EP1563105A1 - Verfahren zum herstellen eines abriebfesten stahlblechs und so hergestelltes stahlblech - Google Patents

Verfahren zum herstellen eines abriebfesten stahlblechs und so hergestelltes stahlblech

Info

Publication number
EP1563105A1
EP1563105A1 EP03786006A EP03786006A EP1563105A1 EP 1563105 A1 EP1563105 A1 EP 1563105A1 EP 03786006 A EP03786006 A EP 03786006A EP 03786006 A EP03786006 A EP 03786006A EP 1563105 A1 EP1563105 A1 EP 1563105A1
Authority
EP
European Patent Office
Prior art keywords
optionally
sheet
temperature
steel
plate
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
EP03786006A
Other languages
English (en)
French (fr)
Other versions
EP1563105B1 (de
Inventor
Jean Beguinot
Jean-Georges Brisson
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.)
Industeel Creusot
Original Assignee
Industeel Creusot
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 Industeel Creusot filed Critical Industeel Creusot
Priority to SI200331112T priority Critical patent/SI1563105T1/sl
Publication of EP1563105A1 publication Critical patent/EP1563105A1/de
Application granted granted Critical
Publication of EP1563105B1 publication Critical patent/EP1563105B1/de
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • C21D2211/008—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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals

Definitions

  • the present invention relates to an abrasion-resistant steel and its method of manufacture.
  • High abrasion resistant steels with a hardness of about 600 Brinell are known. These steels contain from 0.4% to 0.6% of carbon and from 0.5% to 3% of at least one alloying element such as manganese, nickel, chromium and molybdenum and are soaked to have a completely martensitic structure. But these steels are very difficult to weld and cut. To overcome these drawbacks, it has been proposed, especially in EP 0 739 993, to use for the same uses, a less hard steel, whose carbon content is about 0.27% and having a quenched structure containing a significant amount of residual austenite. But these steels are still difficult to weld or cut.
  • the object of the present invention is to overcome these disadvantages, by proposing an abrasion-resistant steel sheet whose abrasion resistance is comparable to that of known steels but whose weldability and thermal cutting ability is better.
  • the subject of the invention is a method for manufacturing a part, and in particular a sheet, made of steel for abrasion, the chemical composition of which comprises, by weight:
  • Nb optionally at least one element selected from Nb, Ta and V in contents such that Nb / 2 + Ta / 4 + V ⁇ 0.5%
  • quenching may be followed by tempering at a temperature below 350 ° C, and preferably below 250 ° C.
  • the invention also relates to a sheet obtained in particular by this method, the steel having a martensitic or martensito-bainitic structure, said structure containing from 5% to 20% retained austenite, as well as carbides.
  • the thickness of the sheet may be between 2 mm and 150 mm and its flatness is characterized by an arrow less than or equal to 12 mm / m and preferably less than 5 mm / m.
  • the carbon content is less than 0.325%, and more preferably less than 0.3%.
  • Ti + Zr / 2 must be greater than 0.35% and preferably greater than 0.4%, and more preferably greater than 0.5%, so as to form a large amount of large carbides. However, this sum must remain less than 1.1% so as to keep enough carbon in solution in the matrix after formation of carbides. Preferably this sum must remain less than 1%, and better still 0.9% and better still less than 0.7% if one needs to favor the tenacity of the material.
  • the titanium content should preferably remain less than 1%, and more preferably less than 0.9%, or even less than 0.7%, and the zirconium content should preferably remain below 2%, and better less than 1, 8%, or even less than 1, 4%.
  • the boron content should preferably be greater than 0.0005% or better 0.001%, and need not exceed substantially 0.01%.
  • - Up to 0.15% sulfur This element is a residual usually limited to 0.005% or less, but its content can be voluntarily increased to improve machinability. It should be noted that in the presence of sulfur, in order to avoid difficulties of hot transformation, the manganese content must be greater than 7 times the sulfur content.
  • Nb / 2 + Ta / 4 + V remains less than 0.5% in order to form relatively large carbides which improve the resistance to abrasion.
  • the carbides formed by these elements are less effective than those formed by titanium or zirconium, that is why they are optional and added in limited quantities.
  • titanium and zirconium can be added to the liquid steel in a very gradual manner, for example by contacting the oxidized liquid steel with an oxidized phase such as a slag loaded with oxides of titanium or zirconium, then deoxidizing the liquid steel, so as to slowly diffuse titanium or zirconium from the oxidized phase to the liquid steel.
  • an oxidized phase such as a slag loaded with oxides of titanium or zirconium
  • the carbon, titanium, zirconium and nitrogen contents must be such that: C - Ti / 4 - Zr / 8 + 7xN / 8> 0.095%
  • C * represents the free carbon content after precipitation of the titanium and zirconium carbides, taking into account the formation of titanium and zirconium nitrides.
  • This free carbon content C * must be greater than 0.095%, and preferably> 0.12%, to have a martensite having a minimum hardness. The lower this content, the better the welding and thermal cutting ability.
  • the chemical composition must be chosen so that the quenchability of the steel is sufficient, given the thickness of the sheet that is to be manufactured.
  • the micrographic structure of the steel consists of martensite or bainite or a mixture of these two structures, and from 5% to 20% retained austenite.
  • This structure further comprises large titanium or zirconium carbides formed at high temperature, or even carbides of niobium, tantalum or vanadium. The inventors have found that the effectiveness of large carbides for improving the abrasion resistance could be obelated by the premature loosening thereof and that this loosening could be avoided by the presence of metastable austenite which is transformed under the effect of abrasion phenomena.
  • the slab or slug is hot rolled to obtain a sheet that is submitted to a heat treatment allowing at the same time to obtain the desired structure and a good flatness without subsequent planing or with limited planing.
  • the heat treatment can be carried out directly in the hot rolling or carried out later, and possibly after a cold planing or half-hot.
  • slightly lower is meant a temperature between T and T - 50 ° C, or better still between T and T - 25 ° C, or better still, between T and T - 10 ° C.
  • the sheet is cooled to a mean core cooling rate Vr of between 0.1 ° C./sec, to obtain a sufficient hardness, and 1150xep "1, 7 , to obtain the desired structure,
  • the sheet is cooled to room temperature, preferably, but not necessarily, at a slow speed.
  • an expansion treatment such as tempering, can be carried out at a temperature of less than or equal to 350 ° C, and preferably less than 250 ° C.
  • steel sheets identified A to C according to the invention and D to E according to the prior art were produced.
  • the chemical compositions of the steel, expressed as 10 "3 wt%, and the hardness and an index of wear resistance Rus, are reported in Table 1.
  • the wear resistance was measured by weight loss of a prismatic test tube rotated in a tank containing calibrated granules of quartzite for 5 hours.
  • the Rus index of a steel is equal to 100 times the ratio of the wear resistance of the steel in question and the wear resistance of a reference steel (steel D).
  • All sheets are 27 mm thick and are hardened after austenitization at 900 ° C.
  • the average cooling rate is 7 ° C / s above the temperature T defined above, and 1 6 ° C / s below, in accordance with 'invention
  • the average cooling rate is 0.8 ° C / s above the temperature T defined above, and 0.15 ° C / s below, according to the invention
  • the steel sheets D and E, given for comparison were cooled at an average speed of 24 ° C / s above the temperature T defined above, and at an average speed of 12 ° C / s below .
  • the comparison of the wear resistances and the hardnesses shows that, although being very substantially less hard than the sheets given for comparison, the sheets according to the invention have a slightly better resistance to wear.
  • the comparison of the free carbons shows that the good abrasion resistance of the sheets according to the invention is obtained with very significantly lower free carbons, which leads to significantly better welding or thermal cutting abilities than for the sheets according to the invention. the prior art.
  • the deformation after cooling, without planing, for steels according to the invention A to C is about 5 mm / m and 16 mm / m for steels D and E given for comparison.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)
  • Heat Treatment Of Articles (AREA)
  • Treatment Of Steel In Its Molten State (AREA)
EP03786006A 2002-11-19 2003-11-13 Verfahren zum herstellen eines abriebfesten stahlblechs und so hergestelltes stahlblech Expired - Lifetime EP1563105B1 (de)

Priority Applications (1)

Application Number Priority Date Filing Date Title
SI200331112T SI1563105T1 (sl) 2002-11-19 2003-11-13 Postopek za izdelavo plocevine iz jekla, odpornega proti abraziji, in dobljena plocevina

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
FR0214426A FR2847272B1 (fr) 2002-11-19 2002-11-19 Procede pour fabriquer une tole en acier resistant a l'abrasion et tole obtenue
FR0214426 2002-11-19
PCT/FR2003/003358 WO2004048619A1 (fr) 2002-11-19 2003-11-13 Procede pour fabriquer une tole en acier resistant a l'abrasion et tôle obtenue

Publications (2)

Publication Number Publication Date
EP1563105A1 true EP1563105A1 (de) 2005-08-17
EP1563105B1 EP1563105B1 (de) 2008-01-02

Family

ID=32187697

Family Applications (1)

Application Number Title Priority Date Filing Date
EP03786006A Expired - Lifetime EP1563105B1 (de) 2002-11-19 2003-11-13 Verfahren zum herstellen eines abriebfesten stahlblechs und so hergestelltes stahlblech

Country Status (19)

Country Link
US (1) US7713362B2 (de)
EP (1) EP1563105B1 (de)
JP (1) JP4535876B2 (de)
KR (1) KR101010571B1 (de)
CN (1) CN100348738C (de)
AR (1) AR042073A1 (de)
AT (1) ATE382716T1 (de)
AU (1) AU2003295014B2 (de)
BR (1) BR0315693B1 (de)
CA (1) CA2506349C (de)
DE (1) DE60318478T2 (de)
ES (1) ES2298605T3 (de)
FR (1) FR2847272B1 (de)
PE (1) PE20040484A1 (de)
PL (1) PL202086B1 (de)
RU (1) RU2326179C2 (de)
UA (1) UA78624C2 (de)
WO (1) WO2004048619A1 (de)
ZA (1) ZA200504150B (de)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP2949775A4 (de) * 2013-01-22 2016-09-07 Baoshan Iron & Steel Ultrafeste und zähe stahlplatte mit niedrigem streckgrenzenverhältnis und herstellungsverfahren dafür
EP3597784A4 (de) * 2017-03-13 2020-02-26 JFE Steel Corporation Abriebfestes stahlblech und verfahren zur herstellung eines abriebfesten stahlblechs

Families Citing this family (57)

* Cited by examiner, † Cited by third party
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FR2847270B1 (fr) * 2002-11-19 2004-12-24 Usinor Procede pour fabriquer une tole en acier resistant a l'abrasion et tole obtenue
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CN105903764A (zh) * 2016-04-22 2016-08-31 柳州凯通新材料科技有限公司 复合耐磨钢板的轧制工艺
RU2625861C1 (ru) * 2016-05-23 2017-07-19 Открытое акционерное общество "Магнитогорский металлургический комбинат" Способ производства листовой стали с высокой износостойкостью
EP3625012B1 (de) 2017-05-16 2022-07-06 Milwaukee Electric Tool Corporation Sägeblatt
CN107385354B (zh) * 2017-08-02 2019-02-12 合肥安力电力工程有限公司 一种电工钳用高硬度耐磨抗氧化钢
CN107916360A (zh) * 2017-11-14 2018-04-17 郑媛媛 一种高强度耐磨安全阀的生产工艺
CN107829033B (zh) * 2017-11-23 2019-10-11 攀钢集团攀枝花钢铁研究院有限公司 含v高耐磨刹车鼓用热连轧合金钢板及其生产方法
RU2674797C1 (ru) * 2018-06-07 2018-12-13 Публичное акционерное общество "Магнитогорский металлургический комбинат" Способ производства высокопрочного хладостойкого листового проката из низколегированной стали
CN108893680A (zh) * 2018-06-26 2018-11-27 澳洋集团有限公司 一种低合金耐磨钢及其制备方法
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ATE382716T1 (de) 2008-01-15
AU2003295014B2 (en) 2009-03-12
FR2847272B1 (fr) 2004-12-24
AU2003295014A1 (en) 2004-06-18
KR101010571B1 (ko) 2011-01-25
FR2847272A1 (fr) 2004-05-21
WO2004048619A1 (fr) 2004-06-10
BR0315693B1 (pt) 2011-06-28
PL202086B1 (pl) 2009-05-29
CN1714159A (zh) 2005-12-28
DE60318478T2 (de) 2008-12-11
PL375543A1 (en) 2005-11-28
KR20050083903A (ko) 2005-08-26
RU2005119205A (ru) 2006-05-10
BR0315693A (pt) 2005-09-20
US20060162826A1 (en) 2006-07-27
CA2506349C (fr) 2012-04-24
JP2006506527A (ja) 2006-02-23
UA78624C2 (en) 2007-04-10
DE60318478D1 (de) 2008-02-14
CN100348738C (zh) 2007-11-14
US7713362B2 (en) 2010-05-11
RU2326179C2 (ru) 2008-06-10
EP1563105B1 (de) 2008-01-02
WO2004048619A8 (fr) 2005-05-26
AR042073A1 (es) 2005-06-08
JP4535876B2 (ja) 2010-09-01
CA2506349A1 (fr) 2004-06-10
ES2298605T3 (es) 2008-05-16
ZA200504150B (en) 2006-09-27
PE20040484A1 (es) 2004-08-18

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