WO2008032816A1 - 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 - Google Patents

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 Download PDF

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Publication number
WO2008032816A1
WO2008032816A1 PCT/JP2007/067915 JP2007067915W WO2008032816A1 WO 2008032816 A1 WO2008032816 A1 WO 2008032816A1 JP 2007067915 W JP2007067915 W JP 2007067915W WO 2008032816 A1 WO2008032816 A1 WO 2008032816A1
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WIPO (PCT)
Prior art keywords
toughness
tool steel
temperature strength
steel
work tool
Prior art date
Application number
PCT/JP2007/067915
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English (en)
Japanese (ja)
Inventor
Kouta Kataoka
Hideshi Nakatsu
Yasushi Tamura
Masayuki Nagasawa
Original Assignee
Hitachi Metals, Ltd.
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
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Application filed by Hitachi Metals, Ltd. filed Critical Hitachi Metals, Ltd.
Priority to US12/440,406 priority Critical patent/US20100193089A1/en
Priority to EP07807322.8A priority patent/EP2065483A4/fr
Priority to KR1020137006463A priority patent/KR20130036076A/ko
Publication of WO2008032816A1 publication Critical patent/WO2008032816A1/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
    • C22C38/02—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 present invention relates to a hot tool steel with improved toughness and high-temperature strength that is optimal for various hot tools such as press dies, forging dies, die casting dies, and extrusion tools, and a method for producing the same. It is about the law.
  • a hot tool Since a hot tool is used while being in contact with a high-temperature work material or a hard work material, it must have both strength and toughness that can withstand thermal fatigue and impact. For this reason, for example, SKD61-based alloy tool steel, which is a JIS steel type, has been used in the field of hot tools. More recently, if the manufacturing time of products manufactured using hot tools has been shortened, the temperature of workpieces has increased due to the formation of complex shapes, and the number of products has increased due to simultaneous simultaneous production of products. As hot tools such as molds have become larger! /, Etc., hot tool materials are required to have high high-temperature strength and high toughness even at large sizes.
  • Patent Document 1 For the purpose of improving the toughness and high-temperature strength of alloy tool steel, a method of improving high-temperature strength while maintaining toughness by determining the chemical composition range (see Patent Document 1), residual A technique for improving toughness and high-temperature strength by regulating the amount of carbide has been proposed (see Patent Document 2).
  • Patent Document 1 Japanese Patent Laid-Open No. 2-179848
  • Patent Document 2 JP 2000-328196 A
  • Patent Document 1 cannot evaluate the level of toughness because there is no specific measurement value of toughness.
  • the range of chemical composition is insufficiently limited.
  • toughness and high temperature strength are hardened. Since it is greatly influenced by structures such as the martensite structure and bainite structure after this, it is not sufficient to specify the amount of residual carbide to control toughness and high-temperature strength at a high level.
  • An object of the present invention is to provide a hot work tool steel having more reliably superior toughness and high temperature strength, and a method for producing the same.
  • the present invention is, by mass%, C: 0.34-0.40%, Si: 0.3-0. 5%, Mn: 0.4 5-0. 75%, Ni: 0 to less than 0.5%, Cr: 4.9 to 5.5%, Mo and W are single or composite (Mo + l / 2W): 2.5 ⁇ 2.9%, V: 0.5 ⁇ 0.7%, balance Fe and inevitable impurities
  • the hot work tool steel of the present invention may be used after its hardness is adjusted to 40 HRC or higher, but it has excellent toughness and high temperature strength in a high hardness range of 43 HRC or higher, particularly 45 HRC or higher. Demonstrate the effect. 49HRC or less is desired!
  • the hot work tool steel of the present invention is preferably C, Si, Mn, Ni, Cr,
  • the present invention is a hot tool steel having the above component composition, the cross-sectional structure at the time of quenching includes a massive structure and a needle-like structure,
  • tempering hardness characterized by tempering the above hot tool steel so that the relationship value X between the tempering hardness (HRC) and the structure ratio represented by the following formula is 40 or more This is an excellent method for producing hot work tool steel.
  • the tempering hardness may be set to 40 to 49 HRC, but the preferable tempering hardness is 43 to 49 HRC, more preferably 45 to 49 HRC.
  • the present invention it is possible to combine the toughness and high-temperature strength of hot tool steel at a very high level. This effect is maximized not only in the hardness range of 40HRC or higher, but also when tempered in a high hardness range of 43HRC or higher, or even 45HRC or higher and 46HRC or higher. Therefore, it is an effective technology for the practical application of hot tool steel that can be applied to various environments.
  • the content of each element is controlled within an optimum range.
  • the content of each element is controlled to a limited range, and more preferably, by recognizing the quenching structure described later, the manufacturing method remains the same as before, for example, a wide range of quenching cooling rates.
  • Part of C is an essential element important for hot work tool steel, partly forming a solid solution in the base to give strength, and partly forming carbides to increase wear resistance and seizure resistance. It is.
  • C which is a solid interstitial atom, co-added with a substitution atom having a high affinity for C, such as Cr, has an I (interstitial atom) S (substitution atom) effect; Bow I Acts as a scratch resistance and is expected to increase strength.
  • the content is less than 0.34 mass%, sufficient hardness and wear resistance as a tool member cannot be secured.
  • the upper limit is made 0.40% by mass. It is preferably 0.35-0.39%, more preferably 0.36-0.38%.
  • Si is an element for improving machinability as well as a deoxidizer during steelmaking. In order to obtain these effects, it is necessary to add 0.3% by mass or more. However, if it is too much, a needle-like structure described later is developed and toughness is lowered. In addition, by suppressing the precipitation of cementite carbides in the bainite structure during quenching and cooling, the precipitation of carbides during alloying during tempering-aggregation and coarsening can be indirectly promoted to reduce high-temperature strength. Therefore, it should be 0.5% by mass or less. Preferably, it is 0.35–0.45%.
  • Mn has an effect of improving hardenability, suppressing the formation of ferrite, and obtaining appropriate quenching and tempering hardness. Moreover, if it exists in the structure as non-metallic inclusions MnS, it has a great effect on improving machinability. In order to obtain these effects, a force S that requires addition of 0.45% by mass or more is required S, and if it is too much, the viscosity of the base is increased and machinability is lowered, so the content is made 0.75% by mass or less. Preferably it is 0.5 to 0.7%.
  • Ni is an element that suppresses the formation of ferrite. Also, together with C, Cr, Mn, Mo, W, etc., it imparts excellent hardenability to the steel of the present invention, and suppresses the formation of needle-like structures described later even at moderate quenching and cooling rates. It is an effective additive element in order to form a martensite-based structure and prevent toughness deterioration. Furthermore, since it provides the essential toughness improvement effect of the base, it is a preferable element to be added, for example, 0.01% or more. The most important thing for the present invention is that the upper limit is strictly controlled even when Ni is added.
  • the amount is too large, the viscosity of the base is increased to reduce machinability, the high temperature strength is decreased, or the massive structure described later is developed to reduce toughness. It is necessary to make it less than 0.5% by mass. Preferably, the amount is restricted to 0.3% by mass or less.
  • Cr is an element that has the effect of enhancing hardenability and forming carbides to improve the base and strengthening wear resistance, and contributes to the improvement of temper softening resistance and high-temperature strength. It is an essential element for the hot work tool steel of the present invention. In order to obtain these effects, it is necessary to add 4.9% by mass or more. However, excessive addition causes a decrease in hardenability and high-temperature strength, so the upper limit is made 5.5% by mass. Preferably it is 5.0 to 5 ⁇ 4%, more preferably 5 ⁇ ;! to 5 ⁇ 3%.
  • Mo and W can be added singly or in combination in order to enhance hardenability and to give strength by precipitating fine carbides by tempering and to improve softening resistance. Since W is about twice the atomic weight of Mo, it can be defined as Mo + 1 / 2W (Of course,! /, Either one of them can be added, or both can be added together) . In order to obtain the above effect, it is necessary to add 2.5% by mass or more in terms of (Mo + 1 / 2W). Since lowering the toughness due to the development of too large a decrease in machinability described later acicular structure, a 2-9 mass 0/0 or less (Mo + 1 / 2W). Preferably, (Mo + 1 / 2W) is 2 ⁇ 6 to 2 ⁇ 8%.
  • V forms carbides and has the effect of enhancing the wear resistance of the base. It also increases resistance to temper softening and suppresses coarsening of crystal grains, contributing to improved toughness. In order to obtain this effect, it is necessary to add 0.5% by mass or more, but if it is too much, the machinability is reduced toughness. Preferably it is 0.55-0.65%.
  • the main elements that may remain as unavoidable impurities are P, S, Co, Cu, Al, Ca, Mg, 0, N, and the like. In order to achieve the maximum effect of the present invention, these should be as low as possible, but on the other hand, such as the form control of inclusions, other mechanical properties, or the improvement of production efficiency, Some inclusions and / or additions may be made for the purpose of obtaining additional effects. In this case, in mass%, P ⁇ 0.03%, S ⁇ 0.01%, Co ⁇ 0.05%, Cu ⁇ 0.25%, A1 ⁇ 0.025%, Ca ⁇ 0.01%, Mg If it is ⁇ 0.01%, O ⁇ 0.01%, N ⁇ 0.03%, it is considered that the basic characteristics of the hot work tool steel of the present invention are not particularly affected!
  • the present invention preferably has a great feature also when a solution approach from the organization is attempted.
  • the hot tool steel of the present invention satisfying the above component composition includes a massive structure and a needle-like structure in a cross-sectional structure at the time of quenching,
  • the quenched structure is a structure mainly composed of martensite and / or bainite obtained by cooling from the austenite temperature range, as is usually used.
  • the hardened structure of the present invention is substantially composed of the above-mentioned martensite and / or bainite and the remaining austenite in an appropriate amount, and the above-mentioned massive structure and acicular structure are the martensite. And / or part of bainite.
  • the massive structure and the acicular structure defined in the hardened structure of the present invention are feathered bainite (upper bainite) and acicular bainite (lower part) used for ordinary bainite fractionation. It is different from what follows the definition of (Bainite).
  • the massive structure of the present invention is a structure in which a large number of fine carbides having several kinds of orientations have grown inside the structure. And in the cross-sectional structure of steel, the block structure of the present invention is pushed and arranged in a “bulk shape” as shown. Since this massive structure is generated even at a cooling rate that is fast enough to air-cool a small sample of about 10 mm square, it is still difficult to reduce the massive structure when quenching a practical steel ingot, but it accounts for most of the entire structure. And toughness reduction. Therefore, in the present invention, it is preferable that the massive structure occupying in the quenched structure be 45% by area or less. More preferably, it is 40 area% or less, and further preferably 30 area% or less.
  • the needle-like structure of the present invention is a structure in which a large number of carbides have grown in the structure in comparison with the carbides in the massive structure having one direction. And then In the surface structure, the needle-like structure of the present invention has a “needle-like” shape.
  • This acicular structure is a force generated at a cooling rate slower than the cooling rate at which the massive structure begins to form. Again, it is difficult to reduce this acicular structure when quenching a practical steel ingot. However, if it accounts for most of the entire structure, the toughness is greatly degraded. Therefore, in the present invention, it is preferable that the acicular structure occupying the hardened structure be 40 area% or less. More preferably, it is 25 area% or less.
  • the massive tissue and the acicular tissue of the present invention can be visually sorted and quantified by cross-sectional observation by utilizing the difference in shape.
  • any cross section of the structure for example, by performing corrosion by the controlled potential electrolytic etching method (SPEED method), both structures having inferior corrosion resistance as compared with the martensite base with no precipitation of carbide are preferentially corroded.
  • the Fig. 1 shows a structure photograph of the corroded surface observed with a scanning electron microscope (X5000).
  • Figs. 2 and 3 as supplemental schematic diagrams, It is possible to quantitatively determine the acicular tissue.
  • FIG. 1 shows one field of view corresponding to the steel 6 of the present invention of Example 3 to be described later, in which the block structure is 27 area% and the acicular structure force is 0 area%.
  • FIG. 4 shows one field of view corresponding to the conventional steel 31 of Example 3 to be described later, in which the massive structure is 44 area% and the acicular structure is 16 area%.
  • the quenched structure structure of the present invention another important force is retained austenite.
  • this structure is a preferable structure for reduction as a deterioration factor of strength characteristics, an appropriate residual amount contributes to improvement of toughness in the present invention. Therefore, in the present invention, the retained austenite in the quenched structure is preferably 5 to 20% by volume. More preferably, it is 10% by volume or more.
  • volume ratio measurement using the diffraction intensity by X-ray diffractometry may be performed according to a conventional method, for example, using an electropolished sample.
  • the target tempering hardness is determined by tempering in the next step. Therefore, a hot tool with excellent toughness can be obtained by performing tempering so that X in the following relational expression is 40 or more. Steel is formed.
  • A% block structure area%
  • B% needle structure area%
  • C% residual austenite volume%
  • the above formula clarifies the specific influence parameters by studying the influence of the structure at the time of quenching and the tempering hardness on the toughness after tempering.
  • it is effective to reduce the massive structure and the needle-like structure.
  • it is particularly effective to reduce the needle-like structure that has a large coefficient on the negative side. It is.
  • the formula has a large coefficient on the positive side, it can be seen that an appropriate amount of retained austenite works to secure toughness.
  • the target hardness for example, 40HRC or more established as hot tool steel may be set, but it is even higher if it is hot tool steel satisfying the composition of composition and the quenching structure of the present invention.
  • Table 1 shows chemical compositions of the steels of the present invention, comparative steels and conventional steels.
  • the comparative steel is a steel having a chemical composition that is outside the limited narrow component range of the present invention
  • the conventional steel is a hot-work tool steel that is, of course, currently in general use, outside the component range of the present invention. .
  • time for example, it takes 10 minutes to cool from 1030 ° C to 525 ° C, it is expressed as “semi-cooled 10 minutes”). It was cooled in about 40 minutes semi-cooling to correspond to the part where the cooling rate was slow, such as the central part of steel. Then tempered at different temperatures, and adjusted to the hardness of 46HRC Bruno 0
  • Conventional steel 31 not only has a low Mo content, but also has a low C content and Ni, which has no added iron. The impact value tends to be low with a large amount of Mo
  • the inventive steels 1 to 13 having the optimum chemical composition maintain excellent toughness even when quenched at a slow cooling rate.
  • the comparative steel 23 is a composition in which only Ni, which is an element that enhances toughness as compared with the optimum composition according to the present invention, deviates from a high level. Therefore, the toughness is good even when the cooling rate is slow.
  • Comparative Steel 23 which is out of the narrow range of the optimum composition of the present invention, was excellent in toughness but inferior in high-temperature strength due to its excessive Ni content.
  • the steel of the present invention Yes It can be seen that the deviation is high and has high temperature strength.
  • the steel of the present invention 6, the comparative steels 21 to 23 and 26, and the conventional steels 31 and 32 produced in Example 1 are targeted for steel materials quenched at a slow cooling rate of about 40 minutes.
  • the following preliminary tissue observation was performed. First, 10 mm square tissue observation samples were collected from these steel materials, and the samples corroded by the S, PEED method were used and observed 5000 times with a scanning electron microscope.
  • images obtained from steel 6 of the present invention and conventional steel 31 are shown in FIGS. Using these images, the area ratio of the massive tissue and needle-like tissue was measured by image analysis.
  • Fig. 2 and Fig. 5 show the schematic diagrams of the massive structure of Invention Steel 6 and Conventional Steel 31 and Fig.
  • FIG. 3 shows the schematic diagram of the measurement of the acicular structure of Invention Steel 6 and Conventional Steel 31 (mark X). And is shown in FIG.
  • the average was taken as the area ratio.
  • the amount of retained austenite was measured by the X-ray diffraction method for the sample finished by electropolishing after repolishing the sample. Table 4 summarizes the above results.
  • Example 1 Although disclosed in Example 1, the result of the Charpy impact test is obtained together with the tempering hardness of the test piece and the value X derived from the relationship between the hardness and the tissue ratio of the present invention. Table 5 shows.
  • Comparative Steel 22 and Comparative Steel 26 with a low Mo content have a low impact value because a massive structure develops because the Ni content is too large. In both samples, the comparative steel 26 also has a high Si content, so a tendency to form a needle-like structure is also observed.
  • the quenched structure of the steel 6 of the present invention with the optimum chemical composition adjusted is evaluated, the needle-like braid develops, but the bulk structure is small, and above all, the toughness is improved. A lot of effective retained austenite remains. It is also excellent in the balance (ie, X value) of the above organization. Note that the hardened structure of comparative steel 23, which has good toughness because it contains a large amount of Ni, satisfies the X value force O or more even though it has a lot of massive structure. As described above, the high-temperature strength is inferior, though the strength is low.
  • FIG. 1 is a cross-sectional microphotograph showing an example of a quenched structure of the hot tool steel of the present invention.
  • FIG. 2 is a schematic diagram in which a massive structure is selected in the quenched structure of FIG.
  • FIG. 3 is a schematic diagram in which a needle-like structure is selected in the quenched structure of FIG.
  • FIG. 4 is a cross-sectional micrograph showing an example of a quenched structure of a hot work tool steel of a comparative example.
  • FIG. 5 is a schematic diagram in which a massive structure is selected for the quenched structure of FIG.
  • FIG. 6 A schematic diagram in which a needle-like structure is selected in the quenched structure of FIG.

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Abstract

L'invention concerne un acier à outils pour formage à chaud présentant une rigidité améliorée et une excellente résistance à des températures élevées. L'invention concerne également un procédé destiné à produire l'acier à outils pour formage à chaud. L'acier à outils pour formage à chaud comporte les composants suivants (en masse) : C : 0,34-0,40 %, Si : 0,3-0,5 %, Mn : 0,45-0,75 %, Ni : 0-0,5 % (exclusif), Cr : 4,9-5,5 %, (Mo + 1/2W) : 2,5-2,9 % (à condition que Mo et W soient contenus isolément ou en combinaison), et V : 0,5-0,7 %, le reste étant constitué de Fe et des inévitables impuretés. De préférence, la structure de section transversale de l'acier à outils pour formage à chaud contient, lors de la trempe, une structure massive et une structure en aiguille, la structure massive (A %) représentant 45 % max. de la surface, la structure en aiguille (B %) représentant 40 % max. de la surface, et l'austénite restante (C %) représentant entre 5 et 20 % du volume. L'invention concerne également un procédé destiné à produire un acier à outils pour formage à chaud, qui consiste à tremper l'acier à outils pour formage à chaud susmentionné de sorte qu'une valeur X définie par l'expression relationnelle suivante entre une dureté après trempage (HRC) et le pourcentage de tissus atteigne 40 ou plus. X = [-0,36 × (HRC) - 1,47 × (A %) - 1,67 × (B %) + 6,55 × (C %) + 72,91].
PCT/JP2007/067915 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 WO2008032816A1 (fr)

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Application Number Priority Date Filing Date Title
US12/440,406 US20100193089A1 (en) 2006-09-15 2007-09-14 Hot-working tool steel having excellent toughness and high-temperature strength and method for production thereof
EP07807322.8A EP2065483A4 (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
KR1020137006463A KR20130036076A (ko) 2006-09-15 2007-09-14 인성 및 고온 강도가 우수한 열간 공구강 및 그의 제조 방법

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JP2006251003 2006-09-15
JP2006-251003 2006-09-15

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WO2008032816A1 true WO2008032816A1 (fr) 2008-03-20

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US (1) US20100193089A1 (fr)
EP (1) EP2065483A4 (fr)
KR (3) KR20120006091A (fr)
CN (2) CN101517114A (fr)
WO (1) WO2008032816A1 (fr)

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KR20160104028A (ko) 2014-05-28 2016-09-02 히타치 긴조쿠 가부시키가이샤 열간 공구 재료 및 열간 공구의 제조 방법
KR20170020879A (ko) 2014-07-23 2017-02-24 히타치 긴조쿠 가부시키가이샤 열간 공구 재료, 열간 공구의 제조 방법 및 열간 공구

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CN103403209B (zh) * 2011-03-03 2016-01-13 日立金属株式会社 韧性优异的热作工具钢及其制造方法
EP2662460A1 (fr) * 2012-05-07 2013-11-13 Valls Besitz GmbH Traitements thermiques bainitiques résistants sur des aciers pour outillage
KR20150121155A (ko) * 2013-03-01 2015-10-28 로발마, 에쎄.아 높은 열 확산도, 높은 인성 및 열처리 도중 균열 위험이 낮은 공구강
WO2018182480A1 (fr) * 2017-03-29 2018-10-04 Uddeholms Ab Acier à outils pour travail à chaud
KR102550394B1 (ko) * 2018-10-05 2023-07-03 가부시키가이샤 프로테리아루 열간 공구강 및 열간 공구
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
CN114535944B (zh) * 2021-12-15 2022-11-29 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
KR20240029270A (ko) 2022-08-26 2024-03-05 현대자동차주식회사 열간 공구강 및 이의 제조방법

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US20100150772A1 (en) * 2008-11-20 2010-06-17 Boehler Edelstahl Gmbh & Co. Kg Hot-forming steel alloy
US20150292067A1 (en) * 2008-11-20 2015-10-15 Boehler Edelstahl Gmbh & Co. Kg Hot-forming steel alloy
KR20160104028A (ko) 2014-05-28 2016-09-02 히타치 긴조쿠 가부시키가이샤 열간 공구 재료 및 열간 공구의 제조 방법
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KR20090043556A (ko) 2009-05-06
US20100193089A1 (en) 2010-08-05
CN102994902A (zh) 2013-03-27
KR20130036076A (ko) 2013-04-09
EP2065483A4 (fr) 2016-03-23
CN101517114A (zh) 2009-08-26
EP2065483A1 (fr) 2009-06-03

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