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
  • C22C38/58—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
  • 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
  • C22C38/18—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
  • C22C38/50—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
  • 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.
• Abrasive steels of hardness close to 400 Brinell containing about 0.15% of carbon as well as manganese, nickel, chromium and molybdenum are known at levels of less than a few% in order to have sufficient quenchability. These steels are soaked so as to have a completely martensitic structure. They have the advantage of being relatively easy to implement by welding, cutting or folding. But they have the disadvantage of having a limited resistance to abrasion. It is certainly known to increase the resistance to abrasion by increasing the carbon content and therefore the hardness. But this way of proceeding has the disadvantage of deteriorating the ability to implement.
• the object of the present invention is to overcome these disadvantages by providing an abrasion-resistant steel sheet which, all things being equal, has a better abrasion resistance than that of known steels having a hardness of 400. Brinell, while having an implementation ability comparable to that of these steels.
• the subject of the invention is a process for manufacturing a part, and in particular a sheet, made of steel for abrasion, the chemical composition of which comprises, by weight: 0.1% ⁇ C ⁇ 0.23%
• Nb, Ta and V in contents such that Nb / 2 + Ta / 4 + V ⁇ 0.5%
• - optionally at least one element selected from Se, Te, Ca, Bi, Pb in contents of less than or equal to 0.1%, the balance being iron and impurities resulting from the preparation, the chemical composition further satisfying the following relationships :
• the part or the sheet is subjected to a quenching heat treatment, carried out in hot hot shaping such as rolling or after austenitization by reheating in an oven, which consists in:
• 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, whose flatness is characterized by an arrow less than or equal to 12 mm / m and preferably less than 5 mm / m, the steel having a structure consisting of 5% to 20% of retained austenite, the rest of the structure being martensitic or martensito- bainitic, and contains carbides.
• the thickness of the sheet may be between 2 mm and 150 mm.
• the hardness is between 280 HB and 450 HB.
• the invention will now be described in a more precise but nonlimiting manner and be illustrated by examples.
• a steel is produced whose chemical composition comprises, in% by weight:
• the sum Ti + Zr / 2 is greater than 0.05%, preferably greater than 0, 1%, and more preferably greater than 0.2%, for the steel to contain large titanium or zirconium carbides which increase the abrasion resistance. But the sum Ti + Zr / 2 must remain below 0.67% because, beyond, the steel would not contain enough free carbon for its hardness is sufficient. In addition, the Ti + Zr / 2 content will be preferentially lower than
• Mo + W / 2 being between 0.05% and 1%, and preferably remains less than 0.8%, or better, less than 0.5% o .
• These elements increase the quenchability and form in martensite or bainite thin carbides hardening, including self-precipitation precipitation during cooling. It is not necessary to exceed a molybdenum content of 1% in order to obtain the desired effect, particularly as regards the precipitation of hardening carbides.
• Molybdenum can be replaced in whole or in part by a double weight of tungsten. However, this substitution is not sought in practice because it offers no advantage over molybdenum and is more expensive.
• the boron content should preferably be greater than 0.0005% o or better 0.001%, and need not exceed substantially 0.01%.
• the steel contains Se and / or Te
• the manganese content must be sufficient in view of the sulfur content so that selenides or tellurides of manganese can be formed.
• the rest being iron and impurities resulting from the elaboration.
• the impurities there is in particular nitrogen, the content of which depends on the production process but does not exceed 0.03%, and remains generally less than
• Nitrogen can react with titanium or zirconium to form nitrides that should not be too big to deteriorate toughness.
• 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.
• the carbon, titanium, zirconium and nitrogen contents are chosen such that:
• C * C - Ti / 4 - Zr / 8 + 7xN / 8> 0.095% And preferably, C *> 0.12% to have a higher hardness and therefore a better abrasion resistance.
• the quantity 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%) to have a martensitic or martensitobasicite structure having a sufficient hardness.
• the chemical composition is chosen so that the quenchability of the steel is sufficient, given the thickness of the sheet that is to be manufactured.
• the chemical composition must satisfy the relation:
• the micrographic structure of the steel consists of martensite or bainite or a mixture of these two structures, and from 5% to 20% > austenite retained .
• this structure comprises large titanium or zirconium carbides formed at high temperature, and optionally carbides of niobium, tantalum or vanadium. Due to the manufacturing process that will be described later, this structure is returned, so that it also includes molybdenum carbides or tungsten and possibly chromium carbides.
• the inventors have found that the effectiveness of large carbides for the improvement of the abrasion resistance could be obelated by 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 transformation of the metastable austenite is by swelling, this transformation in the abraded undercoat increases the resistance to carburetion and thus improves abrasion resistance.
• This slower cooling in the bainitomensitic range has, in addition, the advantage of causing self-tempering which gives rise to the formation of molybdenum, tungsten or chromium carbides and improves the resistance to wear of the matrix surrounding the large carbides.
• the steel is made, cast in the form of a slab or ingot.
• the slab or slug is hot-rolled to obtain a sheet which is subjected to a heat treatment which makes it possible 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 in the hot rolling or later, possibly after a cold or mid-heat planing.
• the steel is heated above the point AC 3 so as to give it a completely austenitic structure, in which, however, titanium or zirconium carbides remain,
• the sheet is cooled to an average cooling rate at heart Vr less than 1150xep "1 , 7 , and greater than 0.1 ° C / s, 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 a tempering at a temperature of less than or equal to 350 ° C, and preferably less than 250 ° C, can be carried out.
• average cooling rate is meant the cooling rate equal to the difference between the start and end temperatures of cooling divided by the cooling time between these two temperatures.
• the wear resistance of the steels is measured by the weight loss of a prismatic specimen rotated in a tank containing calibrated granules of quartzite for a period of 5 hours.
• the wear resistance index Rus of a steel is the ratio of the wear resistance of the steel F, taken as a reference, to the wear resistance of the steel under consideration.
• the sheets A to H are austenitized at 900 ° C. After austenitization:
• the steel sheet A is cooled at an average speed of 0.7 ° C./s above the temperature defined above (approximately 460 ° C.), and at an average speed of 0.13 ° C./s. below, according to the invention;
• the steel sheets B, C, D are cooled at an average speed of 6 ° C./s above the temperature T defined above (approximately 470 ° C.), and at an average speed of 1.4 ° C. s below, according to the invention;
• the steel sheets E, F, G and H given by way of comparison, were cooled at an average speed of 20 ° C./s above the temperature T defined above, and at an average speed of 12 ° C. C / s below.
• the sheets A to D have a martensite-bainitic self-regenerating structure containing about 10% retained austenite, as well as titanium carbides, while the plates E to G have a completely martensitic structure, the sheets G and H also containing large titanium carbides. It can be seen that, although having hardnesses less than those of the E and F sheets, the sheets A, B, C and D have substantially better abrasion resistance. The lower hardnesses, which correspond, for the most part, to lower free carbon contents, lead to better processability.

Priority Applications (1)

Applications Claiming Priority (3)

Publications (2)

Family

ID=32187696

Family Applications (1)

Country Status (20)

Families Citing this family (54)

Family Cites Families (15)

• 2002
  • 2002-11-19 FR FR0214425A patent/FR2847271B1/fr not_active Expired - Fee Related
• 2003
  • 2003-11-13 JP JP2004554593A patent/JP4535875B2/ja not_active Expired - Lifetime
  • 2003-11-13 EP EP03782550A patent/EP1563103B1/de not_active Expired - Lifetime
  • 2003-11-13 BR BRPI0315694-0A patent/BR0315694B1/pt active IP Right Grant
  • 2003-11-13 US US10/535,176 patent/US7462251B2/en active Active
  • 2003-11-13 AT AT03782550T patent/ATE388247T1/de active
  • 2003-11-13 WO PCT/FR2003/003357 patent/WO2004048618A1/fr active IP Right Grant
  • 2003-11-13 DE DE60319567T patent/DE60319567T2/de not_active Expired - Lifetime
  • 2003-11-13 CA CA2506347A patent/CA2506347C/fr not_active Expired - Lifetime
  • 2003-11-13 PL PL375541A patent/PL203154B1/pl unknown
  • 2003-11-13 KR KR1020057009066A patent/KR101010593B1/ko active IP Right Grant
  • 2003-11-13 CN CNB2003801036481A patent/CN100348739C/zh not_active Expired - Lifetime
  • 2003-11-13 ES ES03782550T patent/ES2300636T3/es not_active Expired - Lifetime
  • 2003-11-13 RU RU2005119211/02A patent/RU2326180C2/ru active
  • 2003-11-13 PT PT03782550T patent/PT1563103E/pt unknown
  • 2003-11-13 UA UAA200505982A patent/UA81134C2/uk unknown
  • 2003-11-18 AR ARP030104258A patent/AR042072A1/es not_active Application Discontinuation
  • 2003-11-18 PE PE2003001169A patent/PE20040486A1/es not_active Application Discontinuation
• 2005
  • 2005-05-23 ZA ZA200504151A patent/ZA200504151B/en unknown
• 2008
  • 2008-06-18 US US12/141,327 patent/US7998285B2/en active Active
• 2009
  • 2009-03-19 AU AU2009201117A patent/AU2009201117B8/en not_active Expired

Non-Patent Citations (1)

Also Published As

Similar Documents

Legal Events