EP2682491B1 - Hot work tool steel having excellent toughness, and process of producing same - Google Patents

Hot work tool steel having excellent toughness, and process of producing same Download PDF

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Publication number
EP2682491B1
EP2682491B1 EP12752790.1A EP12752790A EP2682491B1 EP 2682491 B1 EP2682491 B1 EP 2682491B1 EP 12752790 A EP12752790 A EP 12752790A EP 2682491 B1 EP2682491 B1 EP 2682491B1
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Prior art keywords
steel
work tool
hot work
less
toughness
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German (de)
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French (fr)
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EP2682491A1 (en
EP2682491A4 (en
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Kouta Kataoka
Yousuke Nakano
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Proterial Ltd
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Hitachi Metals Ltd
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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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
    • C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
    • C21C7/0006—Adding metallic additives
    • 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
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • 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
    • 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
    • C22C38/24—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

Definitions

  • the present invention relates to a hot work tool steel having improved toughness, which is optimally used for various kinds of hot work tools such as stamping dies, forging dies, die-casting molds and extrusion tools, and a process of producing the same.
  • Patent Literature 2 is a low-carbon steel of excellent machinability having a composition consisting of, by mass, 0.001-1.5% C, ⁇ 3% Si, 0.01-3% Mn, 0.001-0.2% P, 0.0001-1.2% S, 0.001-0.5% Zn, 0.0001-0.02% N, and 0.0005-0.05% O, and furthermore 0.002-0.5% Sn and/or 0.0005-0.5% B.
  • the present inventors have conducted diligent studies on elements, which have not been positively used as an alloying element in the field of steel materials, instead of expensive and special elements, and consequently found that toughness can be significantly improved by adding Zn, which conventionally has been treated as an impurity, in a predetermined content range (see Patent Literature 3). That is, the hot work tool steel contains, in mass%, C: 0.3% to less than 0.55%, Si: not more than 1.5%, Mn: not more than 1.5%, and Cr: 3.00 to 5.65%, wherein the hot work tool steel contains Zn: 0.001 to 0.015%. 81-72857EP/AS
  • Patent Literature 3 The technique of adding Zn proposed in Patent Literature 3 is effective as a novel method for improving the toughness of a hot work tool steel. Further, utilizing the method of Patent Literature 3 allows scraps of Zn-plated steel to be used as a recycling raw material, which is also suitable for reducing an environmental load. While focusing on the toughness improving effect by positive addition of Zn, the present inventors have studied on the possibility to compensate for the deterioration of toughness due to other impurity elements.
  • the permissible amount of those impurity elements can be appropriately increased, it becomes possible to reduce the amount of energy usage required for removing impurities while increasing the usage rate of low level scraps with a high impurity content, the discharge amount of which is expected to increase in the future, thereby further reducing a load on the environment in the production process of hot work tool steels.
  • the present inventors have investigated the effects of impurity elements contained in hot work tool steels on the toughness thereof and the environment. Consequently, they have found that in particular P (phosphorus) is the element that significantly reduces the toughness of the hot work tool steel, and also the element that takes a large amount of energy to be removed and, for those reasons, hinders promotion of usage of low grade scraps to impose a large load on the environment. Accordingly, to reduce the environmental load, the present inventors have studied a method of maintaining sufficient toughness even when the permissible amount of P is increased. Consequently, they have determined that deterioration of toughness due to increase in P content can be ceased by adding an appropriate amount of Zn with respect to the P content. Then, the present inventors have arrived at the present invention by making clear the quantitative relationship between P and Zn in which the supplemental effect of toughness can be sufficiently utilized, and a method of adjusting the chemical components suitable for achieving the quantitative relationship.
  • the present invention is a hot work tool steel having excellent toughness, including, in mass%, C: 0.3% to less than 0.6%, Si: 0.2 to 1.5%, Mn: 1.0 to 1.5%, at least one of Mo and W, wherein an amount of (Mo + 1/2W) is 1.0 to 3.5%, and Cr: 3.0 to less than 6.0%, characterized in that Zn is more than 0.0025 to 0.025% and P is not less than 0.005%, and Zn/P is more than 0.5.
  • P is not less than 0.01%.
  • V not more than 1.5% may be further included.
  • the present invention is a hot work tool steel containing: C: 0.3 to less than 0.6%, Si: 0.2 to 1.5%, Mn: 1.0 to 1.5%, Ni: not more than 1.5% (including 0%), Cr: 3.0 to less than 6.0%, Mo and W singly or in combination wherein an amount of (Mo + 1/2W) is 1.0 to 3.5%, V: not more than 1.5%, Nb: not more than 0.3% (including 0%), Co: not more than 5.0% (including 0%), Zn: more than 0.0025 to 0.025%, P: not less than 0.005%, wherein Zn/P is more than 0.5, and the balance is composed of Fe and inevitable impurities.
  • P is not less than 0.01%.
  • the chemical composition of the molten steel obtained in the first step includes, in mass%, P: not less than 0.01%
  • the chemical composition of the steel ingot after the casting in the third step includes, in mass%, P: not less than 0.01%.
  • the chemical composition of the steel ingot preferably is the hot work tool steel including, in mass%, C: 0.3 to less than 0.6%, Si: 0.2 to 1.5%, Mn: 0.1 to 1.5%, and Cr: 3.0 to less than 6.0%.
  • Mo and W are included singly or in combination wherein an amount of (Mo + 1/2W) is 1.0 to 3.5%, and as desired, V: not more than 1.5% may be further included.
  • the chemical composition of the steel ingot after the casting in the third step is most typically a hot work tool steel including, in mass%, C: 0.3 to less than 0.6%, Si: 0.2 to 1.5%, Mn: 0.1 to 1.5%, Ni: not more than 1.5% (including 0%), Cr: 3.0 to less than 6.0%, Mo and W singly or in combination, with an amount of (Mo + 1/2W): 1.0 to 3.5%, V: not more than 1.5%, Nb: not more than 0.3% (including 0%), Co: not more than 5.0% (including 0%), Zn: more than 0.0025 to 0.025%, P: not less than 0.005%, with Zn/P being more than 0.5, and the balance being composed of Fe and inevitable impurities.
  • P is not less than 0.01%.
  • the present invention since sufficient toughness of a hot work tool steel can be maintained even without controlling P (phosphorus) included therein to be at a very low value, it is possible to save energy consumption for lowering a P content, thereby reducing a load on the environment. Further, the amount of Zn to maintain sufficient toughness can be precisely adjusted by the adding method of the present invention. As so far described, the present invention can dramatically improve the toughness of hot work tool steels, and thus provides an effective technique for practically implementing hot work tool steels which are applicable to various uses and environments.
  • a major feature of the present invention is that Zn which has conventionally been treated as an impurity is positively added to improve the toughness of a hot work tool steel. That is, the relationship between P, which is an element that significantly reduces toughness, and the adding amount of Zn of the present invention is made clear so that the content of P is permitted within a certain limit. That is, the present inventors have found that utilizing Zn as an alloying element for a hot work tool steel can exhibit the effect of improving toughness, even if the content of P have increased. Thus, since the content of P, which conventionally needed to be reduced to a very low level, can be permitted up to an increased level, the use amount of expensive low-P scraps can be reduced when selecting raw materials, which is suitable for recycling of scraps.
  • Zn is the most important additive element for the present invention, and its addition remarkably improves the toughness of steel. This effect can be sufficiently achieved by adding an amount of more than 0.0025%. A preferable adding amount is not less than 0.003%. On the other hand, even if a larger amount of Zn is added, its effect will be saturated. Further, if extreme segregation occurs in grain boundaries due to the excessive addition, it may rather be a factor to cause deterioration of toughness. Moreover, since the adding technique thereof will become complicated, the upper limit of Zn is set to 0.025%. It is preferably not more than 0.020%, and more preferably not more than 0.015%.
  • P phosphorous
  • P is an element that segregates in original austenite grain boundaries during a heat treatment such as tempering, thereby embrittling the grain boundaries. Therefore, to improve the toughness of a hot work tool steel, P is an impurity element which has been controlled generally to be as low as possible.
  • Zn addition which is required for the toughness improvement, can be achieved by adjusting the amount of Zn addition with respect to the P content to be described below.
  • a hot work tool steel of the present invention can permit a P content of not less than 0.005%. Sufficient toughness can be maintained even when the P content is preferably not less than 0.01%, or more preferably not less than 0.02%.
  • Zn is added to the molten steel at a timing when the P content is fixed by adjusting the chemical composition of the molten steel to that of the hot work tool steel in advance, not by adjusting Zn at the same timing as for other additive elements, thereby making it possible to reduce the passage of time to subsequent casting and to suppress the variation of Zn/P ratio due to the evaporation of Zn, and so on.
  • the present invention includes a first step of obtaining a molten steel having a chemical composition of a hot work tool steel including not less than 0.005 mass% of P; a second step of adding Zn to the molten steel having the chemical composition of the hot work tool steel; and a third step of casting the above-described molten steel to which Zn has been added to obtain a steel ingot.
  • Zn is added in the second step such that the chemical composition of the steel ingot after casting in the third step becomes the hot work tool steel including Zn: more than 0.0025 to 0.025 mass% and P: not less than 0.005 mass%, with Zn/P being more than 0.5.
  • the content of P included in the steel ingot after casting in the above-described third step is preferably not less than 0.01 mass%, and more preferably not less than 0.02 mass%.
  • a hot work tool steel satisfying the chemical composition of the present invention is produced by melting.
  • the casting in the third step of the present invention is not limited to a normal ingot-making process, but may be a continuous casting process and other special ingot-making processes.
  • C is an element that is partially solid-solved into the matrix, thereby adding strength thereto, and partially forms carbide, thereby improving the wear resistance and seizure resistance.
  • C which is an interstitial atom in a solid solution
  • a substitutional atom having a large affinity with C, such as Cr it is expected to work as the drag resistance for solute atoms due to an I(interstitial)-S(substitutional) interaction, thereby enhancing the strength of steel.
  • C is 0.3 to less than 0.6%, and preferably less than 0.55%.
  • Si silicon is a deoxidizer at the time of steel making, and is an element that improves the machinability of the steel material. To achieve these effects, although addition may be less than 0.2%, addition of not less than 0.2% is defined. However, since excessive addition will cause the generation of ferrite, the amount of addition is not more than 1.5%.
  • Mn manganese
  • MnS manganese-based quenching and tempering hardness
  • addition may be less than 0.1% to achieve these effects, addition of not less than 0.1% is defined. However, since excessive addition will increase the viscosity of the matrix, thereby deteriorating machinability, the amount of addition is not more than 1.5%.
  • Cr chromium
  • Cr is an element that increases hardenability, forms carbide, and has effects of strengthening the matrix and improving wear resistance. Cr also contributes to the improvements of the resistance to temper softening, and of high-temperature strength. However, excessive addition will cause deterioration of hardenability and high-temperature strength. Therefore, the amount of addition is 3.0 to less than 6.0%, and is preferably not more than 5.65%.
  • Mo and W is added singly or in combination to add strength by causing fine carbides to precipitate or aggregate by tempering, thereby improving the resistance to softening.
  • the amount of addition in this case can be specified together in terms of a Mo equivalent, (Mo + 1/2W), since W has an atomic weight approximately twice of that of Mo (of course, only either one of them may be added or both may be added together).
  • the amount of addition may be less than 1.0% in terms of the value of (Mo + 1/2W)
  • the addition of not less than 1.0% is defined.
  • the amount of addition is not more than 3.5% in terms of the value of (Mo + 1/2W).
  • V vanadium
  • V vanadium
  • the amount of addition may be less than 0.5% to achieve these effects, the addition of not less than 0.5% is preferable. However, since excessive addition will cause deterioration of machinability and toughness, a preferable amount of addition is not more than 1.5%.
  • Ni nickel is an element that suppresses the generation of ferrite. Moreover, Ni is an effective element that adds, along with C, Cr, Mn, Mo, W and the like, excellent hardenability to a hot work tool steel, and allows the formation of a microstructure predominantly made up of martensite even when the cooling rate at the time of quenching is slow, thus preventing deterioration of toughness. Further, since Ni improves intrinsic toughness of the matrix, Ni is added as needed in the present invention. However, excessive addition will increase the viscosity of the matrix, thereby deteriorating machinability. Therefore, even when it is added, an amount of not more than 1.5% is preferable. Also, when it is added, a preferable amount is not less than 0.1%.
  • Nb niobium
  • Nb forms carbides and has effects of strengthening the matrix, and improving wear resistance.
  • Nb increases the resistance to temper softening, and suppresses the coarsening of crystal grains thereby contributing to the improvement of toughness
  • Nb is added as needed in the present invention.
  • a preferable amount is not more than 0.3%.
  • a preferable amount is not less than 0.05%.
  • Co forms a very fine protective oxide film having good adhesiveness on a surface of a hot work tool steel according to the present invention when using the hot work tool as a tool at an increased temperature.
  • the oxide film prevents metallic contact with a counterpart material, thereby suppressing temperature rise at the surface of the tool, and providing excellent wear resistance. Therefore, Co is added as needed in the present invention. However, excessive addition will cause deterioration of toughness. Therefore, even when it is added, an amount of not more than 5.0% is preferable. Also, when it is added, a preferable amount is not less than 0.3%.
  • Major elements which may remain in steel as an inevitable impurity are S, Cu, Al, Ca, Mb, O (oxygen), N (nitrogen), and so on.
  • the contents of these elements are preferably as low as possible.
  • additional actions and effects such as morphology control of inclusions, improvements of other mechanical properties and productivity, they may be included and/or added in a slight amount.
  • the ranges of S ⁇ 0.01%, Cu ⁇ 0.25%, Al ⁇ 0.025%, Ca ⁇ 0.01%, Mg ⁇ 0.01%, O ⁇ 0.01%, and N ⁇ 0.03% are fully permissible, and indicate the upper limits of preferable specifications of the present invention.
  • a hot work tool steel relating to the present invention is preferably subjected to a homogenizing heat treatment, for example, during processing of a steel ingot after casting to finish it into a steel product.
  • the quenching and tempering hardness is preferably not more than 50 HRC, and is more preferably not more than 48 HRC.
  • molten steel adjusted to have a chemical composition of a hot work tool steel including not less than 0.005 mass% of P was maintained by a vacuum induction melting furnace.
  • the chemical composition at this time was adjusted to be the chemical composition of a target steel ingot after subsequent Zn addition (that is, charging of a Zn source).
  • Zn was added to the molten steel by using a Zn plated steel sheet as the Zn source, and the molten steel was cast to fabricate a steel ingot weighing 7 to 10 kg.
  • Table 1 shows the chemical compositions of the steel ingots after casting. The Zn contents were measured by an X-ray fluorescence analysis.
  • Inventive steels were obtained by adding Zn to have a chemical composition of a generally used hot work tool steel of JIS-SKD61 (specified P: not more than 0.030%) such that the Zn/P ratio of the present invention was satisfied, thereby permitting an increased amount of P content. It is noted that in all the steel ingots, none of S, Cu, Al, Ca, Mg, O, and N was added (although, the case in which Al was added as a deoxidizer in the melting process was included), wherein S ⁇ 0.01%, Cu ⁇ 0.25%, Al ⁇ 0.025%, Ca ⁇ 0.01%, Mg ⁇ 0.01%, O ⁇ 0.01%, and N ⁇ 0.03%.
  • these steel ingots were hot forged at 1150°C to fabricate a steel product of 20 mm thickness, 60 mm width, and about 500 to 800 mm length. Then, after being annealed at 860°C, the steel product was machined into a size of Sharpy impact test specimen to be used for the evaluation described below, and was oil-quenched from 1030°C and tempered at various temperatures to obtain specimens for evaluating toughness at respective thermally refined hardnesses.
  • Fig. 1 shows the results of 2 mm U-notch Sharpy impact test of Inventive steels 1, 3, 5 to 7, and Comparative steels 1, 3 to 6 at their respective hardnesses.
  • the Sharpy test specimen was directed in the T-L direction according to ASTM E399-90.
  • Inventive steels 1, 3, 5 to 7 in which Zn was added so as to satisfy the Zn/P ratio of the present invention exhibited more excellent Sharpy impact values than Comparative steels 1, 3, 4 in which no Zn was added, in the combinations of: Inventive steels 1, 3 and Comparative steel 1; Inventive steels 5 and Comparative steel 3; and Inventive steels 6, 7 and Comparative steel 4, where the respective steels included the same level of P in each combination.
  • Comparative steel 6 Even though having included P at a high density of more than 0.02%, Inventive steel 6 exhibited toughness of the same level as that of Comparative steel 1, which contained less than 0.01% of P, owing to the addition of Zn. Comparative steel 6, which was obtained by adding Zn to Comparative steel 5 including the same level of P, did not satisfy Zn/P of the present invention, and exhibited no improvement in toughness.
  • Fig. 2 shows the results of 2 mm V-notch Sharpy impact test of Inventive steels 2, 4 to 7 and Comparative steels 2 to 6 at temperatures from room temperature to 400°C, wherein the steels have a hardness of 45 HRC by thermally refining.
  • the Sharpy test specimen was directed in the T-L direction according to ASTM E399-90.
  • Inventive steels 2, 4 to 7 in which Zn was added so as to satisfy the Zn/P ratio of the present invention exhibited more excellent Sharpy impact values than those of Comparative steels 2 to 4 which included the same level of P, at any test temperature, in the respective combinations of: Inventive steels 2, 4 and Comparative steel 2; Inventive steels 5 and Comparative steel 3; and Inventive steels 6, 7 and Comparative steel 4, where the respective steels included the same level of P in each combination. Further, even though having included P at a higher density of more than 0.02%, Inventive steel 6, which satisfied the Zn/P ratio of the present invention as the result of addition of Zn, maintained the same level of toughness as that of Comparative steel 2 which contained less than 0.01% of P.
  • Example 2 Steel ingots having chemical compositions of Table 2 were fabricated in the same manner as described in Example 1.
  • Inventive steel A was prepared by adding Zn to the chemical composition of a hot work tool steel such that Zn/P ratio of the present invention was satisfied.
  • Comparative steel B had the same chemical composition as that of Inventive steel A excepting that no Zn was added. It is noted that in both the steel ingots, none of S, Cu, Al, Ca, Mg, O, and N was added (although, Al was added as a deoxidizer in the melting process), wherein S ⁇ 0.01%, Cu ⁇ 0.25%, Al ⁇ 0.025%, Ca ⁇ 0.01%, Mg ⁇ 0.01%, O ⁇ 0.01%, and N ⁇ 0.03%.
  • Fig. 3 shows the results of 2 mm U-notch Sharpy impact test of Inventive steel A and Comparative steel B at room temperature at respective degrees of hardness.
  • the Sharpy test specimen was oriented in the T-L direction according to ASTM E399-90. These steels originally had high toughness because Ni was added thereto.
  • Inventive steel A, to which Zn was added so as to satisfy Zn/P ratio of the present invention exhibited more excellent Sharpy impact values compared to those of Comparative steel B to which Zn was not added.
  • Fig. 4 shows the results of 2 mm V-notch Sharpy impact test of Inventive steel A and Comparative steel B at temperatures from room temperature to 400°C wherein the steels have a hardness of 45 HRC by thermal refining.
  • the Sharpy test specimen was oriented in the T-L direction according to ASTM E399-90.
  • Inventive steel A to which Zn was further added so as to satisfy the Zn/P ratio of the present invention, exhibited more excellent Sharpy impact values at any test temperature compared with Comparative steel B to which Zn was not added.

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EP12752790.1A 2011-03-03 2012-02-28 Hot work tool steel having excellent toughness, and process of producing same Active EP2682491B1 (en)

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JP2011046103 2011-03-03
JP2011148203 2011-07-04
PCT/JP2012/054868 WO2012118053A1 (ja) 2011-03-03 2012-02-28 靭性に優れた熱間工具鋼およびその製造方法

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EP2682491A4 EP2682491A4 (en) 2015-04-08
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US10119174B2 (en) 2014-05-28 2018-11-06 Hitachi Metals, Ltd. Hot work tool material and method for manufacturing hot work tool
CN106574335B (zh) * 2014-07-23 2019-06-18 日立金属株式会社 热作工具材料、热作工具的制造方法及热作工具
WO2016136401A1 (ja) * 2015-02-25 2016-09-01 日立金属株式会社 熱間工具およびその製造方法
CN107429345B (zh) * 2016-03-18 2019-04-19 日立金属株式会社 冷作工具材料及冷作工具的制造方法
US20210262071A1 (en) * 2018-10-05 2021-08-26 Hitachi Metals, Ltd. Hot work tool steel and hot work tool
CN112442626A (zh) * 2019-09-03 2021-03-05 建德市亚力达工具有限公司 一种高速圆切机的切刀制备工艺

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4886640A (en) 1988-08-22 1989-12-12 Carpenter Technology Corporation Hot work tool steel with good temper resistance
EP0733719A1 (de) 1995-03-23 1996-09-25 BÖHLER Edelstahl GmbH Eisenbasislegierung zur Verwendung bei erhöhter Temperatur
WO1999050468A1 (en) 1998-03-27 1999-10-07 Uddeholm Tooling Aktiebolag Steel material for hot work tools
JP2000119818A (ja) 1998-10-14 2000-04-25 Daido Steel Co Ltd 冷間加工性にすぐれたマルテンサイト系耐熱鋼
JP2004019001A (ja) 2002-06-20 2004-01-22 Daido Steel Co Ltd 耐溶損性に優れた熱間工具鋼及び金型部材
JP2007224418A (ja) 2006-01-30 2007-09-06 Hitachi Metals Ltd 靭性に優れた熱間工具鋼
EP2503016A1 (en) 2009-11-17 2012-09-26 Villares Metals S/A Steel with high temper resistance

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
AT410447B (de) 2001-10-03 2003-04-25 Boehler Edelstahl Warmarbeitsstahlgegenstand
JP3602102B2 (ja) * 2002-02-05 2004-12-15 日本高周波鋼業株式会社 熱間工具鋼
JP4267260B2 (ja) * 2002-06-14 2009-05-27 新日本製鐵株式会社 被削性に優れた鋼
JP3996824B2 (ja) * 2002-09-12 2007-10-24 新日本製鐵株式会社 耐低温変態割れ性に優れた液相拡散接合用鋼材
CN101517114A (zh) * 2006-09-15 2009-08-26 日立金属株式会社 韧性和高温强度优异的热加工工具钢及其制造方法
JP4473928B2 (ja) * 2007-04-18 2010-06-02 新日本製鐵株式会社 被削性と衝撃値に優れた熱間加工鋼材

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US4886640A (en) 1988-08-22 1989-12-12 Carpenter Technology Corporation Hot work tool steel with good temper resistance
EP0733719A1 (de) 1995-03-23 1996-09-25 BÖHLER Edelstahl GmbH Eisenbasislegierung zur Verwendung bei erhöhter Temperatur
WO1999050468A1 (en) 1998-03-27 1999-10-07 Uddeholm Tooling Aktiebolag Steel material for hot work tools
JP2000119818A (ja) 1998-10-14 2000-04-25 Daido Steel Co Ltd 冷間加工性にすぐれたマルテンサイト系耐熱鋼
JP2004019001A (ja) 2002-06-20 2004-01-22 Daido Steel Co Ltd 耐溶損性に優れた熱間工具鋼及び金型部材
JP2007224418A (ja) 2006-01-30 2007-09-06 Hitachi Metals Ltd 靭性に優れた熱間工具鋼
EP2503016A1 (en) 2009-11-17 2012-09-26 Villares Metals S/A Steel with high temper resistance

Non-Patent Citations (3)

* Cited by examiner, † Cited by third party
Title
BENEDYK, J.K.: "Ferrous - FeUH H-13", HIGH PERFORMANCE ALLOYS DATABASE, August 2008 (2008-08-01), XP055554761, Retrieved from the Internet <URL:https://cindasdata.com/products/docs/hpad/hpad-example-h13.pdf>
HOLTZER, M. ET AL.: "Environmental impact of the use of automotive scrap as charge material in metallurgical processes", METALURGIJA, vol. 42, October 2003 (2003-10-01), pages 265 - 270, XP055554768, ISSN: 9543-5846
MESQUITA, R.A. ET AL.: "New tool steel with improved hot Resistance", TECNOLOGIA EM METALURGIA E MATERIALS, vol. 3, no. 3, 2007, Sao Paulo, pages 63 - 68, XP055554763, Retrieved from the Internet <URL:http://tecnologiammm.com.br/files/v3n3/v3n3a12.pdf>

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CN103403209A (zh) 2013-11-20
TW201250011A (en) 2012-12-16
WO2012118053A1 (ja) 2012-09-07

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