in the structure.
  • the granular structure according to the invention takes a “granular shape” on the whole as shown in its name. Since the granular structure is produced even at a cooling rate as high as air-cooling rate of a small sample of about 10 mm cubic, it is still more difficult to reduce the granular structure when a practical steel ingot is quenched. However, if the granular structure occupies most of the structure, the toughness decreases.
  • the area percentage of the granular structure in the quenched structure is defined to be preferably not more than 45%, further preferably not more than 40%, and still further preferably not more than 30%.
  • the acicular structure of the invention is a structure in which many long carbides as compared with those in the granular structure, grow in the structure in a direction.
  • the acicular structure according to the invention takes a “needle shape”.
  • this acicular structure is generated at a cooling rate lower than the cooling rate at which the granular structure begins to be generated, it is still difficult to reduce the acicular structure when a practical steel ingot is quenched.
  • the area percentage of the acicular structure in the quenched structure is defined to be preferably not more than 40%, further preferably not more than 25%.
  • the granular structure and the acicular structure of the invention can be distinguished and quantitatively determined by visual observation of its cross section by utilizing the difference in shape. Specifically, in any structure cross section, both the structures having poor corrosion resistance as compared with the martensite matrix in which no carbide is precipitated are corroded preferentially by for example, the selective potentiostatic etching by electrolytic dissolution method (SPEED method).
  • FIG. 1 is a micrograph obtained by observing the corroded surface by using a scanning electron microscope (magnification of 5000).
  • FIGS. 2 and 3 as supplementary schematic views, the granular structure and the acicular structure of the invention can be distinguished and quantitatively determined.
  • FIG. 1 shows one field of example steel 6 of the invention described in example 3 later, having 27 area % of the granular structure and 30 area % of the acicular structure.
  • FIG. 4 shows one field of view of conventional steel 31 described in example 3 later, having 44 area % of the granular structure and 16 area % of the acicular structure.
  • retained austenite is important.
  • Retained austenite is a structure preferably to be reduced since it deteriorates the strength properties.
  • a proper amount of the retained austenite contributes to improve toughness. Therefore, in the invention, the volume percentage of retained austenite in the quenched structure is preferably 5 to 20%, further preferably not less than 10%.
  • a quantitative analysis of the retained austenite can be performed by an ordinary method, for example, by volume percentage measurement utilizing diffracted intensity obtained by the X-ray diffractometry using e.g. an electropolished sample.
  • the above-described requirements for composition and quenched structure are met, and then a target hardness in tempering of the next process is determined, and then tempering is performed such that X in the following relational expression is not less than 40. Thereby, a hot-working tool steel having excellent toughness is produced.
  • the above expression clarifies specific influence parameters as a result of a study on the influence of quenched structure and tempered hardness on the toughness after tempering.
  • the reduction in granular structure and acicular structure is effective.
  • the reduction in acicular structure having a larger negative coefficient in the expression is especially effective.
  • a proper amount of retained austenite acts advantageously to secure the toughness because the retained austenite has a large positive coefficient in the expression.
  • the target hardness may be set, for example, at not less than 40HRC that effectuates the hot-working tool steel.
  • the hot-working tool steel meeting the requirements for composition and quenched structure configuration of the invention will secure a sufficient toughness, even if the target hardness is higher, for example, 43HRC or more, or 45HRC or more.
  • the tempered hardness is preferably kept to not more than 49HRC in order to maintain a remarkable toughness.
  • Table 1 gives chemical compositions of steels of the invention, comparative steels, and conventional steels.
  • the comparative steels have a chemical compositions deviating from the limited narrow composition range of the invention.
  • the conventional steels are hot-working tool steels generally used at present, which naturally have chemical compositions out of the composition range of the invention.
  • comparative steels, and conventional steels, steels having a thickness of 30 mm and a width of 60 mm were produced as followed.
  • Steel ingots were produced by melting by 10 kg in a vacuum induction furnace and then homogenized by heat treatment at 1250° C. for five hours. They were then hot forged at 1150° C. After annealed at 860° C., they were quenched from 1030° C. The quenching was performed by cooling in pressurized gas.
  • the time required for cooling the steel from the quenching temperature (1030° C.) to an intermediate temperature (525° C.) between the quenching temperature and room temperature (20° C.) is defined as a “half cooling time”.
  • half cooling is expressed to be 10 minutes.
  • Some steels were cooled for about three minutes in half cooling time as “rapid cooling”, and some were cooled for about 40 minutes in half cooling time as a part in which the cooling rate is low, such as the central part of a large-size steel. Subsequently, the steels were tempered at various temperatures so as to have a hardness of 46HRC.
  • comparative steel 23 having a composition out of the optimum composition of the invention provides excellent toughness but low high-temperature strength since it contains too high Ni content.
  • all of steels of the invention have high high-temperature strength.
  • the measured granular structures of steel of the invention 6 and conventional steel 31 are shown in schematic views of FIGS. 2 and 5 , respectively, and the measured acicular structures of steel of the invention 6 and conventional steel 31 are shown in schematic views of FIGS. 3 (excluding “x” mark) and 6 , respectively.
  • Three fields of view were measured on each structure of each sample, and the mean value was made as an area percentage.
  • the above-mentioned sample was polished again, and then finished by electropolishing to measure the quantity of retained austenite through the X-ray diffractometry. The results of the above measurements are collectively given in Table 4.
  • comparative steel 22 and comparative steel 26 have low Mo content but too high Ni content, the granular structure develops so that the impact value is low.
  • comparative steel 26 shows a tendency to generate the acicular structure since the Si content thereof is high in addition thereto.
  • the quenched structure of steel of the invention 6 having optimally controlled chemical composition has a developed acicular structure, less granular structure, and much retained austenite effective in improving the toughness.
  • the balance of structures (that is, the value X) is also excellent.
  • the quenched structure of comparative steel 23 which has high toughness due to high Ni content meets a condition that the value X is not less than 40 although it has much granular structure.
  • comparative steel 23 has low high-temperature strength as described above.
  • a hot-working tool steel having improved toughness and high-temperature strength according to the invention can be applied not only to many kinds of hot-working tools such as press dies, forging dies, die-casting dies, and extruding tools but also to hot-working tool members such as dies to which high load is applied.
  • FIG. 1 is a cross-sectional micrograph showing an example of the quenched structure of a hot-working tool steel according to the invention
  • FIG. 2 is schematic view selecting a granular structure from the quenched structure shown in FIG. 1 ;
  • FIG. 3 is schematic view selecting an acicular structure from the quenched structure shown in FIG. 1 ;
  • FIG. 4 is a cross-sectional micrograph showing an example of the quenched structure of a hot-working tool steel of a comparative example
  • FIG. 5 is schematic view selecting a granular structure from the quenched structure shown in FIG. 4 ;
  • FIG. 6 is schematic view selecting an acicular structure from the quenched structure shown in FIG. 4 .

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PCT/JP2007/067915 WO2008032816A1 (fr) 2006-09-15 2007-09-14 Acier à outils pour formage à chaud présentant d'excellentes qualités de rigidité et de résistance à des températures élevées, et son procédé de production

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* Cited by examiner, † Cited by third party
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US20100150772A1 (en) * 2008-11-20 2010-06-17 Boehler Edelstahl Gmbh & Co. Kg Hot-forming steel alloy
WO2018182480A1 (en) * 2017-03-29 2018-10-04 Uddeholms Ab Hot work tool steel
US10533235B2 (en) 2014-07-23 2020-01-14 Hitachi Metals, Ltd. Hot-working tool material, method for manufacturing hot-working tool, and hot-working tool
CN113604730A (zh) * 2021-07-05 2021-11-05 昆山东大特钢制品有限公司 一种耐高温和高韧性的热作模具钢及其生产工艺
CN114535944A (zh) * 2021-12-15 2022-05-27 河北工业职业技术学院 一种短流程贝氏体热作模具及其制备方法
US11535917B2 (en) 2019-12-03 2022-12-27 Daido Steel Co., Ltd. Steel for mold, and mold

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JP5515442B2 (ja) * 2009-06-16 2014-06-11 大同特殊鋼株式会社 熱間工具鋼及びこれを用いた鋼製品
EP2682491B1 (en) * 2011-03-03 2018-07-04 Hitachi Metals, Ltd. Hot work tool steel having excellent toughness, and process of producing same
EP2662460A1 (en) * 2012-05-07 2013-11-13 Valls Besitz GmbH Tough bainitic heat treatments on steels for tooling
KR20150121155A (ko) * 2013-03-01 2015-10-28 로발마, 에쎄.아 높은 열 확산도, 높은 인성 및 열처리 도중 균열 위험이 낮은 공구강
WO2015182586A1 (ja) 2014-05-28 2015-12-03 日立金属株式会社 熱間工具材料および熱間工具の製造方法
CN114000059B (zh) * 2018-10-05 2022-08-16 日立金属株式会社 热作工具钢及热作工具
KR20240029270A (ko) 2022-08-26 2024-03-05 현대자동차주식회사 열간 공구강 및 이의 제조방법

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS58123861A (ja) * 1982-01-18 1983-07-23 Daido Steel Co Ltd 熱間工具鋼
JP2700264B2 (ja) * 1988-12-30 1998-01-19 愛知製鋼株式会社 熱間工具鋼
JPH08188852A (ja) * 1995-01-04 1996-07-23 Kobe Steel Ltd 鍛造金型及びその製造方法
SE511758C2 (sv) * 1998-03-27 1999-11-22 Uddeholm Tooling Ab Stålmaterial för varmarbetsverktyg
JP2003268500A (ja) * 2002-03-15 2003-09-25 Daido Steel Co Ltd 被削性に優れた熱間工具鋼及びその製造方法
JP2006104519A (ja) * 2004-10-05 2006-04-20 Daido Steel Co Ltd 高靭性熱間工具鋼およびその製造方法

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20100150772A1 (en) * 2008-11-20 2010-06-17 Boehler Edelstahl Gmbh & Co. Kg Hot-forming steel alloy
AU2009238307B2 (en) * 2008-11-20 2013-12-19 Bohler Edelstahl Gmbh & Co Kg Hot-forming steel alloy
AU2009238307C1 (en) * 2008-11-20 2014-03-13 Bohler Edelstahl Gmbh & Co Kg Hot-forming steel alloy
US10533235B2 (en) 2014-07-23 2020-01-14 Hitachi Metals, Ltd. Hot-working tool material, method for manufacturing hot-working tool, and hot-working tool
WO2018182480A1 (en) * 2017-03-29 2018-10-04 Uddeholms Ab Hot work tool steel
US11535917B2 (en) 2019-12-03 2022-12-27 Daido Steel Co., Ltd. Steel for mold, and mold
CN113604730A (zh) * 2021-07-05 2021-11-05 昆山东大特钢制品有限公司 一种耐高温和高韧性的热作模具钢及其生产工艺
CN114535944A (zh) * 2021-12-15 2022-05-27 河北工业职业技术学院 一种短流程贝氏体热作模具及其制备方法

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