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EP0172544B2 - Procédé de traitement thermique d'aciers laminés à chaud sous forme de barres ou de fils pour béton précontraint - Google Patents
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EP0172544B2 - Procédé de traitement thermique d'aciers laminés à chaud sous forme de barres ou de fils pour béton précontraint - Google Patents

Procédé de traitement thermique d'aciers laminés à chaud sous forme de barres ou de fils pour béton précontraint Download PDF

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Publication number
EP0172544B2
EP0172544B2 EP85110316A EP85110316A EP0172544B2 EP 0172544 B2 EP0172544 B2 EP 0172544B2 EP 85110316 A EP85110316 A EP 85110316A EP 85110316 A EP85110316 A EP 85110316A EP 0172544 B2 EP0172544 B2 EP 0172544B2
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EP
European Patent Office
Prior art keywords
content
steel
thread
ribs
hot
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
EP85110316A
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German (de)
English (en)
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EP0172544A3 (en
EP0172544B1 (fr
EP0172544A2 (fr
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.)
dywidag-Systems International GmbH
Stahlwerk Annahutte Max aicher & Cokg GmbH
Original Assignee
Stahlwerk Annahuette Max Aicher & Co Kg GmbH
Dyckerhoff and Widmann AG
Stahlwerk Annahuette Max Aicher GmbH and Co KG
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Application filed by Stahlwerk Annahuette Max Aicher & Co Kg GmbH, Dyckerhoff and Widmann AG, Stahlwerk Annahuette Max Aicher GmbH and Co KG filed Critical Stahlwerk Annahuette Max Aicher & Co Kg GmbH
Priority to AT85110316T priority Critical patent/ATE49779T1/de
Publication of EP0172544A2 publication Critical patent/EP0172544A2/fr
Publication of EP0172544A3 publication Critical patent/EP0172544A3/de
Application granted granted Critical
Publication of EP0172544B1 publication Critical patent/EP0172544B1/fr
Publication of EP0172544B2 publication Critical patent/EP0172544B2/fr
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

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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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
    • C21D8/08—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires for concrete reinforcement
    • 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
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10S—TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10S148/00—Metal treatment
    • Y10S148/902—Metal treatment having portions of differing metallurgical properties or characteristics
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10S—TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10S148/00—Metal treatment
    • Y10S148/902—Metal treatment having portions of differing metallurgical properties or characteristics
    • Y10S148/907—Threaded or headed fastener

Definitions

  • the invention relates to a method for the heat treatment of hot-rolled prestressing steels in the form of rods or wires.
  • Prestressing steel as used in construction as tendons for prestressed concrete, but also as anchor steel for ground and rock anchors as formwork anchors, for suspension cables from suspension bridges, inclined cables from inclined cable bridges, bracing, etc., generally have a yield strength of 835 to 1 080 N. / mm 2 and a tensile strength that varies from 1 030 to 1 230 N / mm 2 .
  • steels with a C content of 0.65 to 0.75%, an Si content of 0.60 to 1.60% and a Mn content of 0.70 to 1 are used as the starting material. 50% and chrome and / or vanadium and other alloying elements are used.
  • Prestressing steels of this type are known in various designs, for example as round wires, which are cold-drawn after hardening for strengthening and then tempered again, as flat steels, for example oval steels, which are tempered over the entire cross-section after rolling and as steel rods. Steel bars with a diameter between approximately 15 and 50 mm are then hot-rolled to increase the yield strength and then tempered for relaxation. In addition to the fact that only limited lengths can be produced because of the stretching, this complex manufacturing process entails high production costs.
  • prestressing steels In addition to the static strength values, prestressing steels must have the highest possible elastic limit and good deformability. In the case of screwable prestressing steels, in which thread anchors can be attached, high wear resistance of the surface and corrosion resistance are important. The relaxation properties and a sufficiently high fatigue strength are also important.
  • reinforcing bars that are used as slack, not prestressed reinforcement for reinforced concrete.
  • Reinforcing steels of this type are used either naturally hard, whereby the strength is determined by the alloy, or cold worked, for example by drawing or cold rolling, the latter primarily for structural steel mesh. Reinforcing steel of this type must be weldable; their analysis is therefore characterized by a low C content.
  • Such reinforcing steels generally have a yield strength between 420 and 500 N / mm 2 and a tensile strength between 500 and 550 N / mm 2 . Reinforcing steels with higher strength values are usually not manufactured.
  • the analyzes used are consistently those of weldable steels with a C content of less than 0.22%.
  • Reinforcing bars are manufactured with a smooth surface and as ribbed reinforcing bars.
  • Reinforced ribs usually have crescent-shaped ribs that run obliquely to the longitudinal axis of the bar, which extend in the transverse direction over a large part of the bar circumference and are intended to improve the bond between the bar in question in the concrete.
  • the invention has for its object to provide an accurate and inexpensive manufacturing process for prestressing steel, especially for screwable prestressing steel with the strength properties mentioned at the outset, which allows metallurgical easy-to-represent and cost-effective analyzes for the production of prestressing steel which is corrosion-resistant and which has a wear-resistant surface which reduces the risk of mechanical damage and is suitable for threading.
  • Prestressing steel should continue to be producible in any bar length, with high yield strength and high strength it should have great ductility or toughness, especially at low temperatures, and with low relaxation it should have high fatigue strength.
  • this object is achieved in that steels with a C content of 0.50 to 0.80%, an Si content of 0.20 to 0.50% and a Mn content of 0.30 to 0 , 80% after the hot rolling from the rolling heat at the exit side of the finishing stand out are subjected to a final rolling temperature which the steel is at the lower limit of the hot workability just above the transformation point a 3 by means of water having a surface quenching such that the material in a peripheral zone is immediately and completely converted into martensite and that the heat content remaining in the core zone during the subsequent cooling does not cause the martensitic peripheral zone to temper beyond the range of the intermediate stage in such a way that the surface temperature of the peripheral zone by temperature compensation in the period between the second and sixth seconds the heat treatment is between 400 degrees and 500 degrees C depending on the rod diameter.
  • the invention is based on the knowledge that the combinatorial interaction of certain factors is required in order to produce a prestressing steel with the specified properties in an economical manner.
  • the size of the austenite grain is determined, among other things, by the recrystallization that occurs during hot rolling after each pass. In absolute terms, the more frequently and more intensively it is deformed, the smaller it is. The final grain size is only achieved in the last rolling pass; Here, too, the deformation and the temperature as well as the dwell time at this temperature until the cooling process begins are decisive.
  • the temperature at the last roll pass is at the lower limit of the hot deformability, that is to say just above the transition point A 3 .
  • the cooling must start so quickly and so intensively that the cooling curve of the edge zone reaches the martensite area without reaching the areas of ferrite, pearlite and the intermediate stage. This is particularly important for a relatively carbon-rich steel, in which the martensite start temperature M S is relatively low.
  • the core zone of the rod must still have such a large heat content in order to cause the martensite present in the peripheral zone to temper.
  • FIG. 1 shows a time-temperature conversion diagram for a steel which roughly has the analysis preferred for the invention, namely 0.76% C, 0 , 23% Si and 0.63% Mn.
  • Curve R 1 shows the profile of the surface temperature of a steel rod with a relatively small diameter, for example 15.1 mm
  • curve K 1 shows the profile of the temperature of the core zone of the rod in question
  • R 2 is the corresponding curve of the surface temperature of a rod with a larger diameter.
  • curve R 1 in the area of tempering is essential for the heat treatment.
  • the curve R 1 of the surface temperature should run in the temperature range between 400 and 500 ° C. in the time between the second and the sixth second of the heat treatment recorded in FIG. 1; under no circumstances should it extend into the pearlite area.
  • the strong cooling of the edge zone also accelerates the heat transfer from the core zone.
  • conversion takes place directly in the intermediate stage or pearlite pre-precipitation takes place. It is considered particularly advantageous if the core zone of the rod converts in the upper intermediate stage area, which is characterized by a finely dispersible distribution of the carbides.
  • the intensity of the cooling of the peripheral zone essentially depends on the cooling capacity of the system available.
  • the cooling capacity depends on several factors.
  • a water quantity of 10 to 20 Vsec kg is considered to be particularly advantageous.
  • Inertia supporting this process can also be achieved through the chemical composition of the steel.
  • the alloy elements can be selected accordingly also to lower the C content to the lower limit.
  • Table 1 shows the analytical values of some melts of the steel grades 835/1 030 (ratio: yield strength / tensile strength) or 885/1 080, which were taken on tie rods with diameters of 26.5 mm and 15.1 mm.
  • Table 2 shows the static strength values, calculated as mean values, of some of the tensioning rods of the diameters 36.0 mm, 26.5 mm and 15.1 mm produced according to the invention.
  • the abbreviations Re here mean the yield strength, Rm the tensile strength, A 10 the elongation at break over a measuring length which corresponds to 10 times the diameter of the rod and A G the uniform elongation.
  • the high corrosion resistance of steels produced according to the invention is above all a result of great uniformity of the structure; due to the low temperature during rolling and the rapid cooling, disruptive factors are prevented from occurring.
  • relaxation tests to determine the inelastic elongation after 1000 hours of standing have shown that the relaxation losses are very low. Bending tests have shown excellent ductility properties of the samples examined.
  • the prestressing steels produced by the method according to the invention have a high level of comfort in the edge zone and a correspondingly high surface strength, they are particularly suitable for the production of screwable prestressing steels.
  • Threaded anchors are often used to transmit the clamping forces to the component in question.
  • Such a non-cutting deformation in contrast to a cut thread, has the advantage that in the threaded area with a reduced core cross-section, the steel structure is strengthened, particularly in the area of the thread fillets, so that the steel bar also has its full cross section, taking into account the allowable stresses corresponding force can be used.
  • a thread with such rounded fillets allows considerably greater tolerances compared to the thread of the nut and thus creates the prerequisite for inaccuracies in the installation of the anchoring bodies to be safely absorbed.
  • the invention accordingly also relates to the application of the method to the production of hot-rolled steel rods or wires with a smooth surface, which at least at the ends are provided with cold rolled threads suitable for screwing on a connecting or anchoring body, in which the fillet in the Thread fillets have a much larger radius of curvature than at the thread tips and on the production of steel rods or wires, which are provided with ribs by hot rolling, which at least in some areas run along a helix, which are arranged on two opposite sides of the rod circumference and Form parts of a thread onto which a connection or anchoring body provided with a corresponding counter thread can be screwed.
  • the fins behave towards the cooling medium like cooling fins during the heat treatment of this rod, that is to say that the heat output in the region of Ribs is comparatively larger than in the area of the smooth rod surface, so that the border zone between the core zone and the peripheral zone of the rod runs in a straight line.
  • This ratio is expediently 0.5 to 1 to 4.
  • the tension rod 1 shown in Fig. 2 is rolled as a smooth rod and has been subjected to the heat treatment according to the invention.
  • a thread 2 was rolled onto the rod end, which is indicated in FIG. 4 in longitudinal section in a large enlargement.
  • This thread is a so-called asymmetrical partial thread, i.e. the radius of curvature in the area of the thread fillets 3 is significantly larger than in the area of the thread tips 4.
  • the tension rod 11 shown in FIGS. 5 and 6 is a so-called threaded rod, which has already been provided with threaded ribs 12 in the course of the hot rolling process.
  • the ribs 12 have a height h, an average width B and are arranged at a distance A from one another, which are approximately in a ratio of 0.5 to 1 to 4.
  • the ribs 12 each extend over approximately one third of the rod circumference to their full height and merge at their end faces 13 into the surface 14 of the rod core 15.
  • the boundary zone 16 between the edge zone R, in which the material of the steel has been converted into martensite by the surface quenching, and the core zone K, the heat content of which remains after the surface quenching causes the subsequent tempering of the martensitic edge zone R approximately straight .
  • This is the result of the increased cooling effect of the ribs during surface quenching and has the advantage of a consistently high surface strength of the steel and very good corrosion resistance.
  • the anchoring and connecting elements such as nuts, sleeves or the like, to be shorter than in the case of known tension rods with a homogeneous rod cross section.
  • the shorter these elements are, the better the force transmission in the thread area between the rod and nut or sleeve.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Organic Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Physics & Mathematics (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)
  • Heat Treatment Of Articles (AREA)
  • Metal Rolling (AREA)
  • Rod-Shaped Construction Members (AREA)
  • Laminated Bodies (AREA)
  • Coating With Molten Metal (AREA)

Claims (7)

  1. Procédé pour le traitement thermique d'aciers de précontrainte laminés à chaud en forme de barres ou de câbles ayant une limite d'élasticité de 835 à 1080 N/mm2 et une résistance à la traction de 1030 à 1230 N/mm2, selon lequel des aciers ayant une teneur en C de 0,50 à 0,80 %, une teneur en Si de 0,20 à 0,50 % et une teneur en Mn de 0,30 à 0,80 % sont, après le laminage à chaud et à partir de la température de laminage sur le côté de sortie de la cage finisseuse présentant une température finale de laminage située à la limite inférieure de la déformabilité à chaud de l'acier et juste au-dessus du point de transformation A3, soumis à une trempe de surface au moyen d'eau de telle sorte que le matériau est transformé directement et totalement en martensite dans une zone marginale (R), et que l'enthalpie résiduelle dans la zone de coeur (K) ne produit pas pendant le refroidissement consécutif un revenu de la zone marginale martensitique (R) au-delà de la plage du domaine bainitique, de telle sorte que la température de surface de la zone marginale est, par égalisation de température, dans la période comprise entre la deuxième et la sixième seconde du traitement thermique, comprise entre 400 degrés et 500 degrés C selon le diamètre de la barre.
  2. Procédé selon la revendication 1, caractérisé en ce que l'on utilise des aciers ayant une teneur en C d'environ 0,75 %, une teneur en Si d'environ 0,25 %, une teneur en Mn d'environ 0,60 %.
  3. Procédé selon la revendication 1 ou 2, caractérisé en ce que la température de laminage finale est comprise entre 860 et 1060°C.
  4. Procédé selon l'une quelconque des revendications 1 à 3, caractérisé en ce que l'on ajoute à l'alliage jusqu'à environ 0,8 % de chrome, jusqu'à environ 0,5 % de cuivre, jusqu'à environ 0,15 % de vanadium, jusqu'à environ 0,06 % de niobium, ainsi que des traces de titane et de bore, individuellement ou en combinaison.
  5. Utilisation du procédé selon l'une quelconque des revendications 1 à 4, pour la fabrication de barres ou de câbles d'acier laminés à chaud et à surface lisse, qui sont munis au moins à leurs extrémités de filetages appropriés et laminés à froid pour y visser un corps de liaison ou d'ancrage, dans lequel l'arrondi des gorges du filetage a un rayon de courbure sensiblement plus important que celui des pointes.
  6. Utilisation du procédé selon l'une quelconque des revendications 1 à 4, pour la fabrication de barres ou de câbles d'acier, qui sont munis de nervures pendant le laminage à chaud, disposées au moins dans les régions partielles le long d'une hélice, qui sont prévues sur les deux côtés mutuellement opposés de la périphérie de la barre et forment une partie d'un filetage sur lequel peut être vissé un corps de liaison ou d'ancrage muni d'un contre-filetage correspondant.
  7. Utilisation du procédé selon la revendication 6, caractérisé en ce que les nervures sont constituées et disposées de manière que le rapport entre la hauteur et la largeur moyenne et la distance entre nervures soit sensiblement d'environ 0,5 à 1 à 4.
EP85110316A 1984-08-23 1985-08-17 Procédé de traitement thermique d'aciers laminés à chaud sous forme de barres ou de fils pour béton précontraint Expired - Lifetime EP0172544B2 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
AT85110316T ATE49779T1 (de) 1984-08-23 1985-08-17 Verfahren zum herstellen von walzstahlerzeugnissen, insbesondere von schraubbaren spannstaehlen oder dergleichen.

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE3431008 1984-08-23
DE3431008A DE3431008C2 (de) 1984-08-23 1984-08-23 Wärmebehandlung von warmgewalzten Stäben oder Drähten

Publications (4)

Publication Number Publication Date
EP0172544A2 EP0172544A2 (fr) 1986-02-26
EP0172544A3 EP0172544A3 (en) 1987-10-28
EP0172544B1 EP0172544B1 (fr) 1990-01-24
EP0172544B2 true EP0172544B2 (fr) 1996-06-05

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ID=6243708

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EP85110316A Expired - Lifetime EP0172544B2 (fr) 1984-08-23 1985-08-17 Procédé de traitement thermique d'aciers laminés à chaud sous forme de barres ou de fils pour béton précontraint

Country Status (10)

Country Link
US (1) US4877463A (fr)
EP (1) EP0172544B2 (fr)
JP (1) JPH0660350B2 (fr)
AT (1) ATE49779T1 (fr)
AU (1) AU565805B2 (fr)
BR (1) BR8504032A (fr)
CA (1) CA1268957A (fr)
DE (2) DE3431008C2 (fr)
ES (1) ES8609490A1 (fr)
ZA (1) ZA856448B (fr)

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US6086305A (en) 1999-01-13 2000-07-11 Illinois Tool Works Inc. Nails having selected heat treatment and hardening
DE19921286A1 (de) * 1999-05-07 2000-11-09 Sms Demag Ag Wärmebehandlungsverfahren zur Herstellung randschichtgehärteter Lang- nd Flachprodukte aus unlegierten oder niedriglegierten Stählen
ITMI20031031A1 (it) * 2003-05-22 2004-11-23 Danieli Off Mecc Metodo di rocchettatura di materiale metallico in barra.
US7624556B2 (en) 2003-11-25 2009-12-01 Bbv Vorspanntechnik Gmbh Threaded deformed reinforcing bar and method for making the bar
US8997420B2 (en) * 2004-11-29 2015-04-07 Victor Amend Reinforced insulated forms for constructing concrete walls and floors
CN1327008C (zh) * 2005-07-07 2007-07-18 东北大学 高强度带肋钢筋轧后超快速冷却生产工艺
DE202010006059U1 (de) * 2010-04-23 2010-07-22 Stahlwerk Annahütte Max Aicher GmbH & Co KG Gewindestab
AU2013205904B2 (en) * 2012-05-17 2017-12-07 Woodstock Percussion Pty Ltd Full Strength Threaded Bar
CH707301B1 (de) * 2013-04-08 2014-06-13 Empa Verfahren zum Erstellen von vorgespannten Betonbauwerken mittels Profilen aus einer Formgedächtnis-Legierung sowie Bauwerk, hergestellt nach dem Verfahren.
CZ201786A3 (cs) * 2017-02-15 2019-01-30 Západočeská Univerzita V Plzni Způsob výroby součástí z ocelí

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DE3431008A1 (de) 1986-03-06
DE3431008C2 (de) 1986-10-16
ES546332A0 (es) 1986-07-16
ZA856448B (en) 1986-04-30
AU565805B2 (en) 1987-10-01
CA1268957A (fr) 1990-05-15
EP0172544A3 (en) 1987-10-28
BR8504032A (pt) 1986-06-10
ES8609490A1 (es) 1986-07-16
JPH0660350B2 (ja) 1994-08-10
EP0172544B1 (fr) 1990-01-24
DE3575577D1 (de) 1990-03-01
US4877463A (en) 1989-10-31
AU4658285A (en) 1986-02-27
EP0172544A2 (fr) 1986-02-26
ATE49779T1 (de) 1990-02-15
JPS6160824A (ja) 1986-03-28

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