CN101622365A - Use postweld heat treatment to improve the method for a seam welding performance - Google Patents
Use postweld heat treatment to improve the method for a seam welding performance Download PDFInfo
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- CN101622365A CN101622365A CN200880006715A CN200880006715A CN101622365A CN 101622365 A CN101622365 A CN 101622365A CN 200880006715 A CN200880006715 A CN 200880006715A CN 200880006715 A CN200880006715 A CN 200880006715A CN 101622365 A CN101622365 A CN 101622365A
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- 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
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- Crystallography & Structural Chemistry (AREA)
- Thermal Sciences (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Optics & Photonics (AREA)
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- Arc Welding In General (AREA)
- Bending Of Plates, Rods, And Pipes (AREA)
Abstract
The present invention provides the method for the seam welding structure of steel that thermal treatment can harden and iron alloy with the welding zone ductility of the welding zone hardness that reduces and improvement and toughness.This method comprises with secondary heat source weld seam is heated rapidly to the temperature that is higher than Ms (martensite start) point but is not higher than lower critical temperature, then makes the weld seam air cooling at once.Prompt tempering of the present invention is particularly suitable for the seam welded pipe of the alloy that high strength can harden and the production of tubing and other member.
Description
Background of invention
The present invention relates to postweld heat treatment and method.More particularly, present invention is directed at welding zone hardness and the welding zone ductility of improvement and the method that toughness improves the mechanical property of weld seam on the iron alloy that can harden to reduce.
The iron alloy of the welding of generally using in all modern industries has become the actual standard in the structural component design.Current trend in many fields turns to high-strength steel and ultrahigh-strength steel with the attention of concentrating from the low strength ordinary low-carbon steel.Dispose these alloys to have the tensile strength that is higher than soft steel, this is because the specific microstructure that produces during the hot mechanical treatment.Some examples that are used for the high-strength steel of automotive industry at present comprise steel and the phase transformation induced plasticity steel that dual phase steel, martensitic steel, boron are handled.Other high-strength alloy comprises the carbon steel and the Martensite Stainless Steel of available air, oil and water quenching.All these steel are designed so that to form the martensite of some percent by volumes in the microstructure of material.Distored body-centered cubic of the gained that forms under the condition of hardening (BCC) or body-centered teteragonal (BCT) martensite crystalline structure are given high strength to this metal.These material ideal ground are suitable for structure unit and assembly, satisfy high intensity and flexible requirement.
Regrettably, these and other superstrength alloy forms martensitic tendency and causes difficulty with relative high hardenability in welding.Heating that weld period takes place in restricted heat affected zone (HAZ) and quick refrigerative thermal cycling are equivalent to the rapid quenching circulation.The chemical constitution of high-strength steel grade causes the transformation fully of from the ferrite to the austenite (γ) under high-temperature, then become hard martensitic phase subsequently through quick cooling.In seam weldering purposes, natural weld seam rate of cooling may be up to 1000 ℃/s, thereby it enough produces martensitic stucture (seeing Fig. 1 and 2) soon in most of high strength, high carbon alloy.Produce to make martensitic stucture extremely crisp under Annealed Strip not.Can comprise because of following several reason generation welding zone crackings:
■ hydrogen refrigeration cracking, this is the hydrogen of catching owing in the distored BCC martensitic crystalline structure.The tensile stress that is applied to weld seam has improved the rimose risk.
■ thermic stress, this is the volume change during owing to the degree of the input of the heat of weld period, joint constraint and martensitic transformation.
The cracking of most of forms results from the shrinkage strains that takes place when weld metal is cooled to envrionment temperature.Be restricted if shrink, then strain will be brought out and cause the rimose residual-tensile stress.There are two kinds of opposite power: the stress that rigidity causes around stress that metal contracts causes and the base mateiral.Big weld size, the input of high heat and the dark welding operation that penetrates have improved shrinkage strains.When filler metal that relates to higher-strength and base mateiral, the stress that these strains cause will increase.For higher yield strength, can there be higher unrelieved stress.
When these problems take place during some steel in welding, and with their state in advance, whether through annealing, harden or harden and tempering irrelevant.They can be followed all types of welding and take place, and described welding comprises GTAW, GMAW, SAW, PAW, laser beam weldering, friction welding (FW), resistance welding and electron beam welding.In all scenario, fusion area and high temperature HAZ will be in " through quenching " state after welding.Any mechanical strain after the welding (in secondary fabrication processes or in use) can cause martensite HAZ cracking.
In addition, in a single day many assemblies are welded and are made by these alloys, then can not be to its solution heat treatment circulation that finally homogenizes.Example comprises that thermal cycling will destroy unique microstructure of alloy thus by hardening in advance or the underlying metal of the special hot mechanical treatment assembly made of dual phase steel for example.In addition, as be welded to the situation of the vehicle structure beam of thick and heavy car body, whole weld assembly be placed into carry out post-weld stress in the stove and eliminate in fact that (physically) is infeasible.Some assemblies can not tolerate the postweld heat treatment of entire structure, are this situation for the automobile fuel box assembly of the welding with thermoplasticity internal part.In any case, if can reduce the fragility of welded condition, then can obtain significant benefits.Do not carry out any other thermal treatment and in the situation that comes into operation, the ductility and the toughness of final weld seam will greatly be improved at the member of welding.
The typical method of control weld seam and HAZ hardness comprises off-line secondary postweld heat treatment (PWHT), for example by heating whole part with weld seam process annealing and tempering.Can use the method for preheating to slow down rate of cooling, thereby reduce the percentage ratio of the martensitic phase that exists.Latent heat in the workpiece reduces the rate of cooling of weld seam, and therefore cracking is suppressed.In the past, can in big (batch) in batches heat treatment furnace, weld before and postweld heat treatment be in the proper heat treatment temperature with gradual (ramp) and holding member group.Use the defective of batch heat method to comprise the long treatment time, this part ground is because the scale of the scale (mass) of big batch-type stove and the parts of heat-treating.In addition, long queuing time is appearring when carrying out assembly with individual component welding and with each batch.The postweld heat treatment of standard for example stress relieving or tempering relates to keep the long-time relatively of about several hrs under specified temperature, is attended by that stove is cold slowly.Make thing more complicated be, before the whole weldering or postweld heat treatment can destroy the required microstructure of underlying metal.For example, except heat-up time and quench rates with the best, if whole part is heat-treated, the total loss that can suffer mechanical property by the part of dual phase steel or martensitic steel manufacturing.
In the manufacturing shop, be well known that, when to the steel that can harden for example chrome-moly steel (chromoly) add man-hour, with oxy-acetylene blowpipe reheat weld seam so that weld seam austenitizing and allow joint slowly cooling in still air again.Welding joint and on every side the heat that keeps of metal slow down the rate of cooling of weld seam behind the reheat effectively, thereby reduce fragility, make joint be in relatively mild as-normalized condition.Yet, this method be variable, slowly, piecemeal and as a result height depend on producer's state of the art.Method as an alternative for example is entitled as those that describe in the U.S. Patent No. 3,046,167 of Heat-Treating Method and Product, provides with torch weld seam austenitizing and then slowly cooling again.In the U.S. Patent No. 6 that is entitled as Postweld Heat Treatment Process of Carbon Steel and Low AlloySteel, 676, similar approach has been described in 777, its regulation to the austenitic area and keep the some time, is then carried out the cooling of " slower than air " with the weld seam reheat.All these methods depend on weld seam be heated to above upper critical temperature and slowly cooling produce required microstructure.
Usually Industrial products and the oil field pipe welding joint that uses to harshness applies conventional controlled " part " post-weld stress elimination.Apply heat by the heating " blanket (blanket) " that constitutes by induction around joint or resistance heating coil.Apply heat very lentamente, allow to stop several minutes to several hours, allow cooling very lentamente in the insulation heating blanket then at peak temperature.
In seam-welded tube production, the ordinary method that solves high-strength alloy inherent welding difficulty is to improve the chemical constitution of material.Typically, but developed the alloy of the air hardenable of low-carbon (LC) form, made weld seam not become complete martensite and will not ftracture at the tubing production period.The example of this method is the United States Patent (USP) 7 that is entitled as Method of Manufacturing Stainless Steel Pipe ForUse In Piping Systems, 157,672, it has described low-carbon (LC) two-phase and the application of stainless material in traditional tubing manufacture method of 0.08%C at most in detail.Similarly, use improved composition to produce pipeline below in the article: Development ofweldable martensitic stainless steel line pipe by HF-ERWprocess, people such as N.Ayukawa, Stainless Steel World 1999 ConferenceProceedings, 1999.In chemical constitution is improved, exist compromise between the easiness of welding and the hardenability of material and the maximum machine performance.
The another kind of method that reduces weld hardness is to add packing material, improves final metallurgical properties thus so that for example martensitic percentage ratio of hard and crisp component reduces.Yet some seam soldering methods (for example Laser Welding or resistance welding) are difficult to use with filler metal.In addition, select expensive filler metal so that non-sclerous when cooling, thereby more low intensive weldment is provided.This makes and must use even bigger weld seam satisfies desired strength of joint.
Other method of improving Weld Performance comprises weld seam mechanical deformation (strain) and processing causing residual compressive stress, thereby reduces the tendency of weld cracking.For all welds geometries (except the simplest), this method is not effectively, or or even infeasible.The U.S. Patent No. 4,072,035 that is entitled as Strengthening of a Welding Seam has described this method in detail.
Known use in seam-welded tube production " weld seam annealing device " improves the mechanical property of weld seam.For at non-hardenable alloys these devices of designing of soft steel and the enterprising line operate of austenitic stainless steel for example, on the weld seam in downstream, welding source (weld source), fully be cooled to the after-applied secondary heat source of envrionment temperature at it.Use two principal features: at first, " weld seam annealing device " with the weld seam reheat to being higher than A
C3Temperature, with material austenitizing and keep certain hour again, allow slowly cooling then, be equivalent to " normalizing " heat treatment cycle; Secondly, the non-alloy that hardens is used " weld seam annealing device ".The example of " weld seam annealing " method is described in the U.S. Patent No. 3 that is entitled as Inductor for Induction Heating Apparatus, 242,299 and be entitled as the U.S. Patent No. 4 of Method For Heat-Treating Straight BeadWelding Pipes For Use in Piping Systems, in 975,128.
The U.S. Patent No. 2,293,481 that is entitled as Welding Apparatus has been described the method that produces the brittle weld seam with reduction with the U.S. Patent No. 2,262,705 that is entitled as Electric Welding.These two kinds of methods all adopt short relatively tempering circulation to the alloy that can harden, and the reheat weld seam is to improve mechanical property.Yet these methods of using on band saw blade and spot weld are different with the present invention.Use the equipment identical to come original position to carry out these methods with producing weld seam.In fact, for U.S. Patent No. 2,262,705 method spot-welding equipment must rest on the appropriate location so that quench suitably, then immediately reheat with the weld seam tempering.The most significant is to be that spot welding type, flush welding type or salient point weldering type weld seam use these methods to discontinuous welding joint.
Ordinary method for example preheats with PWHT in batches and is unsuitable for cheaply, high-quality, a large amount of production.Regrettably, these methods are not cost, time or Energy Efficient for the high production level relevant with modern manufacturing method.The ideal method will allow from fusion welding (promptly not using filler metal) or use to have the filler metal (this filler metal can harden to high-strength joint) of the intensity that matches of similar chemical constitution with the underlying metal that welds and have rapid heating concurrently and cheap air cooling circulates.
The inventor has described the method for multiple raising weld seam and HAZ ductility in following patent: the U.S. Patent No. 7,232,053 that on June 19th, 2007 authorized; The U.S. Provisional Patent Application No.60/879 that on January 10th, 2007 submitted to, 861; The U. S. application No.11/542 that on October 4th, 2006 submitted to, 970; The U. S. application No.11/526 that on September 22nd, 2006 submitted to, 258; The U. S. application No.11/519 that on September 11st, 2006 submitted to, 331; The U. S. application No.10/519 that on December 30th, 2004 submitted to, 910; The international application No.PCT/US02/20888 that on July 1st, 2002 submitted to; The U.S. Provisional Application No.60/301 that submit to June 29 calendar year 2001,970.Incorporate each piece integral body in these reference into this paper by reference.Regrettably, in addition these methods also have shortcoming.
Therefore, from productive viewpoint, hope provides at production period and can be preferred thermal treatment so that improve the mechanical property of seam welding head.Preferably, can use simple PWHT method obviously to improve the ductility of weld seam and HAZ.
Summary of the invention
In brief, according to the present invention, provide the improved method of formation steel member (include but not limited to weld tubing member).In broad terms, present invention is directed at the improved postweld heat treatment (PWHT) of the iron alloy that can harden.
The method of formation steel member of the present invention comprises the conventional weld seam that processing forms together the time in two surface-welding of the iron alloy that can harden.Form this initial weld seam by executing thermal source (being preferably conventional welding plant form), so that make the surface of adjacency have sufficiently high temperature, so that make the iron alloy fusing and form weld seam.For the iron alloy that can harden, allow weld seam to be cooled to be lower than martensitic transformation then and begin (M
S) temperature.Weld seam can be cooled to envrionment temperature.Scheme as an alternative, the martensitic transformation that weld seam can be cooled to iron alloy begins (M
S) medium temperature between temperature and the envrionment temperature.
Be cooled to be lower than martensitic transformation at weld seam and begin (M
S) after the temperature, in the postweld heat treatment process with the weld seam tempering.The martensitic transformation that weld seam is heated rapidly to the hardened iron alloy that is higher than weld seam with 10 ℃/s or bigger speed begins (M
S) temperature.Yet, weld seam is not heated to above the lower critical temperature (A of the hardened iron alloy of weld seam
C1).Importantly, with the speed rapid heating weld seam of at least 10 ℃/s, the speed of preferred 200 ℃/s.Although local heat source is preferred, can use various thermals source to apply heat to weld seam.Local heat source includes but not limited to propane or oxy-acetylene blowpipe, resistance, electric arc, laser, conduction, irradiation, convection current or high-frequency induction method.The local heat source of Miao Shuing provides heat to weld seam and neighboring region herein, but does not heat whole parts.
For the iron alloy that can harden, in case begin (M by weld seam is heated to above martensitic transformation
S) temperature but be not higher than lower critical temperature (A
C1) butt welded seam carried out tempering, then at once the weld seam air cooling do not kept soaking certain hour under the temperature.Carrying out air quenching greater than 15 ℃/minute, yet preferably be not higher than 200 ℃/second as providing by water-cooled.
But operable many kinds " iron alloy that can harden " in enforcement of the present invention comprise are thought those steel and the alloy of air hardenable.Think that the method for formation steel member of the present invention and postweld heat treatment method are specially adapted to the Martensite Stainless Steel, particularly those of 410,420 and 440 types that can harden.Because different alloys can have different lower critical temperatures, martensitic transformation begins (M
S) temperature and martensitic transformation end (M
F) temperature, and change because weld seam character will depend on Welding Design, so tempering speed, tempering outlet temperature and rate of cooling will change.
Think also that the method for formation steel member of the present invention is specially adapted to form seam welded pipe and tubing member and for producing girth seam (for example on gas tank or liquid tank).
Therefore, an object of the present invention is to provide the method for the weldable steel member of the iron alloy that formation can harden.
Other purpose of the present invention provides the modification method that forms the steel member, wherein can heat-treat during initial production so that improve the properties of its welded joints of seam weldering.
Another purpose of the present invention provides the postweld heat treatment system, and this system will improve the ductility of weld seam and HAZ and not increase the treatment time.
A further object of the present invention provides the method that forms the steel member, and it is cheap and simple relatively that this method implements.
By the detailed description below in conjunction with accompanying drawing, these and other other purpose of the present invention and advantage will be clearly for those skilled in the art.
Accompanying drawing is briefly described
But Fig. 1 is the synoptic diagram that is shown in 4 kinds of different microstructures zones that welding back observes in the heat affected zone (HAZ) of the steel of air hardenable;
But Fig. 2 runs through not carry out in advance in the Martensite Stainless Steel of air hardenable or the coordinate diagram of the microhardness of the typical weld seam of postheat treatment;
Fig. 3 is the coordinate diagram of the conventional tempered postweld heat treatment temperature curve of comparing with temperature curve of the present invention;
Fig. 4 is a schema of describing postweld heat treatment process of the present invention;
Fig. 5 is the perspective exploded view of the typical clamshell style canister assembly that is made of the housing that hardens in advance before the flange seam weldering;
Fig. 6 is the skeleton view of the typical clamshell style canister assembly that is made of the housing that hardens in advance after the flange seam weldering;
Fig. 7 is the skeleton view of the typical clamshell style canister assembly after the weldering of flange seam, has shown the local weld seam thermal treatment of carrying out with the shaping resistance heating coil;
Fig. 8 is the skeleton view of the typical clamshell style canister assembly after the weldering of flange seam, has shown the local weld seam thermal treatment of adopting used shaping resistance heating coil to carry out;
Fig. 9 is the cross-sectional side view of the typical clamshell style canister assembly after the flange seam weldering, has shown the local weld seam thermal treatment of adopting the heater coil (resistance or induction) that is positioned at clamp-on holder to carry out;
Figure 10 is the cross-sectional side view of the typical clamshell style canister assembly after the weldering of flange seam, has shown for local weld seam thermal treatment, passes the local weld seam thermal treatment that housing carries out by making electric current; With
The average result of testing for 62 times is used in maximum strain during the fracture of DIN EN 895 longitudinal stretching samples that the histogram of Figure 11 has compared the 410 groove parts welderings sample of handling according to the present invention.
Detailed Description Of The Invention
Though as shown in the accompanying drawing, the present invention allows the embodiment of various ways, but hereinafter will describe the preferred embodiments of the invention, think that promptly present disclosure is an example of the present invention and and be not intended to the present invention is limited to illustrated particular with such understanding.
The present invention includes the weld seam that processing made by high-strength steel and other alloy that can harden or the method for seam weldering member.Think that the present invention is specially adapted to change into through the seam weldering alloy of martensite weld seam and HAZ microstructure, therefore describes below and is specially adapted to such steel.Method of the present invention allows to improve the ductility of welding zone and toughness and reduces the fragility of weld seam and to hydrogen refrigeration rimose susceptibility.The present invention allows to improve mechanical strain and the distortion of welding zone (fusion area and HAZ), thereby has eliminated the needs to other for example process annealing of postwelding solution heat treatment, subcritical annealing or the stress relieving of whole member.Partial heat treatment of the present invention has been eliminated and has been changed the material property of underlying metal and the risk of microstructure, makes the present invention be suitable for welding the alloy of preceding hot mechanical treatment and can not standing heat treated those alloys of whole parts physically.
Such as in SAEJ412 standard (GENERAL CHARACTERISTICS AND HEATTREATMENTS OF STEELS) general introduction, " hardenability or may be the most important single standard of selecting steel to heat treated response.Hardenability is to determine by from being higher than transition range the quench distribution of caused hardness and the rigidity matter of the degree of depth ... term hardens and shows the hardness that can improve material by suitable processing, is usually directed to be heated to suitable austenitizing temperature and then cools off with certain minimum-rate according to alloy content.Finish if quench, then the gained tissue is a martensite ... its hardness depends on the carbon content of steel ".
As herein defined, term " alloy that can harden " is meant the steel grade and the heat treated iron alloy of response that can directly harden.In addition, " alloy that can harden " has enough carbon contents, has other alloy element concurrently, thereby forms martensitic microstructure at routine seam postwelding in fusion and HAZ." alloy that can harden " of this paper definition has the transition temperature that clearly limits, and this temperature depends on the particular chemical composition of alloy, comprising: A
C3-upper critical temperature, A
C1-lower critical temperature, M
S-Ms (martensite start) point and M
F-martensitic transformation end temp." alloy that can harden " but comprise and think those steel and the alloy of air hardenable that this is because be welded with the natural quenching cooling rate of pass greater than air quenching with seam.As defined herein, term " alloy that can harden " does not comprise those steel and the iron alloy that is considered to " low-carbon (LC) carburizing grade ", and it is only by making element injecting material surface via the surface hardening processing and thermal treatment being responded.
The alloy that the present invention's representativeness applicatory can be hardened includes but not limited to:
SAE?1030、1034、1035、1037、1038、1039、1040、1042、1043、1044、1045、1046、1049、1050、1053、1536(1036)、1541(1041)、1547(1047)、1547(1047)、1548(1048)、1551(1051)、1552(1052)
SAE?1055、1059、1060、1064、1065、1069、1070、1074、1075、1078、1080、1084、1085、1086、1090、1095、1561(1061)1566(1066)、1572(1072)
SAE?1330、1335、1340
SAE?4037、4047、4130、4135、4137、4140、4142、4145、4150、4161、4340
SAE?5046、50B40、50B44、50B46、50B50、5060、50B60、
SAE?5130、5132、5135、5140、5145、5147、5150、5155、51B60
SAE?6150
SAE?8630、8637、8640、8642、8645、8650、8655、8660、8740
SAE?81B45、86B45、94B30
SAE?9254、9255、9260
SAE?50100、51100、52100
SAE?51410、51414、51420、51431、51440A、51440B、51440C、51501
22MnB5
30MnB5
DP600
DP800
DP1000
The preferred method of the present invention comprises that the formation weld seam is to engage two surfaces of the martensitic steel that can harden.Allow weld seam to be cooled to be lower than the Ms (martensite start) point-M of weld seam
SThe temperature of weld seam can be cooled to be lower than the martensitic transformation end temp or even cool to room temperature, perhaps can be not the temperature of weld seam be cooled to be lower than martensitic transformation end temp or even cool to room temperature.As shown in Fig. 3 and Fig. 4, thereafter the weld seam of finishing is heated rapidly to the A of weld metal
C1-lower critical temperature (eutectoid temperature) perhaps is heated to above martensitic transformation and begins (M
S) the low medium temperature of temperature, and allow weld seam to carry out air cooling.As in first embodiment of called after method " A " among Fig. 3 and as temperature with respect to the block diagram of time on shown in the dotted line, weld seam is heated to A
C1Temperature but be no more than A
C1-lower critical temperature.This embodiment will allow the maximum of weld seam softening, because all martensites will stand maximum high tempering.As in second embodiment of called after method " B " among Fig. 3 and as temperature with respect to the block diagram of time on shown in the dotted line, be heated to the toughness that tensile strength that medium temperature can not overbate weld seam by reducing fragility and excessively do not reduce weld seam is used to improve weld seam.
To carry out the rapid heating of weld seam greater than the speed of 10 ℃/s.Preferably, carry out the rapid heating of weld seam more apace with about 200 ℃/s.At once carrying out air quenching (not keeping the soaking time under the temperature) after this rapid heating.Air cooled by being heated rapidly to " at once " change mean should be broadly interpreted as relatively comprised several seconds or even the tour of several minutes, it can be that manufacturing processed is incidental.Yet air cooled by being heated rapidly to " at once " tour, do not mean the isothermal soaking time of the obvious change that comprises the crystal microstructure that allows the generation iron alloy, the alligatoring and the recrystallize of described Change Example such as carbon precipitate.The preferred quench rates consistent with air cooling is greater than 15 ℃/minute but less than 200 ℃/s.
The thermal source of available moulding in the present invention perhaps heats (as stitch the situation of weldering continuously on milling train) piecemeal with the whole heating of weld seam.Use any local heat source in the various local heat sources that heat is applied to weld seam, described thermal source includes but not limited to propane or oxy-acetylene blowpipe, resistance, electric arc, laser, conduction, irradiation, convection current or high-frequency induction.Use term " part " to describe that regional area to parts provides heat herein but the thermal source that do not heat whole parts for example provides by stove or baking oven.In processed continuously situation, for example in the production of seam welded pipe and tubing, for than large pipeline, optionally heating local welded seam area will be the most effective embodiment.Scheme as an alternative for example can remain in the spirit of the present invention by the whole circumference of water back circlewise with helical induction coil or other means.Think that this annular heating is suitable for less pipeline and pipe diameter.With reference to Fig. 5 and 6, in preferred embodiments, can heat whole welding line simultaneously, this is applicable to comprising the alloy fuel jar that for example can harden or the various structures of the girth seam on the liquid tank.
Except that the hardness that changes welding zone (promptly reduce and/or regulate the martensitic amount that exists in the welding region microstructure), this method has weakened several other HAZ contribution factors that ftracture, and comprising:
● with this method heating steel the time, allow hydrogen diffusion and the release of other time.When that stand to apply or remaining tensile stress, this residual hydrogen is hydrogen refrigeration rimose reason in the martensitic microstructure.
● owing to shrinkage strains and the stress eliminated along the thermal gradient of the reduction of welding bead length in the weld seam.
● improve ductility and the toughness of fusion area and HAZ.
● make any martenaging martempering that forms among weld seam and the HAZ.
As shown in Fig. 7 and 8, can use the resistance heating coil of shaping to come partial heat treatment to center on the weld seam of whole jar of periphery.Heater coil can be from the top side, bottom side or both sides apply and place and remain on the appropriate location by directly contact or leave weld face with weld face, up to reaching peak temperature.Remove coil then and allow the weld seam air cooling to room temperature.Atmosphere does not need protection; Yet, if necessary, can in non-oxidizing atmosphere, carry out this processing.
With reference to Fig. 9 and 10, scheme as an alternative uses the ruhmkorff coil that is shaped or flame or other method that heat is applied to weld seam.Heater coil can be packed into (Fig. 9) in the pressing machine die member, it suppresses weld seam warpage takes place during handling.In another embodiment of shown heat treated, electric current is delivered to another parts from parts in Figure 10, and the weld seam resistive heating is arrived suitable temperature.
The Typical automotive structural applications that needs seam to weld the hardenable alloys of hardening in advance comprises vehicle chassis component, A, B and C column, roof rai, carline, impact beam and collision bumper.The size of final vehicle body component and amplitude stop any full member post-weld stress to eliminate processing.Postweld heat treatment method of the present invention is ideally suited in the joint performance of the welded condition that improves these or similar type purposes.
In practice, but the initial testing result of air hardenable Martensite Stainless Steel just finds to have significant ductility and tough property improvement according to the weld seam that above-mentioned first and second embodiments are handled when comparing with the welded condition sample.For example, on the seam weldering test band of the use 410 type stainless steels (UNS41000, SAE51410) of 0.5mm, 1.0mm and 2.0mm thickness, test with the present invention.Linear-seam weldering test fixer is designed to the test band is welded from dock GTAW moltenly with 60 inchages, partly chooses test sample from the center stable state of weld seam thus.Implement the single-sided linear ruhmkorff coil according to the present invention in the downstream of GTAW torch body.Use noncontact 3.9 mum wavelength infrared pyrometers to obtain the direct surface temperature measurement result.
For 410 type stainless steels, allow weld seam to be cooled to about 180 ℃, be lower than Ms (martensite start) point-M
S, also be lower than martensitic transformation end temp-M
f, they are respectively about 330 ℃ and 230 ℃.The weld seam of finishing is heated rapidly to about 650 ℃ then, just is lower than and is about 675 ℃ lower critical temperature-A
C1, and allow its air cooling at once.As drawn along as shown in Figure 11 of the maximum elongation rate of weld seam (longitudinal stretching) direction, carry out tempering by the method according to this invention, the remarkable improvement that seam weldering sample shows weld seam and HAZ ductility.See maximum benefit on thicker test band, this is that heat treating method of the present invention has alleviated described constraint and unrelieved stress because thicker specification applies seam welding head constraint largely and therefore applies higher unrelieved stress.When handling different-alloy, execute the A that is heated to weld seam
C1-lower critical temperature (eutectoid temperature) or can provide the different mechanical propertys of welding zone to lower medium temperature, and its selection will be depended on employed material and required mechanical property.
The present invention is ideally suited in all seam welderings and handles for example Laser Welding, electric-resistance seam-welding and electric-arc welding.Except that from the melting welding seam, the present invention also is ideal for handling the weld seam that uses the weld filler alloy that can harden in order to the fragility that reduces fusion area and HAZ.Last temperature threshold, A
C1-lower critical temperature (eutectoid temperature) (ferrite and carbide are stable when being lower than this temperature) and M
S-Ms (martensite start) point all depends on the chemical constitution of weld seam and base alloy.Naturally cooling speed depends on material thickness, joint geometry, types of alloys and envrionment conditions.
Though illustrate and described some particular forms of the present invention, will be clear that, can make various changes and do not deviate from the spirit and scope of the present invention.Therefore, except that following claims, the present invention is not intended to be restricted.According in order to allow those skilled in the art understand the present invention, to reproduce the present invention and implement the such viewpoint of the present invention and described the present invention, and determine its present preferred embodiment, we ask for protection as follows:
Claims (13)
1. form the method for steel member, comprise step:
The first surface of the iron alloy that can harden is provided;
The second surface of the iron alloy that can harden is provided;
Described first surface is placed near described second surface;
, described first surface is seam welded to described second surface by applying first thermal source so that thereby described first surface and described second surface are higher than their fusing point formation weld seam to described first surface and described second surface with sufficiently high temperature;
Make described weld seam be cooled to be lower than the Ms (martensite start) point of the described iron alloy that hardens;
After the described step of the Ms (martensite start) point that described weld seam is cooled to be lower than the described iron alloy that hardens, described weld seam is carried out tempering, and described tempering comprises and with 10 ℃/second or bigger speed described weld seam is heated to above Ms (martensite start) point but is not higher than the lower critical temperature of the described iron alloy that hardens; With
After described weld seam is carried out the described step of tempered with 15 ℃/minute or the bigger described weld seam of speed air cooling.
2. the method for the formation steel member of claim 1 is wherein implemented described weld seam is carried out the described step of tempered with 10 ℃/second to 200 ℃/second speed, and implements the described step of the described weld seam of air cooling with 15 ℃/minute to 200 ℃/second speed.
3. the method for the formation steel member of claim 1 is wherein carried out described weld seam the described step of tempered and is comprised and utilize local heat source to heat described weld seam.
4. the method for the formation steel member of claim 3 is wherein implemented described weld seam is carried out the described step of tempered with 10 ℃/second to 200 ℃/second speed, and implements the described step of the described weld seam of air cooling with 15 ℃/minute to 200 ℃/second speed.
5. the method for the formation steel member of claim 1, but the Martensite Stainless Steel that the wherein said iron alloy that hardens is an air hardenable, this stainless steel has the carbon content that is equal to or greater than 0.08 weight %.
6. the method for the formation steel member of claim 1, wherein each described iron alloy that hardens Martensite Stainless Steel that is 410,420 or 440 types.
7. the method for the formation steel member of claim 1, it comprises that also with described steel member roll forming be desired shape, with described first surface and second surface welds together and described weld seam carried out the tempered step after carry out described roll forming step.
8. the method for the formation steel member of claim 7, wherein said steel member is a tubing, and described first surface defines first edge of roll forming band of iron alloy and second edge of the roll forming band that described second surface defines iron alloy.
9. form the method for steel member, comprise step:
The first surface of the iron alloy that can harden is provided;
The second surface of the iron alloy that can harden is provided;
Described first surface is placed near described second surface;
, described first surface is seam welded to described second surface by applying first thermal source so that thereby described first surface and described second surface are higher than their fusing point formation weld seam to described first surface and described second surface with sufficiently high temperature;
Make described weld seam be cooled to be lower than the Ms (martensite start) point of the described iron alloy that hardens;
After the described step of the Ms (martensite start) point that described weld seam is cooled to be lower than the described iron alloy that hardens described weld seam is carried out tempering, described tempering comprises and with 10 ℃/second to 200 ℃/second speed described weld seam is heated to above Ms (martensite start) point with local heat source but is not higher than the lower critical temperature of the described iron alloy that hardens; With
After described weld seam is carried out the described step of tempered with 15 ℃/minute to 200 ℃/second the described weld seam of speed air cooling at once.
10. the method for the formation steel member of claim 9, but the Martensite Stainless Steel that the wherein said iron alloy that hardens is an air hardenable, this stainless steel has the carbon content that is equal to or greater than 0.08 weight %.
11. the method for the formation steel member of claim 9, wherein each described iron alloy that hardens Martensite Stainless Steel that is 410,420 or 440 types.
12. the method for the formation steel member of claim 9, it comprises that also with described steel member roll forming be desired shape, with described first surface and second surface welds together and described weld seam carried out the tempered step after carry out described roll forming step.
13. the method for the formation steel member of claim 12, wherein said steel member is a tubing, and described first surface defines first edge of roll forming band of iron alloy and second edge of the roll forming band that described second surface defines iron alloy.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US88075707P | 2007-01-17 | 2007-01-17 | |
| US60/880,757 | 2007-01-17 | ||
| PCT/US2008/000586 WO2008088834A1 (en) | 2007-01-17 | 2008-01-17 | Method for improving the performance of seam-welded joints using post-weld heat treatment |
Publications (2)
| Publication Number | Publication Date |
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| CN101622365A true CN101622365A (en) | 2010-01-06 |
| CN101622365B CN101622365B (en) | 2012-11-14 |
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| CN2008800067150A Expired - Fee Related CN101622365B (en) | 2007-01-17 | 2008-01-17 | Method for improving the performance of seam-welded joints using post-weld heat treatment |
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| Country | Link |
|---|---|
| EP (1) | EP2126145A1 (en) |
| JP (1) | JP2010516471A (en) |
| KR (1) | KR20090112705A (en) |
| CN (1) | CN101622365B (en) |
| WO (1) | WO2008088834A1 (en) |
Cited By (7)
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| CN101786213A (en) * | 2010-03-26 | 2010-07-28 | 哈尔滨工业大学 | Method for controlling generation of cold crack in welding process based on electromagnetic induction heating |
| CN101805822A (en) * | 2010-04-14 | 2010-08-18 | 攀钢集团冶金工程技术有限公司 | Thermal treatment method of 15CrMoG steel annular welding line |
| CN103028851A (en) * | 2012-11-29 | 2013-04-10 | 中联重科股份有限公司 | Welding method, thermal treatment device and welding system |
| CN104080568A (en) * | 2011-12-20 | 2014-10-01 | Skf公司 | Method for manufacturing a steel component by flash butt welding and a component made by using the method |
| CN106167882A (en) * | 2015-05-19 | 2016-11-30 | 福特全球技术公司 | For the method strengthening the service structure performance of metal plate component |
| CN108723560A (en) * | 2018-07-03 | 2018-11-02 | 华北水利水电大学 | Improve the heat treatment method of high strength weld joints low-temperature flexibility |
| CN110592362A (en) * | 2019-10-25 | 2019-12-20 | 无锡市华立石化工程有限公司 | Postweld heat treatment method for 304L welding part of liquid nitrogen storage tank |
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| KR101359221B1 (en) | 2011-09-30 | 2014-02-05 | 주식회사 포스코 | Method for improving pitting corrosion resistance in welds through surface modification and stainless steel comprising the welds |
| MX2016006485A (en) | 2013-11-25 | 2016-08-05 | Magna Int Inc | Structural component including a tempered transition zone. |
| KR102010080B1 (en) * | 2017-12-26 | 2019-10-21 | 주식회사 포스코 | Heat treating method for welding part of steel plate |
| FR3086671B1 (en) * | 2018-09-27 | 2021-05-28 | Psa Automobiles Sa | PROCESS FOR THERMAL TREATMENT OF annealing or reshuffling of weld spots by induction heating |
| BR112021009133B1 (en) * | 2018-11-19 | 2023-05-09 | Arcelormittal | WELDING METHOD |
| CN109783880A (en) * | 2018-12-21 | 2019-05-21 | 中煤北京煤矿机械有限责任公司 | Application method of the welding simulation in hydraulic support structural member |
| KR102154624B1 (en) * | 2019-01-11 | 2020-09-10 | 울산대학교 산학협력단 | Apparatus for additive manufacturing high strength materials for punch dies |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS62227040A (en) * | 1986-03-28 | 1987-10-06 | Nippon Steel Corp | Improvement of resistance to impact fracture of weld zone of rail |
| US7475478B2 (en) * | 2001-06-29 | 2009-01-13 | Kva, Inc. | Method for manufacturing automotive structural members |
| JP2005531414A (en) * | 2001-06-29 | 2005-10-20 | マッククリンク，エドワード，ジェイ． | Seam welded air quenchable steel pipe |
| FR2834722B1 (en) * | 2002-01-14 | 2004-12-24 | Usinor | MANUFACTURING PROCESS OF A COPPER-RICH CARBON STEEL STEEL PRODUCT, AND THUS OBTAINED STEEL PRODUCT |
| JP4390576B2 (en) * | 2003-03-04 | 2009-12-24 | 株式会社小松製作所 | Rolling member |
| US7588837B2 (en) * | 2005-04-29 | 2009-09-15 | The Timken Company | Welding together low and high carbon steels |
-
2008
- 2008-01-17 KR KR1020097017097A patent/KR20090112705A/en not_active Application Discontinuation
- 2008-01-17 CN CN2008800067150A patent/CN101622365B/en not_active Expired - Fee Related
- 2008-01-17 EP EP08724553A patent/EP2126145A1/en not_active Withdrawn
- 2008-01-17 JP JP2009546418A patent/JP2010516471A/en active Pending
- 2008-01-17 WO PCT/US2008/000586 patent/WO2008088834A1/en active Application Filing
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN101786213A (en) * | 2010-03-26 | 2010-07-28 | 哈尔滨工业大学 | Method for controlling generation of cold crack in welding process based on electromagnetic induction heating |
| CN101786213B (en) * | 2010-03-26 | 2012-05-23 | 哈尔滨工业大学 | Method for controlling generation of cold crack in welding process based on electromagnetic induction heating |
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| CN104080568A (en) * | 2011-12-20 | 2014-10-01 | Skf公司 | Method for manufacturing a steel component by flash butt welding and a component made by using the method |
| CN103028851A (en) * | 2012-11-29 | 2013-04-10 | 中联重科股份有限公司 | Welding method, thermal treatment device and welding system |
| CN106167882A (en) * | 2015-05-19 | 2016-11-30 | 福特全球技术公司 | For the method strengthening the service structure performance of metal plate component |
| CN108723560A (en) * | 2018-07-03 | 2018-11-02 | 华北水利水电大学 | Improve the heat treatment method of high strength weld joints low-temperature flexibility |
| CN108723560B (en) * | 2018-07-03 | 2021-03-19 | 华北水利水电大学 | Heat treatment method for improving low-temperature toughness of high-strength welded joint |
| CN110592362A (en) * | 2019-10-25 | 2019-12-20 | 无锡市华立石化工程有限公司 | Postweld heat treatment method for 304L welding part of liquid nitrogen storage tank |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2010516471A (en) | 2010-05-20 |
| KR20090112705A (en) | 2009-10-28 |
| WO2008088834A1 (en) | 2008-07-24 |
| CN101622365B (en) | 2012-11-14 |
| EP2126145A1 (en) | 2009-12-02 |
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