EP2089552B1 - Procédé de production en continu de fils d'acier ou de barres d'acier - Google Patents

Procédé de production en continu de fils d'acier ou de barres d'acier Download PDF

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Publication number
EP2089552B1
EP2089552B1 EP07816241.9A EP07816241A EP2089552B1 EP 2089552 B1 EP2089552 B1 EP 2089552B1 EP 07816241 A EP07816241 A EP 07816241A EP 2089552 B1 EP2089552 B1 EP 2089552B1
Authority
EP
European Patent Office
Prior art keywords
temperature
steel
rolling
carried out
final
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.)
Not-in-force
Application number
EP07816241.9A
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German (de)
English (en)
Other versions
EP2089552A1 (fr
Inventor
Lotfi Chabbi
Ulrich Urlau
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.)
Swiss Steel AG
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Swiss Steel AG
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Filing date
Publication date
Application filed by Swiss Steel AG filed Critical Swiss Steel AG
Priority to PL07816241T priority Critical patent/PL2089552T3/pl
Publication of EP2089552A1 publication Critical patent/EP2089552A1/fr
Application granted granted Critical
Publication of EP2089552B1 publication Critical patent/EP2089552B1/fr
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    • 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
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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

Definitions

  • the invention relates to a method for the continuous production of wire or bar steel.
  • the above method is characterized in that the final forming always takes place in the two-phase region and that reheating or, at best, holding at the final rolling temperature is always necessary after final shaping.
  • the transition to the heat retention temperature is thus not effected by the cooling process (see transition from (6) to (7) in FIG Fig. 2 from CN 1088265 A ).
  • the object of the invention is to provide an improved process for the continuous production of rod or wire steel, which allows a good control of the properties of the process products and at the same time simplifies the process management.
  • the products produced by the process according to the invention after cooling to room temperature are suitable for further cold processing without annealing. Unlike the conventional method, it is therefore not necessary to reheat the wire or bar steel produced.
  • the heat retention time to be applied in the third method step of the method according to the invention is significantly shorter than the duration of the subsequent heat treatment in the case of the conventional methods. As a result, the process duration and the process chain in the process according to the invention are thus significantly shorter than in the conventional processes.
  • the method according to the invention is suitable, on the one hand, for steels having a comparatively low proportion by weight of 0.02 to 0.2% carbon and up to 0.25% molybdenum and up to 0.008% boron; On the other hand, it is also suitable for steels with a medium to high weight content of 0.2 to 0.65% carbon and 0.25 to 0.50% molybdenum and up to 1.7% chromium.
  • the holding temperature must be selected as explained below.
  • the steel has a weight fraction of 0.02 to 0.2% carbon and up to 0.15% silicon, 0.25 to 1.0% manganese, up to 0.025% phosphorus, up to 0.004% sulfur, up to 0.25% molybdenum, bis to 0.1% chromium, up to 0.25% copper, up to 0.008% boron, up to 0.2% nickel, and up to 0.1% vanadium, the heat hold temperature being essentially at Ar 1 e .
  • the steel in the preferred method according to claim 3 a weight fraction of 0.2 to 0.65% carbon and up to 0.15% silicon, 0.25 to 1.0% manganese, up to 0.035% phosphorus, up to 0.004% sulfur, 0.25 to 0.50% molybdenum up to 1.7% chromium, up to 0.25% copper, up to 0.2% nickel and up to 0.1% vanadium, wherein the holding temperature is substantially in the range of Ar 1 b to Ar 1 e .
  • Ar 1 b and Ar 1 e denote in a known manner the beginning (upper index “b") and the end (upper index “e") of the austenite-pearlite transformation in the cooling direction (where “r” stands for “refroidatorium” ).
  • the final deformation is carried out at a temperature above Ar 3 .
  • the final transformation is carried out at most Ar 3 + 60 ° C.
  • the final forming is carried out at a temperature just below Ar. 3
  • the final deformation is carried out at a temperature in the range of Ar 1 to Ar 3 , wherein the final deformation temperature does not fall below 690 ° C. This allows a further shortening of the required holding time to about one-eighth of the known rolling process.
  • the in the Fig. 1 The rolling device shown has unspecified propulsion means for a steel strand 2, which convey it in a propulsion direction V through the device.
  • propulsion direction V a propulsion direction
  • certain assemblies of the rolling apparatus are used only for certain final dimensions, or depending on the final dimension, a certain function is taken over by one or the other assembly. First, however, the rolling process will be described generally.
  • the steel strand 2 passes to a first hot-forming device 6, where a first hot working takes place by rolling at a temperature above the recrystallization temperature. Depending on the final dimension, the first hot deformation takes place by six to twenty stitches at a temperature above 950 ° C.
  • the steel strand passes through a first cooling device 8 (for bar steel) or 8a (for wire), by means of which it is cooled below the recrystallization temperature. Thereafter, the steel strand passes into a second hot working apparatus 10 (for bar steel) and 10a (for wire), where a final forming is carried out at a temperature in the region of the non-recrystallized austenite.
  • the beam strand is optionally supplied to a wire station 14 or to a bar station 16.
  • These stations are equipped with second cooling devices 18 (for wire) and 20 (for bar steel) and with not shown holding devices for the cut-to-length rolled product in the form of wire rings or rods.
  • the first hot rolling device 6 is formed by a first stand group 22.
  • the first cooling device 8 is a direct water cooling system 24 in the area of the first stand group 22.
  • a waiting loop 26 with continuous cooling 28 is used as the first cooling device 8. If necessary, both cooling variants can be used.
  • the second hot rolling apparatus 10 may be formed by a downstream second stand group 30 as in the arrangement shown here. Subsequently, the rolling stock reaches the bar station 16, which as mentioned includes a second cooling device 20.
  • the first hot rolling device 6 comprises the first stand group 22 and the second stand group 30.
  • the first cooling device 8a is configured as a downstream waiting loop 32, which advantageously comprises a water cooling 34.
  • the second hot rolling apparatus 10 a is formed by a downstream third skeleton group 36. Subsequently, the rolling stock reaches the wire station 14, which includes a second cooling device 18 as mentioned.
  • Fig. 2 to 4 show on the basis of the relevant temperature-time profiles a comparison between a previously known rolling process ( Fig. 2 ) and two variants of the process according to the invention ( Fig. 3 and 4 ).
  • the steel strand is first heated to about 1'150 ° C. Thereafter, a hot working is carried out by rolling at a temperature above 950 ° C, which is above the recrystallization temperature. In the example shown this is done by 6 stitches. Subsequently, the rolling stock, depending on the final size or rolling station, within 5 to 10 s at 820 to 920 ° C and then cooled at a cooling rate of 0.3 to 1.9 ° C / s to room temperature.
  • the product thus obtained is not suitable for cold processing, but it requires a heat treatment lasting several hours. For example, the product must be reheated to a temperature of 680 to 720 ° C and typically held at that temperature for about 14 hours. The product treated in this way can finally be cooled to room temperature and is then available for cold further processing.
  • a first hot working is carried out above the recrystallization temperature, wherein the degree of deformation in this process step is at least 60%.
  • the rolling stock - unlike the previously described method of Fig. 2 - Initially cooled below the recrystallization temperature and then made a final deformation at a temperature in the region of the non-recrystallized austenite.
  • the total degree of deformation in the final forming is at least 30% and is accomplished in the examples shown by two stitches. It is essential that the cooling below the recrystallization temperature is carried out in such a way that no grain growth of the austenite takes place in the rolling stock before the final shaping.
  • the rolling stock is substantially cooled to the Ar 1 temperature, for example at 680 to 720 ° C, and then left at this holding temperature for a certain holding time. A rewarming process is accordingly not required. Finally, the product is cooled to room temperature.
  • the keep-warm time is determined in preliminary tests. It is chosen so that the properties of the products after cooling to room temperature are comparable to those after conventional rolling and additional heat treatment. This ensures that the product is cold processed without further heat treatment.
  • the rolling device is to be dimensioned or set up accordingly.
  • the controlled cooling processes are realized by means of water cooling and possibly by means of waiting loops.
  • different numbers and positions of the rolling stands are selected depending on the type and dimension of the product to be produced (ie wire steel, steel bars) different numbers and positions of the rolling stands are selected. Keeping warm takes place - also depending on the type of product - in suitable holding facilities.
  • a steel with the chemical composition "A" according to Table 1 was heated to 1'150 ° C and then rolled in 6 passes, the initial diameter was 38 mm and the final diameter was 17.2 mm. This matches with a total degree of deformation of 80%.
  • the final rolling temperature was approx. 980 ° C.
  • the rolling stock was cooled within 6 seconds to 820 to 960 ° C and then with a cooling rate of 0.3 to 1.9 ° C / s (depending on the rolling station) to room temperature.
  • the product thus obtained was then subjected to a heat treatment at 680 ° C for 4 hours.
  • a steel having the same composition as in Comparative Example 1 was heated to 1'150 ° C and then rolled in 4 passes, the initial diameter being 38 mm and the final diameter being 23.8 mm. This corresponds to a total degree of deformation at the first hot deformation of 60%.
  • the temperature was after the 4th stitch at about 1'020 ° C. After intensive cooling, the rolling stock was then rolled within 13 seconds in a further 4 passes from 23.8 to 17.2 mm. This corresponds to a total deformation rate of 47% for the final forming.
  • the final rolling temperature was 880 ° C, which is about 20 ° C above Ar 3 . After the last pass, the rolling stock was cooled to 680 ° C within 6 seconds, which essentially corresponds to Ar 1 e , and left at this temperature for 2 hours.
  • a steel having the same composition as in Comparative Example 1 was heated to 1'150 ° C and then rolled in 4 passes, the initial diameter being 38 mm and the final diameter being 23.8 mm.
  • the temperature was after the 4th stitch at about 1'020 ° C.
  • the rolling stock was then rolled within 13 seconds in another 2 passes from 23.8 to 17.2 mm.
  • the final rolling temperature was 850 ° C, which is just under 10 ° C below Ar 3 .
  • the rolling stock was cooled to 680 ° C in 6 seconds, which essentially corresponds to Ar 1 e , and left at this temperature for 1 hour.
  • a steel with the chemical composition "C" according to Table 1 was heated to 1'150 ° C and then rolled in 6 passes, the initial diameter of 38 mm and the final diameter was 17.2 mm. This corresponds to a Monumformgrad of 80%.
  • the final rolling temperature was approx. 980 ° C.
  • the rolling stock was cooled in 5 seconds to about 820 to 970 ° C and then with a cooling rate of 0.3 to 1.9 ° C / s to room temperature.
  • the product thus obtained was then subjected to a heat treatment at 680 ° C for 4 hours.
  • a steel having the same composition as in Comparative Example 2 was heated to 1'150 ° C and then rolled in 4 passes, the initial diameter being 38 mm and the final diameter being 23.8 mm. This matches with a total degree of deformation at the first hot deformation of 60%.
  • the temperature was after the 4th stitch at about 1'020 ° C.
  • the rolling stock was then rolled within 13 seconds in another 2 passes from 23.8 to 17.2 mm. This corresponds to a total deformation rate of 47% for the final forming.
  • the final rolling temperature was 800 ° C, which is above Ar 3 .
  • the rolling stock was cooled to 680 ° C within 6 seconds, which is between Ar 1 b and Ar 1 e , and left at this temperature for 2 hours.
  • a steel having the same composition as in Comparative Example 2 was heated to 1'150 ° C and then rolled in 4 passes, the initial diameter being 38 mm and the final diameter being 23.8 mm.
  • the temperature was after the 4th stitch at about 1'020 ° C.
  • the rolling stock was then rolled within 13 seconds in another 2 passes from 23.8 to 17.2 mm.
  • the final rolling temperature was 690 ° C, which is below Ar 3 .
  • the rolling stock was cooled to 680 ° C within 6 seconds, which is between Ar 1 b and Ar 1 e , and left at this temperature for 0.5 hour.
  • Fig. 5 represents the microstructure of quenched samples after the last pass, depending on the final rolling temperature. It can be seen that the final forming in Comparative Example 2 (see Fig. 5a ) and Example 3 (see Fig. 5b ) in metastable austenite. In contrast, this was done in Example 4 (see Fig. 5c ) in the (ya) two-phase region.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Metal Rolling (AREA)

Claims (5)

  1. Procédé de production en contenu de fils ou de barres d'acier comprenant les étapes suivantes :
    a) dans une première étape de procédé, un acier renfermant en proportion pondérale 0,02 à 0,65 % de carbone, plus de 0 et jusqu'à 0,15 % de silicium, 0,25 à 1,5 % de manganèse, jusqu'à 0,035 % de phosphore, jusqu'à 0,004 % de soufre, plus de 0 et jusqu'à 0,5 % de molybdène, plus de 0 et jusqu'à 1,7 % de chrome, plus de 0 et jusqu'à 0,25 % de cuivre, jusqu'à 0,008 % de bore, plus de 0 et jusqu'à 0,2 % de nickel, jusqu'à 0,25 % de vanadium, plus de 0 et jusqu'à 0,026 % d'aluminium, ainsi que d'autres impuretés usuelles dans les aciers, est chauffé à 1 050 à 1 200° C, puis, un premier formage thermique est effectué par laminage à une température située au-dessus de la température de recristallisation, le taux de déformation total lors du premier formage thermique étant d'au moins 60 %,
    b) dans une seconde étape de procédé, le produit laminé est refroidi au-dessous de sa température de recristallisation puis un formage final à une température située dans la zone de l'austénite non recristallisée est effectuée, ce refroidissement étant mis en oeuvre de façon à empêcher, avant le formage final, une croissante possible de grains d'austénite dans le produit laminé, et le taux de déformation total lors du formage final étant d'au moins 30 %, et
    c) dans une troisième étape de procédé, le produit laminé est refroidi sans réchauffage jusqu'à une température de maintien thermique située dans la zone de Ar1 b à Ar1 e autour de la température critique Ar1 et maintenu pendant un temps de maintien thermique à cette température de maintien thermique.
  2. Procédé conforme à la revendication 1,
    caractérisé en ce que
    l'acier renferme en proportion pondérale 0,02 à 0,2 % de carbone et jusqu'à 0,15% de silicium, 0,25 à 1,0% de manganèse, jusqu'à 0,025 % de phosphore, jusqu'à 0,004 % de soufre, jusqu'à 0,25 % de molybdène, jusqu'à 0,1 % de chrome, jusqu'à 0,25 % de cuivre, jusqu'à 0,008 % de bore, jusqu'à 0,2 % de nickel, jusqu'à 0,026 % d'aluminium et jusqu'à 0,1 % de vanadium, et la température de maintien thermique est essentiellement égale à Ar1 e.
  3. Procédé conforme à la revendication 1,
    caractérisé en ce que
    l'acier renferme en proportion pondérale 0,2 à 0,65% de carbone et jusqu'à 0,15% de silicium, 0,25 à 1,0 % de manganèse, jusqu'à 0,035 % de phosphore, jusqu'à 0,004 % de soufre, 0,25 à 0,50 % de molybdène, jusqu'à 1,7 % de chrome, jusqu'à 0,25 % de cuivre, jusqu'à 0,2 % de nickel, jusqu'à 0,026 % d'aluminium et jusqu'à 0,1 % de varadium et la température de maintien thermique est située dans la zone de Ar1 b à Ar1 e.
  4. Procédé conforte à l'une des revendications 1 à 3,
    caractérisé en ce que
    le formage final est effectué à une température au plus égale à la température critique Ar3 + 60° C.
  5. Procédé conforme à l'une des revendications 1 à 3,
    caractérisé en ce que
    le formage final est effectué à une température située dans la zone de Ar1 à Ar3, étant précisé que la température de formage final n'est pas inférieure à 690° C.
EP07816241.9A 2006-11-17 2007-11-12 Procédé de production en continu de fils d'acier ou de barres d'acier Not-in-force EP2089552B1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
PL07816241T PL2089552T3 (pl) 2006-11-17 2007-11-12 Sposób ciągłego wytwarzania drutu lub pręta stalowego

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CH18482006 2006-11-17
PCT/CH2007/000558 WO2008058410A1 (fr) 2006-11-17 2007-11-12 Procédé de production en continu de fils d'acier ou de barres d'acier

Publications (2)

Publication Number Publication Date
EP2089552A1 EP2089552A1 (fr) 2009-08-19
EP2089552B1 true EP2089552B1 (fr) 2017-01-25

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Family Applications (1)

Application Number Title Priority Date Filing Date
EP07816241.9A Not-in-force EP2089552B1 (fr) 2006-11-17 2007-11-12 Procédé de production en continu de fils d'acier ou de barres d'acier

Country Status (4)

Country Link
EP (1) EP2089552B1 (fr)
ES (1) ES2623430T3 (fr)
PL (1) PL2089552T3 (fr)
WO (1) WO2008058410A1 (fr)

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS58171526A (ja) * 1982-03-31 1983-10-08 Nippon Steel Corp 極低温用鋼の製造法
US4604145A (en) * 1984-01-13 1986-08-05 Sumitomo Metal Industries, Ltd. Process for production of steel bar or steel wire having an improved spheroidal structure of cementite
US4619714A (en) * 1984-08-06 1986-10-28 The Regents Of The University Of California Controlled rolling process for dual phase steels and application to rod, wire, sheet and other shapes
EP1371737A1 (fr) * 2002-06-10 2003-12-17 Von Moos Stahl AG Procédé et dispositif pour la fabrication de fils ou de barres en acier

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

Also Published As

Publication number Publication date
PL2089552T3 (pl) 2017-07-31
WO2008058410A1 (fr) 2008-05-22
EP2089552A1 (fr) 2009-08-19
ES2623430T3 (es) 2017-07-11

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