WO2023042974A1 - 피로저항특성 및 용접부의 잔류응력으로 인한 변형에 대한 저항성이 우수한 가스 실드 아크 용접용 와이어와 용접부재 및 그 제조방법 - Google Patents
피로저항특성 및 용접부의 잔류응력으로 인한 변형에 대한 저항성이 우수한 가스 실드 아크 용접용 와이어와 용접부재 및 그 제조방법 Download PDFInfo
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Images
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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
- B23K35/308—Fe as the principal constituent with Cr as next major constituent
- B23K35/3086—Fe as the principal constituent with Cr as next major constituent containing Ni or Mn
-
- 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
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
-
- 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
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
- B23K35/0261—Rods, electrodes, wires
-
- 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
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
- B23K35/0261—Rods, electrodes, wires
- B23K35/0266—Rods, electrodes, wires flux-cored
-
- 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
-
- 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
-
- 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
- B23K35/3066—Fe as the principal constituent with Ni as next major constituent
-
- 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
- B23K35/3073—Fe as the principal constituent with Mn as next major constituent
-
- 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
- B23K9/16—Arc welding or cutting making use of shielding gas
-
- 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
- B23K9/16—Arc welding or cutting making use of shielding gas
- B23K9/173—Arc welding or cutting making use of shielding gas and of a consumable electrode
-
- 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
- Y02P10/20—Recycling
Definitions
- the present invention relates to a wire and a welding member for gas shielded arc welding having excellent fatigue resistance and resistance to deformation due to residual stress at a welded portion, and a manufacturing method thereof.
- Chassis parts which are important for automobile driving performance, also require application of high-strength steel materials for weight reduction according to this trend.
- high-strength materials are essential, and guaranteeing durability of parts made of high-strength steel materials in an environment where repeated fatigue loads are applied is an important factor.
- arc welding which is mainly used to secure strength when assembling automobile chassis parts, overlapping joints between parts are welded by welding wires, so it is inevitable to give geometric shapes to the joints.
- Patent Document 1 in order to improve the fatigue characteristics of an arc welded part manufactured using steel with a plate thickness of 5 mm or less and a tensile strength of 780 MPa or more, the concept of material control for each temperature zone position of the weld bead toe, that is, the heat-affected zone (HAZ) (For example, the location of the minimum hardness at a depth of 0.1 mm from the surface must be at least 0.3 mm away from the melting line), but the strength of the weld metal is improved through the improvement of the properties of the welding material and the stress characteristics of the welded part are improved. Control technology has limitations that cannot be presented
- Patent Document 2 suggests that fatigue characteristics can be improved by applying compressive stress by forming a plastic deformation region by continuously hitting the end of a weld bead with a chipper (hitting pin), and in Patent Document 3, a subframe and In order to reduce the toe angle of the arc welding bead between brackets, a method of re-melting the end of the welding bead through a plasma heat source after welding was proposed.
- the above proposed methods have a problem in that processing costs increase when manufacturing parts due to the addition of a post-welding process.
- Patent Document 1 Japanese Unexamined Patent Publication No. 2013-220431
- Patent Document 2 Japanese Unexamined Patent Publication No. 2014-014831
- Patent Document 3 Japanese Unexamined Patent Publication No. 2014-004609
- One aspect of the present invention is to provide a wire for gas shielded arc welding capable of imparting excellent fatigue resistance characteristics and resistance to deformation due to residual stress to a welded portion.
- Another aspect of the present invention is to provide a welding member having excellent fatigue resistance and resistance to deformation due to residual stress of a welded portion and a manufacturing method thereof.
- One embodiment of the present invention in weight%, C: 0.06 ⁇ 0.16%, Si: 0.001 ⁇ 0.2%, Mn: 1.6 ⁇ 1.9%, Cr: 1.2 ⁇ 6.0%, Mo: 0.4 ⁇ 0.65%, P: 0.015% or less (excluding 0%), S: 0.01% or less (excluding 0%), Al: 0.20% or less (excluding 0%), the balance including Fe and other unavoidable impurities, and the value of formula 1 below is 300 to Provided is a wire for gas shielded arc welding having excellent fatigue resistance characteristics of 500 and resistance to deformation due to residual stress at a welded portion.
- Another embodiment of the present invention is a welding member including a base material and a welded portion, wherein the welded portion, in weight%, C: 0.05 ⁇ 0.16%, Si: 0.001 ⁇ 1.0%, Mn: 1.4 ⁇ 2.5%, Cr: 0.4 ⁇ 5.0%, Mo: 0.1 to 1.5%, P: 0.015% or less (excluding 0%), S: 0.01% or less (excluding 0%), Al: 0.20% or less (excluding 0%), balance Fe and others contains unavoidable impurities, and includes bainite; acicular ferrite; and at least one of granular ferrite, martensite, and retained austenite; has a microstructure including, wherein the microstructure has an average effective grain size of 10 ⁇ m or less, and a misorientation angle between grains relative to the entire grain boundary ) is 55 ⁇ or more, the ratio of high angle grain boundaries is 40% or more, and the value of R expressed by the following formula 2 is 10.5 to 18.5, providing a welding member with excellent resistance to de
- K is the ratio (%) of grain boundaries with an orientation difference angle between grains of 55 ⁇ or more relative to all grain boundaries in the weld
- G is the average effective grain size of the weld ( ⁇ m)
- T is the thickness of the base material ( mm)
- Q mean the welding heat input (kJ / cm)
- the Q is defined by the following [Equation 3].
- Another embodiment of the present invention is a method for manufacturing a welding member in which two or more base materials are prepared and gas shielded arc welding is performed using a welding wire, wherein the welding wire is % by weight, C: 0.06 ⁇ 0.16%, Si: 0.001 to 0.2%, Mn: 1.6 to 1.9%, Cr: 1.2 to 6.0%, Mo: 0.4 to 0.65%, P: 0.015% or less (excluding 0%), S: 0.01% or less (excluding 0%), Al: 0.20% or less (excluding 0%), the balance includes Fe and other unavoidable impurities, the value of Equation 1 below is 300 to 500, and the value of Equation 4 below is 1.2 to 1.6 during the gas shielded arc welding Provided is a method for manufacturing a welding member having excellent fatigue resistance characteristics and resistance to deformation due to residual stress of a welded portion.
- T means the thickness of the base material (mm) and Q means the welding heat input (kJ/cm).
- a wire for gas shielded arc welding capable of imparting excellent fatigue resistance characteristics and resistance to deformation due to residual stress to a welded portion.
- Example 1 is an IQ (Image Quality) and IPF (Inverse Pole Figure) photograph of Inventive Example 1 according to an embodiment of the present invention observed by EBSD.
- FIG. 2 is a graph of a grain boundary ratio according to an orientation difference angle between grains of Inventive Example 1 according to an embodiment of the present invention.
- Example 3 is an IQ (Image Quality) and IPF (Inverse Pole Figure) photograph of Inventive Example 2 according to an embodiment of the present invention observed by EBSD.
- FIG. 4 is a graph of a grain boundary ratio according to an orientation difference angle between grains of Inventive Example 2 according to an embodiment of the present invention.
- Example 5 is an IQ (Image Quality) and IPF (Inverse Pole Figure) photograph of Inventive Example 3 according to an embodiment of the present invention observed by EBSD.
- FIG. 6 is a graph of a grain boundary ratio according to an orientation difference angle between grains of Inventive Example 3 according to an embodiment of the present invention.
- Example 7 is an IQ (Image Quality) and IPF (Inverse Pole Figure) photograph of Inventive Example 4 according to an embodiment of the present invention observed by EBSD.
- FIG. 8 is a graph of a grain boundary ratio according to an orientation difference angle between grains of Inventive Example 4 according to an embodiment of the present invention.
- FIG. 10 is a graph of a grain boundary ratio according to an orientation difference angle between grains of Comparative Example 1 according to an embodiment of the present invention.
- the content of the alloy composition described below is % by weight.
- the C is an element that is advantageous for the action of atomizing the volume by stabilizing the arc, and is also advantageous for securing hardenability. If the content of C is less than 0.06%, the arc becomes unstable due to coarsening of the volume, the amount of spatter increases, and it may be difficult to secure sufficient strength of the weld metal, and if it exceeds 0.16%, the molten metal There may be disadvantages in that the viscosity of the bead is lowered, resulting in a poor bead shape, and excessive hardening of the weld metal, resulting in a decrease in toughness.
- the lower limit of the C content is more preferably 0.062%, even more preferably 0.065%, and most preferably 0.07%.
- the upper limit of the C content is more preferably 0.12%, even more preferably 0.10%, and most preferably 0.09%.
- the Si is an element that promotes deoxidation of molten metal during arc welding (deoxidation element) and is an element that is advantageous for suppressing the occurrence of blowholes. If the content of Si is less than 0.001%, there may be a disadvantage in that the deoxidation effect is insufficient and blowholes are easily generated. Due to deoxidation, the surface activation of the welded part is insufficient, and there may be a disadvantage in that the weldability of the molten metal is lowered.
- the lower limit of the Si content is more preferably 0.01%, even more preferably 0.02%, and most preferably 0.04%.
- the upper limit of the Si content is more preferably 0.15%, even more preferably 0.10%, and most preferably 0.08%.
- Mn is a deoxidizing element and is advantageous for suppressing blowhole generation by accelerating deoxidation of molten metal during arc welding. If the content of Mn is less than 1.6%, there may be a disadvantage in that the deoxidation effect is insufficient and blowholes are easily generated. There may be a disadvantage in that molten metal cannot be introduced and a bead shape defect is likely to occur as a humping bead is formed.
- the lower limit of the Mn content is more preferably 1.65%, even more preferably 1.7%, and most preferably 1.75%.
- the upper limit of the Mn content is more preferably 1.87%, even more preferably 1.85%, and most preferably 1.8%.
- the Cr is a ferrite stabilizing element and is an element advantageous to securing hardenability for improving the strength of the weld metal. If the Cr content is less than 1.2%, it may be difficult to secure sufficient strength of the weld metal, and if it exceeds 6.0%, in some cases, the brittleness of the weld metal may be unnecessarily increased, making it difficult to secure sufficient toughness. there is.
- the lower limit of the Cr content is more preferably 1.25%, more preferably 1.30%, and most preferably 1.35%.
- the upper limit of the Cr content is more preferably 5.8%, more preferably 5.5%, and most preferably 5.2%.
- the Mo is a ferrite stabilizing element and is an element advantageous to securing hardenability for improving the strength of the weld metal. If the Mo content is less than 0.4%, it may be difficult to secure sufficient strength of the weld metal, and if it exceeds 0.65%, the toughness of the weld metal may deteriorate in some cases.
- the lower limit of the Mo content is more preferably 0.42%, even more preferably 0.44%, and most preferably 0.46%.
- the upper limit of the Mo content is more preferably 0.62%, more preferably 0.60%, and most preferably 0.58%.
- P is an element that is generally incorporated as an unavoidable impurity in steel, and is also an element included as a common impurity in a solid wire for arc welding. When the P content exceeds 0.015%, hot cracking of the weld metal may become significant.
- the P content is more preferably 0.014% or less, even more preferably 0.012% or less, and most preferably 0.01% or less.
- S is an element that is generally incorporated as an unavoidable impurity in steel, and is also an element included as a common impurity in a solid wire for arc welding.
- the S content is more preferably 0.008% or less, even more preferably 0.006% or less, and most preferably 0.005% or less.
- Al is a deoxidizing element that can improve the strength of the weld metal by promoting deoxidation of the molten metal during arc welding even in a small amount.
- the Al content exceeds 0.20%, the production of Al-based oxides increases, and in some cases, the strength and toughness of the weld metal are lowered, and the electrodeposition coating defect of the welded part due to the non-conductive oxide may be sensitive.
- the Al content is more preferably 0.15% or less, even more preferably 0.12% or less, and most preferably 0.10% or less.
- the remaining components of the present invention are iron (Fe).
- Fe iron
- the above impurities can be known to anyone skilled in the art, all of them are not specifically mentioned in the present invention.
- the wire of the present invention may further include one or more of Ni: 0.40% or less and Cu: 0.50% or less in addition to the above-described alloy composition.
- the Ni is an element that can improve the strength and toughness of the weld metal. However, when the content of Ni exceeds 0.40%, there may be a disadvantage of being sensitive to cracking.
- the Ni content is more preferably 0.30% or less, more preferably 0.20% or less, and most preferably 0.10% or less.
- the Cu is usually contained in about 0.02% as an impurity in the steel constituting the wire, but in the case of a solid wire for arc welding, the content can be determined mainly due to copper plating performed on the surface of the wire.
- the Cu is an element capable of stabilizing the supply and conductivity of the wire.
- the Cu content is more preferably 0.45% or less, even more preferably 0.40% or less, and most preferably 0.30% or less.
- the wire of the present invention preferably satisfies the alloy composition described above and has a value of 300 to 500 in Equation 1 below.
- Equation 1 below utilizes the lower bainite transformation including acicular ferrite to make the microstructure of the weld metal part a dense structure in which acicular ferrite and bainite are interlocked in a complex form, and the transformation expansion by lowering the low-temperature transformation start temperature This is to offset the contraction tensile stress generated during the solidification of the molten pool or to add additional compressive stress to the compressive residual stress of the welded part.
- Equation 1 below If the value of Equation 1 below is less than 300, the hardenability is too increased and the low-temperature transformation structure is excessively developed, resulting in insufficient toughness of the weld metal, and the low-temperature transformation initiation temperature is too low, resulting in an increase in the retained austenite fraction and the transformation expansion effect.
- the lower limit of the value of the following formula 1 is more preferably 312, even more preferably 315, and most preferably 318.
- the upper limit of the value of Formula 1 below is more preferably 498, even more preferably 496, and most preferably 494.
- the shape or type of the wire is not particularly limited, but, for example, the wire of the present invention may be one of a solid wire, a metal cored wire, and a flux cored wire.
- the welding member of the present invention includes a base material and a welding part.
- the alloy composition of the welded portion will be described first.
- the content of the alloy composition described below is % by weight.
- C is a main element that can lower the temperature at which acicular ferrite, bainite, and martensite transformations start through diffusionless transformation as the weld metal is continuously cooled in the high-temperature austenite phase during the solidification process. If the content of C is less than 0.05%, the hardenability is reduced, making it difficult to secure sufficient strength of the weld metal, and the low-temperature transformation initiation temperature is not sufficiently lowered according to the above-described principle, resulting in a low-temperature transformation expansion effect in the cooling process. There may be disadvantages in that a tensile residual stress offset effect is remarkably low and a high-angle grain boundary structure having a large azimuthal difference between grains cannot be formed.
- the C content exceeds 0.16%, the viscosity of the molten metal is lowered, resulting in poor bead shape, excessive hardening of the weld metal, deterioration in toughness, and excessively lowering of the low-temperature transformation initiation temperature, resulting in tensile residual stress at the welded part.
- the lower limit of the C content is more preferably 0.052%, even more preferably 0.055%, and most preferably 0.58%.
- the upper limit of the C content is more preferably 0.12%, even more preferably 0.1%, and most preferably 0.09%.
- Si is an element that promotes deoxidation of molten metal during arc welding (deoxidation element), is advantageous for suppressing the occurrence of blowholes, and increases the low-temperature transformation initiation temperature. If the Si content is less than 0.001%, there may be a disadvantage in that the deoxidation effect is insufficient and blowholes are likely to occur, and the low-temperature transformation initiation temperature is excessively lowered, thereby reducing the effect of offsetting the tensile residual stress of the welded part.
- the lower limit of the Si content is more preferably 0.01%, even more preferably 0.02%, and most preferably 0.04%.
- the upper limit of the Si content is more preferably 0.85%, even more preferably 0.75%, and most preferably 0.65%.
- Mn is a deoxidizing element, promotes deoxidation of molten metal during arc welding, is advantageous in suppressing the generation of blowholes, and, like C, is an element that reduces the low-temperature transformation initiation temperature. If the content of Mn is less than 1.4%, the deoxidation effect is insufficient, so blowholes are easily generated, and the low-temperature transformation initiation temperature rises, so that a sufficient compressive stress effect due to low-temperature transformation may not be obtained.
- the low-temperature transformation initiation temperature may be too low, and the effect of offsetting the tensile residual stress of the welded part may be degraded.
- the lower limit of the Mn content is more preferably 1.45%, even more preferably 1.50%, and most preferably 1.55%.
- the upper limit of the Mn content is more preferably 2.47%, even more preferably 2.45%, and most preferably 2.43%.
- the Cr is a ferrite stabilizing element, lowers the low-temperature transformation initiation temperature, and is an element advantageous to improving strength by securing hardenability of the weld metal. If the Cr content is less than 0.4%, the ratio of high-angle grain boundaries of the weld metal decreases, and it is difficult to sufficiently obtain a compressive stress effect due to low-temperature transformation, and it may be difficult to secure sufficient strength of the weld metal. On the other hand, if the Cr content exceeds 5.0%, brittleness of the weld metal unnecessarily increases in some cases, making it difficult to secure sufficient toughness, and the low-temperature transformation initiation temperature may be too low to sufficiently secure the compressive stress of the welded part.
- the lower limit of the Cr content is more preferably 0.44%, even more preferably 0.47%, and most preferably 0.50%.
- the upper limit of the Cr content is more preferably 4.8%, more preferably 4.5%, and most preferably 4.2%.
- Mo is a ferrite stabilizing element, lowers the low-temperature transformation initiation temperature, and is advantageous for improving strength by securing hardenability of the weld metal. If the content of Mo is less than 0.1%, it may be difficult to obtain sufficient strength of the weld metal, as well as to reduce the ratio of high-angle grain boundaries of the weld metal and to obtain a sufficient compressive stress effect due to low-temperature transformation. On the other hand, when the content of Mo exceeds 1.5%, the toughness of the weld metal is lowered in some cases, and the low-temperature transformation initiation temperature is too low, so that the compressive stress of the welded part may not be sufficiently secured.
- the lower limit of the Mo content is more preferably 0.16%, more preferably 0.18%, and most preferably 0.2%.
- the upper limit of the Mo content is more preferably 1.48%, even more preferably 1.46%, and most preferably 1.44%.
- the P is an element that is generally incorporated as an unavoidable impurity. When the P content exceeds 0.015%, hot cracking of the weld metal may become significant.
- the P content is more preferably 0.014% or less, even more preferably 0.012% or less, and most preferably 0.01% or less.
- the S is an element that is generally incorporated as an unavoidable impurity.
- the content of S exceeds 0.01%, the toughness of the weld metal deteriorates in some cases, and the surface tension of the molten metal becomes insufficient during welding, so that it is melted by gravity during high-speed high-speed welding (welding from top to bottom during vertical welding).
- the S content is more preferably 0.008% or less, even more preferably 0.006% or less, and most preferably 0.005% or less.
- Al is a deoxidizing element that can improve the strength of the weld metal by promoting deoxidation of the molten metal during arc welding even in a small amount.
- the Al content exceeds 0.20%, the production of Al-based oxides increases, and in some cases, the strength and toughness of the weld metal are lowered, and the electrodeposition coating defect of the welded part due to the non-conductive oxide may be sensitive.
- the Al content is more preferably 0.15% or less, even more preferably 0.12% or less, and most preferably 0.10% or less.
- the remaining components of the present invention are iron (Fe).
- Fe iron
- the above impurities can be known to anyone skilled in the art, all of them are not specifically mentioned in the present invention.
- the welding member of the present invention may contain at least one of Ni: 0.40% or less and Cu: 0.50% or less.
- the Ni is an element that can improve the strength and toughness of the weld metal. However, when the content of Ni exceeds 0.40%, there may be a disadvantage of being sensitive to cracking.
- the Ni content is more preferably 0.30% or less, more preferably 0.20% or less, and most preferably 0.10% or less.
- the Cu is an element effective in improving the strength of the weld metal.
- the Cu content is more preferably 0.45% or less, even more preferably 0.40% or less, and most preferably 0.30% or less.
- 0.01% or more of Cu may be contained in the weld metal.
- the welding portion of the welding member of the present invention is bainite; It is preferable to have a microstructure including acicular ferrite; and at least one of granular ferrite, martensite, and retained austenite.
- the microstructure of the weld metal part is formed by utilizing the lower bainite transformation including acicular ferrite in the former austenite crystal grains generated in the cooling process after welding.
- a dense structure in which bainite is interlocked in a complex form that is, a structure in which the azimuth angle between crystal grains has a high angle, and the low-temperature transformation initiation temperature is lowered to solidify the molten pool with the compressive residual stress of the weldment generated through low-temperature transformation expansion It is possible to obtain the effect of offsetting the contraction tensile stress that occurs during application or adding additional compressive stress.
- the average effective crystal grain size of the microstructure of the welded part is 10 ⁇ m or less. In this way, by finely controlling the size of the average effective crystal grain, an effect of securing relatively excellent strength and toughness of the weld metal can be obtained. When the size of the average effective crystal grain exceeds 10 ⁇ m, it is difficult to simultaneously secure sufficient strength and toughness of the weld metal as described above.
- the average effective crystal grain size is more preferably 7 ⁇ m or less, even more preferably 5 ⁇ m or less, and most preferably 4 ⁇ m or less. Meanwhile, the average effective grain size may be defined as an average size of grains converted from the number of grains per unit area.
- the microstructure of the welded part preferably has a ratio of high-angle grain boundaries having an orientation difference angle of 55° or more to total grain boundaries of 40% or more.
- a ratio of high-angle grain boundaries having an orientation difference angle of 55° or more to total grain boundaries of 40% or more.
- the ratio of the high angle grain boundaries is more preferably 44% or more, even more preferably 47% or more, and most preferably 50% or more.
- the value of R represented by the following formula 2 is 10.5 to 18.5 for the welded part.
- Equation 2 below is intended to increase the orientation difference angle between crystal grains implemented according to the effect of Equation 1 described above, and to form a microstructure having a more dense and complex structure by refining effective crystal grains constituting this. If the value of Equation 2 below is less than 10.5, there may be a disadvantage in that the strength and toughness of the weld metal are not sufficiently secured, and if it exceeds 18.5, the brittleness of the weld metal is too high and there may be a disadvantage in that it is sensitive to cracking.
- the lower limit of the value of the following formula 2 is more preferably 10.6, still more preferably 10.8, and most preferably 11.
- an orientation difference angle between crystal grains may be defined as an angle formed by each grain boundary when a series of lattice arrangements constituting crystal grains are regarded as one crystal grain.
- K is the ratio (%) of grain boundaries with an orientation angle between grains of 55 ⁇ or more relative to all grain boundaries in the weld
- G is the average effective grain size of the weld ( ⁇ m)
- T is the thickness of the base material (mm)
- Q means welding heat input (kJ / cm)
- the Q is defined by the following [Equation 3].
- I means welding current (A)
- E means welding voltage (V)
- ⁇ means welding speed (cm/min).
- the welded portion of the present invention provided as described above may have a fatigue strength of 140 MPa or more.
- the welded portion may have a compressive residual stress of 90 MPa or more in an area within 5 mm from the end of the weld bead in a direction perpendicular to the base material.
- there are tensile residual stress and compressive residual stress as types of the residual stress and in the case of tensile residual stress, it may cause a problem of deteriorating the fatigue resistance characteristic of the welded part in particular.
- an appropriate level of compressive residual stress is applied to the welded portion.
- the welding member of the present invention is excellent in fatigue resistance and resistance to deformation due to residual stress at the welded part, so that when applied to automotive parts, etc., it is possible to effectively improve the durability and assembly quality of the product.
- the alloy composition of the base material is not particularly limited.
- the base material contains, by weight, C: 0.05 to 0.13%, Si: 0.2 to 2.0%, Mn: 1.3 to 3.0%, Cr: 0.01 to 2.0%, Mo: 0.01 to 2.0%, Al: 0.01 ⁇ 0.1%, P: 0.001 ⁇ 0.05%, S: 0.001 ⁇ 0.05%, balance Fe and other unavoidable impurities.
- the base material may further include one or more of Ti: 0.01 to 0.2% and Nb: 0.01 to 0.1%.
- the base material may have a thickness of 0.8 to 4.0 mm.
- the manufacturing method of the welding member is not particularly limited. However, one of the advantageous methods for manufacturing the welding member of the present invention will be described as follows.
- the welding wire in manufacturing a welding member by preparing two or more base materials and then performing gas shielded arc welding using a welding wire, the welding wire preferably satisfies the above-described alloy composition and the value of Equation 1.
- the base material may also have the above-described alloy composition.
- the lower limit of the value of Equation 4 below is more preferably 1.24, even more preferably 1.26, and most preferably 1.28.
- the upper limit of the value of the following formula 1 is more preferably 1.58, even more preferably 1.56, and most preferably 1.54.
- T means the thickness of the base material (mm) and Q means the welding heat input (kJ/cm).
- the microstructure was observed with an optical microscope after taking a specimen from the welded part, micropolishing the cross-sectional structure and etching with a Nital solution.
- the Kikuchi pattern was analyzed through EBSD (Electron Backscattered Diffraction) to obtain IQ (Image Quality) and IPF (Inverse Pole Figure) Maps visualizing grain boundary and grain orientation information.
- IQ Image Quality
- IPF Inverse Pole Figure Maps visualizing grain boundary and grain orientation information.
- the average effective grain size was calculated by calculating the average size of the grains converted from the number of grains per unit area. measured.
- the ratio of high-angle grain boundaries with an orientation angle between grains of 55 ⁇ or more relative to all grain boundaries in the weld is considered as a series of lattice arrays that form grains through the above-mentioned EBSD analysis method, and at this time, the angle formed by each grain boundary is After the measurement, it was measured by a method of extracting the ratio of grain boundaries having an orientation angle of 55° or more among the entire distribution of orientation angles between grains.
- Fatigue strength was defined as the maximum load that satisfies 2 ⁇ 10 6 Cycles of fatigue life by conducting a fatigue test after taking a specimen from the welded part of the welding member.
- the fatigue life (Cycles) was measured using a tensile-tensile high cycle fatigue test for each load. At this time, the ratio of the minimum load and the maximum load was 0.1, and the repetition load frequency was 15 Hz.
- the fatigue life corresponding to the converted strength (MPa) was derived by dividing the load (kN) by the area according to the width and thickness of each specimen.
- the minimum load means the minimum value of the repeated load having the above-described constant load application frequency
- the maximum load means the maximum value of the repeated load.
- Residual stress is calculated by measuring the amount of added stress change by measuring the change in distance between lattices constituting crystal grains using the principle of X-ray diffraction for an area within 5 mm from the end of the weld bead in the direction perpendicular to the base metal. did At this time, X-rays were generated from the Cr tube with a voltage of 30 kV and a current of 6.7 mA. On the other hand, if the value of residual stress is negative (-), it is determined as compressive residual stress, and if it is positive (+), it is determined as tensile residual stress.
- the bead start part means a weld bead formed after welding starts
- the bead end part means a weld bead formed after welding is finished
- the bead center part means a weld bead located in the middle of the bead start part and the bead end part.
- FIG. 1 is an IQ (Image Quality) and IPF (Inverse Pole Figure) photograph of Inventive Example 1 observed by EBSD
- FIG. 2 is a graph of a grain boundary ratio according to an orientation difference angle between crystal grains of Inventive Example 1.
- FIG. 3 is an IQ (Image Quality) and IPF (Inverse Pole Figure) photograph of Inventive Example 2 observed by EBSD
- FIG. 4 is a graph of a grain boundary ratio according to an orientation difference angle between crystal grains of Inventive Example 2.
- FIG. 5 is an IQ (Image Quality) and IPF (Inverse Pole Figure) photograph of Inventive Example 3 observed by EBSD
- FIG. 6 is a graph of a grain boundary ratio according to an orientation difference angle between crystal grains of Inventive Example 3.
- FIG. 7 is an IQ (Image Quality) and IPF (Inverse Pole Figure) photograph of Inventive Example 4 observed by EBSD
- FIG. 8 is a graph of a grain boundary ratio according to an orientation difference angle between crystal grains of Inventive Example 4.
- FIG. 9 is an image quality (IQ) and inverse pole figure (IPF) photograph of Comparative Example 1 observed by EBSD
- FIG. 10 is a graph of a grain boundary ratio according to an orientation difference angle between grains of Comparative Example 1.
- FIG. 11 is an IQ (Image Quality) and IPF (Inverse Pole Figure) photograph of Comparative Example 2 observed by EBSD
- FIG. 12 is a graph of a grain boundary ratio according to an orientation difference angle between grains of Comparative Example 2.
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Abstract
Description
모재 No. |
합금조성(중량%) | ||||||||||
C | Si | Mn | Cr | Mo | Al | P | S | Ni | Cu | 잔부 | |
1 | 0.070 | 1.100 | 2.10 | 0.90 | 0.01 | 0.025 | 0.009 | 0.001 | 0.02 | 0.02 | Fe |
2 | 0.090 | 0.900 | 2.00 | 0.20 | 0.20 | 0.025 | 0.009 | 0.001 | 0.01 | 0.02 | Fe |
와이어No. | 합금조성(중량%) | |||||||||||
C | Si | Mn | Cr | Mo | Al | P | S | Ni | Cu | 잔부 | 식 1 | |
1 | 0.16 | 0.04 | 1.70 | 4.80 | 0.50 | 0.004 | 0.006 | 0.001 | 0.04 | 0.14 | Fe | 317 |
2 | 0.08 | 0.09 | 1.74 | 4.92 | 0.49 | 0.008 | 0.004 | 0.003 | - | 0.30 | Fe | 337 |
3 | 0.07 | 0.06 | 1.77 | 1.35 | 0.55 | 0.009 | 0.005 | 0.004 | - | 0.34 | Fe | 495 |
4 | 0.07 | 0.37 | 1.65 | 0.50 | 0.30 | 0.006 | 0.011 | 0.006 | 3.00 | 0.25 | Fe | 511 |
5 | 0.08 | 0.08 | 1.70 | 0.04 | 0.007 | 0.010 | 0.012 | 0.005 | 0.023 | 0.19 | Fe | 585 |
6 | 0.27 | 0.04 | 1.70 | 4.80 | 0.50 | 0.004 | 0.006 | 0.001 | 0.04 | 0.14 | Fe | 295 |
[식 1] 732 - 202×C + 216×Si - 85×Mn - 37×Ni - 47×Cr - 39×Mo |
용접부재 No. |
모재 No. |
와이어 No. |
합금조성(중량%) | ||||||||||
C | Si | Mn | Cr | Mo | Al | P | S | Ni | Cu | 잔부 | |||
발명예1 | 1 | 1 | 0.10 | 0.56 | 1.87 | 2.60 | 0.22 | 0.013 | 0.008 | 0.0013 | 0.038 | 0.08 | Fe |
발명예2 | 1 | 2 | 0.08 | 0.51 | 1.82 | 2.43 | 0.21 | 0.017 | 0.011 | 0.0015 | 0.009 | 0.16 | Fe |
발명예3 | 2 | 2 | 0.08 | 0.62 | 1.90 | 1.30 | 0.24 | 0.014 | 0.013 | 0.0022 | 0.007 | 0.17 | Fe |
발명예4 | 2 | 3 | 0.08 | 0.59 | 1.90 | 0.50 | 0.26 | 0.011 | 0.011 | 0.0028 | 0.006 | 0.18 | Fe |
비교예1 | 2 | 4 | 0.08 | 0.63 | 1.80 | 0.32 | 0.21 | 0.008 | 0.015 | 0.0041 | 1.3 | 0.14 | Fe |
비교예2 | 2 | 5 | 0.08 | 0.52 | 1.80 | 0.13 | 0.06 | 0.010 | 0.013 | 0.0031 | 0.014 | 0.11 | Fe |
비교예3 | 1 | 6 | 0.17 | 0.56 | 1.87 | 2.60 | 0.22 | 0.013 | 0.008 | 0.0013 | 0.038 | 0.08 | Fe |
용접부재 No. |
모재두께 (T)(mm) |
입열량 (Q)(kJ/cm) |
미세조직 | 전체 결정립계 대비 결정립간 방위차 각도가 55˚ 이상인 고경각 결정립계의 비율(K)(%) | 평균 유효 결정립 크기 (G)(㎛) |
R |
발명예1 | 3.5 | 5.2 | AF+B+M | 40 | 3.3 | 18.1 |
발명예2 | 2.0 | 2.6 | AF+B | 53 | 6.2 | 11.2 |
발명예3 | 2.9 | 3.8 | AF+B | 50 | 5.6 | 11.6 |
발명예4 | 2.9 | 3.9 | AF+PF+B | 40 | 4.8 | 11.2 |
비교예1 | 2.9 | 3.7 | AF+PF+B | 39 | 4.8 | 10.3 |
비교예2 | 2.9 | 3.9 | AF+PF | 39 | 6.6 | 8.0 |
비교예3 | 2.0 | 3.4 | B+M+RA | 37 | 8.4 | 7.5 |
AF: 침상 페라이트, PF: 입상 페라이트, B: 베이나이트, M: 마르텐사이트, RA: 잔류 오스테나이트 R = (K / G) × (Q / T) Q = (I × E) × 0.048 / υ(I: 용접전류(A), E: 용접전압(V), υ: 용접속도(cm/min)) |
No. | 최대 하중 (MPa) |
최소 하중 (MPa) |
피로수명(Cycles) | ||||||
발명예1 | 발명예2 | 발명예3 | 발명예4 | 비교예1 | 비교예2 | 비교예3 | |||
1 | 240 | 24 | 98,430 | 118,790 | 102,638 | 미측정 | 미측정 | 미측정 | 미측정 |
2 | 220 | 22 | 123,528 | 155,943 | 137,269 | 72,109 | 미측정 | 미측정 | 미측정 |
3 | 200 | 20 | 213,637 | 241,957 | 226,372 | 131,479 | 미측정 | 미측정 | 미측정 |
4 | 180 | 18 | 357,832 | 473,419 | 382,836 | 169,252 | 107,392 | 84,738 | 147,392 |
5 | 170 | 17 | 824,365 | 2,000,000 | 2,000,000 | 231,985 | 162,498 | 126,647 | 212,637 |
6 | 160 | 16 | 2,000,000 | 2,000,000 | 2,000,000 | 294,719 | 217,603 | 158,603 | 276,423 |
7 | 140 | 14 | 2,000,000 | 2,000,000 | 2,000,000 | 2,000,000 | 327,626 | 252,512 | 537,246 |
8 | 120 | 12 | 2,000,000 | 2,000,000 | 2,000,000 | 2,000,000 | 694,714 | 361,843 | 2,000,000 |
9 | 110 | 11 | 2,000,000 | 2,000,000 | 2,000,000 | 2,000,000 | 2,000,000 | 853,274 | 2,000,000 |
10 | 100 | 10 | 2,000,000 | 2,000,000 | 2,000,000 | 2,000,000 | 2,000,000 | 2,000,000 | 2,000,000 |
용접부재 No. |
측정지점 | 잔류응력(MPa) | ||||
1.0mm | 2.0mm | 3.0mm | 4.0mm | 5.0mm | ||
발명예1 | 비드시작부 | -362.4 | -309.4 | -274.9 | -270.5 | -370.5 |
비드중심부 | -254.7 | -198.6 | -247.6 | -195.6 | -284.3 | |
비드종단부 | -424.8 | -362.9 | -460.6 | -522.3 | -492.3 | |
발명예2 | 비드시작부 | -170.6 | -231.0 | -174.1 | -207.4 | -264.2 |
비드중심부 | -147.9 | -221.6 | -141.9 | -139.2 | -102.3 | |
비드종단부 | -110.2 | -147.0 | -167.9 | -130.3 | -114.6 | |
발명예3 | 비드시작부 | -196.3 | -280.7 | -260.3 | -363.5 | -402.9 |
비드중심부 | -389.1 | -247.6 | -359.4 | -316.8 | -295.7 | |
비드종단부 | -424.3 | -409.2 | -519.9 | -506.5 | -435.1 | |
발명예4 | 비드시작부 | -121.3 | -178.6 | -157.5 | -159.0 | -194.9 |
비드중심부 | -93.0 | -129.9 | -182.4 | -134.0 | -103.4 | |
비드종단부 | -239.4 | -215.2 | -186.7 | -181.8 | -217.8 | |
비교예1 | 비드시작부 | 285.1 | 144.6 | 194.3 | 218.2 | 153.2 |
비드중심부 | 184.2 | 122.8 | 170.4 | 129.8 | 100.6 | |
비드종단부 | 218.2 | 228.1 | 229.2 | 202.9 | 196.4 | |
비교예2 | 비드시작부 | 338.3 | 354.6 | 318.2 | 295.4 | 175.6 |
비드중심부 | 243.3 | 220.5 | 225.4 | 274.6 | 216.8 | |
비드종단부 | 221.4 | 284.6 | 251.6 | 135.7 | 110.6 | |
비교예3 | 비드시작부 | -75.2 | -87.6 | -67.3 | -56.7 | -83.5 |
비드중심부 | -56.7 | -43.8 | -62.9 | -53.4 | -73.6 | |
비드종단부 | -84.6 | -72.4 | -87.2 | -86.3 | -73.4 |
Claims (14)
- 중량%로, C: 0.06~0.16%, Si: 0.001~0.2%, Mn: 1.6~1.9%, Cr: 1.2~6.0%, Mo: 0.4~0.65%, P: 0.015% 이하(0%는 제외), S: 0.01% 이하(0%는 제외), Al: 0.20% 이하(0%는 제외), 잔부 Fe 및 기타 불가피한 불순물을 포함하고,하기 식 1의 값이 300~500인 피로저항특성 및 용접부의 잔류응력으로 인한 변형에 대한 저항성이 우수한 가스 실드 아크 용접용 와이어.[식 1] 732 - 202×C + 216×Si - 85×Mn - 37×Ni - 47×Cr - 39×Mo(단, 상기 [식 1]에서 각 원소의 함량은 중량%임.)
- 청구항 1에 있어서,상기 와이어는 추가로 Ni: 0.40% 이하 및 Cu: 0.50% 이하 중 1종 이상을 포함하는 피로저항특성 및 용접부의 잔류응력으로 인한 변형에 대한 저항성이 우수한 가스 실드 아크 용접용 와이어.
- 청구항 1에 있어서,상기 와이어는 솔리드 와이어, 메탈 코어드 및 플럭스 코어드 와이어 중 하나인 피로저항특성 및 용접부의 잔류응력으로 인한 변형에 대한 저항성이 우수한 가스 실드 아크 용접용 와이어.
- 모재 및 용접부를 포함하는 용접부재로서,상기 용접부는,중량%로, C: 0.05~0.16%, Si: 0.001~1.0%, Mn: 1.4~2.5%, Cr: 0.4~5.0%, Mo: 0.1~1.5%, P: 0.015% 이하(0%는 제외), S: 0.01% 이하(0%는 제외), Al: 0.20% 이하(0%는 제외), 잔부 Fe 및 기타 불가피한 불순물을 포함하고,베이나이트; 침상 페라이트;와 입상 페라이트, 마르텐사이트 및 잔류 오스테나이트 중 하나 이상;을 포함하는 미세조직을 가지며,상기 미세조직은 평균 유효 결정립 크기가 10㎛ 이하이고, 전체 결정립계 대비 결정립간 방위차 각도(misorientation angle)가 55˚ 이상인 고경각 결정립계의 비율이 40% 이상이며,하기 식 2로 표현되는 R의 값이 10.5~18.5인 피로저항특성 및 용접부의 잔류응력으로 인한 변형에 대한 저항성이 우수한 용접부재.[식 2] R = (K / G) × (Q / T)(단, 상기 [식 2]에서 K는 용접부 내 전체 결정립계 대비 결정립간 방위차 각도가 55˚ 이상인 결정립계의 비율(%), G는 용접부의 평균 유효 결정립 크기(㎛), T는 모재의 두께(mm) 및 Q는 용접입열량(kJ/cm)를 의미하며, 상기 Q는 하기 [식 3]으로 정의됨.)[식 3] Q = (I × E) × 0.048 / υ(단, 상기 [식 3]에서 I는 용접전류(A), E는 용접전압(V) 및 υ는 용접속도(cm/min)를 의미함.)
- 청구항 4에 있어서,상기 용접부는 추가로 Ni: 0.40% 이하 및 Cu: 0.50% 이하 중 1종 이상을 포함하는 피로저항특성 및 용접부의 잔류응력으로 인한 변형에 대한 저항성이 우수한 용접부재.
- 청구항 4에 있어서,상기 용접부는 피로강도가 140MPa 이상인 피로저항특성 및 용접부의 잔류응력으로 인한 변형에 대한 저항성이 우수한 용접부재.
- 청구항 4에 있어서,상기 용접부는 용접비드의 끝단부로부터 모재와 수직한 방향으로 5mm 이내의 영역의 압축 잔류응력이 90MPa 이상인 피로저항특성 및 용접부의 잔류응력으로 인한 변형에 대한 저항성이 우수한 용접부재.
- 청구항 4에 있어서,상기 모재는 중량%로, C: 0.05~0.13%, Si: 0.2~2.0%, Mn: 1.3~3.0%, Cr: 0.01~2.0%, Mo: 0.01~2.0%, Al: 0.01~0.1%, P: 0.001~0.05%, S: 0.001~0.05%, 잔부 Fe 및 기타 불가피한 불순물을 포함하는 피로저항특성 및 용접부의 잔류응력으로 인한 변형에 대한 저항성이 우수한 용접부재.
- 청구항 8에 있어서,상기 모재는 추가로 Ti: 0.01~0.2% 및 Nb: 0.01~0.1% 중 1종 이상을 포함하는 피로저항특성 및 용접부의 잔류응력으로 인한 변형에 대한 저항성이 우수한 용접부재.
- 청구항 4에 있어서,상기 모재는 0.8~4.0mm의 두께를 갖는 피로저항특성 및 용접부의 잔류응력으로 인한 변형에 대한 저항성이 우수한 용접부재.
- 2매 이상의 모재를 준비한 뒤, 용접 와이어를 이용하여 가스 실드 아크 용접하는 용접부재의 제조방법으로서,상기 용접 와이어는 중량%로, C: 0.06~0.16%, Si: 0.001~0.2%, Mn: 1.6~1.9%, Cr: 1.2~6.0%, Mo: 0.4~0.65%, P: 0.015% 이하(0%는 제외), S: 0.01% 이하(0%는 제외), Al: 0.20% 이하(0%는 제외), 잔부 Fe 및 기타 불가피한 불순물을 포함하고, 하기 식 1의 값이 300~500이고,상기 가스 실드 아크 용접시, 하기 식 4의 값이 1.2~1.6이 되도록 하는 피로저항특성 및 용접부의 잔류응력으로 인한 변형에 대한 저항성이 우수한 용접부재의 제조방법.[식 1] 732 - 202×C + 216×Si - 85×Mn - 37×Ni - 47×Cr - 39×Mo(단, 상기 [식 1]에서 각 원소의 함량은 중량%임.)[식 4] Q/T(단, 상기 [식 4]에서 T는 모재의 두께(mm) 및 Q는 용접입열량(kJ/cm)를 의미하고, 상기 Q는 하기 [식 3]으로 정의됨.)[식 3] Q = (I × E) × 0.048 / υ(단, 상기 [식 3]에서 I는 용접전류(A), E는 용접전압(V) 및 υ는 용접속도(cm/min)를 의미함.)
- 청구항 11에 있어서,상기 모재는 중량%로, C: 0.05~0.13%, Si: 0.2~2.0%, Mn: 1.3~3.0%, Cr: 0.01~2.0%, Mo: 0.01~2.0%, Al: 0.01~0.1%, P: 0.001~0.05%, S: 0.001~0.05%, 잔부 Fe 및 기타 불가피한 불순물을 포함하는 피로저항특성 및 용접부의 잔류응력으로 인한 변형에 대한 저항성이 우수한 용접부재의 제조방법.
- 청구항 12에 있어서,상기 모재는 추가로 Ti: 0.01~0.2% 및 Nb: 0.01~0.1% 중 1종 이상을 포함하는 피로저항특성 및 용접부의 잔류응력으로 인한 변형에 대한 저항성이 우수한 용접부재의 제조방법.
- 청구항 11에 있어서,상기 모재는 0.8~4.0mm의 두께를 갖는 피로저항특성 및 용접부의 잔류응력으로 인한 변형에 대한 저항성이 우수한 용접부재의 제조방법.
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JPH08108281A (ja) * | 1994-10-05 | 1996-04-30 | Japan Steel & Tube Constr Co Ltd | ガスシールドアーク溶接法によるレールの溶接方法 |
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