WO2009104798A1 - Joint soudé qui présente d'excellentes caractéristiques de résistance à la fatigue, et procédé de réalisation associé - Google Patents

Joint soudé qui présente d'excellentes caractéristiques de résistance à la fatigue, et procédé de réalisation associé Download PDF

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Publication number
WO2009104798A1
WO2009104798A1 PCT/JP2009/053302 JP2009053302W WO2009104798A1 WO 2009104798 A1 WO2009104798 A1 WO 2009104798A1 JP 2009053302 W JP2009053302 W JP 2009053302W WO 2009104798 A1 WO2009104798 A1 WO 2009104798A1
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Prior art keywords
weld
welded joint
steel
less
welded
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PCT/JP2009/053302
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English (en)
Japanese (ja)
Inventor
野瀬哲郎
白幡浩幸
島貫広志
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新日本製鐵株式会社
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Application filed by 新日本製鐵株式会社 filed Critical 新日本製鐵株式会社
Priority to JP2009516761A priority Critical patent/JP4719297B2/ja
Priority to KR1020097018596A priority patent/KR101134158B1/ko
Priority to CN2009800002199A priority patent/CN101678511B/zh
Publication of WO2009104798A1 publication Critical patent/WO2009104798A1/fr

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Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • B23K31/00—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups
    • B23K31/12—Processes relevant to this subclass, specially adapted for particular articles or purposes, but not covered by only one of the preceding main groups relating to investigating the properties, e.g. the weldability, of materials
    • 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
    • B23K9/02—Seam welding; Backing means; Inserts
    • B23K9/025—Seam welding; Backing means; Inserts for rectilinear seams
    • 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
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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

Definitions

  • the present invention relates to a welded joint having excellent fatigue resistance and a method for producing the welded joint, and more particularly, to a welded joint capable of improving the reliability of the welded structure and extending the life by adopting the welded structure. And its manufacturing method.
  • FIG. 6 is a schematic cross-sectional view showing an example of the welded joint 1, and shows a situation where the steel materials 2 and 2 ′ are joined by the weld metal 3.
  • the fatigue strength of the weld is significantly lower than the fatigue strength of the base metal, mainly because of the significant concentration of stress at the weld toes 6, 6 'and the tensile residual stress at the weld toes. It is known that the crystal grains are coarsened in the weld heat affected zone 4.
  • Japanese Patent Laid-Open No. 2 0 3 -1 1 1 3 4 1 8 proposes a method for improving the fatigue life of a metal material by performing ultrasonic impact treatment on a place where the fatigue of the metal material is a problem. It is disclosed that by applying ultrasonic impact treatment, the weld toe is deformed to have a predetermined curvature, and stress concentration is alleviated.
  • Japanese Patent Laid-Open No. 2 0 4-1 3 0 3 1 an ultrasonic vibration terminal is provided in the vicinity of a lap fillet weld toe where two steel plates are overlapped and the ends are welded.
  • a method for improving fatigue strength by hitting with discloses a punch for pinning, a driving means for rotationally driving the punch, and punching for hitting the rotating punch against a material to be peened.
  • a method of punching a material to be peened and applying local surface hardening and residual stress with an apparatus having means has been proposed. Disclosure of the invention
  • ultrasonic impact treatment is an effective way to improve fatigue strength.
  • the combination of conventional steel and welding material that is, the combination of base metal and weld metal is inappropriate, and the effect of ultrasonic shock treatment is not fully utilized. It could not be said that the fatigue strength of the welded joint was sufficiently improved.
  • an object of the present invention is to provide a welded joint in which the effect of ultrasonic impact treatment is more efficiently exhibited and the fatigue strength is further improved, and a method for manufacturing the same.
  • the present invention has been made to solve the above-described problems.
  • Welded joints that improve the fatigue resistance efficiently by controlling the ratio between the hardness of the weld metal heat affected zone of the weld metal part and the base metal and the hardness of the base metal and applying ultrasonic shock treatment, and its manufacturing method It is to provide.
  • the gist is as follows.
  • the chemical composition of the steel material of the welded joint is, by mass%, C: 0.03 to 0.25%, Si: 0.01 to: 1.0%, Mn: 0.1 ⁇ 2.0%, P: 0.04% or less, S: 0.05% or less, the balance consists of Fe and inevitable impurities, and the chemical composition of the weld metal part is mass% , C: 0.0 3 to 0.15%, S i: 0.:! To 0.8%, M n: 0.3 to 1.6%, P: 0.0 3% or less, S: 0.03% or less, Ni: 0.01 to 3.0%, Cr: 0.01 to: 1.5%, Mo:
  • the weld joint having excellent fatigue resistance according to (1), characterized by containing 0.01 to 0.8% and the balance being Fe and inevitable impurities.
  • the steel material of the welded joint is further in mass, Cr: 0.01 to 1.5%, Ni: 0.01 to 3.0%, Mo: 0.01 ⁇ 0.8%, T i: 0.0. 0 2 ⁇ 0.5%, N b: 0. 0 0 2 ⁇ 0.2% 1 type or 2 types or more (2 ) Welded joints with excellent fatigue resistance.
  • the relationship between the average hardness of the steel, weld metal and weld heat affected zone of the welded joint is determined in advance for the combination of steel, welding material and welding conditions.
  • the welding material and welding conditions for the welded joint steel were selected so that the average hardness of the weld metal and weld heat-affected zone was 15 to 50% higher than the average hardness of the steel.
  • the weld toe of the welded joint is subjected to ultrasonic impact treatment, and the radius of curvature r in the cross section perpendicular to the weld line is 1.0 to 10 mm, from the steel surface in the thickness direction.
  • a method for producing a welded joint with excellent fatigue resistance characterized by forming an ultrasonic impact treatment mark having a depth d of 1.0 mm or less.
  • the chemical composition of the steel material of the welded joint is mass%, C: 0.03 to 0.25%, Si: 0.01 to: L.0%, Mn: 0.:! ⁇ 2.0%, P: 0.04% or less, S: 0.05% or less, the balance is Fe and inevitable impurities, the chemical composition of the weld metal part is by mass, C : 0.0 3 to 0.15%, S i: 0.1 to 0.8%, M n
  • the steel material of the welded joint is, in mass%, Cr: 0.01 to 1.5%, Ni: 0.01 to 3.0%, Mo: 0.0 1 to 0.8%, T i: 0. 0 0 2 to 0.5%, N b: 0. 0 0 2 to 0.5%, 1 type or 2 types or more
  • the ultrasonic shock treatment is performed at a power of 0.01 to 4 kW with a vibration terminal excited at a frequency of 20 kHz to 50 kHz.
  • the ultrasonic impact treatment is performed using a rod-shaped vibration terminal having a radius of curvature of a cross section in the axial direction of a tip portion of the vibration terminal of 1.0 to 10.0 mm.
  • the average hardness of the weld metal part and the average hardness of the welded heat-affected zone of the steel material (base material) are 15 to 50% higher than the average hardness of the steel material (base material).
  • the fatigue strength of both the weld metal and weld heat affected zone of the welded joint is higher than the fatigue strength of the base metal, and the occurrence of fatigue cracks in these parts is greatly suppressed. It is done.
  • a predetermined ultrasonic impact mark is formed at the weld toe of this weld joint by ultrasonic impact treatment, and the steep shape is relaxed as the radius of curvature of the toe increases.
  • FIG. 1 (a) is a schematic cross-sectional view showing a situation where ultrasonic impact marks are formed on the welded joint of the present invention.
  • FIG. 1 (b) is a schematic cross-sectional view of the shape of the ultrasonic impact scar formed on the welded joint of the present invention.
  • Fig. 2 (a) is a schematic plan view showing an example of a welded joint having an ultrasonic impact scar of the present invention, and is a diagram showing a case of butt welding.
  • FIG. 2 (b) is a schematic plan view showing another example of a welded joint having an ultrasonic impact scar according to the present invention, and is a diagram showing a case of fillet welding.
  • FIG. 3 is a diagram for explaining an example of a hardness measurement method according to the present invention.
  • FIG. 4 is a partially cutaway schematic diagram showing an example of an ultrasonic impact treatment apparatus.
  • FIG. 5 (a) is a perspective view showing an outline of a plate-like test body, and shows a case of a cruciform joint.
  • FIG. 5 (b) is a perspective view showing an outline of the plate-like test body, and is a view showing a case of a rotating joint.
  • FIG. 5 (c) is a perspective view showing an outline of the plate-like specimen, and is a view showing a case of a butt joint.
  • Fig. 6 is a schematic cross-sectional view showing the situation of a conventional welded joint.
  • BEST MODE FOR CARRYING OUT THE INVENTION As a result of studying the improvement of fatigue resistance by ultrasonic impact treatment on the welded part of welded joints, this includes an increase in the radius of curvature of the weld toe, the introduction of compressive residual stress around the weld toe, and crystallization. Grain refinement contributes in an overlapping manner, and the stress concentration coefficient at the toe becomes smaller as the radius of curvature becomes larger, and cracks are suppressed by making the grains finer. In addition, it has been found that fatigue resistance is improved by suppressing crack growth by compressive residual stress.
  • the strength of the weld metal part is set to the strength (yield strength) level of the steel material (base material).
  • Welding materials have been selected to be equivalent or about 10% higher.
  • the strength of the weld metal part is not so high as compared to the strength of the steel (base metal), and the compressive residual stress after ultrasonic impact treatment around the weld part, especially around the weld toe part. This was not enough to improve the fatigue resistance of welded joints. If ultrasonic shock treatment was not applied, the strength of the weld metal part was reduced to steel. When the strength (yield strength) of the material (base material) exceeds 10%, the strain concentration at the weld toe becomes conspicuous due to the high strength difference between the two parts. High fatigue properties could not be obtained.
  • the hardness of both the weld metal part and the weld heat-affected zone of the weld joint is 15 to 50% higher than that of the steel material (base metal), and further, at the weld toe.
  • the average hardness of the weld metal part and the average hardness of the heat-affected zone is 15 to 50% higher than the average hardness of the steel (base metal), if it is less than 15%, there will be sufficient residual compression in the weld.
  • the average hardness of the weld metal part and the weld heat-affected zone is 15 to 50% higher than the average hardness of the steel (base metal). Preferably, it is 20% to 50%.
  • Average hardness of weld metal and weld heat affected zone of welded joint In order to increase the hardness of the steel material (base material) by 15 to 50%, after considering the strength characteristics (hardness level) of the base material and the strength (hardness) level of the weld heat affected zone, This is achieved by selecting and welding a welding material in which the weld metal part has the strength (hardness) level as described above.
  • the hardness of the weld metal part and the weld heat affected zone of the formed welded joint are often affected by welding conditions such as welding heat input and cooling rate. It is preferable to select a welding material.
  • the hardness of the weld heat affected zone in welded joints varies depending on the type of steel, and is generally higher than the hardness of the steel (base metal). There are some things that get lower. Therefore, in order to increase the hardness of the weld heat affected zone by 15 to 50% higher than that of the steel (base metal), it is necessary to select appropriately considering the composition and structure of the steel. Since the strength level (hardness level) is easily affected by welding conditions such as heat input and cooling rate, the strength characteristics of the weld heat-affected zone and the steel material (base material) are grasped including the welding conditions. The welding material shall be selected.
  • steel materials of a strength level where fatigue resistance is a problem include steel materials with a tensile strength of 400 MPa to 80 OMPa class, and their chemical composition is mass%, and C: 0.0 3 to 0.25%, S i: 0.0 1 to: 1.0%, M n: 0.1 to 2.0%, P: 0.0 4% or less, S: 0.0 5% It is preferable that the following is contained, and the balance consists of Fe and inevitable impurities.
  • C is an element necessary to secure the strength of the steel (base metal) and the weld heat affected zone, and 0.03% or more is necessary for that purpose. However, if it exceeds 0.25%, the toughness of the steel material will deteriorate the weld crack resistance. Therefore, the range is 0. 0 3 0. 25%. More preferably, it is 0.05 0.2%.
  • S i S i is a deoxidizing element and an element effective for securing the strength of the base metal and the weld heat-affected zone. However, if it is less than 0.01%, deoxidation is insufficient and the strength is secured. Disadvantageous. If it exceeds 1.0%, a coarse oxide is formed, and ductility leads to deterioration of toughness. Therefore, the range of S i is 0 • 0 1 L. 0%. More preferably 0.2 1
  • M n is an element required to secure the strength and toughness of the base metal and the weld heat affected zone. * It is necessary to contain at least 0.1%, but if it is contained excessively, The base metal toughness, weld toughness, and weld cracking properties deteriorate due to formation and grain boundary embrittlement, so the upper limit is 2.0%, and the range is set to 0.1 2.0%. More preferably 1. 0 2. 0%
  • P P is an impurity element, and it is preferable to reduce it as much as possible because it deteriorates ductility and toughness. More preferably, it is 0.02% or less.
  • S S is an impurity element, and it is preferable to reduce it as much as possible because it deteriorates ductility and toughness.
  • the material deterioration is not so great that the allowable amount is 0.05% or less. More preferably, 0.0
  • the steel material can contain one or more of CrNi, Mo, TiNb as necessary.
  • C r is an element effective for improving the strength, and 0.0 1% or more is necessary to exert this effect. If it exceeds 1.5%, the toughness is reduced and the weldability is increased. The range is 0. 0 1 1 5%. More preferably, it is 0.0 to 1.0%.
  • Ni is effective in improving the strength of the base metal. If the Ni content is less than 0.01%, the effect is not sufficient, and if it exceeds 3.0%, the weldability deteriorates. For this reason, the range is 0.0 1 to 3.0%. More preferably, it is 0.01 to 10%.
  • M o is an element that is extremely effective in improving strength and hardness. In order to exert the effect, a force that is required to be 0.1% or more is 0.1%.
  • T i T 1 is an element effective for increasing the strength by precipitation strengthening and improving the toughness by refining the structure. 0.0 to achieve this effect
  • 0.02 to 0.5% More preferably, 0.0.02 to 0.3.
  • N b is an element effective for increasing the strength by precipitation strengthening and improving the toughness by refining the structure, as is the case with T i. In order to exert this effect, it is necessary to add 0.002% or more. On the other hand, if it exceeds 0.2%, weld cracking tends to occur and the weldability deteriorates. Therefore, the range is from 0.0 0 2 to 0.2%. More preferably, it is 0.02 to 0.15%.
  • the weld metal part has a chemical composition of mass%, C: 0.03 to 1.5%, Si: 0.:! To 0.8%, Mn: 0.3 to: 1. 6%, P: 0.03% or less, S: 0.03% or less, Ni: 0.01 to 3.0%, Cr: 0.01 to: L.5%, Mo : It is preferable to contain 0.01 to 0.8%, with the balance being Fe and inevitable impurities. The reason for limitation will be described below.
  • C C is an element necessary for ensuring the strength and hardness of the weld metal part, and is required to be 0.03% or more. However, if it exceeds 0.15%, weld toughness and weld cracking resistance may decrease, so the range is set to 0.03 0.15%. Good looking ⁇ is 0. 0 6 0
  • S 1 S 1 has the effect of lowering the oxygen level of the weld metal as a deoxidizing element.
  • the amount of Si in the weld metal part is less than 0.1%, the deoxidation effect cannot be obtained sufficiently, and the wettability of the welded end part is lowered. If it exceeds 0.8%, the toughness of the weld will deteriorate, so the range should be 0.10.8%. More preferably, it is 0.20.6%.
  • M n M n is known as an element that increases strength and promotes solid solution of N.
  • the lower limit of M n 0.3%, is the lowest value at which the effect of securing strength can be obtained.
  • excessive addition causes the deterioration of the toughness of the weld metal and the precipitation of intermetallic compounds that are harmful to the corrosion resistance, so it is preferably 1 to 6% or less, and the range is 0.3 to 1.6%. More preferably, it is 1.0.1.5%.
  • P and S P and S are impurity elements, and they are preferably reduced as much as possible because they deteriorate ductility and toughness.
  • the material is not greatly deteriorated, and the allowable amount is 0.03% or less. More preferably, it is 0.015% or less.
  • Ni Ni is effective in improving the toughness of the weld and lowering the phase transformation temperature from the austenite phase to the martensite phase during welding cooling. If the amount of Ni in the weld metal is less than 0.01%, there is no effect in improving toughness, and if it exceeds 3.0%, weldability deteriorates, so the range is 0.01. 3. 0%. More preferably, it is 0.01 to 2.5%.
  • C r is an element effective for improving the strength and hardness. In order to exert the effect, the strength exceeds 0.0 1.5%, which is necessary for more than 0.01%.
  • the hardness is too high and causes a decrease in toughness, so the range is from 0.01 to 1.5%. More preferably, it is 0.01 to: I.0%.
  • M o is an element that is extremely effective in improving strength and hardness, and in order to exert the effect, it is necessary to be not less than 0.01%, but if it exceeds 0.8%, The range is from 0.01 to 0.8% because the hardness becomes too high and the toughness is reduced. More preferably, it is 0.01 to 0.6%.
  • the strength characteristics of the weld metal part, weld heat-affected zone and base metal of the welded joint are evaluated as average hardness. This is a limited range in which the present invention is called a weld zone. It is specified to evaluate the characteristics.
  • Fig. 3 is a schematic diagram showing a cross section perpendicular to the weld line of the welded portion in an example of a weld joint in which the steel materials 2 and 2 'are welded with the weld metal portion 3 interposed therebetween.
  • the metal structure is revealed with a nital etchant and evaluated by the Vickers hardness measured by the following method.
  • the picker hardness is determined in accordance with the Vickers hardness test method specified in JISZ 2 2 4 4.
  • intersection point c between the above line L and the melt line 5 is defined as a base, and it is used as a trough, with an interval of 0.5 mm toward the weld metal part 3 side and a pushing load of 1 kg.
  • the hardness HVI is measured, and the average value of 6 points is taken as the average hardness of the weld metal part 3.
  • steel plate 2 or 2 ' is based on the point moved from the intersection C or C' between the line L and the fusion line 5 to the 10mm steel plate 2 or 2 side. 0 "on the side
  • the average hardness of steel, weld metal, and weld heat-affected zone is determined by measuring 6 points each.
  • the average hardness is not limited to 6 points. If there are enough measurement points,
  • the indentation load is not limited to 1 kg, and it is needless to say that the average hardness can be calculated by selecting an appropriate load such as 4 kg, 5 k or 500 g as required.
  • FIG. 1 (a) and FIG. 1 (b) are schematic views showing the shape of a cross section perpendicular to the weld line of the weld joint of the present invention.
  • Fig. 1 (a) shows the situation where an ultrasonic shock mark is formed
  • Fig. 1 (b) is a schematic diagram showing the shape of the formed ultrasonic shock mark.
  • Fig. 1 (a) and Fig. 1 (b) in welded joint 1, steel materials (base materials) 2 and 2 'are joined by weld metal 3, and weld heat affected zone 4 is formed on the steel material side of melt line 5.
  • Ultrasonic impact marks 7 are formed in a region including the weld toe 6 between the weld metal 3 and the steel material 2 by the impact treatment by the vibration terminal 8 using ultrasonic waves. As shown in Fig. 1 (b), this ultrasonic impact mark 7 has a radius of curvature r in the cross section perpendicular to the weld line of 1.0 to 10.0 mm and a depth d from the steel surface in the thickness direction. Is less than 1.0 mm.
  • the radius of curvature r of the ultrasonic impact scar 7 applied to the weld toe 6 is less than 1.0 mm, it is not sufficient to alleviate the stress concentration on the weld and it cannot be expected to improve fatigue resistance. .
  • the radius of curvature r exceeds 10.O m m, the effect of relaxing the stress concentration is saturated, no further improvement in fatigue resistance is obtained, and a longer processing time is required. Therefore, the radius of curvature r of the ultrasonic impact scar is 1.0 to: L O .O mm. Preferably, it is' 1.5-5. O mm.
  • the ultrasonic impact scar 7 is formed around the toe 6 but is preferably formed to include at least a part of the weld metal 3 and the weld heat affected zone 4. It is also preferable to select the ultrasonic impact position and the radius of curvature of the formed ultrasonic impact mark in consideration.
  • the depth in the thickness direction of steel material 7 shall be 1.0 mm or less. Preferably, it is 0.5 mm or less.
  • the ultrasonic impact scar is shown only on one welded end 6 but it is not on the other welded end 6 '. Needless to say, it is preferable to form the film.
  • the weld joint of the welded joint in which the average hardness of the weld metal portion and the average hardness of the weld heat affected zone is 15 to 50% higher than the average hardness of the steel (base material).
  • Ultrasonic impact treatment is applied to the end, and in a cross section perpendicular to the welding line, the radius of curvature r is 1.0 to 10.0 mm, and the depth d from the steel surface in the thickness direction is 1.0 mm or less. A certain ultrasonic shock mark is formed.
  • the method for manufacturing a welded joint in which the average hardness of the weld metal part and the average hardness of the heat affected zone is 15 to 50% higher than the average hardness of the steel (base metal) is as follows. Considering the strength characteristics of the base metal) and the weld heat affected zone, including the welding conditions such as heat input and cooling rate, the weld metal and weld strips with the above-mentioned hardness levels are included in the weld metal part. This can be achieved by selecting and welding.
  • the relationship between the average hardness of the welded steel, weld metal and weld heat affected zone is determined in advance. Based on this relationship, the average hardness of the weld metal and weld heat affected zone of the welded joint is 15 to 50% higher than the average hardness of the steel. Select welding materials and welding conditions and weld to make a welded joint.
  • ultrasonic welding was applied to the weld toe of this welded joint, and the radius of curvature r in the cross section perpendicular to the weld line was 1.0 to 10.0 mm.
  • the ultrasonic shock treatment trace having a depth d of 1.0 mm or less is formed.
  • the chemical composition of the steel and welding material (welded metal) used as the welded joint is not particularly limited, but preferably has the chemical composition of the steel material and welded material (welded metal) of the welded joint described above. It is preferable that The reason for limiting the chemical composition is omitted because it overlaps with the above description.
  • FIG. 4 is a partially broken schematic view showing an example of an ultrasonic impact device for performing an ultrasonic impact treatment.
  • the ultrasonic impact device 9 is basically composed of an ultrasonic oscillating unit 10, a wave guide unit 11 in front of it, and a vibration terminal (pin) 8 at its tip.
  • FIG. 4 shows a case where there are three vibrating terminals 8, three or more may be used, and a single case may be used as shown in FIG. 1 (a).
  • the ultrasonic impact device 9 amplifies the ultrasonic vibration generated by the ultrasonic oscillating unit 10 by the front wave guide unit 11 and propagates it to the tip to vibrate the vibration terminal 8 at the tip. While the vibration terminal 8 is vibrated, the surface of the weld toe is moved along the weld line to perform an impact treatment, thereby forming an ultrasonic impact mark having the shape described above.
  • the ultrasonic shock treatment is performed by using the ultrasonic oscillator 10 to make the vibration terminal 8 a frequency. It is necessary to vibrate at 20 kHz to 50 kHz and apply at a power of 0.0 1 to 4 kW. It is preferable to set it to 0.10 kW to 2 kW.
  • the metal on the surface of the weld toe is plasticized by oscillating at a frequency of 20 kHz to 50 kHz and applying ultrasonic impact treatment with a power of 0.01 to 4 kW. It can flow and release the tensile residual stress that has been formed with the cooling of the weld zone, and can form a compressive residual stress field.
  • the reason why the vibration frequency of the vibration terminal 8 is 20 kHz or more is that if it is less than 20 kHz, a heat insulation effect due to impact cannot be obtained, and the frequency is 50 kHz or less. This is because industrially applicable ultrasonic frequencies are generally below 50 kHz.
  • the reason why the work rate of the vibration terminal 8 is set to 0. Ol kW or more is that it takes too much time for ultrasonic impact treatment to be less than 0.0 1 kW. This is because even if impact treatment is performed at a work rate exceeding this, the effect is saturated and the economic efficiency is lowered.
  • the vibration terminal (pin) 8 has a rod shape as shown in FIG. 1 (a) or FIG. 4, and the radius of curvature of the cross section in the axial direction of the tip is preferably 1.0 to 1 O mm.
  • the radius of curvature of the axial cross section at the tip is smaller than 1. O mm, it takes a long time to form a predetermined ultrasonic impact mark with a radius of curvature of 1.0 to 10. O mm. This is because if it exceeds 10 O mm, it becomes difficult to form ultrasonic impact marks having a predetermined radius of curvature. That is, by making the tip of the vibration terminal equal to the radius of curvature of the ultrasonic shock mark, a predetermined ultrasonic shock mark is efficiently formed. It is possible to Example
  • steel plates having a tensile strength level of 40 OMPa to 80 OMPa class were used as the steel material.
  • the composition is shown in Table 1 in mass%. Plates with a thickness of 15 mm, a length of 100 mm, and a width of 100 mm were prepared from steel plates of any composition and used for welding, ultrasonic impact treatment, and fatigue tests. did.
  • FIG. 5 (a) The joint shape of each specimen is either cross, turn or butt, and is shown in Table 1.
  • Figures 5 (a) to 5 (c) show an outline of the specimen in a perspective view.
  • a load non-transmitting fillet weld is used, and the longitudinal steel plate 1 2 (2) (width 10 0) is perpendicular to the longitudinal direction of the specimen at the center of the specimen.
  • 0 mm, 50 mm in height, and 10 mm in thickness were welded to both sides of steel plate 2 to produce cruciform specimen 1 3.
  • Fig. 5 (a) a load non-transmitting fillet weld
  • the longitudinal steel plate 1 2 (2) width 10 0
  • a joint test specimen 14 was produced by welding and rotating a 100 mm height, 50 mm height, and a plate thickness of 10 mm) to both sides of the steel sheet 2.
  • the leg length for fillet welding was 8 mm for both the cruciform joint and the turning joint.
  • a plate test body with a length of 100 mm is cut in advance at the center to obtain two plates with a length of 500 mm, and the butt weld is X-shaped.
  • FC AW Flux Cored wires Arc Welding
  • GM Table 1 shows one of AW (Gas Metal Arc Welding), G TAW (Gas Tungsten Arc Welding), and S MAW (Shielded Metal Arc Welding).
  • FC AW Flu Cored wires Arc Welding
  • G TAW Gas Tungsten Arc Welding
  • S MAW shielded Metal Arc Welding
  • Specimens 13 of the present invention are obtained by butt welding plates having different compositions on the left and right sides.
  • the average hardness of steel materials and the average hardness of the heat affected zone in Table 2 (Table 1 continued) are The average hardness was shown.
  • Table 2 shows the resonance frequency (khz), power (kW), and radius of curvature (mm) of the vibration terminal used when ultrasonic shock treatment was applied. Shown in Also, Table 2 (Table 1 continued) shows the presence or absence of ultrasonic impact marks, the curvature mm of impact marks, and the depth mm of impact marks.
  • Ultrasonic impact In the impact treatment, a single vibration terminal with each curvature is mounted on the ultrasonic impact treatment device, and the impact trace continues at a speed of 30 cm / min along the weld toe at a pressing load of approximately 4 kg. Processed. The curvature and depth of the impact mark were measured by making a mold with an impression material.
  • Comparative examples 16 to 17 are prepared by comparing six test specimens that are not subjected to ultrasonic impact treatment for comparison, one for measuring cross-sectional hardness and the remaining five for fatigue testing. Comparison was made with the case.

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  • Engineering & Computer Science (AREA)
  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Plasma & Fusion (AREA)
  • Butt Welding And Welding Of Specific Article (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

Cette invention se rapporte à un joint soudé qui présente l'effet d'un traitement par choc ultrasonore de manière plus efficace, et qui présente également des caractéristiques de résistance à la fatigue améliorées. L'invention concerne également un procédé de réalisation du joint. Dans ce joint, la dureté moyenne de la zone de soudure et de la zone affectée par la chaleur est plus élevée de 15 % à 50 % que celle de la matière première d'acier, et au niveau du raccordement soudé, se forme une cicatrice de choc ultrasonore qui présente un rayon de courbure r compris entre 1,0 mm et 10,0 mm, sur la section transversale perpendiculaire à la ligne de soudure, et une épaisseur d inférieure ou égale à 1,0 mm, à partir de la surface de la matière première d'acier.
PCT/JP2009/053302 2008-02-19 2009-02-18 Joint soudé qui présente d'excellentes caractéristiques de résistance à la fatigue, et procédé de réalisation associé WO2009104798A1 (fr)

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JP2009516761A JP4719297B2 (ja) 2008-02-19 2009-02-18 耐疲労特性に優れた溶接継手及びその製造方法
KR1020097018596A KR101134158B1 (ko) 2008-02-19 2009-02-18 내피로 특성이 우수한 용접 이음부 및 그 제조 방법
CN2009800002199A CN101678511B (zh) 2008-02-19 2009-02-18 耐疲劳特性优异的焊接接头及其制造方法

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JP2008037719 2008-02-19

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CN102470489A (zh) * 2009-11-07 2012-05-23 新日本制铁株式会社 焊趾部的多重敲击处理方法
JP2012106285A (ja) * 2010-10-26 2012-06-07 Nippon Steel Corp 溶接継手及び溶接継手の製造方法
JP2015127063A (ja) * 2013-11-26 2015-07-09 国立大学法人大阪大学 溶接部の補強方法
CN106975992A (zh) * 2017-03-18 2017-07-25 郑州煤矿机械集团股份有限公司 液压支架结构件疲劳延寿方法
CN109423587A (zh) * 2017-08-28 2019-03-05 天津大学 超声冲击表面改性辅助钛合金扩散连接方法
JP2019084544A (ja) * 2017-11-02 2019-06-06 日産自動車株式会社 溶接構造体、および溶接構造体の製造方法
JP2020530815A (ja) * 2017-06-14 2020-10-29 マシネンファブリック アルフィング ケスラー ゲーエムベーハーＭａｓｃｈｉｎｅｎｆａｂｒｉｋ Ａｌｆｉｎｇ Ｋｅｓｓｌｅｒ Ｇｅｓｅｌｌｓｃｈａｆｔ Ｍｉｔ Ｂｅｓｃｈｒａｎｋｔｅｒ Ｈａｆｔｕｎｇ クランクシャフトの渡り部を衝撃処理するための方法及び装置
JP2020530814A (ja) * 2017-06-14 2020-10-29 マシネンファブリック アルフィング ケスラー ゲーエムベーハーＭａｓｃｈｉｎｅｎｆａｂｒｉｋ Ａｌｆｉｎｇ Ｋｅｓｓｌｅｒ Ｇｅｓｅｌｌｓｃｈａｆｔ Ｍｉｔ Ｂｅｓｃｈｒａｎｋｔｅｒ Ｈａｆｔｕｎｇ クランクシャフトの渡り部を衝撃処理するための方法及び装置
WO2021095796A1 (fr) * 2019-11-12 2021-05-20 株式会社小松製作所 Châssis de carrosserie de véhicule de transport, véhicule de transport et procédé de fabrication de châssis de carrosserie de véhicule de transport

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CN104975163A (zh) * 2015-06-29 2015-10-14 柳州金茂机械有限公司 一种焊接接头的表面处理工艺
CN104975164A (zh) * 2015-06-29 2015-10-14 柳州金茂机械有限公司 一种管板焊接接头的表面处理工艺
CN111132793B (zh) * 2017-09-27 2021-09-07 杰富意钢铁株式会社 搭接角焊接头的锤击处理方法及焊接结构物
CN108707741B (zh) * 2018-06-06 2019-08-09 江苏省特种设备安全监督检验研究院 一种奥氏体不锈钢焊接接头的表面复合处理工艺
EP3808488A4 (fr) * 2018-06-18 2021-08-18 Posco Élément de soudure en tôle d'acier plaquée ayant une excellente résistance à la porosité et une excellente propriété de fatigue de zone de soudure, et son procédé de fabrication

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JP2004130313A (ja) * 2002-10-08 2004-04-30 Nippon Steel Corp 重ね隅肉溶接継手の疲労強度向上方法
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JP2007119811A (ja) * 2005-10-26 2007-05-17 Sumitomo Metal Ind Ltd 溶接継手及びその製造方法
JP2007210023A (ja) * 2006-02-13 2007-08-23 Nippon Steel Corp 溶接部脆化割れ特性に優れた高強度溶接鋼管
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CN102470489A (zh) * 2009-11-07 2012-05-23 新日本制铁株式会社 焊趾部的多重敲击处理方法
JP2012106285A (ja) * 2010-10-26 2012-06-07 Nippon Steel Corp 溶接継手及び溶接継手の製造方法
JP2015127063A (ja) * 2013-11-26 2015-07-09 国立大学法人大阪大学 溶接部の補強方法
CN106975992A (zh) * 2017-03-18 2017-07-25 郑州煤矿机械集团股份有限公司 液压支架结构件疲劳延寿方法
JP7129432B2 (ja) 2017-06-14 2022-09-01 マシネンファブリック アルフィング ケスラー ゲーエムベーハー クランクシャフトの渡り部を衝撃処理するための方法及び装置
JP7013492B2 (ja) 2017-06-14 2022-01-31 マシネンファブリック アルフィング ケスラー ゲーエムベーハー クランクシャフトの渡り部を衝撃処理するための方法及び装置
JP2020530815A (ja) * 2017-06-14 2020-10-29 マシネンファブリック アルフィング ケスラー ゲーエムベーハーＭａｓｃｈｉｎｅｎｆａｂｒｉｋ Ａｌｆｉｎｇ Ｋｅｓｓｌｅｒ Ｇｅｓｅｌｌｓｃｈａｆｔ Ｍｉｔ Ｂｅｓｃｈｒａｎｋｔｅｒ Ｈａｆｔｕｎｇ クランクシャフトの渡り部を衝撃処理するための方法及び装置
JP2020530814A (ja) * 2017-06-14 2020-10-29 マシネンファブリック アルフィング ケスラー ゲーエムベーハーＭａｓｃｈｉｎｅｎｆａｂｒｉｋ Ａｌｆｉｎｇ Ｋｅｓｓｌｅｒ Ｇｅｓｅｌｌｓｃｈａｆｔ Ｍｉｔ Ｂｅｓｃｈｒａｎｋｔｅｒ Ｈａｆｔｕｎｇ クランクシャフトの渡り部を衝撃処理するための方法及び装置
CN109423587B (zh) * 2017-08-28 2021-05-04 天津大学 超声冲击表面改性辅助钛合金扩散连接方法
CN109423587A (zh) * 2017-08-28 2019-03-05 天津大学 超声冲击表面改性辅助钛合金扩散连接方法
JP2019084544A (ja) * 2017-11-02 2019-06-06 日産自動車株式会社 溶接構造体、および溶接構造体の製造方法
JP7035458B2 (ja) 2017-11-02 2022-03-15 日産自動車株式会社 溶接構造体、および溶接構造体の製造方法
WO2021095796A1 (fr) * 2019-11-12 2021-05-20 株式会社小松製作所 Châssis de carrosserie de véhicule de transport, véhicule de transport et procédé de fabrication de châssis de carrosserie de véhicule de transport
CN114650945A (zh) * 2019-11-12 2022-06-21 株式会社小松制作所 搬运车辆的车身框架、搬运车辆、以及搬运车辆的车身框架制造方法
EP4039539A4 (fr) * 2019-11-12 2023-11-08 Komatsu Ltd. Châssis de carrosserie de véhicule de transport, véhicule de transport et procédé de fabrication de châssis de carrosserie de véhicule de transport
JP7514249B2 (ja) 2019-11-12 2024-07-10 株式会社小松製作所 運搬車両の車体フレーム、運搬車両、及び、運搬車両の車体フレーム製造方法

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KR20090122937A (ko) 2009-12-01
CN101678511A (zh) 2010-03-24
CN101678511B (zh) 2011-12-07
KR101134158B1 (ko) 2012-04-09
JP4719297B2 (ja) 2011-07-06
JPWO2009104798A1 (ja) 2011-06-23
TWI365789B (fr) 2012-06-11

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