EP2154260A1 - Automatenlegierungswerkzeugstahl - Google Patents

Automatenlegierungswerkzeugstahl Download PDF

Info

Publication number
EP2154260A1
EP2154260A1 EP09009568A EP09009568A EP2154260A1 EP 2154260 A1 EP2154260 A1 EP 2154260A1 EP 09009568 A EP09009568 A EP 09009568A EP 09009568 A EP09009568 A EP 09009568A EP 2154260 A1 EP2154260 A1 EP 2154260A1
Authority
EP
European Patent Office
Prior art keywords
amount
added
tool steel
quenching
hardenability
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.)
Granted
Application number
EP09009568A
Other languages
English (en)
French (fr)
Other versions
EP2154260B1 (de
Inventor
Takayuki Shimizu
Tetsuya Masuda
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
Original Assignee
Daido Steel Co 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
Publication date
Application filed by Daido Steel Co Ltd filed Critical Daido Steel Co Ltd
Publication of EP2154260A1 publication Critical patent/EP2154260A1/de
Application granted granted Critical
Publication of EP2154260B1 publication Critical patent/EP2154260B1/de
Not-in-force legal-status Critical Current
Anticipated expiration legal-status Critical

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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • 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
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese

Definitions

  • the present invention relates to a free-cutting alloy tool steel. More specifically, the present invention related to a free-cutting alloy tool steel which is particularly prevented from heat treatment deformation by quenching as well as deformation by machining.
  • the objective products of the present invention include a cold mold used for the processing by forging or a progressive die press in cold working, and a machine structural member.
  • Examples of the cold mold include a block punch, a button die, a pilot punch, a straight punch, a drawing punch, a drawing die, a bending punch/die, a punch-type cutter/roll-type cutter, a thread or groove rolling type, a forging type, a punching member/die for gears, and a swaging die.
  • Examples of the machine structural member include a base plate, a guide plate, a spacer, a stripper, a screw plug, a retainer, a guide bush, a dowel bush, a stripper guide, a knock out pin, a shank, a guide post, a fixing key, a plastic forming tool, a screw member, a cam component, a seal plate and gauges.
  • the mold or structural member in uses above also includes a cold mold or structural member subjected to a surface treatment such as CVD treatment, PVD treatment, TD treatment and nitridation, or a surface modification such as shot peening.
  • a surface treatment such as CVD treatment, PVD treatment, TD treatment and nitridation, or a surface modification such as shot peening.
  • the carbon tool steel or alloy tool steel is disadvantageously poor in the hardenability due to a small added amount of the alloy elements.
  • Mn is an effective element of most enhancing the hardenability
  • a large amount of Mn is added, a large amount of retained austenite remains after quenching. Therefore, addition of Mn is naturally limited and Mn cannot be added above a certain amount.
  • the carbon tool steel or alloy tool steal cannot be applied to a large mold or the like, and the objective product is limited to a small article of 30 mm or less in thickness.
  • the cold die steel is sufficient in the hardenability due to a large added amount of the alloy elements.
  • Patent Document 1 discloses an invention related to "Cold Tool Steel for Flame Hardening”
  • Patent Document 2 discloses an invention related to "Cold Tool Steel Having Constant Strain by Heat Treatment and Method For Producing Cold Tool Using the Same”
  • Patent Document 3 discloses an invention related to "Cold Tool Steel with Excellent Machinability", but all of these inventions differ in the technical idea from the present invention. Accordingly, working examples falling in the component range of the present invention are not found in all of the publications above, and these are an invention different from the present invention.
  • the present invention has been made with an aim to provide a free-cutting alloy tool steel ensuring that both the material deformation due to heat treatment at quenching and the material deformation due to machining are inhibited and hardness necessary as a cold mold or a machine structural component is obtained.
  • the present invention provides the following items.
  • the present invention has characteristic features that high hardenability of an alloy tool steel is ensured owing to a cooperative action between the action brought about by the addition of Mn and the action brought about by the addition of Cr as well as the added amount of Cr is reduced by virtue of the hardenability enhancing effect resulting from addition of Mn, thereby suppressing the formation of carbide and improving the worsening of machinability due to carbide; and that although hardness in the quenched and tempered state is usually reduced by the addition of Mn, the required hardness is maintained owing to decrease in the added amount of Mo.
  • Mn+0.08Cr is added in a range of 1.35 to 2.05% based on the premise of adding Mn in an amount of 0.8% or more, the ratio of Mn/Cr is set to from 0.1 to 0.23 so as to bring a balance between the added amount of Mn and the added amount of Cr, and further, the ratio of (Mo+0.5W)/Mn is set to 0.55 or less so as to bring a balance between the added amount of Mn and the added amount of (Mo+0.5W).
  • the material deformation caused by a heat treatment at the quenching can be suppressed by ensuring sufficient hardenability as in the conventional cold die steel.
  • the added amount of alloy elements is preferably increased.
  • the material deformation caused by machining can be suppressed by reducing the amount of carbide. That is, in terms of material deformation caused by machining, the added amount of alloy elements is preferably reduced.
  • Main examples of the elements forming a carbide include C, Cr, Mo, W and V and accordingly, the amounts of such elements are preferably reduced as much as possible.
  • main examples of the elements not contributing to the formation of a carbide include Si, Mn and Ni and accordingly, the amounts of such elements are preferably increased as much as possible.
  • the present invention has been accomplished based on such ideas or findings.
  • Fig. 1 shows the relationship between the added amount of Cr and the added amount of Mn in the alloy tool steel of the present invention.
  • the region H is the region for the added amounts of Cr and Mn in the present invention.
  • the added amount of Cr that is an expensive alloy element can be reduced to allow for the material cost down and also, the machining is facilitated to bring about reduction in the cost required for working, so that a mold or the like can be produced at a low cost with high effects.
  • the quenching temperature is preferably set to a quenching temperature of 1,000°C or more (and 1,050°C or less).
  • the quenching at the temperature above also has the following meaning.
  • a steel in which Cr is added in a predetermined amount and which is quenched at a quenching temperature of 1,000 to 1,050°C is a quantitatively predominant steel as a tool steel, and accordingly, a heat treatment furnace for quenching is also premised on quenching at such a temperature, that is, a furnace for quenching at 1,000 to 1,050°C is used in general.
  • quenching temperature is less than the temperature above, equipment therefor needs to be installed and in turn, the cost for a quenching treatment rises.
  • the proper quenching temperature of the material is from 1,000 to 1,050°C, a heat treatment furnace need not be newly installed and the quenching treatment can be performed at a low cost as is conventionally done.
  • C needs to be added according to the required hardness so as to bring about martensite formation at the quenching and enhance the hardness.
  • at least 0.50% or more of C needs to be added.
  • the added amount is too large, the amount of carbide proportionally increases. Accordingly, the added amount thereof needs to be 0.90% or less. From the above-described standpoint, the added amount thereof is preferably from 0.65 to 0.80%.
  • Si from 0.50 to 2.20%
  • Si solid dissolves to produce an effect of enhancing the martensite hardness. Since this element enhances the hardenability without forming any , it is added in an amount of 0.50% or more. The added amount thereof is set to 2.20% or less, because if it is too large, a ferrite is produced and the quenching hardness decreases.
  • Mn is an element that effectively enhances the hardenability. In order to ensure the hardenability as an alternative for Cr, Mo, W and V, this element must be added in an amount of 0.8% or more.
  • the proportion of Mn In order to reduce the amount of carbide and ensure the hardenability, it is preferred to raise the proportion of Mn. If the above ratio is less than the lower limit, the amount of carbide is too large and the strain generated due to working cannot be sufficiently decreased, whereas if it exceeds the upper limit, the amount of Mn becomes excessively large and retained austenite is produced in a large amount, failing in ensuring the hardness. Also, if the above ratio exceeds the upper limit, the amount of Cr becomes too small and therefore, insufficient hardenability results.
  • the hardenability is more enhanced as the total added amount of Mn+0.08Cr is larger, but if the total added amount thereof is excessively large, retained austenite is produced in a large amount and the hardness cannot be ensured, whereas if it is too small, insufficient hardenability results.
  • the coefficient of 0.08 of Cr indicates the contribution ratio of Cr to the hardenability based on Mn.
  • Ni from 0.01 to 0.30%
  • Ni has the same effect as Mn.
  • Ni is added in an amount of 0.01% or more.
  • the added amount thereof is 0.30% or less, because if it is excessively large, the amount of retained austenite increases and the hardness decreases.
  • Mo and W have the same effect.
  • the effect of W is half of the effect of Mo and therefore, the coefficient is 0.5. Since the alloy tool steel comes to have nearly sufficient hardenability by the addition of Mn and Cr, these elements should not be preferably added. However, their addition is required in view of hardness and these must be added in an amount of 0.01%. The added amount thereof is 0.50% or less, because if it is excessively large, the amount of unnecessary carbide increases.
  • Mn is added in a large amount of 0.8% or more.
  • Mo+0.5W is excessively large, the Ms point or Mf point lowers too much to reduce the hardness in the quenched and tempered state and a hardness of HRC 58 or more cannot be obtained.
  • the ratio of (Mo+0.5W)/Mn is set to 0.55 or less.
  • Fig. 2 shows the relationship between (Mo+0.5W)/Mn and the quenching/tempering hardness.
  • a steel having the composition above is melted in a vacuum induction furnace to produce 50 kg of an ingot, and the ingot is subjected to soaking at 1,160°C for 10 hours and then forged at a temperature between 900°C and 1,160°C into a square bar of 45 mm ⁇ 45 mm ⁇ 1,500 mm.
  • the tool steel in the square bar state is subjected to a spheroidizing annealing treatment of performing gradual cooling from 900°C at a cooling rate of 20°C/h, and the material after heat treatment is cut and worked into dice of about 20 mm ⁇ 20 mm ⁇ 20 mm.
  • Fig. 2 is a view showing this hardness after quenching/tempering with respect to (Mo+0.5W)/Mn.
  • the added amount of Mo or W is decreased too much, this generally causes reduction of quenching/tempering hardness or reduction of hardenability.
  • the added amounts of components such as C, Mn and Cr are specified so that sufficient quenching/tempering hardness can be obtained.
  • V from 0.01 to 0.15%
  • V is an element having the same effects as Mo and W and in the present invention, this element is added in the range of 0.01 to 0.15%.
  • Se+Te from 0.01 to 0.15%
  • Pb+2Bi from 0.01 to 0.15%
  • these elements all are an element that enhances the cutting or grinding machinability. Depending on the scrap used as the raw material, these elements are sometimes added in large amounts and therefore, can be utilized as an alternative to the addition of S. In order to obtain the machinability enhancing effect by the addition of these elements, the added amounts of these elements need to be more than the lower limits as defined above. However, even if added in excess of the upper limits as defined above, the effect is saturated.
  • Nb+Ta+Ti+Zr from 0.01 to 0.15%
  • These elements all have an effect of forming a carbide or a nitride and preventing coarsening of the grains at the quenching and holding temperature.
  • the addition of Cr, Mo, W and V is reduced as much as possible and therefore, the amount of carbide becomes small. As a result, coarsening of the grains readily occurs.
  • these elements may be added in a total amount of 0.01% or more. However, even if added in excess of the upper limit of 0.15%, the effect is saturated.
  • the minimal amount thereof present in the steel is the smallest non-zero amount used in the Examples of the developed steels as summarized in Table 1.
  • the maximum amount thereof present in the steel is the maximum amount used in the Examples of the developed steels as summarized in Table 1.
  • the quenching temperature of a carbon tool steel or a special tool steel is less than 1,000°C and therefore, the amount of solid-dissolved elements is small, giving rise to poor hardenability.
  • the quenching temperature of a cold die steel (corresponding to SKD) is 1,000°C or more and the amount of solid-dissolved elements increases.
  • a quenching temperature of 1,000°C or more is preferred.
  • a temperature not more than that temperature is preferred.
  • This forged material was cut into a predetermined size required for each test. After the cutting, the material was worked into each specimen and heat-treated at the quenching/tempering temperature shown in Table 2. The hardness after this heat treatment is also shown in Table 2 (when parenthesized, hardness at the quenching temperature in the parenthesis is indicated). Further, as for the evaluation of hardenability and the drill machinability, the test was performed in the spheroidizing annealed state.
  • a specimen of ⁇ 3 mm ⁇ 10 mm was prepared and after holding it at the quenching temperature shown in Table 2 for 5 minutes, cooled to 100°C or less at a uniform cooling rate.
  • the minimum limited cooling rate for obtaining a specimen hardness of HRC 58 or more with respect to each cooling rate when the cooling rate was varied is indicated as the hardenability.
  • the hardenability necessary for the usage concerned is 15°C/min or less.
  • a specimen of 20 mm ⁇ 50 mm ⁇ 100 mm was prepared and after holding it at the quenching temperature shown in Table 2 for 30 minutes, quenched at the cooling rate shown for hardenability. Also, tempering was thereafter performed.
  • the size of the difference needs to be 0.1 mm or less.
  • the difference in the state before heat treatment was set to 0.020 mm (0.020%) or less.
  • a specimen of 50 mm ⁇ 50 mm ⁇ 200 mm was prepared and subjected to punching work by a steam-treated SKH51 HSS drill ( ⁇ 6 mm).
  • the punching work was repeated by changing the cutting rate under constant conditions of dry process, 0.15 mm/rev and bore depth of 15 mm until the drill was damaged by melting or breaking.
  • the cutting rate was gradually decreased, and the cutting rate at which 70 or more bores were obtained was evaluated as the drill lifetime. A larger cutting rate indicates more excellent drill machinability.
  • a specimen of 20 mm ⁇ 50 mm ⁇ 200 mm was prepared and subjected to scraping work of scraping 0.5 mm from the surface of 50 mm ⁇ 200 mm by a flat grinding disc. Assuming that the working time of Comparative Example 6 is 100, the time necessary for 0.5 mm scraping was evaluated. When the time required is half, the grindability was rated 200. A larger numerical value indicates better grindability.
  • the difference between maximum height and minimum height out of the length of 100 mm was measured by a three-dimensional dimension measuring device.
  • the size of the difference needs to be 0.1 mm or less.
  • the difference in the state before grinding work was set to 0.020 mm (0.020%) or less.
  • the specimen was tested in accordance with the method described in JIS Z 2242. As for the specimen, a 10R notch specimen with a notch part of 10R and a depth of 2 mm was prepared. The test was performed at room temperature, and the value was evaluated by the impact value.
  • the specimen was tested by the method described in JIS Z 2274.
  • the specimen used was No. 1 specimen (parallel part: ⁇ 8 mm) and the test was performed at room temperature.
  • the strength causing no breakage when repeating the test 10 7 times was evaluated as a fatigue limit.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Articles (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)
  • Heat Treatment Of Steel (AREA)
  • Accessories And Tools For Shearing Machines (AREA)
EP09009568A 2008-07-23 2009-07-23 Automatenlegierungswerkzeugstahl Not-in-force EP2154260B1 (de)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2008189726 2008-07-23
JP2009091602A JP5504680B2 (ja) 2008-07-23 2009-04-03 快削合金工具鋼

Publications (2)

Publication Number Publication Date
EP2154260A1 true EP2154260A1 (de) 2010-02-17
EP2154260B1 EP2154260B1 (de) 2011-03-30

Family

ID=41136750

Family Applications (1)

Application Number Title Priority Date Filing Date
EP09009568A Not-in-force EP2154260B1 (de) 2008-07-23 2009-07-23 Automatenlegierungswerkzeugstahl

Country Status (6)

Country Link
EP (1) EP2154260B1 (de)
JP (1) JP5504680B2 (de)
KR (1) KR101608087B1 (de)
CN (1) CN101634002B (de)
AT (1) ATE503853T1 (de)
DE (1) DE602009000974D1 (de)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2020161359A1 (en) * 2019-02-08 2020-08-13 Rovalma, S.A. Low cost high performant tool steels
CN112639150A (zh) * 2018-08-31 2021-04-09 霍加纳斯股份有限公司 改性高速钢颗粒，使用其的粉末冶金方法，和由其得到的烧结部件

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102791540B (zh) 2010-03-04 2015-12-16 本田技研工业株式会社 车辆的安全带装置
WO2013100613A1 (ko) * 2011-12-28 2013-07-04 주식회사 포스코 피삭성과 연성이 우수한 내마모 오스테나이트계 강재 및 그의 제조방법
CN104640654B (zh) * 2012-08-20 2017-05-10 日立金属株式会社 冷作工具钢的切削方法和冷作模具材料的制造方法
US9735555B2 (en) 2015-08-27 2017-08-15 Eaton Corporation Mechanical door interlock device for protecting power electrical switching apparatus and users
CN106119738A (zh) * 2016-06-28 2016-11-16 浙江工贸职业技术学院 一种用于海洋钻井平台仪表阀阀芯的合金材料及制作方法

Citations (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1989003898A1 (en) * 1987-10-28 1989-05-05 Uddeholm Tooling Aktiebolag Use of a tool steel for tools for pressing motor car sheet steel
JPH11131182A (ja) 1997-10-31 1999-05-18 Daido Steel Co Ltd フレームハード用冷間工具鋼
JP2001020041A (ja) * 1999-07-08 2001-01-23 Hitachi Metals Ltd 溶接性および被削性に優れた工具鋼ならびに工具、金型
JP2001234278A (ja) 2000-02-16 2001-08-28 Daido Steel Co Ltd 被削性に優れた冷間工具鋼
JP2001316769A (ja) * 2000-05-10 2001-11-16 Daido Steel Co Ltd 冷間工具鋼
JP2002167644A (ja) 2000-11-30 2002-06-11 Daido Steel Co Ltd 熱処理定歪み冷間工具鋼及びこれを用いた冷間工具の製造方法
US20050252580A1 (en) * 2004-05-14 2005-11-17 Daido Steel Co., Ltd. Cold work tool steel
JP2007197746A (ja) * 2006-01-25 2007-08-09 Daido Steel Co Ltd 工具鋼
JP2008189726A (ja) 2007-02-01 2008-08-21 Kao Corp 洗剤粒子
JP2009091602A (ja) 2007-10-04 2009-04-30 Mitsubishi Electric Corp 表面処理方法

Family Cites Families (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH04280942A (ja) * 1991-01-24 1992-10-06 Daido Steel Co Ltd 被削性の優れた鋳鋼
JP2001049394A (ja) * 1999-08-17 2001-02-20 Hitachi Metals Ltd 溶接性及び被削性に優れた工具鋼ならびにそれを用いた金型
JP2001064754A (ja) * 1999-08-30 2001-03-13 Hitachi Metals Ltd 溶接性及び被削性に優れ経年変化を抑制した工具鋼ならびにそれを用いた金型
JP2001294974A (ja) * 2000-04-12 2001-10-26 Hitachi Metals Ltd 被削性に優れ熱処理変寸が小さい工具鋼およびその製造方法
JP3602102B2 (ja) * 2002-02-05 2004-12-15 日本高周波鋼業株式会社 熱間工具鋼

Patent Citations (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO1989003898A1 (en) * 1987-10-28 1989-05-05 Uddeholm Tooling Aktiebolag Use of a tool steel for tools for pressing motor car sheet steel
JPH11131182A (ja) 1997-10-31 1999-05-18 Daido Steel Co Ltd フレームハード用冷間工具鋼
JP2001020041A (ja) * 1999-07-08 2001-01-23 Hitachi Metals Ltd 溶接性および被削性に優れた工具鋼ならびに工具、金型
JP2001234278A (ja) 2000-02-16 2001-08-28 Daido Steel Co Ltd 被削性に優れた冷間工具鋼
JP2001316769A (ja) * 2000-05-10 2001-11-16 Daido Steel Co Ltd 冷間工具鋼
JP2002167644A (ja) 2000-11-30 2002-06-11 Daido Steel Co Ltd 熱処理定歪み冷間工具鋼及びこれを用いた冷間工具の製造方法
US20050252580A1 (en) * 2004-05-14 2005-11-17 Daido Steel Co., Ltd. Cold work tool steel
JP2007197746A (ja) * 2006-01-25 2007-08-09 Daido Steel Co Ltd 工具鋼
JP2008189726A (ja) 2007-02-01 2008-08-21 Kao Corp 洗剤粒子
JP2009091602A (ja) 2007-10-04 2009-04-30 Mitsubishi Electric Corp 表面処理方法

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN112639150A (zh) * 2018-08-31 2021-04-09 霍加纳斯股份有限公司 改性高速钢颗粒，使用其的粉末冶金方法，和由其得到的烧结部件
WO2020161359A1 (en) * 2019-02-08 2020-08-13 Rovalma, S.A. Low cost high performant tool steels
US12319993B2 (en) 2019-02-08 2025-06-03 Rovalma, S.A. Low cost high performant tool steels

Also Published As

Publication number Publication date
KR20100010918A (ko) 2010-02-02
EP2154260B1 (de) 2011-03-30
JP5504680B2 (ja) 2014-05-28
JP2010047831A (ja) 2010-03-04
ATE503853T1 (de) 2011-04-15
DE602009000974D1 (de) 2011-05-12
KR101608087B1 (ko) 2016-03-31
CN101634002A (zh) 2010-01-27
CN101634002B (zh) 2013-07-31

Similar Documents

Publication Publication Date Title
JP5618978B2 (ja) 鋼、鋼ブランクの製造方法、およびこの鋼製の部品を製造する方法
EP2418296B1 (de) Einsatzstahl mit hervorragender kaltumformbarkeit, zerspanbarkeit und ermüdungseigenschaften nach härten aus dem einsatz und herstellungsverfahren dafür
EP2357260B1 (de) Einsatzstahl, aufgekohlte komponente und verfahren zur herstellung des einsatzstahls
US8801873B2 (en) Carburized steel part
KR101369113B1 (ko) 기계 구조용 강과 그 제조 방법 및 기소강 부품과 그 제조 방법
KR20100135205A (ko) 열간가공 공구강 및 이를 이용한 철강제품
JP2013213255A (ja) 熱間金型鋼
US20100132429A1 (en) Cold-work die steel and dies for cold pressing
EP2154260B1 (de) Automatenlegierungswerkzeugstahl
JP4385019B2 (ja) 鋼製軟窒化機械部品の製造方法
JP7172275B2 (ja) ホットスタンプ用金型用鋼、ホットスタンプ用金型およびその製造方法
CN115279932B (zh) 热加工用模具用钢、热加工用模具及其制造方法
JP5597999B2 (ja) 被削性に優れた冷間工具鋼
JP5345415B2 (ja) 被削性、熱処理変寸特性、衝撃特性に優れた冷間プレス金型用鋼およびプレス金型
JP7540437B2 (ja) ホットスタンプ用金型用鋼、ホットスタンプ用金型およびその製造方法
JP5821512B2 (ja) 窒化部品およびその製造方法
JP2016156081A (ja) 合金工具鋼
JP2005281857A (ja) ブローチ加工性に優れた窒化部品用素材及びその素材を用いた窒化部品の製造方法
JP4997709B2 (ja) ブローチ加工性に優れた窒化部品用素材及びその製造方法
JP7608772B2 (ja) 金型用鋼及び金型
JP2000192195A (ja) 快削性冷間工具鋼
JP2006249494A (ja) ブローチ加工性に優れた窒化部品用素材及びその製造方法
JP2015224361A (ja) 低温焼入れ可能な高硬度高靭性の冷間工具鋼

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO SE SI SK SM TR

AX Request for extension of the european patent

Extension state: AL BA RS

17P Request for examination filed

Effective date: 20100816

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REF Corresponds to:

Ref document number: 602009000974

Country of ref document: DE

Date of ref document: 20110512

Kind code of ref document: P

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602009000974

Country of ref document: DE

Effective date: 20110512

REG Reference to a national code

Ref country code: NL

Ref legal event code: VDEP

Effective date: 20110330

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110701

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

LTIE Lt: invalidation of european patent or patent extension

Effective date: 20110330

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110630

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110801

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110730

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110711

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

Ref country code: NL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20110731

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

26N No opposition filed

Effective date: 20120102

REG Reference to a national code

Ref country code: FR

Ref legal event code: ST

Effective date: 20120330

REG Reference to a national code

Ref country code: IE

Ref legal event code: MM4A

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20110801

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602009000974

Country of ref document: DE

Effective date: 20120102

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20110723

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20110723

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110630

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: TR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20110330

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20130723

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20130723

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20130731

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20130731

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20150714

Year of fee payment: 7

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: AT

Payment date: 20150625

Year of fee payment: 7

Ref country code: SE

Payment date: 20150713

Year of fee payment: 7

REG Reference to a national code

Ref country code: DE

Ref legal event code: R119

Ref document number: 602009000974

Country of ref document: DE

REG Reference to a national code

Ref country code: SE

Ref legal event code: EUG

REG Reference to a national code

Ref country code: AT

Ref legal event code: MM01

Ref document number: 503853

Country of ref document: AT

Kind code of ref document: T

Effective date: 20160723

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20170201

Ref country code: SE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20160724

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: AT

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20160723