EP2957647A2 - Acier pour outil de travail à froid - Google Patents

Acier pour outil de travail à froid Download PDF

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Publication number
EP2957647A2
EP2957647A2 EP15171821.0A EP15171821A EP2957647A2 EP 2957647 A2 EP2957647 A2 EP 2957647A2 EP 15171821 A EP15171821 A EP 15171821A EP 2957647 A2 EP2957647 A2 EP 2957647A2
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EP
European Patent Office
Prior art keywords
steel
die
cold working
working tool
less
Prior art date
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Granted
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EP15171821.0A
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German (de)
English (en)
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EP2957647B1 (fr
EP2957647A3 (fr
Inventor
Motohiro Ibuki
Takayuki Shimizu
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Daido Steel Co Ltd
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Daido Steel Co Ltd
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Priority claimed from JP2014243681A external-priority patent/JP6439227B2/ja
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Publication of EP2957647A3 publication Critical patent/EP2957647A3/fr
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Classifications

    • 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C21D1/84—Controlled slow cooling
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
    • 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
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • 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
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C21D1/32—Soft annealing, e.g. spheroidising
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/02—Hardening by precipitation

Definitions

  • the present invention relates to a steel for cold working tool, and in particular, relates to a steel for cold working tool, which is preferable for forming a high tensile steel plate.
  • steel for cold working tool represented by SKD11 is usually used at approximately HRC 60 to HRC 63 after being subjected to a quenching treatment at a temperature higher than or equal to 1,000°C and then being subjected to a tempering treatment at a temperature higher than or equal to 450°C.
  • a die for cold pressing and a die for cold forging are exemplified.
  • Patent Document 1 discloses a steel for cold working tool which achieves high hardness and high toughness by improving the size and the distribution of carbide.
  • the high tensile steel plate is also called "High Tensile Strength Steel Sheets", and indicates a steel plate having a high tensile strength.
  • the common steel plate has tensile strength greater than or equal to 270 MPa, whereas a steel plate having tensile strength of 340 MPa to 790 MPa is generally defined as the high tensile steel plate.
  • a steel plate having tensile strength greater than or equal to 1,000 MPa is particularly called a super high tensile steel plate.
  • Patent Document 1 JP-A-H02-277745
  • the cold working die when focused on a manufacturing process of the cold working die, the cold working die is usually machined at room temperature and is finished into a final shape.
  • This machining process is a repetition of a rupture due to shear deformation of a die material (steel for cold working tool) and abrasion of ruptured swarf and the tool, and a temperature on a machined surface of the die material temporarily and instantaneously increases. If the die is difficult to be deformed at this high temperature, that is, if hardness at a high temperature increases, machinability decreases. That is, a load for the tool machining the die increases (a tool abrasion amount increases), and thus the cost of a machine tool and the time for manufacturing the die increase, and productivity of the die decreases.
  • the present invention was made in consideration of the circumstances described above, and is to solve the above-described problem by providing a steel for cold working tool, which can improve productivity of a die while ensuring necessary hardness and a necessary impact value of the die.
  • a first aspect of the present invention is a steel for cold working tool, which contains, on a % by mass basis:
  • a second aspect of the present invention is the steel for cold working tool according to the first aspect, which further contains, on a % by mass basis, at least one of the following:
  • a third aspect of the present invention is the steel for cold working tool according to the first or the second aspect, which has an amount of retaining austenite after quenching being less than or equal to 25 vol%.
  • a fourth aspect of the present invention is the steel for cold working tool according to any one of the first, the second and the third aspects, which has a highest hardness after a tempering treatment at a temperature higher than or equal to 450°C being greater than or equal to 64 HRC.
  • the present invention ensures the hardness and impact value necessary for a die by adjusting C, Si, Cr, Mo, W, and V to be in a predetermined range.
  • a balance among Mo, W, and V is optimized, and a relational expression of 1.66 (Mo + 1/2W) + V ⁇ 5.7% is specified in order to improve productivity of the die.
  • the die is machined at room temperature, and the temperature of the die is temporarily and instantaneously increased by machining heat during the machining. In this case, when focused on hardness of the die, the hardness is highest at room temperature and decreases as the temperature rises.
  • the steel for cold working tool disclosed in Patent Document 1 described above realizes high hardness and high toughness by improving the size and the distribution of carbide, but does not have the characteristics of the present invention and thus has completely different technical concepts.
  • the steel for cold working tool according to one embodiment of the present invention (hereinafter, referred to as the steel for cold working tool of this embodiment) will be described in detail.
  • the steel for cold working tool of this embodiment is able to be applied to a forming die for a high tensile steel plate, a punch and die for cold forging, a bending die, a die for cold forging, a die for swaging, a die for thread rolling, a punch member, a slitter knife, a die for punching a lead frame, a gauge, a deep drawing punch, a bending punch, a shear blade, a bending die for stainless steel, a drawing die, a tool for plastic working such as heading, a punch for a gear, a cam component, a die for press punching, a die for progressive punching, a seal plate for a sediment transport device, a screw member, a rotary plate for a concrete spraying machine, a die for sealing an IC, and a precision
  • the steel for cold working tool of this embodiment is also able to be used for various cold metal dice used after performing a surface treatment such as a CVD treatment, a PVD treatment, and a TD treatment. Among them, it is particularly preferable to be used for a super high tensile steel plate having tensile strength greater than or equal to 1,000 MPa.
  • C is a necessary element for ensuring strength and abrasion resistance, and forms a carbide by being bonded to a carbide forming element such as Cr, Mo, W, V, and Nb.
  • C is also necessary for ensuring hardness by being dissolved into a matrix phase to form a solid solution at the time of quenching to thereby form a martensite structure.
  • a lower limit of the content of C is set to be 0.70%.
  • the carbide forming element and C are bonded to form a coarse carbide and thus an impact value may decrease.
  • hot workability at the time of performing hot forging with respect to an ingot after casting may decrease.
  • an upper limit of the content of C is set to be 0.90%. From the viewpoints described above, a more preferred range of the content of C is 0.75% to 0.85%.
  • Si is dissolved into a matrix phase to form a solid solution, can accelerate precipitation of other carbides, and can contribute to secondary hardening.
  • a lower limit of the content of Si is set to be 0.60%.
  • an upper limit of the content of Si is set to be 0.80%.
  • Mn is added for improving quenching properties and stabilizing austenite.
  • Mn forms MnS when S is inevitably contained, and can prevent a decrease in an impact value caused by a distortion (facilitation of anisotropy) due to a heat treatment.
  • a lower limit of the content of Mn is set to be 0.30%.
  • an upper limit of the content of Mn is set to be 0.50%.
  • P is inevitably contained in steel. P is easily segregated on a crystal grain boundary and may cause a decrease in toughness. For this reason, an upper limit of the content of P is set to be 0.3%.
  • MnS can be formed by adding S to prevent a decrease in an impact value caused by a distortion (facilitation of anisotropy) due to a heat treatment, and thus the content of S is limited to be less than or equal to 0.03%.
  • Cu is an element stabilizing austenite.
  • the content of Cu is set to be 0.01% to 0.25%.
  • Ni is an element stabilizing austenite.
  • the content of Ni is set to be 0.01% to 0.25%.
  • Cr is an element improving corrosion resistance.
  • a lower limit of the content of Cr is set to be 6.0%.
  • an upper limit of the content of Cr is set to be 7.0%.
  • Mo and W form fine carbides, and are important elements contributing to secondary hardening.
  • a total amount of a content of Mo and 1/2 of a content of W is limited.
  • a lower limit of the content of Mo + 1/2W is set to be 2.50%.
  • an upper limit of the content of Mo + 1/2W is set to be 3.00%.
  • V 0.70% to 0.85%
  • V can be bonded to C to form a carbide.
  • the carbide can contribute to suppression of coarsening in a crystal grain diameter.
  • a lower limit of the content of V is set to be 0.70%.
  • an upper limit of the content of V is set to be 0.85%.
  • N is an interstitial type element and can contribute to an increase in hardness of a martensite structure. N has a stronger y stabilizing ability compared to carbon which is the same interstitial type element. However, when the content of N is excessively large, nitrogen in a steel material may concentrate during solidification to exceed a limit of nitrogen gas ejection, and thus voids easily occur in an ingot. For this reason, an upper limit of the content of N is set to be 0.020%.
  • O is an element which is inevitably contained in molten steel.
  • O may be bonded to Si and Al to form coarse oxides which become an inclusion, and thus toughness may decrease.
  • an upper limit of the content of O is set to be 0.0100%.
  • Al is an element which is added as a deoxidizing agent.
  • Al may be bonded to O to form a coarse oxide and it may become a starting point of a crack.
  • an upper limit of the content of Al is set to be 0.100%.
  • the steel for cold working tool of this embodiment may optionally contain one or more kinds of elements selected from the elements described below in addition to the above-described essential elements. That is, the steel for cold working tool of this embodiment may consist only of, on a % by mass basis: 0.70 ⁇ C ⁇ 0.90; 0.60 ⁇ Si ⁇ 0.80; 0.30 ⁇ Mn ⁇ 0.50; P ⁇ 0.30; S ⁇ 0.030; 0.01 ⁇ Cu ⁇ 0.25; 0.01 ⁇ Ni ⁇ 0.25; 6.0 ⁇ Cr ⁇ 7.0; 2.50 ⁇ Mo + 1/2W ⁇ 3.00; 0.70 ⁇ V ⁇ 0.85; N ⁇ 0.020; 0 ⁇ 0.0100; and A1 ⁇ 0.100, with the balance being Fe and inevitable impurities in which 1.66 (Mo + 1/2W) + V ⁇ 5.7% is satisfied, but it may optionally contain one or more kinds of elements selected from the elements with its contents as described below.
  • Nb 0.001% to 0.30%
  • Ta 0.001% to 0.30%
  • Ti 0.20% or less
  • Zr 0.001% to 0.30%
  • Nb, Ta, Ti, and Zr are elements which are bonded to C and N to form carbonitrides, and may contribute to suppression of coarsening in a crystal grain.
  • machinability at the time of finishing may decrease, and thus productivity of a die may decrease. For these reason, a content of each element is set to be in the range described above.
  • an amount of retaining austenite after quenching is less than or equal to 25 vol%. This is because when the amount of retaining austenite after quenching increases, a change in dimension of a die due to an amount of retaining austenite to be decomposed after tempering may increase, and thus it may take time to perform precision machining with respect to the die. Furthermore, it is preferable that the quenching temperature is 1,000°C to 1,100°C.
  • the highest hardness after a tempering treatment at a temperature greater than or equal to 450°C is greater than or equal to 64 HRC.
  • the steel for cold working tool of this embodiment is used as a cold working die for a high tensile steel plate, it is necessary to ensure hardness and an impact value by applying secondary hardening.
  • a cubic test piece of which a side was 10 mm was cut out from the rod material after the heat treatment described above and was treated in heat treatment conditions shown in Table 3 (a quenching temperature and a tempering temperature).
  • a measuring surface and a grounding surface of the cubic test piece were ground up to #400.
  • hardness of the cubic test piece was measured by using a Rockwell C Scale. The hardness indicates the highest hardness in the case where a tempering treatment has been conducted at a temperature higher than or equal to 450°C.
  • a 10R-notch Charpy test piece in which a notch of 2 mm having a depth of 10R was formed in a square rod material of 10 mm x 10 mm x 55 mm cut out from the rod material of 60 mm square described above was prepared.
  • the 10R-notch Charpy test piece was subjected to a quenching treatment and a tempering treatment at a temperature shown in Table 3, and then an impact value thereof was measured at room temperature. The impact value was obtained as an average value of three test pieces.
  • Test Piece 55 mm x 55 mm x 200 mm Machining Tool: a square end mill of super hard M20 ( ⁇ 10 mm) Machining Distance: 10m Machining Speed: 100 m/min Transport Speed per Revolution: 0.2 mm/rev Cutout Width (Horizontal Direction): 0.5 mm Cutout Height (Vertical Direction): 0.5 mm Machine Oil: none
  • the end mill was detached from a holder after machining of 10 m, and the maximum abrasion amount of a corner portion of the square end mill was measured.
  • the maximum abrasion amount of the corner portion of the square end mill was measured by real measurement using a CCD camera of 3 magnifications.
  • the "maximum abrasion amount of the corner portion of the square end mill” indicates a maximum value of a distance from a tip of the corner portion of the square end mill to a position where peeling and abrasion are able to be confirmed.
  • a square rod material of 10 mm x 10 mm x 2 mm which was cut out from the rod material of 60 mm square was maintained at the quenching temperature shown in Table 3 for 30 minutes, and then was cooled at an average cooling speed of 50°C/min.
  • a measuring surface of the square rod material (test piece) was ground up to #800 defined by JIS-R6001 (1998), and was measured by an X-ray diffraction device.
  • a peak intensity of (200) and (211) of ferrite and a peak intensity of (200), (220) and (311) of austenite were obtained by X-ray measurement, and then an amount of retaining austenite (vol%) was calculated from a peak intensity ratio.
  • Tables 1 and 2 chemical compositions of the invention steels and steels of Comparative Examples are shown.
  • Table 3 heat treatment conditions and test results of the invention steels and the Comparative steels are shown.
  • FIG. 1 a relationship between a tool abrasion amount (machinability) and addition amounts of Mo, W and V of the invention steels and the Comparative steels are shown.
  • FIG. 2 a relationship between an impact value and a numerical value of hardness of the invention steels and the Comparative steels are shown.
  • Comparative steel 14 With reference to Table 1, Table 2 and Table 3, since the contents of Mo and V were below the lower limit of the limited range of the present invention and the content of Cr exceeded the upper limit of the limited range of the present invention, the Comparative steel 14 could not achieve a sufficient hardness. In addition, since the content of C exceeded the upper limit of the limited range of the present invention, the Comparative steel 14 had a low impact value.
  • Comparative steel 16 in Table 3 is an example in which a test was performed in a condition of a composition identical to that of Comparative steel 14 in Table 2, and a tempering temperature and a quenching temperature different from that of Comparative steel 14 in Table 3.
  • the Invention steels achieved excellent results in any test result of the hardness measurement test, the Charpy impact test, the machinability test, and the measurement test of the amount of retaining austenite, compared to these Comparative steels. From the results described above, according to the steel for cold working tool of the present embodiment, it is possible to improve productivity of the die while ensuring necessary hardness and a necessary impact value of the die.

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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 Articles (AREA)
  • Heat Treatment Of Steel (AREA)
EP15171821.0A 2014-06-19 2015-06-12 Acier pour outil de travail à froid Active EP2957647B1 (fr)

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2014125901 2014-06-19
JP2014218985 2014-10-28
JP2014243681A JP6439227B2 (ja) 2014-06-19 2014-12-02 冷間工具鋼

Publications (3)

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EP2957647A2 true EP2957647A2 (fr) 2015-12-23
EP2957647A3 EP2957647A3 (fr) 2016-01-13
EP2957647B1 EP2957647B1 (fr) 2017-02-15

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EP (1) EP2957647B1 (fr)
CN (1) CN105274444B (fr)
TW (1) TWI647318B (fr)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112011740A (zh) * 2020-08-31 2020-12-01 天津钢研海德科技有限公司 一种高韧性高硬度模具钢及其制备方法
CN115948644A (zh) * 2023-02-10 2023-04-11 攀钢集团江油长城特殊钢有限公司 一种冷作模具钢棒材制造方法

Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH02277745A (ja) 1989-01-20 1990-11-14 Hitachi Metals Ltd 高硬度、高靭性冷間工具鋼

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH03134136A (ja) * 1989-10-18 1991-06-07 Hitachi Metals Ltd 高硬度、高靭性冷間工具鋼
JP2765392B2 (ja) * 1992-08-31 1998-06-11 住友金属工業株式会社 二相ステンレス鋼熱延鋼帯の製造方法
JP4239300B2 (ja) * 1999-06-14 2009-03-18 大同特殊鋼株式会社 冷間金型用鋼
JP4403875B2 (ja) * 2004-05-14 2010-01-27 大同特殊鋼株式会社 冷間工具鋼
JP5338188B2 (ja) * 2007-10-31 2013-11-13 大同特殊鋼株式会社 合金工具鋼及びその製造方法

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH02277745A (ja) 1989-01-20 1990-11-14 Hitachi Metals Ltd 高硬度、高靭性冷間工具鋼

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112011740A (zh) * 2020-08-31 2020-12-01 天津钢研海德科技有限公司 一种高韧性高硬度模具钢及其制备方法
CN115948644A (zh) * 2023-02-10 2023-04-11 攀钢集团江油长城特殊钢有限公司 一种冷作模具钢棒材制造方法

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TW201604291A (zh) 2016-02-01
CN105274444A (zh) 2016-01-27
EP2957647B1 (fr) 2017-02-15
EP2957647A3 (fr) 2016-01-13
CN105274444B (zh) 2019-03-19
TWI647318B (zh) 2019-01-11

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