US20060251537A1 - Cold die steel excellent in characteristic of suppressing dimensional change - Google Patents

Cold die steel excellent in characteristic of suppressing dimensional change Download PDF

Info

Publication number
US20060251537A1
US20060251537A1 US10/538,367 US53836705A US2006251537A1 US 20060251537 A1 US20060251537 A1 US 20060251537A1 US 53836705 A US53836705 A US 53836705A US 2006251537 A1 US2006251537 A1 US 2006251537A1
Authority
US
United States
Prior art keywords
less
die steel
dimensional change
cold die
present
Prior art date
Legal status (The legal status 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 status listed.)
Abandoned
Application number
US10/538,367
Other languages
English (en)
Inventor
Kunichika Kubota
Hideshi Nakatsu
Shugo Komatsubara
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.)
Proterial Ltd
Original Assignee
Individual
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
Publication date
Application filed by Individual filed Critical Individual
Assigned to HITACHI METALS, LTD. reassignment HITACHI METALS, LTD. ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: KOMATSUBARA, SHUGO, KUBOTA, KUNICHIKA, NAKATSU, HIDESHI
Publication of US20060251537A1 publication Critical patent/US20060251537A1/en
Priority to US12/343,923 priority Critical patent/US8815147B2/en
Abandoned legal-status Critical Current

Links

Images

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
    • 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
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • 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
    • C22C38/60—Ferrous alloys, e.g. steel alloys containing lead, selenium, tellurium, or antimony, or more than 0.04% by weight of sulfur

Definitions

  • the present invention generally relates to a tool material, and particularly relates to a cold die steel preferably used in a die assembly for molding components for a household electrical appliance, a mobile telephone, an automobile and the like.
  • JIS SKD11 has been in heavy usage for a cold die steel, but some attempts have been made to modify the SKD11 in order to improve machinability, toughness and hardness after secondary hardening.
  • a cold die steel referred to 10% Cr SKD which has improved machinability and toughness, in which amounts of added carbon and chromium are adjusted so as to reduce non-solute carbides while the matrix composition are maintained to be that of SKD11 as much as possible
  • a cold die steel referred to 8% Cr SKD which has improved secondary hardening capability, in which an amount of non-solute carbides are reduced and an amount of molybdenum is increased while the matrix composition are maintained to be that of SKD11 as much as possible.
  • the dilatational change of dimension in tempering is caused by a release of a residual stress formed in a previous quenching step (by decomposition of retained austenite), and is promoted by precipitation of temper carbides formed by molybdenum and the like which are conventionally added expecting for secondary hardening.
  • the retained austenite is restrained by non-solute primary carbides which have been formed in casting and originally existed, the decomposition thereof in the tempering step is suppressed.
  • the present invention is to provide a cold die steel particularly suitable for a tool material, in which dimensional change is suppressed in quenching and tempering, so that the working and adjusting steps after heat treatment can be reduced which has increased the number of die-manufacturing steps.
  • the present inventors searched for techniques of canceling the dimensional change adversely to suppress the dimensional change which has been difficult to sufficiently suppress, under the condition that the target steel maintains all characteristics required for a cold die steel in tempering. Furthermore, they studied in detail the structural change of a matrix during tempering, and discovered that temper carbides themselves do not contribute to secondary hardening so much. Thus, they have found new means for suppressing the dimensional change and also increasing hardness, and could obtain a cold die steel having other characteristics sufficiently as well.
  • the present invention provides a cold die steel having a chemical composition described below and excellent characteristics of suppressing the dimensional change.
  • Important features of the present invention are to suppress the dimensional change by offsetting it, which has been difficult to be basically suppressed, while the characteristics required of a cold die steel are maintained.
  • the above described temper carbides have been used for secondary hardening in spite of being the factor of promoting the dilatational change of dimension in tempering, the inventors discovered that the secondary hardening capability thereof are small through a detailed study of the hardening behavior of the cold work die steel during heat treatment as described above.
  • the present inventors have found means for compensating the shortage of the secondary hardening capability while suppressing the dimensional change. According to the compensation means, the excellent characteristics of suppressing the dimensional change and having high hardness can be achieved without lowering necessary characteristics including machinability and abrasion resistance.
  • a principle of the present invention is to provide a cold die steel excellent in characteristics of suppressing the dimensional change and having high hardness, which is based on a chemical composition in which the primary carbides are reduced and the dimensional change is suppressed in an extent of satisfying the characteristics, and to which adequate amounts of nickel and aluminum are added, and besides an adequate amount of cupper is added corresponding to the amounts of nickel and aluminum.
  • nickel and aluminum form intermetallic compounds precipitating in a secondary hardening region when the above described tool steel is tempered (aged), which cause a contractional change of dimension, and thereby can cancel the above described dilatation due to the decomposition of the retained austenite. It is important for the above described setoff effect to precipitate the Ni—Al intermetallic compounds at the secondary hardening temperature of the tool steel, and the amount of cupper having the effect therefor should be appropriately controlled.
  • the present inventors studied in detail the structural change of the matrix in heat treatment for high-temperature tempering in which the retained austenite decomposes and temper carbides precipitate, which particularly causes many problems of the dilatational change of dimension.
  • temper carbides which promote the dimensional change greatly contribute to improve abrasion resistance, but can not confirm that fine carbides are precipitated, although they have been conventionally considered to particularly contribute to secondary hardening. They found that the degree of secondary hardening is greatly affected by factors in the matrix.
  • Ni—Al intermetallic compounds adopted in the present invention have a secondary hardening effect as a precipitation strengthening element, thereby further compensates the secondary hardening in addition to the above described setoff effect of the dimensional change.
  • excellent resistance to the dimensional change and high hardness characteristics can be achieved without lowering other necessary characteristics such as machinability and abrasion resistance.
  • the precipitation strengthening method with intermetallic compounds has been conventionally often applied to a maraging steel, but has not been used in the field of a tool steel including 0.2 mass % or more of carbon, and particularly in the field of a cold die steel which relates to the present invention.
  • the present inventors knew that temper carbides do not actually have such a high secondary hardening effect on the tool steel in itself as has been considered, and consequently noticed to use such an intermetallic compound. Because nickel and aluminum act individually to lower the required properties of the tool steel, an appropriate composition and alloy design for the tool steel are necessary in consideration of the mutual interaction of them with cupper.
  • the degree of the dimensional change depends on an amount of a solid solute carbon existing in a matrix when it is quenched. In other words, the dimensional change is generated due to the expansion of crystal lattices by the force of a solute carbon in a martensitic structure.
  • an alloy composition is totally designed so that the amount of solid-solute carbon can be in the vicinity of 0.6 (mass %) when quenched, which value is analogous to SKD11.
  • the cold die steel according to the present invention is designed to have such a composition that the amount of solid-solute carbon is intended to be about 0.53% which is lower than that in the conventional steel.
  • the design of the composition is achieved by addition of elements such as cupper, nickel and aluminum, which decrease the amount of solid-solute carbon. That is a principle of the design for suppressing dilatation in quenching.
  • FIG. 1 shows a summarized concept for the above conditions.
  • reference character A shows “an effect for suppressing dilatation due to decrease of an amount of solid-solute carbon”
  • reference character B shows “that the dimensional change are setoff due to precipitation strengthening”
  • reference character C denotes “a secondary hardening temperature of the steel according to the present invention.”
  • a principle of the present invention is to simultaneously satisfy the two points of: (1) decreasing the amount of solid-solute carbon in quenching (see the reference character A in FIG. 1 ); and (2) offsetting a volume change of a matrix in secondary hardening, due to addition of cupper, nickel and aluminum (see the reference character B in FIG. 1 ).
  • the concept for the item (1) it is most important industrially to control the amount of solid-solute carbon to be approximately 0.53% at a general-purpose quenching temperature of about 1,030° C.
  • the concept for the item (2) as it is concerned that adding of cupper and nickel might degrade hot and cold workabilities, it is important to keep a balance between the level for preventing the degradation thereof and that for causing the maximum precipitation strengthening.
  • composition of the cold die steel according to the present invention will be explained below.
  • a notation of % means mass percent, for indicating a content of each element.
  • Carbon (C) is an important element which partly solutes in a matrix to impart strength thereto, and partly forms carbides to improve wear resistance and resistance to seizure.
  • a ratio of an amount of solid-solute carbon to that of carbon in carbides in the steel is mainly determined by an interaction between carbon and chromium, so that the carbon content must be simultaneously specified with chromium content in consideration of the interaction therebetween.
  • the amount of carbon is independently in a range of 0.7 to 1.6%, preferably in a range of 0.9 to 1.3%.
  • Silicon (Si) is an important element for the cold die steel according to the present invention. Although about 0.3% of silicon is normally added as a deoxidizing agent, 0.5% or higher of silicon is added in the present invention which is higher than usual. It is important to prevent a softening of the steel below a tempering temperature of about 490° C., because it is concerned that quenching hardness of the steel may be lowered due to a design of the composition for suppressing the dilatation in quenching. However, as an excessive silicon content causes formation of a delta ferrite, the upper limit is defined to be 3.0%. A preferable amount of silicon is in a range of 0.9 to 2.0%.
  • Manganese (Mn) is used for a deoxidizing agent as well as silicon, and the steel contains at least 0.1% of manganese. However, as an excessive manganese content lowers machinability, the upper limit is defined to be 3.0%. A preferable amount of manganese is in a range of 0.1 to 1.0%.
  • Chromium (Cr) is an indispensable element for forming carbides as well as for enhancing hardenability.
  • a ratio of an amount of solute chromium with respect to that of chromium in carbides is determined by interaction between chromium and carbon as in the case of carbon.
  • the chromium content must be simultaneously specified with the carbon content in consideration of the interaction therebetween.
  • an amount of chromium is independently in a range of 7.0 to 13.0%, preferably in a range of 8.0 to 11.0%.
  • Molybdenum (Mo) and tungsten (W) impart a similar working-effect to the steel, the level of which can be specified by (Mo+(W/2)) in consideration of an atomic weight.
  • Molybdenum and tungsten are considered to play an important role in secondary hardening of a tool steel, so that large amounts of molybdenum and tungsten are added to a high-speed tool steel requiring high hardness, for they are used in small products such as a byte or a drill.
  • molybdenum and tungsten are indispensably added because they greatly contribute to a matrix condition for developing secondary hardening. If the content is less than 0.5% a sufficient effect is not obtained.
  • an amount of (Mo+(W/2)) is defined to be in a range of 0.5 to 1.7%, preferably in a range of 0.75 to 1.5%.
  • Aluminum (Al) is coupled with nickel to form a Ni—Al intermetallic compound such as Ni 3 Al or NiAl, and causes secondary hardening through its precipitation. A matrix is retracted through the precipitation reaction, which cancels the dilatation reaction in the tool steel in secondary hardening. As a result, the dimensional change is suppressed.
  • the aluminum content of less than 0.1% does not provide a sufficient effect, but on the other hand, an excessive content exceeding 0.7% causes a remarkable formation of a delta ferrite, so that an amount of Aluminum is specified to be in a range of 0.1 to 0.7%, preferably in a range of 0.1 to 0.5%, further preferably in a range of 0.15 to 0.45%.
  • Nickel (Ni) is coupled with aluminum to form a Ni—Al intermetallic compound which precipitates as described above, and simultaneously thereby causes secondary hardening and the suppression of the dimensional change.
  • nickel is an important element in the present invention.
  • it is an useful element for preventing red brittleness of the cold die steel according to the present invention which contained cupper as described below.
  • the nickel content of less than 0.3% does not provide a sufficient effect, but on the other hand, an excessive content exceeding 1.5% increases a solubility limit of carbon in iron and lowers the workability in an annealed state.
  • an amount of nickel is specified to be in a range of 0.3 to 1.5%, preferably in a range of 0.4 to 1.5%, further preferably in a range of 0.5 to 1.3%.
  • a preferable ratio of nickel to aluminum is 1.2 to 3.7.
  • a more preferable one is in a range of 1.3 to 3.7, and a further preferable one is in a range of 2.5 to 3.5.
  • a metal phase of cupper starts to precipitate from a temperature of about 480° C. or higher and forms a nucleus of precipitation for an intermetallic compound, so that it enables the above described Ni—Al intermetallic compound to precipitate just at the vicinity of a secondary hardening temperature of the tool steel, although the compound originally precipitates at a higher temperature. Accordingly, it makes the tool steel according to the present invention develop fully the offset effect of the dimensional change and the secondary hardening effect due to the precipitation of the Ni—Al intermetallic compound.
  • the amount thereof is important in the present invention to specify the amount thereof to be in a range of 0.1 to 1.0%, preferably in a range of 0.2 to 0.8%.
  • S Sulfur
  • S is an useful and indispensable element for the cold die steel according to the present invention, because it improves machinability.
  • the content is in a range of 0.01 to 0.12%, preferably 0.03 to 0.09%.
  • Columbium (Nb) is a preferable element to be contained for the cold work die steel according to the present invention, because it functions to make carbides distribute uniformly in a structure and reduce deformation due to heat treatment.
  • An amount of columbium is preferably 0.03% or more, but is desirably 0.3% or less, because columbium contained in the steel forms an MX compound and an excessive amount of the compound impairs machinability.
  • Phosphor (P) is controlled to be less than 0.05%, preferably 0.02% or less, because it is an element which lowers toughness.
  • Vanadium (V) can be added to improve hardenability, but it lowers machinability. Thus an amount of vanadium is limited to be less than 0.7%, preferably 0.5% or less, even though it is added.
  • the present invention provides a cold die steel which satisfies the above described conditions and contains iron (Fe) substantially as the balance. Characteristics of suppressing a dimensional change and excellent secondary hardening are achieved by the cold die steel which consists of, for instance, the above described elements, iron, and other elements of 20% or less, 10% or less, or 5% or less in total, or which consist of the above described elements and the balance of iron with unavoidable impurities.
  • FIG. 1 is a view which shows dimensional changes and hardness due to tempering for cold die steels to explain an effect of the present invention
  • FIG. 2 is a view showing dimensional changes of cold die steels due to heat treatment
  • FIG. 3A is a front view of a test piece used in an example according to the present invention, for measuring a quantity of torsion of cold die steels due to heat treatment;
  • FIG. 3B is a side view of a test piece used in an example according to the present invention, for measuring a quantity of torsion of cold die steels due to heat treatment;
  • FIG. 4 is a view showing a quantity of torsion of cold die steels due to heat treatment.
  • Samples No. 1 to 6 according to the present invention and comparative examples No. 7 to 9 were melt with a high-frequency induction heating device in the ambient atmosphere, and formed into ingots with a cross section size of 80 ⁇ 80 mm, each of which has a composition shown in Table 1 with the balance of iron and unavoidable impurities.
  • the sample No. 7 is a material referred to JIS SKD11
  • the sample No. 8 is 8% Cr SKD
  • the sample No. 9 is 10% Cr SKD.
  • these ingots were hot-worked into a wire material with a cross section size of 15 mm ⁇ 15 mm. They were then annealed, and test pieces of 8 mm ⁇ 80 mmL were formed, and the longitudinal dimensions thereof were measured. Then, they were quenched at 1,030° C. (nitrogen cooling at a pressure of 0.506 MPa), and subsequently subjected to high-temperature tempering twice to be secondary hardened so as to have a hardness around 60 to 63 HRC. The dimensions were measured again at this condition.
  • the sample No. 8 (8% Cr SKD) is secondary hardened at a tempering temperature of about 525° C., and the other samples are secondary hardened at a tempering temperature of about 510° C. All samples of No. 1 to 6 after heat treatment have higher hardness than that of SKD11 (No. 7), which means that those samples have excellent secondary hardening capability.
  • FIG. 2 shows a dimensional change of each sample due to heat treatment, or, a dimensional change during secondary hardening.
  • the dimensional change during heat treatment was calculated from the measurements on longitudinal dimensions before and after the above described heat treatment, by using the following formula.
  • dimensional change during heat treatment ((dimension after heat treatment-dimension before heat treatment)/dimension before heat treatment) ⁇ 100
  • the sample No. 8 has the largest dilatation and shows the largest dimensional change. This is because it contains excessive molybdenum.
  • the samples No. 7 and 9 have compositions adequately adjusted to have an amount of molybdenum equivalent of (Mo+(W/2)) being about 1.0%, but still cause the dilatation around 0.05%.
  • the samples of No. 1 to 6 containing the appropriate amounts of nickel, cupper and aluminum show the dimensional change due to heat treatment controlled to be 0.01% or less. The result shows that a precipitation reaction of Ni—Al intermetallic compounds in a secondary hardening region offsets the dilatation.
  • FIGS. 3A front view
  • 3 B side view
  • each clearance (gap size) at the positions of arrow (1) (at 2.5 mm from the left), arrow (2) (at 5.0 mm from the left) and arrow (3) (at 7.5 mm from the left) is 0.5 mm.
  • the test pieces were then heat-treated in the same way as in Example 1, and the clearances at the same positions were measured again.
  • the results of the calculated quantities of torsion are shown in FIG. 4 .
  • the sample No. 7 has the largest quantity of torsion. This is because the sample contains a large amount of solid-solute carbon in the martensite and a large amount of non-solute carbide, and thereby a strong inner stress is generated by the dilatation of the matrix and the restraint by the non-solute carbides.
  • the samples No. 8 and 9 have a large quantity of torsion in spite of containing few non-solute carbides, but the samples of No. 1 to 6, in which the inner stress of the matrix is offset by the precipitation of Ni—Al intermetallic compounds, obviously have small quantities of torsion. Furthermore, the sample No. 6 containing the appropriate amount of columbium provides an adequate result that torsion was not measured within the measurement accuracy of ⁇ 0.0001 mm.
  • the tool steel in the present invention are not dimensional changed and deformed due to heat treatment, and makes it possible to reduce/omitted finish working for correction after heat treatment. Thus, manufacturing cost for the die assembly can be reduced.
  • the tool steel further make it possible to shorten a period for manufacturing the die assembly, and to heat treat a die having a more complicated shape, so that the present invention is an industrially extremely useful technology.
  • the cold die steel according to the present invention is preferably used as a tool material for forming components in machines.
US10/538,367 2002-12-25 2003-12-19 Cold die steel excellent in characteristic of suppressing dimensional change Abandoned US20060251537A1 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
US12/343,923 US8815147B2 (en) 2002-12-25 2008-12-24 Cold die steel excellent in characteristic of suppressing dimensional change

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP2002-373727 2002-12-25
JP2002373727 2002-12-25
PCT/JP2003/016392 WO2004059023A1 (ja) 2002-12-25 2003-12-19 変寸抑制特性に優れた冷間ダイス鋼

Related Child Applications (1)

Application Number Title Priority Date Filing Date
US12/343,923 Continuation US8815147B2 (en) 2002-12-25 2008-12-24 Cold die steel excellent in characteristic of suppressing dimensional change

Publications (1)

Publication Number Publication Date
US20060251537A1 true US20060251537A1 (en) 2006-11-09

Family

ID=32677266

Family Applications (2)

Application Number Title Priority Date Filing Date
US10/538,367 Abandoned US20060251537A1 (en) 2002-12-25 2003-12-19 Cold die steel excellent in characteristic of suppressing dimensional change
US12/343,923 Active 2024-11-10 US8815147B2 (en) 2002-12-25 2008-12-24 Cold die steel excellent in characteristic of suppressing dimensional change

Family Applications After (1)

Application Number Title Priority Date Filing Date
US12/343,923 Active 2024-11-10 US8815147B2 (en) 2002-12-25 2008-12-24 Cold die steel excellent in characteristic of suppressing dimensional change

Country Status (7)

Country Link
US (2) US20060251537A1 (ja)
EP (1) EP1580290B1 (ja)
JP (1) JP4258772B2 (ja)
CN (1) CN100513609C (ja)
AT (1) ATE549428T1 (ja)
AU (1) AU2003289470A1 (ja)
WO (1) WO2004059023A1 (ja)

Families Citing this family (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP4737606B2 (ja) * 2004-11-18 2011-08-03 日立金属株式会社 変寸抑制特性および耐カジリ性に優れた冷間ダイス鋼
JP4844874B2 (ja) * 2005-05-26 2011-12-28 日立金属株式会社 プレス成形品の製造方法
CN100422375C (zh) * 2006-01-25 2008-10-01 周向儒 一种铬钢系模具钢及其热处理工艺
CN100413991C (zh) * 2006-02-08 2008-08-27 周向儒 一种高合金模具钢及其热处理工艺
CN101392354B (zh) * 2008-10-24 2010-09-08 宁波禾顺新材料有限公司 一种高合金冷作模具钢
JP5776959B2 (ja) * 2009-12-18 2015-09-09 日立金属株式会社 熱間加工性に優れた金型用鋼
CN103834872A (zh) * 2012-11-26 2014-06-04 天工爱和特钢有限公司 高耐磨性模具钢
CN104046891B (zh) * 2013-03-13 2017-04-26 香港城市大学 纳米金属间化合物强化的超高强度铁素体钢及其制造方法
CN104611645B (zh) * 2014-12-29 2018-09-21 芜湖金龙模具锻造有限责任公司 一种耐高温合金模具钢
JP6424951B2 (ja) * 2015-03-26 2018-11-21 日立金属株式会社 摺動部品および摺動構造体
CN105089711B (zh) * 2015-06-25 2017-08-08 重庆德蚨乐机械制造有限公司 涡轮增压器及其喷嘴环
CN110656281A (zh) * 2018-06-29 2020-01-07 宝钢特钢有限公司 一种高硬模具钢及其制备方法
CN110016617B (zh) * 2019-05-08 2021-05-04 上海大学 一种冷作模具钢及其制备方法

Family Cites Families (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5218419A (en) * 1975-08-02 1977-02-12 Nippon Steel Corp Method of manufacturing si-cont. steel
JPS62211351A (ja) 1986-03-11 1987-09-17 Daido Steel Co Ltd 被削性の優れた工具鋼
JPS62263922A (ja) * 1986-05-09 1987-11-16 Japan Casting & Forging Corp 鍛鋼の製造法
JPS6411945A (en) * 1987-07-03 1989-01-17 Daido Steel Co Ltd Cold tool steel
JP2636816B2 (ja) 1995-09-08 1997-07-30 大同特殊鋼株式会社 合金工具鋼
JP3507879B2 (ja) 1997-09-12 2004-03-15 日本高周波鋼業株式会社 冷間工具鋼
JP3657110B2 (ja) 1998-03-26 2005-06-08 日本高周波鋼業株式会社 耐摩耗性、被削性に優れたプレハードン用高硬度冷間工具鋼
SE511747C2 (sv) * 1998-03-27 1999-11-15 Uddeholm Tooling Ab Kallarbetsstål
JP3736721B2 (ja) * 1998-11-11 2006-01-18 山陽特殊製鋼株式会社 高耐食快削ステンレス鋼
JP4352491B2 (ja) * 1998-12-25 2009-10-28 大同特殊鋼株式会社 快削性冷間工具鋼
JP3365624B2 (ja) 1999-07-30 2003-01-14 日立金属株式会社 被削性および熱処理性に優れた工具鋼およびそれを用いた金型
CN1097642C (zh) * 1999-07-30 2003-01-01 日立金属株式会社 焊接性、切削性和热处理性好的工具钢及其制成的金属模
FR2823768B1 (fr) * 2001-04-18 2003-09-05 Usinor Acier a outils a tenacite renforcee, procede de fabrication de pieces dans cet acier et pieces obtenues

Also Published As

Publication number Publication date
EP1580290B1 (en) 2012-03-14
ATE549428T1 (de) 2012-03-15
US20090120540A1 (en) 2009-05-14
EP1580290A1 (en) 2005-09-28
US8815147B2 (en) 2014-08-26
JPWO2004059023A1 (ja) 2006-04-27
WO2004059023A1 (ja) 2004-07-15
AU2003289470A1 (en) 2004-07-22
EP1580290A4 (en) 2006-02-08
JP4258772B2 (ja) 2009-04-30
CN100513609C (zh) 2009-07-15
CN1723293A (zh) 2006-01-18

Similar Documents

Publication Publication Date Title
US8815147B2 (en) Cold die steel excellent in characteristic of suppressing dimensional change
US20050161125A1 (en) Alloy tool steel
US6767414B2 (en) Maraging steel having high fatigue strength and maraging steel strip made of same
JP5655366B2 (ja) ベイナイト鋼
WO2010074017A1 (ja) 鋼の焼入方法
US20060243352A1 (en) Process for producing steel products having improved grain size properties and machinability
KR20190031446A (ko) 석출 경화 강(precipitation hardening steel) 및 그의 제조
KR20120053616A (ko) 내마모성과 내충격성이 향상된 건설기계용 버켓 투스
JP3449311B2 (ja) 高靱性・高耐食性継目無鋼管
US6841122B2 (en) Hot working die steel excelling in molten corrosion resistance and strength at elevated temperature and member for high temperature use formed of the hot working die steel
JP2007308784A (ja) 合金鋼
EP0498105B1 (en) High strength and high toughness stainless steel and method of manufacturing the same
JP2003201513A (ja) 高強度肌焼鋼
JP4487257B2 (ja) 変寸抑制特性に優れた冷間ダイス鋼
JP2021095606A (ja) 軟化抵抗性及び窒化特性に優れた高強度熱間工具鋼
JP2591807B2 (ja) 冷間鍛造性及び高周波焼入れ性に優れた機械構造用炭素鋼
KR101776491B1 (ko) 내식성이 우수한 고강도 스프링강
KR101655181B1 (ko) 고강도 강 및 기어 제조 방법
KR102463015B1 (ko) 열간가공성이 우수한 고강도 오스테나이트계 스테인리스강
JPH07207412A (ja) 結晶粒安定化浸炭用鋼
JP2001131683A (ja) 小ロット生産用金型鋼
KR20240002518A (ko) 냉간단조용 합금강 부품의 제조방법
KR101605964B1 (ko) 금형강 및 이의 제조방법
KR940000822B1 (ko) 내마멸성 강철
KR19990024462A (ko) 저온 볼.너트용 cr-mo(-b) 강재 및 그의 제조방법

Legal Events

Date Code Title Description
AS Assignment

Owner name: HITACHI METALS, LTD., JAPAN

Free format text: ASSIGNMENT OF ASSIGNORS INTEREST;ASSIGNORS:KUBOTA, KUNICHIKA;NAKATSU, HIDESHI;KOMATSUBARA, SHUGO;REEL/FRAME:018071/0376

Effective date: 20050527

STCB Information on status: application discontinuation

Free format text: ABANDONED -- FAILURE TO RESPOND TO AN OFFICE ACTION