EP0185341B2 - Procédé pour augmenter la résistance des aciers à béton - Google Patents

Procédé pour augmenter la résistance des aciers à béton Download PDF

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Publication number
EP0185341B2
EP0185341B2 EP85116005A EP85116005A EP0185341B2 EP 0185341 B2 EP0185341 B2 EP 0185341B2 EP 85116005 A EP85116005 A EP 85116005A EP 85116005 A EP85116005 A EP 85116005A EP 0185341 B2 EP0185341 B2 EP 0185341B2
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EP
European Patent Office
Prior art keywords
temperature
steel
cooled
rolling
strength
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.)
Expired - Lifetime
Application number
EP85116005A
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German (de)
English (en)
Other versions
EP0185341A2 (fr
EP0185341B1 (fr
EP0185341A3 (en
Inventor
Ernst Dr.-Ing. Günther
Klaus Dipl.-Ing. Fischer
Jochen Dipl.-Ing. Schmidt
Norbert Dr.-Ing. Brennecke
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.)
SKET Walzwerkstechnik GmbH
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SKET Walzwerkstechnik GmbH
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Application filed by SKET Walzwerkstechnik GmbH filed Critical SKET Walzwerkstechnik GmbH
Priority to AT85116005T priority Critical patent/ATE67793T1/de
Publication of EP0185341A2 publication Critical patent/EP0185341A2/fr
Publication of EP0185341A3 publication Critical patent/EP0185341A3/de
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Publication of EP0185341B1 publication Critical patent/EP0185341B1/fr
Publication of EP0185341B2 publication Critical patent/EP0185341B2/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
    • C21D8/08—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires for concrete reinforcement

Definitions

  • the invention relates to a method for increasing strength, especially the yield strength of ribbed reinforcing steel with good weldability and cold formability, the as wire rod in the form of coils on continuous High-performance wire lines are manufactured, in which the emerging from the last roll stand at high speed Wire through a rotating laying tube in non-concentric Windings fanned out on a winding conveyor becomes.
  • These steels achieve the required strength properties due to their alloy content and are in the rolled state used. They are therefore also called naturally hard steels designated.
  • Form the alloy basis of the naturally hard steels the elements C, Si and Mn.
  • the content of these elements does not increase arbitrarily be, so that depending on the requirements for weldability high yield strength values of e.g. B. 400 to 500 MPa or above only by adding precipitation hardening alloy elements how V, Ti or Nb can be realized.
  • This So-called micro alloying elements are, however, very expensive and subject to change a constant price increase, so that when adding Microalloying elements the cost of steel making increase significantly.
  • microalloying elements to increase the Strength can be combined with a High temperature thermomechanical treatment (HTMB) with transformation in the pearlite stage or one controlled cooling, in which the wire rod with a predetermined speed up into and through the Temperature range of the pearlite stage transformation is cooled.
  • HTMB High temperature thermomechanical treatment
  • a partial remuneration from the rolling heat is achieved in that the steel passes through a water cooling section arranged in the technological line of the rolling mill immediately after the last rolling pass, the areas near the surface being quenched by intensive pressurized water cooling to below the martensite point and then in the course of the subsequent temperature compensation the heat remaining in the core is tempered to a certain compensation temperature.
  • the steel treated in this way has a concentric edge zone made from tempering structure (high-tempered martensite and / or bainite) and a ferritic-pearlitic core.
  • a transition zone consisting of a mixture of the two microstructures can be arranged between the edge and the core.
  • the yield strength or tensile strength of the partially tempered steels depends on the area share of the different structures in the total cross-section of the rolling stock. So z. B. To ensure a minimum yield strength of 500 MPa, the area share of the tempered strip zone in the total cross-section is at least 30 - 40%.
  • Partially tempered rebars are produced from 8 mm nominal diameter on fine steel mills as bar steel at rolling speeds up to a maximum of about 20 m / s. Maximum rolling speeds of 50 - 100 m / s, sometimes even higher, are achieved on continuous high-performance wire mills. If at such rolling speeds the cooling in a pressurized water cooling section is to take place to such an extent that a martensitic edge zone with a cross-sectional proportion of 30-40% is formed, the braking forces are also so great in DC cooling tubes that the rolling core breaks out between the last stand and the cooling section. In addition, trouble-free winding of the wire that has cooled down is no longer possible.
  • the aim of the invention is to use a method to be developed for the alloying effort to reduce the production of high-strength reinforcing steels with good weldability and cold formability and thus significantly reducing the manufacturing costs compared to the solutions known for continuous high-performance wire mills.
  • the invention has for its object a method for Increase in strength, in particular the yield strength, of ribbed reinforcing bars with good weldability and cold formability, which as a wire rod in a coil form on continuous High-performance wire lines are manufactured where the one emerging from the last roll stand at high speed Wire through a rotating laying tube in non-concentric Windings fanned out on a winding conveyor will develop where the desired mechanical Properties of the ribbed reinforcing steel without the addition of special ones Alloy additives in a continuous process can be achieved.
  • the object is achieved using the Measures mentioned in claim 1 solved in that the Steel, e.g. B. wire rod, in the final phase of the hot rolling process in a given period of time that is not significantly exceeded with a certain change in shape (Decrease in cross section) is formed and immediately after the Forming very quickly to a temperature between 850 and 600 ° C is quenched so that at the beginning the ⁇ - ⁇ conversion is a very fine or incompletely recrystallized Austenite structure is present.
  • This will make a very fine-grained secondary structure, which gives the steel high strength values with very good plastic properties confers without the need for special alloy additives are.
  • the forming in the final phase of the hot rolling process carried out in one or more rolling passes can be at least 60% and less take less than 1 second and the final roll temperature is about 1050 ° C and the wire rod in less immediately after the forming than 2 seconds into the temperature range cooled between 850 and 600 ° C and in be left in this temperature range until the ⁇ - ⁇ conversion is largely completed.
  • the cooling down to the temperature range between the recrystallization temperature of the austenite and the Ar 1 transformation temperature can also take place so abruptly that a concentric edge zone of hardening structure (martensite and / or bainite) forms and the predetermined temperature only occurs in the course of the subsequent temperature compensation between Edge and core sets, leaving the hardened edge zone high.
  • a concentric edge zone of hardening structure martensite and / or bainite
  • the predetermined temperature only occurs in the course of the subsequent temperature compensation between Edge and core sets, leaving the hardened edge zone high.
  • it is useful if the cooling takes place in less than 2 seconds to a compensation temperature between 720 and 600 ° C and it is ensured that the area portion of the hardened and tempered edge zone max. 20 - 30% of the total cross section.
  • the cooling down to the temperature range between the recrystallization temperature of the austenite and the Ar 1 transformation temperature can also take place in such a way that a complete transformation in the pearlite stage is ensured.
  • An advantageous embodiment of the solution according to the invention is that the steel is in the final stage of the hot rolling process with a cross section change of 82% in eight Roll passes and a total time of 0.4 seconds and the rolling temperature is 1050 ° C.
  • Variant 1 (conventional treatment):
  • Variant 2 (method according to the invention):
  • Variant 3 (method according to the invention):

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

Claims (5)

  1. Procédé d'accroissement de la solidité, en particulier de la limite d'étirement, d'aciers à béton crantés, ayant une bonne aptitude au soudage et une bonne aptitude à la déformation à froid, qui sont préparés sous forme de fils machine en écharpes annulaires dans des trains à fils de grande capacité continus, dans lequel le fil sortant à grande vitesse de la dernière cage de laminoir est déformé par un tube de pose en rotation en spires non concentriques sur un transporteur de spires, l'acier dans la phase finale de laminage à chaud étant déformé avec une modification de section d'au moins 60%, qui est effectuée en une ou plusieurs passes et qui doit se faire en moins d'une seconde, la température finale des cylindres s'élevant à environ 1050°C, et étant refroidi immédiatement après la déformation en moins de deux secondes jusque dans l'intervalle de température compris entre 850 et 600°C, puis laissé dans cet intervalle de température jusqu'à ce que la transformation γ-α soit achevée le plus largement possible.
  2. Procédé selon la revendication 1, caractérisé en ce que l'acier immédiatement après la déformation est refroidi en moins de deux secondes jusqu'à la zone de températures comprise entre 720 et 600°C, de manière qu'apparaisse une zone marginale concentrique constituée d'une structure cristalline de durcissement recuite (martensite et/ou baïnite) et que la température est réglée entre 720 et 600°C par l'équilibrage des températures entre la zone marginale et le noyau.
  3. Procédé selon la revendication 1, caractérisé en ce que l'acier immédiatement après la déformation est refroidi en moins de deux secondes à une température située entre 850 et 700°C, et en ce que l'acier est refroidi jusqu'à une température d'environ 600°C avec une vitesse déterminée selon la composition chimique de l'acier de manière qu'on obtienne pratiquement une déformation complète en l'étape perlite.
  4. Procédé selon la revendication 2, caractérisé en ce que l'acier est refroidi de la température d'équilibrage jusqu'a environ 600°C avec une vitesse déterminée selon la composition chimique de l'acier, de manière qu'on obtienne une transformation pratiquement complète de la zone noyau en l'étape perlite.
  5. Procédé selon la revendication 1, caractérisé en ce que l'acier dans la phase finale du processus de laminage à chaud est déformé avec une modification de section de 82% en huit passes et en un temps total de 0,4 seconde, la température finale des cylindres s'élevant à 1050°C.
EP85116005A 1984-12-17 1985-12-16 Procédé pour augmenter la résistance des aciers à béton Expired - Lifetime EP0185341B2 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AT85116005T ATE67793T1 (de) 1984-12-17 1985-12-16 Verfahren zur erhoehung der festigkeit von bewehrungsstaehlen.

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DD270878 1984-12-17
DD84270878A DD231577B1 (de) 1984-12-17 1984-12-17 Verfahren zur erhoehung der festigkeit von bewehrungsstaehlen

Publications (4)

Publication Number Publication Date
EP0185341A2 EP0185341A2 (fr) 1986-06-25
EP0185341A3 EP0185341A3 (en) 1988-10-05
EP0185341B1 EP0185341B1 (fr) 1991-09-25
EP0185341B2 true EP0185341B2 (fr) 1999-02-10

Family

ID=5563382

Family Applications (1)

Application Number Title Priority Date Filing Date
EP85116005A Expired - Lifetime EP0185341B2 (fr) 1984-12-17 1985-12-16 Procédé pour augmenter la résistance des aciers à béton

Country Status (4)

Country Link
EP (1) EP0185341B2 (fr)
AT (1) ATE67793T1 (fr)
DD (1) DD231577B1 (fr)
DE (1) DE3584235D1 (fr)

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
AT501551B1 (de) * 2005-03-07 2008-03-15 Evg Entwicklung Verwert Ges Verfahren und anlage zum herstellen von hochduktilem stahldraht aus warmgewalztem walzdraht

Family Cites Families (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
GB1001233A (en) * 1961-01-23 1965-08-11 Bernhard Matuschka Improvements in or relating to steel
DE2900271C2 (de) * 1979-01-05 1984-01-26 Stahlwerke Peine-Salzgitter Ag, 3150 Peine Schweißbarer Betonstahl und Verfahren zu seiner Herstellung
DD149943C4 (de) * 1980-03-31 1993-01-28 Brandenburg Stahl Walzwerk Verfahren zur herstellung von hochfesten schweissbaren betonstaehlen

Also Published As

Publication number Publication date
DD231577B1 (de) 1987-09-09
EP0185341A2 (fr) 1986-06-25
DE3584235D1 (de) 1991-10-31
ATE67793T1 (de) 1991-10-15
DD231577A1 (de) 1986-01-02
EP0185341B1 (fr) 1991-09-25
EP0185341A3 (en) 1988-10-05

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