EP0185341B1 - 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
EP0185341B1
EP0185341B1 EP85116005A EP85116005A EP0185341B1 EP 0185341 B1 EP0185341 B1 EP 0185341B1 EP 85116005 A EP85116005 A EP 85116005A EP 85116005 A EP85116005 A EP 85116005A EP 0185341 B1 EP0185341 B1 EP 0185341B1
Authority
EP
European Patent Office
Prior art keywords
temperature
steel
cooled
strength
less
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
Other languages
German (de)
English (en)
Other versions
EP0185341A3 (en
EP0185341B2 (fr
EP0185341A2 (fr
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
Original Assignee
STAHL- und WALZWERK BRANDENBURG GmbH
SKET Schwermaschinenbau Magdeburg GmbH
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
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Application filed by STAHL- und WALZWERK BRANDENBURG GmbH, SKET Schwermaschinenbau Magdeburg GmbH filed Critical STAHL- und WALZWERK BRANDENBURG 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
Publication of EP0185341B1 publication Critical patent/EP0185341B1/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 the strength of reinforcing steels.
  • the process is particularly suitable for increasing the strength of ribbed reinforcing steel, which is produced as wire rod in the form of coils on continuous high-performance wire mills, in which the wire emerging at high speed from the last rolling stand is fanned out by a rotating laying tube in non-concentric turns on a winding conveyor becomes.
  • These steels achieve the required strength properties due to their alloy content and are used in the rolled state. They are therefore also referred to as naturally hard steels.
  • the alloy basis of the naturally hard steels is formed by the elements C, Si and Mn.
  • the content of these elements cannot be increased arbitrarily, so that, depending on the requirements for weldability, high yield strength values of e.g. B. 400 to 500 MPa or above can only be realized by adding precipitation hardening alloy elements such as V, Ti or Nb.
  • precipitation hardening alloy elements such as V, Ti or Nb.
  • micro-alloying elements are very expensive and are subject to a constant price increase, so that the cost of steel production increases considerably when micro-alloying elements are added.
  • the effect of the microalloy elements to increase the strength can be combined with a high temperature thermomechanical treatment (HTMB) with conversion in the pearlite stage or a controlled cooling in which the wire rod is cooled at a predetermined speed up to and through the temperature range of the pearlite stage transformation.
  • HTMB high temperature thermomechanical treatment
  • the rolling process is divided into a roughing and finish rolling phase, the finish rolling with a predetermined degree of deformation in the lower austenite area, i.e. H. in the temperature range of about 900 - 750 C.
  • the rolling blocks are not mechanically designed for rolling in the temperature range of the finish rolling phase.
  • the heat generated during the forming process cannot be dissipated due to the high rolling speeds and leads to a reheating of the rolling stock up to the final rolling temperature of around 1000 C.
  • a partial tempering 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 rolled 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.
  • the aim of the invention is to use a process to be developed to reduce the alloying effort for the production of high-strength reinforcing steels with good weldability and cold formability and thus to significantly reduce the manufacturing costs compared to the solutions known for continuous high-performance wire mills.
  • the invention has for its object to develop a method for increasing the strength, in particular the yield strength of reinforcing steels while ensuring good weldability and good plastic properties.
  • the process is said to be suitable for the production of ribbed reinforcing steel as coiled wire in the form of a coil, preferably on continuous high-performance wire mills, in which the wire emerging from the last mill stand at high speed is fanned out by a rotating laying tube in non-concentric turns on a winding conveyor.
  • the object is achieved using the measures mentioned in claim 1 in that the steel, for. B. wire rod, in the final phase of the hot rolling process within a predetermined period of time, which may not be exceeded significantly, with a certain change in shape (decrease in cross-section) and immediately after the forming very quickly to a temperature below the recrystallization temperature of the austenite, but above the Ar 1 Transformation temperature is quenched, so that at the beginning of the ⁇ - ⁇ transformation there is a very fine or incompletely recrystallized austenite structure.
  • the forming in the final phase of the hot rolling process which can be carried out in one or more passes, must be at least 60% and take place in less than 1 second and the steel, e.g. B. wire rod, in less than 2 seconds to the above.
  • Temperature range which is between about 850 and 600 ° C can be cooled and 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 Ari transition temperature can also take place in such a way that a complete transformation in the pearlite stage is ensured.
  • Variant 1 (conventional treatment):
  • Variant 2 (method according to the invention):
  • Variant 3 (method according to the invention):

Landscapes

  • 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 (4)

1. Procédé d'accroissement de la solidité, en particulier de la limite d'étirement des aciers à béton avec 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, où l'acier est déformé dans la phase finale du procédé de laminage à chaud avec une modification de la section d'au moins 60%, qui est conduite en une ou plusieurs passes et doit s'effectuer en moins d'une seconde, et immédiatement après la déformation, on refroidit en moins de deux secondes jusqu'a la zone de températures comprise entre la température de recristallisation de l'austénité et les températures de transformation d'Ar1, en règle générale entre 850 et 800 ° C, et est laissé dans cet intervalle de températures jusqu'à ce que la transformation y-a soit terminée dans la plus grande mesure 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'or obtienne une transformation pratiquement complète de la zone noyau en l'étape perlite.
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 true EP0185341B1 (fr) 1991-09-25
EP0185341B2 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
DE3584235D1 (de) 1991-10-31
DD231577B1 (de) 1987-09-09
ATE67793T1 (de) 1991-10-15
EP0185341A3 (en) 1988-10-05
EP0185341B2 (fr) 1999-02-10
EP0185341A2 (fr) 1986-06-25
DD231577A1 (de) 1986-01-02

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