WO2008058410A1 - 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
WO2008058410A1
WO2008058410A1 PCT/CH2007/000558 CH2007000558W WO2008058410A1 WO 2008058410 A1 WO2008058410 A1 WO 2008058410A1 CH 2007000558 W CH2007000558 W CH 2007000558W WO 2008058410 A1 WO2008058410 A1 WO 2008058410A1
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WO
WIPO (PCT)
Prior art keywords
temperature
final
rolling
steel
carried out
Prior art date
Application number
PCT/CH2007/000558
Other languages
German (de)
English (en)
Inventor
Lotfi Chabbi
Ulrich Urlau
Original Assignee
Swiss Steel Ag
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 Swiss Steel Ag filed Critical Swiss Steel Ag
Priority to ES07816241.9T priority Critical patent/ES2623430T3/es
Priority to EP07816241.9A priority patent/EP2089552B1/fr
Publication of WO2008058410A1 publication Critical patent/WO2008058410A1/fr

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Classifications

    • 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.
  • a) first, a first hot working by rolling is carried out at a temperature between Ac 3 + 100 0 C and Ac 3 , the Automatumformgrad is at least 50%; b) then the rolling stock is cooled to a temperature between Ar 3 + 10O 0 C and Ar 3 and a second hot working carried out, the Bacumformgrad is at least 20%;
  • the rolling stock is placed in an oven with a temperature between Ac-] and Ac-I - 100 0 C and held there for at least 30 minutes, then to be cooled to room temperature.
  • 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 therefore not effected by the cooling process (compare transition from (6) to (7) in FIG. 2 of CN 1088265 A).
  • the object of the invention is to provide an improved process for the continuous production of rod or wire steel, which permits a good control of the properties of the process products and at the same time simplifies the process control.
  • the process according to the invention comprises the following process stages:
  • the rolling stock is cooled below the recrystallization temperature and then a final deformation at a
  • Temperature is carried out in the region of the non-recrystallized austenite, wherein the cooling is carried out in such a way that possible grain growth of the austenite is prevented in the rolling stock before the final shaping and the total degree of deformation in the final deformation amounts to at least 30%;
  • the rolling stock is cooled without reheating to a predetermined holding temperature by the Ar ⁇ temperature and left for a predetermined holding time at the said warming temperature.
  • the method according to the invention requires only two instead of three forming steps. This first of all ensures that only one controlled intermediate cooling is required instead of two such cooling operations between the forming steps. This simplifies the process and the required facility. Moreover, in the process according to the invention, the transition to the holding temperature takes place directly in the course of the cooling process. Reheating to the holding temperature is therefore not required, which not only simplifies the process, but also allows energy savings.
  • the method according to the invention is suitable on the one hand for steels with 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 substantially at Ar 1 6 .
  • the steel has 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,
  • Ar 1 15 and Ar 1 6 denote in a known manner the beginning (upper index “b") and the end (upper index “e") of the austenite-perlite transformation in the cooling direction (where “r” stands for “refroidari” ).
  • the final deformation is carried out at a temperature above Ar 3 .
  • the final transformation is carried out at most Ar 3 + 6O 0 C.
  • the final deformation is carried out at a temperature just below Ar 3 .
  • the final deformation is carried out at a temperature in the range of A ⁇ to Ar 3 , wherein the Endumformtemperatur 690 0 C does not fall below. This allows a further shortening of the required holding time to about one-eighth of the known rolling process.
  • Fig. 1 shows an apparatus for the continuous production of wire or
  • Fig. 2 is a temperature-time profile for a rolling process according to the prior art
  • 3 shows a temperature-time profile for a first embodiment of the rolling method according to the invention
  • Fig. 5 structure of quenched samples after the last stitch as a function of the final rolling temperature (steel C).
  • the rolling apparatus shown in Fig. 1 has not shown driving means for a steel strand 2, which convey it in a direction of advance V through the device.
  • driving means for a steel strand 2 which convey it in a direction of advance V through the device.
  • 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 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 device 10 (for bar steel) or 10a (for wire), where a final reforming is carried out at a temperature in the region of the non-recrystallized austenite. Finally, 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) as well as with unheated 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 (FIGS. 3 and 4).
  • FIG. 2 of the steel strand is initially heated to about 1,150 0 C. Thereafter, a hot working is carried out by rolling at a temperature above 950 0 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 dimension or rolling station, within 5 to
  • 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.
  • first 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 is - unlike in 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 final forming takes place at a temperature which is above Ar 3 ; in the variant of Fig. 4, the final rolling temperature is even lower and is just below Ar 3 in the range between Ar ⁇ and Ar 3 .
  • the final forming could Depending on the rolling station, dimension or rolling speed cause re-heating of the rolling stock. This circumstance must be taken into account, ie it is necessary to avoid that the temperature temporarily rises again above the desired final rolling temperature.
  • the rolling stock is substantially on the Ar 1
  • 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 WaIz device must 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 0 C and then rolled in 6 passes, the initial diameter was 38 mm and the final diameter 17.2 mm. This matches with a total degree of deformation of 80%.
  • the final rolling temperature at about 980 0 C. was Ansch read send the rolled stock has been s (depending on the rolling station) cooled within 6 seconds at 820-960 0 C and then at a cooling rate of 0.3 to 1.9 ° C / 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 1'15O 0 C and then rolled into 4 stitches, wherein the initial diameter of 38 mm and the final diameter was 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 1O20 ° C. Subsequently, the
  • a steel having the same composition as in Comparative Example 1 was heated to 1'15O 0 C and then rolled into 4 stitches, wherein the initial diameter of 38 mm and the final diameter was 23.8 mm. It was the
  • a steel having the chemical composition according to "C" in Table 1 was heated to 1,150 0 C and then rolled in 6 passes, wherein the initial diameter was 17.2 mm and the final diameter of 38 mm. This corresponds to a Monumformgrad of 80%. The final rolling temperature was approx.
  • a steel having the same composition as in Comparative Example 2 was heated to 1,150 0 C and then rolled into 4 stitches, wherein the initial diameter of 38 mm and the final diameter was 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 conversion rate of 47% for the final forming.
  • the final rolling temperature 800 0 C, which is above Ar 3 was.
  • the rolling stock was cooled to 680 0 C within 6 seconds, which was between Ar
  • a steel having the same composition as in Comparative Example 2 was heated to 1,150 0 C and then rolled into 4 stitches, wherein the initial diameter of 38 mm and the final diameter was 23.8 mm.
  • the temperature was after the 4th stitch at about 1'020 0 C.
  • the mixture was then rolled WaIz- the well after an intensive cooling within 13 seconds in a further 2 stitches of 23.8 to 17.2 mm.
  • the final rolling temperature was 690 0 C, which is below Ar 3 . After the last stitch, the rolling stock was within
  • Fig. 5 shows the structure of quenched samples after the last pass as a function of the final rolling temperature. It can be seen that the final forming took place in metastable austenite in Comparative Example 2 (see Fig. 5a) and in Example 3 (see Fig. 5b) , In contrast, this was done in Example 4 (see Fig. 5c) in the ( ⁇ - ⁇ ) -Zweiphasen receptor.

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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)

Abstract

La présente invention concerne un procédé de fabrication en continu de fils d'acier ou de barres d'acier dans lequel une première déformation à chaud est réalisée par laminage à une température supérieure à la température de recristallisation, le degré de déformation complète lors de la première déformation à chaud étant d'au moins 60 %. Ensuite, le produit laminé est refroidi en dessous de la température de recristallisation et ensuite, une déformation finale est réalisée à une température dans la plage de l'austénite non recristallisée, le refroidissement étant réalisé de telle sorte que dans le produit laminé, un éventuel grossissement du grain de l'austénite soit empêché avant la déformation finale et le degré de déformation complète lors de la déformation finale étant d'au moins 30 %. Enfin, le produit laminé est refroidi jusqu'à une température prédéterminée de maintien de la chaleur autour de la température Ar1 et pendant une durée prédéterminée de maintien de la chaleur à ladite température de maintien de la chaleur.
PCT/CH2007/000558 2006-11-17 2007-11-12 Procédé de production en continu de fils d'acier ou de barres d'acier WO2008058410A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
ES07816241.9T ES2623430T3 (es) 2006-11-17 2007-11-12 Procedimiento para la fabricación en continuo de acero en alambre o barras
EP07816241.9A EP2089552B1 (fr) 2006-11-17 2007-11-12 Procédé de production en continu de fils d'acier ou de barres d'acier

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
CH1848/2006 2006-11-17
CH18482006 2006-11-17

Publications (1)

Publication Number Publication Date
WO2008058410A1 true WO2008058410A1 (fr) 2008-05-22

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Application Number Title Priority Date Filing Date
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

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

Citations (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
FR2558174A1 (fr) * 1984-01-13 1985-07-19 Sumitomo Metal Ind Procede pour la production de barres ou fils d'acier ayant une structure spheroidale de cementite amelioree
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

Patent Citations (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
FR2558174A1 (fr) * 1984-01-13 1985-07-19 Sumitomo Metal Ind Procede pour la production de barres ou fils d'acier ayant une structure spheroidale de cementite amelioree
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
"Energy saving prodn. of medium carbon steel wires with spherical cementite", DERWENT, 22 June 1994 (1994-06-22), XP002221735 *

Also Published As

Publication number Publication date
EP2089552B1 (fr) 2017-01-25
PL2089552T3 (pl) 2017-07-31
ES2623430T3 (es) 2017-07-11
EP2089552A1 (fr) 2009-08-19

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