EP2662166A1 - Matière première avec grande résistance à l'usure - Google Patents

Matière première avec grande résistance à l'usure Download PDF

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Publication number
EP2662166A1
EP2662166A1 EP12450026.5A EP12450026A EP2662166A1 EP 2662166 A1 EP2662166 A1 EP 2662166A1 EP 12450026 A EP12450026 A EP 12450026A EP 2662166 A1 EP2662166 A1 EP 2662166A1
Authority
EP
European Patent Office
Prior art keywords
matrix
hip
max
carbon
wear resistance
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.)
Withdrawn
Application number
EP12450026.5A
Other languages
German (de)
English (en)
Inventor
Gert Kellezi
Devrim Caliskanoglu
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.)
Voestalpine Boehler Edelstahl GmbH and Co KG
Original Assignee
Boehler Edelstahl GmbH and Co KG
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 Boehler Edelstahl GmbH and Co KG filed Critical Boehler Edelstahl GmbH and Co KG
Priority to EP12450026.5A priority Critical patent/EP2662166A1/fr
Priority to TW102113250A priority patent/TWI565543B/zh
Priority to ARP130101388A priority patent/AR090840A1/es
Priority to JP2013103491A priority patent/JP2013234387A/ja
Priority to RU2013120934/02A priority patent/RU2542885C2/ru
Priority to US13/888,862 priority patent/US9855603B2/en
Priority to KR1020130051458A priority patent/KR20130125329A/ko
Priority to UAA201305846A priority patent/UA109247C2/uk
Priority to CN2013101670928A priority patent/CN103388108A/zh
Publication of EP2662166A1 publication Critical patent/EP2662166A1/fr
Withdrawn legal-status Critical Current

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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/24—After-treatment of workpieces or articles
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/12—Both compacting and sintering
    • B22F3/14—Both compacting and sintering simultaneously
    • B22F3/15—Hot isostatic pressing
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
    • 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
    • C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
    • B22F3/24—After-treatment of workpieces or articles
    • B22F2003/248—Thermal after-treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
    • B22F2998/10—Processes characterised by the sequence of their steps
    • 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
    • C21D2211/007—Ledeburite
    • 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
    • C21D2241/00—Treatments in a special environment
    • C21D2241/01—Treatments in a special environment under pressure
    • C21D2241/02—Hot isostatic pressing
    • 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

Definitions

  • the invention relates to a production of ledeburitic tool steels by means of a powder metallurgical process, which PM materials have isotropic, mechanical properties, improved wear resistance and high hardness potential.
  • High-alloyed tool steels which solidify ledeburitically due to their composition, often have coarse carbides and carbide accumulations in the microstructure locally, which line up in a hot deformation of the ingot and ultimately form carbide lines or a deformation structure dependent on the deformation direction.
  • This microstructure requires anisotropic properties of the material with respect to the respective stress direction of the part.
  • hardness potential refers to the extent of the increase in hardness during the tempering of an austenite-structured martensitic material with retained austenite.
  • PM materials may be slightly less resistant to wear when compared, although in a conventional production, carbide-phase amounts are equally high in the matrix.
  • the invention is based on the object of specifying a method of the type mentioned above, by means of which PM materials on receipt of the isotropy of the mechanical properties improved resistance to wear and an increased hardness potential is mediated.
  • the invention aims to provide a powder metallurgy produced material from a ledeburitic tool steel alloy with high hardness potential and high resistance to abrasive wear.
  • the object is achieved according to the invention in a production by the PM method of ledeburitic tool steel alloys, in which a HIP block and / or made of this semifinished a high annealing at a temperature of about 1100 ° C, but at least 10 ° C below subjected to the melting temperature of the lowest-melting structural phase with a duration of more than 12 hours and the average carbide phase size of the material increased by at least 65%, rounded their surface shape and the matrix are homogenized, after which further processing it to tools with high wear resistance or to Abrassion claimed parts takes place.
  • the process according to the invention has the advantages that, on the one hand, the carbide phases are increased at temperatures above 1100 ° C. and, on the other hand, the matrix is homogenized, the strength properties remaining approximately the same in the uncured state of the material, the elongation at break and, in particular, the fracture constriction being increased, resulting in processing and property benefits.
  • thermo quenching by tempering and tempering of high-alloy material produced according to the invention high tempering hardness values are achieved even at low hardening temperatures.
  • Tool steel alloy a high speed steel material with a chemical composition of% by weight Carbon (C) 0.8 to 1.4 Chrome (Cr) 3.5 to 5.0 Molybdenum (Mo) 0.1 to 10.0 Vanadin (V) 0.8 to 10.5 Tungsten (W) 0.1 to 10.0 Cobalt (Co) 1.0 to 12.0 and Si, Mn, S, N and, alternatively, Ni, Al, Nb, Ti and impurities residual iron, wherein the carbon content of the matrix is adjusted to 0.45 to 0.75 and the average carbide phase diameter therein greater than 2.8 microns.
  • C Carbon
  • Cr Chrome
  • V Vanadin
  • W 0.8 to 10.5 Tungsten
  • Cobalt Co
  • the contents of carbon, on important carbide formers and on the matrix toughness and hot hardness particularly promoting element cobalt and the carbon concentration of the matrix are specified in limits, which, as the material investigations yielded essential to the process, wherein a carbide phase diameter according to the invention is set.
  • Such comparatively coarse carbide phase diameters are retained even in the case of coarse, abrasive loads in the microstructure, or are not discharged or dissolved out, since the matrix containing these hard phases was also given advantageous properties by high-temperature annealing.
  • the method according to the invention can also be used in a favorable manner with a cold work steel material having a chemical composition of in% by weight.
  • the further object of the invention is achieved by providing a material which has isotropic mechanical properties and, when thermally annealed, has a carbide phase content of M 6 C and MC carbides of at least 7.0% by volume with an average carbide phase size greater than 2.8 ⁇ m in the matrix, which matrix has a carbon concentration of (0.45 to 0.75) in wt .-%.
  • An equal carbide phase fraction has been found to reduce wear when an increased average carbide phase size is present in a homogeneous matrix.
  • the material has a chemical composition in wt .-% of Carbon (C) 0.8 to 3.0 Chrome (Cr) to 12.0 Molybdenum (Mo) 0.1 to 5.0 Vanadin (V) 0.8 to 10.5 Tungsten (W) 0.1 to 3.0 and Si, Mn, S, N, and alternatively Ni, Al, Nb, Ti and impurities have residual iron.
  • the carbide phases M 6 C and MC were prepared by carbide phase selection using the image processing software Image J.
  • the material with the designation S500 served as a comparative material of conventional production, because this has the state of the art according to good wear properties.
  • the alloy according to the composition designated S599 was melted and made from it by the PM method, by atomizing the melt with nitrogen to powder - filling a capsule with it and hot isostatic pressing it, a HIP block.
  • This HIP block was partially processed into S599-PM samples and tools in a conventional manner.
  • Tab. 2 provides the chemical composition of the matrix and the proportions of the carbide phases in the comparative material S500 and in the material S599PM-H produced according to the invention.
  • Fig. 1 are the mechanical properties, namely: yield strength R P0.2 , tensile strength Rm , elongation at break A and breakage Z of the materials S500, S599PM and S599PM-H shown in a bar chart.
  • the elongation A and the constriction Z of the material S599PM-H are clearly increased by the high-temperature annealing according to the invention, which is brought about by a homogenization of the matrix.
  • Fig. 2 shows in the micrograph a material S599PM in the as-annealed state with carbide phases of the type M 6 C and MC in the matrix.
  • the phase size of the carbides is about 2.0 ⁇ m on average.
  • the fine M 23 C 6 carbides are not included in the evaluation of the material with a hardness of approx. 258 HB.
  • Fig. 3 shows in the microsection of the material S599PM-H, which was prepared according to the invention. At the same carbide phase proportions, the carbides are significantly coarsened and have an average diameter of about 4.0 microns.
  • fine M 23 C 6 carbides are incorporated again because the material is in the soft-annealed state.
  • Fig. 4 shows a material produced according to the invention S599PM-H in a SEM analysis (scanning electron microscope), which material is annealed to a hardness of 68.7 HRC.
  • Fig. 5 are the carbide phases of type M 6 C, selected by an aforementioned graphic program of analysis, can be seen.
  • the M 6 C carbide phase content is about 7.4% by volume, this value being the average of more than 6 measurements.
  • Fig. 7 shows in a micrograph (polished, with 3% HNO3 solution etched) a powder metallurgically produced material S599PM in the thermally tempered state with a homogeneous distribution of fine carbides with an average carbide phase size of 1.6 microns.
  • the material hardness is approx. 68.2 HRC.
  • Fig. 8 is the same material, which is thermally tempered with identical parameters, but which was subjected to a high-temperature annealing according to the invention, shown in the micrograph, wherein the measurements of the average carbide phase size yielded a value of 3.6 microns.
  • Fig. 9 shows in the microsection of the structure of a manufactured using a cast block material S500 in the annealed state with a hardness of 239 HB, which material has angular, slightly spaced, coarser carbide phases.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Powder Metallurgy (AREA)
  • Manufacture And Refinement Of Metals (AREA)
  • Sliding-Contact Bearings (AREA)
  • Heat Treatment Of Steel (AREA)
  • Ceramic Products (AREA)
  • Carbon And Carbon Compounds (AREA)
EP12450026.5A 2012-05-08 2012-05-08 Matière première avec grande résistance à l'usure Withdrawn EP2662166A1 (fr)

Priority Applications (9)

Application Number Priority Date Filing Date Title
EP12450026.5A EP2662166A1 (fr) 2012-05-08 2012-05-08 Matière première avec grande résistance à l'usure
TW102113250A TWI565543B (zh) 2012-05-08 2013-04-15 具高耐磨損抵抗性的材料及其製造方法
ARP130101388A AR090840A1 (es) 2012-05-08 2013-04-25 Procedimiento para la produccion de materiales con propiedades mecanicas isotropicas y resistencia mejorada al desgaste y elevado potencial de dureza, y material con elevada resistencia contra el desgaste abrasivo producido de acuerdo a dicho procedimiento
JP2013103491A JP2013234387A (ja) 2012-05-08 2013-04-25 高い耐摩耗性を持つ材料
RU2013120934/02A RU2542885C2 (ru) 2012-05-08 2013-05-07 Материал с высокой стойкостью к износу
US13/888,862 US9855603B2 (en) 2012-05-08 2013-05-07 Material with high resistance to wear
KR1020130051458A KR20130125329A (ko) 2012-05-08 2013-05-07 높은 내마모성을 갖는 재료
UAA201305846A UA109247C2 (uk) 2012-05-08 2013-05-07 Спосіб одержання ледебуритної інструментальної сталі з високою стійкістю до зносу і ледебуритна інструментальна сталь
CN2013101670928A CN103388108A (zh) 2012-05-08 2013-05-08 具有高抗磨损性的材料

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP12450026.5A EP2662166A1 (fr) 2012-05-08 2012-05-08 Matière première avec grande résistance à l'usure

Publications (1)

Publication Number Publication Date
EP2662166A1 true EP2662166A1 (fr) 2013-11-13

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Family Applications (1)

Application Number Title Priority Date Filing Date
EP12450026.5A Withdrawn EP2662166A1 (fr) 2012-05-08 2012-05-08 Matière première avec grande résistance à l'usure

Country Status (9)

Country Link
US (1) US9855603B2 (fr)
EP (1) EP2662166A1 (fr)
JP (1) JP2013234387A (fr)
KR (1) KR20130125329A (fr)
CN (1) CN103388108A (fr)
AR (1) AR090840A1 (fr)
RU (1) RU2542885C2 (fr)
TW (1) TWI565543B (fr)
UA (1) UA109247C2 (fr)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2691327C2 (ru) * 2014-04-14 2019-06-13 Уддехольмс АБ Инструментальная сталь для холодной обработки
CN111347220A (zh) * 2018-12-24 2020-06-30 溧阳市金昆锻压有限公司 一种莱氏体钢高耐磨性压辊壳制造方法

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AT515148B1 (de) * 2013-12-12 2016-11-15 Böhler Edelstahl GmbH & Co KG Verfahren zur Herstellung von Gegenständen aus Eisen-Cobalt-Molybdän/Wolfram-Stickstoff-Legierungen
JP6345945B2 (ja) * 2014-02-26 2018-06-20 山陽特殊製鋼株式会社 耐摩耗性に優れた粉末高速度工具鋼およびその製造方法
CN104128600B (zh) * 2014-07-09 2016-04-13 浙江工业大学 一种用于热作模具激光组合制造专用粉末及其制造工艺
SE539733C2 (en) * 2016-03-16 2017-11-14 Erasteel Sas A steel alloy and a tool
CN108315664B (zh) * 2018-04-26 2020-05-12 河冶科技股份有限公司 搓丝板材料的制备方法
CN110643903B (zh) * 2019-09-29 2022-03-15 沈阳屹辰科技有限公司 一种高速钢打印针的制备方法
DE102019133017A1 (de) * 2019-12-04 2021-06-10 Vulkan Inox Gmbh Abrasiv zum Strahlschneiden
CN114318164B (zh) * 2021-03-22 2023-01-20 武汉钜能科技有限责任公司 耐磨耐蚀工具钢
CN114318131B (zh) * 2021-03-22 2023-01-20 武汉钜能科技有限责任公司 耐磨合金
CN113957332A (zh) * 2021-09-08 2022-01-21 僖昴晰(上海)新材料有限公司 高硬度耐磨材料组合物

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US20070056657A1 (en) * 2005-05-09 2007-03-15 Crucible Materials Corporation Corrosion and wear resistant alloy
US20090257903A1 (en) 2005-09-08 2009-10-15 Stefan Sundin Powder Metallurgically Manufactured High Speed Steel

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Publication number Priority date Publication date Assignee Title
WO1986004360A1 (fr) 1985-01-16 1986-07-31 Kloster Speedsteel Aktiebolag Acier a outils
US20070056657A1 (en) * 2005-05-09 2007-03-15 Crucible Materials Corporation Corrosion and wear resistant alloy
WO2007021243A1 (fr) * 2005-08-18 2007-02-22 Erasteel Kloster Aktiebolag Acier fabrique a l'aide de la metallurgie des poudres, outil comprenant cet acier et procede de fabrication de cet outil
US20090257903A1 (en) 2005-09-08 2009-10-15 Stefan Sundin Powder Metallurgically Manufactured High Speed Steel

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2691327C2 (ru) * 2014-04-14 2019-06-13 Уддехольмс АБ Инструментальная сталь для холодной обработки
US10472704B2 (en) 2014-04-14 2019-11-12 Uddeholms Ab Cold work tool steel
CN111347220A (zh) * 2018-12-24 2020-06-30 溧阳市金昆锻压有限公司 一种莱氏体钢高耐磨性压辊壳制造方法

Also Published As

Publication number Publication date
KR20130125329A (ko) 2013-11-18
US9855603B2 (en) 2018-01-02
RU2542885C2 (ru) 2015-02-27
RU2013120934A (ru) 2014-11-20
TW201350232A (zh) 2013-12-16
AR090840A1 (es) 2014-12-10
UA109247C2 (uk) 2015-07-27
TWI565543B (zh) 2017-01-11
JP2013234387A (ja) 2013-11-21
US20130343944A1 (en) 2013-12-26
CN103388108A (zh) 2013-11-13

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