WO2008088834A1 - Procédé pour améliorer la performance de joints à soudure continue utilisant un traitement thermique après soudure - Google Patents

Procédé pour améliorer la performance de joints à soudure continue utilisant un traitement thermique après soudure Download PDF

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Publication number
WO2008088834A1
WO2008088834A1 PCT/US2008/000586 US2008000586W WO2008088834A1 WO 2008088834 A1 WO2008088834 A1 WO 2008088834A1 US 2008000586 W US2008000586 W US 2008000586W WO 2008088834 A1 WO2008088834 A1 WO 2008088834A1
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Prior art keywords
weld
seam
hardenable
steel structure
seam weld
Prior art date
Application number
PCT/US2008/000586
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English (en)
Inventor
Edward J. Mccrink
Daniel S. Codd
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Kva, Inc.
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Publication date
Application filed by Kva, Inc. filed Critical Kva, Inc.
Priority to KR1020097017097A priority Critical patent/KR20090112705A/ko
Priority to JP2009546418A priority patent/JP2010516471A/ja
Priority to EP08724553A priority patent/EP2126145A1/fr
Priority to CN2008800067150A priority patent/CN101622365B/zh
Publication of WO2008088834A1 publication Critical patent/WO2008088834A1/fr

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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/24—Selection of soldering or welding materials proper
    • B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
    • B23K35/3053—Fe as the principal constituent
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K11/00—Resistance welding; Severing by resistance heating
    • B23K11/16—Resistance welding; Severing by resistance heating taking account of the properties of the material to be welded
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K13/00—Welding by high-frequency current heating
    • B23K13/01—Welding by high-frequency current heating by induction heating
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K15/00—Electron-beam welding or cutting
    • B23K15/0046—Welding
    • B23K15/0093—Welding characterised by the properties of the materials to be welded
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
    • B23K20/22—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating taking account of the properties of the materials to be welded
    • B23K20/227—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating taking account of the properties of the materials to be welded with ferrous layer
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K26/00—Working by laser beam, e.g. welding, cutting or boring
    • B23K26/20—Bonding
    • B23K26/32—Bonding taking account of the properties of the material involved
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K9/00—Arc welding or cutting
    • B23K9/23—Arc welding or cutting taking account of the properties of the materials to be welded
    • 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
    • C21D1/34—Methods of heating
    • C21D1/42—Induction heating
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
    • 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
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
    • C21D9/505—Cooling thereof
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/02—Iron or ferrous alloys
    • B23K2103/04—Steel or steel alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/02—Iron or ferrous alloys
    • B23K2103/04—Steel or steel alloys
    • B23K2103/05—Stainless steel
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/50—Inorganic material, e.g. metals, not provided for in B23K2103/02 – B23K2103/26
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • 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
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Definitions

  • This invention relates to post-weld thermal treatments and methods. More particularly, this invention is directed to methods for improving the mechanical properties of seam welds with reduced weld-zone hardness and improved weld-zone ductility and toughness on hardenable ferrous alloys.
  • welded ferrous alloys have become the de facto standard in structural component design.
  • Current trends in many fields have focused interest away from low-strength common mild steels towards high and ultra high strength steels. These alloys are formulated to have greater tensile strengths than low-carbon steels, due to the specific microstructures that are produced during thermomechanical processing.
  • Some examples of high strength steels currently in use in the automotive industry include dual-phase, martensitic, boron-treated, and transformation-induced plasticity steels.
  • Other high- strength alloys include air, oil and water hardenable carbon steels and martensitic stainless steels. All of these are designed so that some volume percentage of martensite forms in the material's microstructure.
  • the resulting distorted body- centered cubic (BCC) or body-centered tetragonal (BCT) martensitic crystal structure formed in the hardened condition imparts high strength to the metal.
  • BCC body-centered cubic
  • BCT body-centered tetragonal
  • Typical methods of controlling weld and HAZ hardness include off-line secondary post- weld heat treatments (PWHT) such as process annealing and tempering of the weld by heating the entire part.
  • PWHT off-line secondary post- weld heat treatments
  • Pre-heating methods can be used to slow the rate of cooling, thereby reducing the percentage of the martensitic phase present.
  • the latent heat in the workpiece reduces the cooling rate of the welded seam, and cracking is thus inhibited.
  • pre- and post-weld heat treatments have been performed in large batch heat treatment furnaces to ramp and hold a group of components at a suitable heat treatment temperature.
  • Drawbacks to the use of batch heat treatment processes include long heat treatment times, due in part to the mass of the large batch furnace and the mass of the components being heat treated.
  • Another method to reduce weld hardness is to add filler material, whereby the final metallurgy is modified in such a way that the percentage of hard and brittle components such as martensite is reduced.
  • some seam welding processes (such as laser or resistance) are difficult to use with filler metals.
  • costly filler metals are selected so as to not harden upon cooling, and thereby provide lower strength weldments. This necessitates an even larger weld to be used to meet the required joint strength.
  • Other methods to improve seam weld properties include mechanically straining and working the weld to induce residual compressive stresses and thereby reduce the tendency of weld seam cracking. This method is not effective, or even possible, for all but the simplest seam weld geometries.
  • U.S. Patent No. 4,072,035 entitled Strengthening of a Welding Seam details this method.
  • seam annealers To improve the mechanical properties of the seam weld.
  • These devices designed to operate on non-hardenable alloys such as loW-carbon steels and austenitic stainless steels, apply a secondary heat source on the seam weld downstream of the weld source after it cools fully to ambient temperature.
  • “seam annealers” reheat the weld to above the A 0 temperature, re-austenitizing the material and hold for some time then allowing to slow cool, equivalent to a "normalizing” heat treatment cycle; secondly, “seam annealers” are employed on non- hardenable alloys. Examples of the “seam-annealing" processes are described in U.S. Patent No. 3,242,299 entitled Inductor for Induction Heating Apparatus, and U.S.
  • U.S. Patent No. 2,293,481 entitled Welding Apparatus and U.S. Patent No. 2,262,705 entitled Electric Welding describe methods to produce welds with reduced brittleness. Both methods utilize a relatively short tempering cycle on hardenable alloys, reheating the weld to improve mechanical properties.
  • these methods employed on band-saw blades and spot welds differ from the present invention. These processes are performed in-situ using the same equipment as used to produce the weld. Indeed, the spot welding equipment must stay in place for proper quenching for the method of U.S. Patent No. 2,262,705, then followed immediately by re-heating to temper the weld. Most significant is that these processes are employed on discrete weld joints: i.e., spot, flash, or projection type welds.
  • the present invention is directed to an improved post-weld heat treatment (PWHT) for hardenable ferrous alloys.
  • PWHT post-weld heat treatment
  • the method of forming a steel structure of the present invention includes treating a traditional weld formed when two surfaces of hardenable ferrous alloys are welded together.
  • the initial weld is formed by applying a heat source, preferably in the form of a traditional welding apparatus, so as to bring adjoining surfaces to sufficiently high temperatures so as to melt the ferrous alloys and form a weld.
  • the weld is then allowed to cool to below the martensitic start (M s ) temperature for the hardenable ferrous alloys.
  • the weld may be cooled to ambient temperature. Alternatively, the weld may be cooled to an intermediate temperature between the ferrous alloys' martensitic start (M s ) temperature and ambient temperature.
  • the seam-weld is tempered in a post-weld heat treating process.
  • the seam- weld is rapidly heated at a rate of 10°C per second or greater to above the martensitic start (M s ) temperature of the hardenable ferrous alloys of the weld.
  • the weld is not heated above the lower critical temperature (A 01 ) of the weld's hardenable ferrous alloys.
  • the weld is heated rapidly, at a rate of at least 10°C per second and a rate of 200°C per second is preferred.
  • Heat to the weld seam may be applied using a variety of heat sources though a localized heat source is preferred.
  • the localized heat sources include, but are not limited to, propane or oxyacetylene torches, resistance, electric arc, lasers, conductive, radiation, convection or high-frequency induction methods.
  • the localized heat sources described herein provide heat to the weld and adjoining areas, but do not heat the entire component.
  • the seam weld is immediately air cooled without a soak time at a holding temperature. Air quenching is conducted at greater than 15°C per minute though preferably not above 200°C per second as may be provided by water cooling.
  • hardenable ferrous alloys may be employed in the practice of the present invention including those steels and alloys that are considered air hardenable.
  • the method of forming a steel structure and methods for post-weld heat treatment of the present invention are believed to have particular application to hardenable martensitic stainless steels, particularly those of type 410, 420 and 440. Because different alloys will possess different lower critical temperatures, martensitic start (M s ) temperatures, and martensitic finish (M F ) temperatures, and because weld characteristics will vary depending on the weld design, the tempering rate, tempering final temperature and cooling rates will vary.
  • the method of forming steel structures of the present invention is also believed to have particular application for forming seam welded pipe and tubing structures, as well as for creating circumferential welds such as on gas or liquid tanks.
  • Fig. 1 is a chart illustrating the four distinct microstructure regions observed in the heat-affected zone (HAZ) of air-hardenable steels after welding;
  • Fig. 2 is a graph of microhardness across a typical weld in an air-hardenable martensitic stainless steel with no pre- or post- heat treatment;
  • Fig. 3 is graph of post- weld heat treatment temperature profiles for conventional tempering compared with the temperature profiles of the present invention
  • Fig. 4 is a flow chart depicting the post- weld heat treatment process of the present invention.
  • Fig. 5 is a perspective exploded view of a typical clamshell tank assembly constructed from pre-hardened shells prior to flange seam welding;
  • Fig. 6 is a perspective view of a typical clamshell tank assembly constructed from pre-hardened shells after flange seam welding
  • Fig. 7 is a perspective view of a typical clamshell tank assembly after flange seam welding showing localized weld seam heat treating with a formed resistance heating coil
  • Fig. 8 is a perspective view of a typical clamshell tank assembly after flange seam welding showing localized weld seam heat treating with a formed resistance heating coil in use;
  • Fig. 9 is a cross-sectional side view of a typical clamshell tank assembly after flange seam welding showing localized weld seam heat treating with a heating coil (resistance or induction) located within clamping fixture;
  • Fig. 10 is a cross-sectional side view of a typical clamshell tank assembly after flange seam welding showing localized weld seam heat treating by passing electrical current through shells for localized weld seam heat treatment;
  • Fig. 11 is a bar graph comparing maximum strain at fracture for DIN EN 895 longitudinal tensile specimens of type 410 seam-welded samples processed according to the present invention with average results for 62 trials.
  • the present invention includes methods of processing seam welds and seam welded structures fabricated from high strength steels and other hardenable alloys.
  • the present invention is believed to have particular application to alloys, which upon seam welding, transform into martensitic weld and HAZ microstructures, and accordingly the following description has particular application to such steels.
  • the process of the present invention allows for improved ductility and toughness of the weld zone and reduced brittleness and susceptibility to hydrogen-induced cold cracking of the weld.
  • the invention allows for improved mechanical straining and deformation of the weld-zone, both the fusion zone and HAZ, eliminating the need for additional post-weld solution heat treatment of the entire structure, such as a process annealing, subcritical annealing or stress relieving.
  • the invention's localized heat treatment eliminates the risk of altering the base metal's material properties and microstructure, making the invention suitable for pre-weld thermomechanically processed alloys as well as those that cannot physically undergo an entire-part heat treatment.
  • Hardenability is that property of steels which determines the depth and distribution of hardness induced by quenching from above the transformation range....
  • the term hardening implies that the hardness of the material is increased by suitable treatment, usually involving heating to a suitable austenitizing temperature followed by cooling at a certain minimum rate which depends upon the alloy content. If quenching is complete, the resulting structure is martensite...its hardness depends upon carbon content of the steel.”
  • hardenable alloys refers to directly hardenable grades of steels and ferrous alloys that are responsive to a heat treatment. Additionally, “hardenable alloys” possess sufficient carbon content, in conjunction with other alloying elements, to form a martensitic microstructure in the fusion and
  • Hardenable alloys as defined herein posses well defined transition temperatures, dependent on the particular chemical composition of the alloy, including: A 03 - upper critical temperature, A 01 - lower critical temperature, M s - martensitic start temperature, and M F - martensitic finish temperature.
  • Hardenable alloys includes those steels and alloys that are considered air-hardenable, as the natural quench cooling rate associated with seam welding is greater than air quenching.
  • the term “hardenable alloys” does not include those steels and ferrous alloys who are considered “low carbon carburizing grades," which respond to heat treatment only through infusing elements into the material's surface via case hardening processes.
  • Representative hardenable alloys for which the present invention is applicable include, but are not limited to: SAE 1030, 1034, 1035, 1037, 1038, 1039, 1040, 1042, 1043, 1044, 1045,
  • the preferred method of the present invention includes forming a seam weld to join two surfaces of hardenable martensitic steel.
  • the seam weld is allowed to cool to below the martensitic start temperature - Ms of the weld.
  • the temperature of the weld may, or may not, be cooled below the martensitic finish temperature or even to ambient temperature. As illustrated in Fig. 3 and Fig.
  • the completed seam weld is rapidly heated, either to the A c ⁇ - lower critical temperature (eutectoid temperature) of the weld metal, or to a lower intermediate temperature greater than the martensitic start (Ms) temperature, and allowing the weld to air-cool, hi a first embodiment identified as Method "A” in Fig. 3 and as depicted by the dashed line on the temperature vs. time chart, the seam weld is heated to the A 01 temperature but not beyond the A 01 - lower critical temperature.
  • This embodiment will allow for maximum softening of the weld seam, as all of the martensite would undergo maximum high-temperature tempering, hi a second embodiment illustrated as Method "B" in Fig.
  • heating to an intermediate temperature will serve to improve the weld seam's toughness by reducing embrittlement without overly softening, and without overly reducing the tensile strength of the weld.
  • the rapid heating of the seam weld is conducted at a rate greater than 10°C/s.
  • rapid heating of the seam weld is conducted even more rapidly at approximately 200°C/s.
  • the rapid heating is followed immediately (no soak times at a holding temperature) by air quenching.
  • the "immediate" transition of rapid heating to air cooling is meant to be construed relatively broadly to include transition periods of a few seconds or even a few minutes as may be incidental to the manufacturing process.
  • the "immediate" transition period of rapid heating to air cooling is not meant to include isothermal soak times where significant changes to the ferrous alloy's crystal microstructure are allowed to occur, such as coarsening of carbide precipitates and recrystallization.
  • Preferred quench rates, consistent with air cooling are greater than 15°C/min but less than 200°C/s.
  • the seam weld can be heated entirely, with shaped heating sources, or piece- wise (as the case for continuous seam welding on a mill) in the present invention.
  • Heat is applied to the weld seam, using any of a variety of localized heat sources including, but not limited to, propane or oxyacetylene torches, resistance, electric arc, lasers, conductive, radiative, convective or high-frequency induction.
  • propane or oxyacetylene torches resistance, electric arc, lasers, conductive, radiative, convective or high-frequency induction.
  • localized is used herein to describe heat sources that provide heat to a localized area of a component, but do not heat the entire component, such as provided by a furnace or oven, hi the case of continuous processes, such as in the production of seam welded pipe and tubing, selectively heating the localized weld seam area would be the most efficient embodiment for larger pipes.
  • annularly heating the full circumference of the pipe such as with a helical induction coil or other means. This annular heating is considered more appropriate for smaller pipe and tubing diameters.
  • the entire weld seam is heated simultaneously which can be practiced for various constructions including circumferential welds, such as on hardenable alloy fuel or liquid tanks.
  • circumferential welds such as on hardenable alloy fuel or liquid tanks.
  • HAZ cracking contributors include:
  • a formed resistance heating coil may be used to locally heat treat the seam weld around an entire tank's periphery.
  • the heating coil can be applied from the top side, the bottom side, or both sides and is held in place, either by direct contact or positioned away from the seam weld surface, until the peak temperature is reached.
  • the coil is then removed and the seam weld is allowed to air cool to room temperature. No protective atmosphere is needed; however, if necessary, the process can be carried out in a non-oxidizing atmosphere.
  • heat is applied to the weld seam using formed induction coils or flame or other methods.
  • the heating coils may be encased in a press die-structure ( Figure 9), which restrains the seam weld from warpage during the process, hi another embodiment of the heating process shown in Fig. 10, electrical current is passed from one component to the other, resistively heating the seam weld to the proper temperature.
  • Typical automotive structural applications that require seam welding of pre- hardened hardenable alloys include chassis components, A, B and C pillars, roof rails, roof bows, impact beams and bumpers.
  • the size and scope of the final vehicle body assembly prohibits any full-structure post-weld stress relieving treatments.
  • the post- weld heat treat process of the current invention is ideally suited to improve the as- welded joint performance of these and similar-type applications.
  • the seam weld was allowed to cool to approximately 180°C, below the martensite start temperature - Ms , as well as below the martensitic finish temperature
  • the application of heat to the weld's A 01 - lower critical temperature (eutectoid temperature) or to a lower intermediate temperature may provide for different mechanical properties of weld zones and the selection of which will depend on the material used and mechanical properties desired.
  • the invention is ideally suited for all seam-welding processes, such as laser welding, resistance seam welding, and arc welding.
  • the invention is also ideal for processing seam welds using hardenable weld filler alloys in addition to autogenous seam welds for reducing the brittleness of the fusion zone and HAZ.
  • Selection of the upper temperature threshold, A 01 - lower critical temperature (eutectoid temperature) below which ferrite and carbide are stable, and M s - martensitic start temperature, are dependent on the weld and base alloy's chemical composition.
  • the natural cooling rate is dependent upon material thickness, joint geometry, alloy type and ambient conditions.

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  • Engineering & Computer Science (AREA)
  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • Physics & Mathematics (AREA)
  • Materials Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Plasma & Fusion (AREA)
  • Optics & Photonics (AREA)
  • Heat Treatment Of Articles (AREA)
  • Arc Welding In General (AREA)
  • Bending Of Plates, Rods, And Pipes (AREA)

Abstract

La présente invention propose un procédé pour traiter thermiquement des constructions à soudure continue d'acier pouvant durcir et d'alliages ferreux avec une dureté de la zone de soudure réduite et une ductilité et une résistance de la zone de soudure améliorée. Ce procédé consiste à chauffer rapidement le cordon de soudure à l'aide d'une source de chaleur secondaire jusqu'à une température plus grande que la température de début de martensite mais pas plus grande que la température critique inférieure, puis en permettant immédiatement un refroidissement par air du cordon de soudure. Le revenu rapide de la présente invention est particulièrement adapté pour la production d'un tuyau ou d'une tuyauterie, ainsi que d'autres structures, à soudure continue d'un alliage pouvant durcir à forte résistance.
PCT/US2008/000586 2007-01-17 2008-01-17 Procédé pour améliorer la performance de joints à soudure continue utilisant un traitement thermique après soudure WO2008088834A1 (fr)

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KR1020097017097A KR20090112705A (ko) 2007-01-17 2008-01-17 후 용접 열처리를 사용한 시임 용접 조인트의 성능 개선 방법
JP2009546418A JP2010516471A (ja) 2007-01-17 2008-01-17 溶接後熱処理を用いてシーム溶接継手の性能を改善する方法
EP08724553A EP2126145A1 (fr) 2007-01-17 2008-01-17 Procédé pour améliorer la performance de joints à soudure continue utilisant un traitement thermique après soudure
CN2008800067150A CN101622365B (zh) 2007-01-17 2008-01-17 使用焊后热处理改善缝焊接头性能的方法

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US88075707P 2007-01-17 2007-01-17
US60/880,757 2007-01-17

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Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109783880A (zh) * 2018-12-21 2019-05-21 中煤北京煤矿机械有限责任公司 焊接仿真在液压支架结构件中的应用方法
FR3086671A1 (fr) * 2018-09-27 2020-04-03 Psa Automobiles Sa Procede de traitement thermique de recuit ou de revenu de points de soudure par chauffage par induction
WO2020104832A1 (fr) * 2018-11-19 2020-05-28 Arcelormittal Procédé de soudage à double passage et double recuit pour assembler des aciers à haute résistance
US10961603B2 (en) 2013-11-25 2021-03-30 Magna International Inc. Structural component including a tempered transition zone

Families Citing this family (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN101786213B (zh) * 2010-03-26 2012-05-23 哈尔滨工业大学 基于电磁感应加热在焊接过程实现控制冷裂纹产生的方法
CN101805822A (zh) * 2010-04-14 2010-08-18 攀钢集团冶金工程技术有限公司 15CrMoG钢环形焊缝热处理方法
KR101359221B1 (ko) 2011-09-30 2014-02-05 주식회사 포스코 용접부의 표면개질을 통한 내공식성 향상방법 및 용접부를 포함하는 스테인리스강
CN104080568A (zh) * 2011-12-20 2014-10-01 Skf公司 通过闪光对接焊制造钢部件的方法以及使用该方法制得的部件
CN103028851B (zh) * 2012-11-29 2015-07-15 中联重科股份有限公司 热处理装置和焊接系统
US9771110B2 (en) * 2015-05-19 2017-09-26 Ford Global Technologies, Llc Method of enhancing in-service structural performance of a sheet metal component
KR102010080B1 (ko) * 2017-12-26 2019-10-21 주식회사 포스코 강판의 용접부의 열처리방법
CN108723560B (zh) * 2018-07-03 2021-03-19 华北水利水电大学 提高高强度焊接接头低温韧性的热处理方法
KR102154624B1 (ko) * 2019-01-11 2020-09-10 울산대학교 산학협력단 펀치금형 고강도소재 적층장치
CN110592362A (zh) * 2019-10-25 2019-12-20 无锡市华立石化工程有限公司 一种用于液氮储罐的304l焊接件的焊后热处理方法

Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS62227040A (ja) * 1986-03-28 1987-10-06 Nippon Steel Corp 軌条溶接部の耐衝撃破壊特性向上法
US20050028898A1 (en) * 2002-01-14 2005-02-10 Usinor Method for the production of a siderurgical product made of carbon steel with a high copper content, and siderurgical product obtained according to said method
US20050257861A1 (en) * 2001-06-29 2005-11-24 Davor Raos Dual seam-welded air hardenable steel tubing and structural members
US20060016519A1 (en) * 2003-03-04 2006-01-26 Komatsu Ltd. Rolling element and method of producing the same
US20060243353A1 (en) * 2005-04-29 2006-11-02 Milam David L Welding together low and high carbon steels
US20070006461A1 (en) * 2001-06-29 2007-01-11 Mccrink Edward J Method for manufacturing automotive structural members

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS62227040A (ja) * 1986-03-28 1987-10-06 Nippon Steel Corp 軌条溶接部の耐衝撃破壊特性向上法
US20050257861A1 (en) * 2001-06-29 2005-11-24 Davor Raos Dual seam-welded air hardenable steel tubing and structural members
US20070006461A1 (en) * 2001-06-29 2007-01-11 Mccrink Edward J Method for manufacturing automotive structural members
US20050028898A1 (en) * 2002-01-14 2005-02-10 Usinor Method for the production of a siderurgical product made of carbon steel with a high copper content, and siderurgical product obtained according to said method
US20060016519A1 (en) * 2003-03-04 2006-01-26 Komatsu Ltd. Rolling element and method of producing the same
US20060243353A1 (en) * 2005-04-29 2006-11-02 Milam David L Welding together low and high carbon steels

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US10961603B2 (en) 2013-11-25 2021-03-30 Magna International Inc. Structural component including a tempered transition zone
FR3086671A1 (fr) * 2018-09-27 2020-04-03 Psa Automobiles Sa Procede de traitement thermique de recuit ou de revenu de points de soudure par chauffage par induction
WO2020104832A1 (fr) * 2018-11-19 2020-05-28 Arcelormittal Procédé de soudage à double passage et double recuit pour assembler des aciers à haute résistance
KR20210076965A (ko) * 2018-11-19 2021-06-24 아르셀러미탈 높은 강도 강들을 결합하기 위한 듀얼 패스, 듀얼 어닐링 용접 방법
RU2771283C1 (ru) * 2018-11-19 2022-04-29 Арселормиттал Двухпроходной способ сварки с двойным отжигом для соединения высокопрочной стали
KR102473004B1 (ko) 2018-11-19 2022-11-30 아르셀러미탈 높은 강도 강들을 결합하기 위한 듀얼 패스, 듀얼 어닐링 용접 방법
CN109783880A (zh) * 2018-12-21 2019-05-21 中煤北京煤矿机械有限责任公司 焊接仿真在液压支架结构件中的应用方法

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EP2126145A1 (fr) 2009-12-02
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JP2010516471A (ja) 2010-05-20
CN101622365B (zh) 2012-11-14

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