CN115338558A - Slag gas combined protection flux-cored wire and postweld heat treatment method thereof - Google Patents
Slag gas combined protection flux-cored wire and postweld heat treatment method thereof Download PDFInfo
- Publication number
- CN115338558A CN115338558A CN202210966092.3A CN202210966092A CN115338558A CN 115338558 A CN115338558 A CN 115338558A CN 202210966092 A CN202210966092 A CN 202210966092A CN 115338558 A CN115338558 A CN 115338558A
- Authority
- CN
- China
- Prior art keywords
- equal
- percent
- cored wire
- flux
- less
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
- 239000002893 slag Substances 0.000 title claims abstract description 38
- 238000000034 method Methods 0.000 title claims abstract description 36
- 238000010438 heat treatment Methods 0.000 title claims abstract description 25
- 238000003466 welding Methods 0.000 claims abstract description 71
- 229910052751 metal Inorganic materials 0.000 claims abstract description 47
- 239000002184 metal Substances 0.000 claims abstract description 47
- 239000000843 powder Substances 0.000 claims abstract description 37
- 239000003795 chemical substances by application Substances 0.000 claims abstract description 26
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 24
- 239000010959 steel Substances 0.000 claims abstract description 24
- 238000005275 alloying Methods 0.000 claims abstract description 11
- 239000003381 stabilizer Substances 0.000 claims abstract description 10
- 238000005496 tempering Methods 0.000 claims abstract description 8
- 230000007704 transition Effects 0.000 claims description 18
- 229910045601 alloy Inorganic materials 0.000 claims description 14
- 239000000956 alloy Substances 0.000 claims description 14
- 239000011572 manganese Substances 0.000 claims description 10
- 229910000640 Fe alloy Inorganic materials 0.000 claims description 9
- 229910052761 rare earth metal Inorganic materials 0.000 claims description 9
- 239000004579 marble Substances 0.000 claims description 8
- 150000002910 rare earth metals Chemical class 0.000 claims description 7
- 239000003814 drug Substances 0.000 claims description 6
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 5
- 229910004298 SiO 2 Inorganic materials 0.000 claims description 5
- 229910002115 bismuth titanate Inorganic materials 0.000 claims description 5
- 229910052796 boron Inorganic materials 0.000 claims description 5
- WUKWITHWXAAZEY-UHFFFAOYSA-L calcium difluoride Chemical compound [F-].[F-].[Ca+2] WUKWITHWXAAZEY-UHFFFAOYSA-L 0.000 claims description 5
- 229910052799 carbon Inorganic materials 0.000 claims description 5
- 239000010436 fluorite Substances 0.000 claims description 5
- 229910052720 vanadium Inorganic materials 0.000 claims description 5
- 229910016036 BaF 2 Inorganic materials 0.000 claims description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 4
- 229910052691 Erbium Inorganic materials 0.000 claims description 4
- 238000011049 filling Methods 0.000 claims description 4
- 239000004576 sand Substances 0.000 claims description 4
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N titanium dioxide Inorganic materials O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 claims description 4
- 229910052845 zircon Inorganic materials 0.000 claims description 4
- GFQYVLUOOAAOGM-UHFFFAOYSA-N zirconium(iv) silicate Chemical compound [Zr+4].[O-][Si]([O-])([O-])[O-] GFQYVLUOOAAOGM-UHFFFAOYSA-N 0.000 claims description 4
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 3
- 229910004261 CaF 2 Inorganic materials 0.000 claims description 3
- 229910019589 Cr—Fe Inorganic materials 0.000 claims description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 3
- 229910018619 Si-Fe Inorganic materials 0.000 claims description 3
- 229910008289 Si—Fe Inorganic materials 0.000 claims description 3
- 229910010413 TiO 2 Inorganic materials 0.000 claims description 3
- 238000004140 cleaning Methods 0.000 claims description 3
- 238000001035 drying Methods 0.000 claims description 3
- UYAHIZSMUZPPFV-UHFFFAOYSA-N erbium Chemical compound [Er] UYAHIZSMUZPPFV-UHFFFAOYSA-N 0.000 claims description 3
- 239000010439 graphite Substances 0.000 claims description 3
- 229910002804 graphite Inorganic materials 0.000 claims description 3
- 239000000203 mixture Substances 0.000 claims description 3
- 229910002091 carbon monoxide Inorganic materials 0.000 claims description 2
- 238000002156 mixing Methods 0.000 claims description 2
- 238000005096 rolling process Methods 0.000 claims description 2
- 229910052742 iron Inorganic materials 0.000 claims 1
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims 1
- 239000007789 gas Substances 0.000 abstract description 28
- 229910052739 hydrogen Inorganic materials 0.000 abstract description 14
- 239000001257 hydrogen Substances 0.000 abstract description 14
- QSHDDOUJBYECFT-UHFFFAOYSA-N mercury Chemical compound [Hg] QSHDDOUJBYECFT-UHFFFAOYSA-N 0.000 abstract description 6
- 229910052753 mercury Inorganic materials 0.000 abstract description 6
- 238000009792 diffusion process Methods 0.000 abstract description 3
- 125000004435 hydrogen atom Chemical class [H]* 0.000 abstract 1
- 230000008569 process Effects 0.000 description 21
- 239000012071 phase Substances 0.000 description 19
- 229910001566 austenite Inorganic materials 0.000 description 15
- 239000000047 product Substances 0.000 description 11
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 10
- 230000000694 effects Effects 0.000 description 8
- 238000013461 design Methods 0.000 description 6
- KRHYYFGTRYWZRS-UHFFFAOYSA-M Fluoride anion Chemical compound [F-] KRHYYFGTRYWZRS-UHFFFAOYSA-M 0.000 description 5
- 238000001816 cooling Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 230000009466 transformation Effects 0.000 description 5
- BVKZGUZCCUSVTD-UHFFFAOYSA-L Carbonate Chemical compound [O-]C([O-])=O BVKZGUZCCUSVTD-UHFFFAOYSA-L 0.000 description 4
- 238000010276 construction Methods 0.000 description 4
- 229910052760 oxygen Inorganic materials 0.000 description 4
- 239000001301 oxygen Substances 0.000 description 4
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 3
- 230000008901 benefit Effects 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000010891 electric arc Methods 0.000 description 3
- 230000006870 function Effects 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 238000002360 preparation method Methods 0.000 description 3
- 239000007787 solid Substances 0.000 description 3
- VTYYLEPIZMXCLO-UHFFFAOYSA-L Calcium carbonate Chemical compound [Ca+2].[O-]C([O-])=O VTYYLEPIZMXCLO-UHFFFAOYSA-L 0.000 description 2
- 239000011324 bead Substances 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 150000002431 hydrogen Chemical class 0.000 description 2
- 229910052500 inorganic mineral Inorganic materials 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 239000011707 mineral Substances 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
- 230000006911 nucleation Effects 0.000 description 2
- 238000010899 nucleation Methods 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- GPPXJZIENCGNKB-UHFFFAOYSA-N vanadium Chemical compound [V]#[V] GPPXJZIENCGNKB-UHFFFAOYSA-N 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 229910018643 Mn—Si Inorganic materials 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 125000004429 atom Chemical group 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 229910000019 calcium carbonate Inorganic materials 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 230000009194 climbing Effects 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000026058 directional locomotion Effects 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 229910001092 metal group alloy Inorganic materials 0.000 description 1
- 238000005272 metallurgy Methods 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 230000005012 migration Effects 0.000 description 1
- 238000013508 migration Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- -1 naF Substances 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 229910052755 nonmetal Inorganic materials 0.000 description 1
- 238000006213 oxygenation reaction Methods 0.000 description 1
- 230000005501 phase interface Effects 0.000 description 1
- 239000004033 plastic Substances 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
- OGIDPMRJRNCKJF-UHFFFAOYSA-N titanium oxide Inorganic materials [Ti]=O OGIDPMRJRNCKJF-UHFFFAOYSA-N 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
- B23K35/3053—Fe as the principal constituent
-
- 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
- B23K35/40—Making wire or rods for soldering or welding
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Nonmetallic Welding Materials (AREA)
Abstract
The invention provides a slag gas combined protection flux-cored wire and a postweld heat treatment method thereof. The flux-cored wire comprises a 4Ni steel sheath and a powder core, wherein the powder core accounts for 18-20% of the total weight of the flux-cored wire; the powder core consists of 28.5-37.0% of slagging agent, 1.5-2% of gas making agent, 1.5-2% of arc stabilizer, 25.5-55.5% of alloying agent and the balance of Fe powder according to mass percentage. The gas-shielded O-type slag-gas combined protection flux-cored wire with the diameter of 1.4mm is adopted, the welding heat input is increased to 30kJ/cm from 10kJ/cm, the specific postweld tempering heat treatment (480-580 ℃, 2-4 h) is carried out, the tensile strength of the welding deposited metal at room temperature reaches 1000-1020MPa, the yield ratio is 0.82-0.85, the product of strength and elongation is more than or equal to 15 GPa%, and the hydrogen diffusion is less than or equal to 4ml/100g (mercury method).
Description
Technical Field
The invention belongs to the technical field of development of welding materials, and particularly relates to a gas-shielded O-shaped flux-cored wire, a preparation method and a postweld heat treatment method thereof, which are used for meeting the requirements that a metal structure at a welding seam welded by using the flux-cored wire can have the advantages of low yield ratio, high product of strength and elongation, giga-grade and ultralow hydrogen through postweld heat treatment.
Background
In recent years, high-strength steel for domestic (major) engineering construction is developing in a direction of light weight and high reinforcement, and particularly, in dynamic load bearing parts such as vehicle engineering, machinery, water conservancy and hydropower and the like, the high yield strength of the high-strength steel is fully utilized in structural design to further reduce the design thickness and weight of the parts. At present, the application of 1GPa (gigapascal) grade high-strength steel enters a substantial design link in key welding structures such as a commercial vehicle bearing beam frame, a hoisting boom, a hydroelectric volute and the like. With the improvement of the service grade of the steel plate and the further strictness of the service working condition of the steel plate in the future, higher requirements are put forward on the safety margin of the high-strength steel welding joint.
At present, the construction of domestic welding engineering is often limited by construction environment and construction period, and welding materials are expected to be suitable for large heat input welding of field environment, so that the welding efficiency of large-scale structural members is improved. In view of welding equipment and process, the manual arc welding and the gas shielded welding can conveniently realize field welding, but the welding efficiency of the manual arc welding is lower. Although the gas shielded welding of the solid welding wire has advantages over the manual arc welding in the aspect of improving the welding efficiency, the gas shielded welding of the solid welding wire cannot realize slag-gas combined protection of a molten pool, and cannot ensure the oxygenation of a welding seam in the efficient welding process. Particularly, from the perspective of welding heat input, the welding heat input range of both manual arc welding and solid gas shielded welding is 10-20kJ/cm, and once the welding heat input is more than 20kJ/cm, various problems of large residual stress, low toughness reserve, poor strength and plasticity and the like are brought to a weld joint, particularly a high-strength steel weld joint, and the structural safety of a 1 GPa-grade high-strength steel weld part is seriously influenced.
Therefore, the flux-cored wire is urgently needed to be developed and designed, the welding efficiency is improved, the welding pool is effectively protected, and the safety margin of the 1GPa grade high-strength steel welding seam metal under the condition of large heat input is improved.
Disclosure of Invention
The invention aims to provide a gas-shielded O-type slag-gas combined protection flux-cored wire, which improves the welding efficiency and the application range of heat input, and the super-strong steel metal structure welded by using the flux-cored wire has the advantages of ultralow hydrogen and Gepa grade with low yield ratio and high strength-plasticity product through postweld heat treatment, in particular, the tensile strength of deposited metal at room temperature is more than or equal to 1000MPa, the yield ratio is less than or equal to 0.85, the strength-plasticity product is more than or equal to 15 GPa%, and the diffusible hydrogen is less than or equal to 4ml/100g (mercury method) through postweld tempering heat treatment (480-580 ℃ for 2-4 h) under the condition that the heat input is increased from 10kJ/cm to 30 kJ/cm.
In order to achieve the above purpose, the content of the invention is as follows:
the invention provides a giga-pascal grade slag gas combined protection flux-cored wire capable of realizing low yield ratio and high product of strength and elongation after welding, which is characterized in that: the flux-cored wire comprises a 4Ni steel sheath and a powder core, wherein the powder core accounts for 18-20% of the total weight of the flux-cored wire; the powder core consists of 28.5-37.0% of slagging agent, 1.5-2% of gas making agent, 1.5-2% of arc stabilizer, 25.5-55.5% of alloying agent and the balance of Fe powder by mass percentage.
Further preferably, the mass percent of C in the 4Ni steel outer skin is less than or equal to 0.02%, the mass percent of Si is less than or equal to 0.02%, the mass percent of Mn is less than or equal to 0.1%, the mass percent of S + P is less than or equal to 0.002%, the mass percent of Ni is about 4.0%, and the balance is Fe.
More preferably, the slag former contains marble, fluorite, rutile, zircon sand and Er 2 O 3 And bismuth titanate, the respective addition amounts of which account for the total mass of the medicine powder core are as follows: 16% -18%,8% -9%,2% -3%, 1% -3% and 0.5% -1%, which form CaO-CaF 2 -TiO 2 -ZrO 2 -SiO 2 -Er 4 S 3 Mainly designed for slag system.
More preferably, the gas generating agent further contains Na in addition to the marble in the slag forming agent 2 CO 3 、K 2 CO 3 And BaCO 3 At least 2.
More preferably, the arc stabilizer is Na in the gas generating agent 2 CO 3 、K 2 CO 3 In addition, it also contains NaF, KF and BaF 2 At least 2 of (a).
More preferably, the alloying agent consists of graphite, 75% Si-Fe alloy, atomized manganese powder, 50% Cr-Fe alloy, 59% Mo-Fe alloy, ni powder, cu powder, 50% V-Fe alloy, 20% B-Fe alloy, C (transition coefficient about 0.6), si (transition coefficient about 0.8), mn (transition coefficient about 0.85), cr (transition coefficient about 0.95), mo (transition coefficient about 0.98), ni (transition coefficient about 0.99), cu (transition coefficient about 0.9) for transition into the deposited metal, to obtain the following deposited metal components in mass percent: c is more than or equal to 0.08 percent and less than or equal to 0.1 percent, si is more than or equal to 0.5 percent and less than or equal to 0.5 percent, mn is more than or equal to 1.8 percent and less than or equal to 1.9 percent, S + P is less than or equal to 0.02 percent, cr is more than or equal to 0.5 percent and less than or equal to 0.6 percent, mo is more than or equal to 0.5 percent and less than or equal to 0.6 percent, ni is more than or equal to 4 percent and less than or equal to 8 percent, cu is more than or equal to 0.2 percent and less than or equal to 0.3 percent, other alloy elements are less than 0.06 percent, and the balance is Fe. The other alloy elements comprise elements such as vanadium, boron, rare earth erbium and the like.
The invention also provides a preparation method of the slag gas combined protection flux-cored wire, which is characterized by comprising the following steps:
rolling and forming a 4Ni steel sheath, filling medicinal powder, and performing roller type closing and multi-pass drawing to obtain the slag-gas combined protection flux-cored wire; wherein the content of the first and second substances,
carrying out the working procedure treatment of absolute ethyl alcohol cleaning and drying for 2-3 times before the 4Ni steel outer skin is rolled and formed;
baking the components of the medicinal powder before mixing.
Preferably, the O-shaped flux-cored wire with the diameter of 1.4mm is finally prepared after the multi-pass drawing.
The invention also provides a postweld heat treatment method for gas shielded welding by adopting the slag-gas combined protection flux-cored wire, which is characterized by comprising the following steps of:
arc welding was performed in an atmosphere of 80% Ar +20% CO2 mixed gas to obtain a weld deposit metal, followed by tempering heat treatment at a temperature of 480 to 580 ℃ for 2 to 4 hours.
By adopting the O-shaped flux-cored wire with the diameter of 1.4mm, even if the heat input is increased to 30kJ/cm from 10kJ/cm, through specific postweld tempering heat treatment (480-580 ℃ C., 2-4 h), the tensile strength of the welding deposited metal at room temperature reaches 1000-1020MPa, the yield ratio is 0.82-0.85, the product of strength and elongation is more than or equal to 15 GPa%, and the hydrogen diffusion is less than or equal to 4ml/100g (mercury method).
Detailed Description
In order to realize the above-mentioned invention contents, the invention adopts the following specific implementation modes:
an "O" pattern 80% of 1.4mm diameter Ar +20% CO 2 The flux-cored wire comprises a 4Ni steel sheath and a powder core, wherein the powder core accounts for 18-20% of the total weight of the flux-cored wire.
The mass percentage of C in the 4Ni steel outer skin is less than or equal to 0.02 percent, the mass percentage of Si is less than or equal to 0.02 percent, the mass percentage of Mn is less than or equal to 0.1 percent, the mass percentage of S + P is less than or equal to 0.002 percent, the mass percentage of Ni is about 4.0 percent, and the balance is Fe. In order to obtain the ultra-low hydrogen welding rod and ensure that the surface of the 4Ni steel is free of oil stains, the outer skin of the 4Ni steel is subjected to the process of absolute alcohol cleaning and drying for 2-3 times.
The components of the powder core consist of a slag former, a gas former, an arc stabilizer, an alloying agent and Fe powder.
Marble, fluorite, rutile, zircon sand and rare earth element oxide Er in slag former 2 O 3 And the addition amount of the bismuth titanate accounts for the percentage of the total mass of the medicine powder core in turn: 16% -18%,8% -9%,2% -3%, 1% -3% and 0.5% -1%, which form CaO-CaF 2 -TiO 2 -ZrO 2 -SiO 2 -Er 4 S 3 Mainly designed for slag system.
The gas former contains Na in addition to the marble in the slag former 2 CO 3 、K 2 CO 3 And BaCO 3 At least 2 kinds of carbonate are added, and the total addition amount is not more than 2% of the total mass percent of the medicine powder core, in order to exert the effectThe content of the additive should not be lower than 1.5 percent.
The arc stabilizer removes Na in the gas generating agent 2 CO 3 And K 2 CO 3 In addition, naF, KF and BaF 2 The total addition amount of the fluoride is at least 2 and is not more than 2 percent of the total mass percent of the medicine powder core, and the content of the fluoride is not less than 1.5 percent in order to play the function.
Alloying agents consist of graphite, 75% Si-Fe alloy, atomized manganese powder, 50% Cr-Fe alloy, 59% Mo-Fe alloy, ni powder, cu powder, 50% V-Fe alloy, 20% B-Fe alloy species for transition into deposited metals, C (transition coefficient about 0.6), si (transition coefficient about 0.8), mn (transition coefficient about 0.85), cr (transition coefficient about 0.95), mo (transition coefficient about 0.98), ni (transition coefficient about 0.99), cu (transition coefficient about 0.9) and Fe elements, ensuring the following deposited metal components (mass%): c is more than or equal to 0.08 percent and less than or equal to 0.1 percent, si is more than or equal to 0.5 percent and less than or equal to 0.5 percent, mn is more than or equal to 1.8 percent and less than or equal to 1.9 percent, S + P is less than or equal to 0.02 percent, cr is more than or equal to 0.5 percent and less than or equal to 0.6 percent, mo is more than or equal to 0.5 percent and less than or equal to 0.6 percent, ni is more than or equal to 4 percent and less than or equal to 8 percent, cu is more than or equal to 0.2 percent and less than or equal to 0.3 percent, other alloy elements are less than 0.06 percent, and the balance of Fe. The other alloying elements include vanadium, boron, and rare earth erbium elements. Except Fe powder, the alloying agent accounts for 25.5 to 55.5 percent of the total mass of the medicine powder core.
In order to obtain the ultralow-hydrogen flux-cored wire, the carbonate, fluoride mineral powder and alloy agent such as marble, fluorite, bismuth titanate, gas former, arc stabilizer and the like in the slag former are baked for 3 to 4 hours at the temperature of between 300 and 350 ℃.
Similarly, rutile, zircon sand and rare earth element oxide Er in the slagging constituent 2 O 3 And baking the rest of the mineral powder at 180-220 ℃ for 2-3h.
The components in the flux-cored wire are fully and uniformly mixed, and then the O-shaped flux-cored wire is prepared according to the filling rate (the percentage of the flux-cored wire in the total weight of the flux-cored wire) of 18-20%. The preparation process comprises the steps of Ni steel outer skin roll forming, powder filling, roller type closing and multi-pass drawing, and finally the O-shaped flux-cored wire with the diameter of 1.4mm is manufactured.
In order to ensure that the O-shaped flux-cored wire designed by the invention realizes the low yield ratio of deposited metal and simultaneously ensures that the strength grade of the deposited metal reaches the gigapascal grade, namely the tensile strength is required to reach more than 1000MPa at the same time, a certain content of austenite enlarging elements such as C, mn, ni and the like are required to be added, the heat treatment temperature of 480-580 ℃ is in a two-phase region, the hard phase and the soft phase are obtained under the air cooling condition through redistribution of the austenite enlarging elements for 2-4h, and thus the preferential yield of the soft phase in the material stretching process is realized, and the aim of low yield strength is fulfilled.
In the heat treatment process of 400-580 ℃, a large amount of austenite enlarging elements are enriched in a 'hard phase', wherein C is diffused more uniformly, but a brittle hard phase is easily formed in the cooling process, so that the O-shaped flux-cored wire adopts a low-carbon design during the design of an alloying agent, and the mass percentage of C in deposited metal is higher than 0.1%, which is unfavorable for toughness. Mn is also an austenitizing element, but because the atomic radius is larger, the diffusion migration rate is lower than that of C, the segregation is easy to occur at a phase interface, mn-Fe intermetallic compounds are easy to form in the temperature range of 100-200 ℃ in the cooling process, the toughness is also unfavorable, but the combination of Mn and Si is a main deoxidation mode of weld metal, the oxygen enrichment of the weld is caused by excessively low Mn content, and the comprehensive mechanical property after welding is not favorable, so the mass percentage of Mn in deposited metal is designed to be 1.8-1.9%. Considering the influence of Mn-Si combined deoxidation capacity and Mn/Si ratio on the fluidity of the welding pool, and simultaneously aiming at improving the escape of gas, especially hydrogen, in the welding pool, the fluidity and the quietness of the welding pool with the Mn/Si ratio set between 3.6 and 4.75 are better, therefore, the mass percent of Si in the deposited metal is preferably designed to be between 0.4 and 0.5 percent. The main functions of Cr and Mo in deposited metal are to improve hardenability and ensure that the Gippe-level welding material has certain yield strength, but the effect is not obvious when the content is too low, and carbide is easily formed with C element when the content is too high, so that the impact toughness is deteriorated, and therefore, the mass percentage range of Cr and Mo in the deposited metal is between 0.5 and 0.6 percent. Ni is the main alloy element for realizing low yield ratio, can obviously reduce the phase change point of heat treatment deposited metal components, and reduces the temperature window of a two-phase region. When the Ni content reaches 4%, the tempering heat treatment temperature is 480 ℃, and the two-phase region can be entered, and the reverse transformation austenite enriched with the austenitizing enlarged element Ni at room temperature is formed, which is beneficial to improving the tensile strength and reducing the yield ratio. However, when the Ni content exceeds 8% and the tempering temperature is higher than 580 ℃, the weld material deposited metal is reduced in tensile strength due to an excessive austenite structure, and therefore, the reasonable composition range of Ni is 4% to 8%.
In order to improve the uniform elongation in the drawing process after the heat treatment of the deposited metal, 0.2 to 0.3 percent of Cu is added in the deposited metal besides the reversed austenite obtained by the heat treatment in the two-phase region. Although Cu is an austenite phase region expanding element, the addition amount of 0.2-0.3% is not enough to significantly expand the austenite region, and the main purpose of Cu is to realize element distribution in the heat treatment process of deposited metal, stabilize reverse transformation austenite, and be dissolved in the reverse transformation austenite in the cooling process, and the Cu-based alloy is characterized in that: the deposited metal after heat treatment can be subjected to plastic deformation preferentially in the stretching process due to the existence of reverse transformed austenite so as to reduce the yield strength; but Cu atoms in the reverse transformed austenite can be gradually and uniformly separated out to form an epsilon-Cu phase and precipitate in the deformed reverse transformed austenite in the deformation process, so that the uniform elongation in the stretching deformation process is further improved; with the increase of the deformation process, the epsilon-Cu phase plays a role in preventing dislocation from sliding and climbing in the reverse transformed austenite, so that the reverse transformed austenite is induced to generate martensite phase transformation in the stretching process, the tensile strength is further improved, and the product of strength and elongation in the final heat treatment state deposited metal stretching process is remarkably improved.
The other alloy elements with the total content not more than 0.06 percent comprise V, B, rare earth Er elements and the like. Metal V micro-addition V capable of separating out micro-nano scale in welding seam metal cooling stage x C y The precipitated phase is combined with the subsequent B element to be used for refining the grain sizes of the BCC and FCC structural phases and simultaneously plays the role of dispersion precipitation strengthening, the mass percent of V in the deposited metal is preferably controlled to be 0.02-0.03%, if the content is too low, the V element exists in a solid solution form, and the V element exists in a solid solution form x C y Less precipitated phase, no effect of refining crystal grains, over high content, serious solidification of C element, reduced weld metal strength, and V x C y The precipitated phase is easy to be coarse and is easy to be aggregated in a grain boundary,embrittling the weld metal. The main purpose of adding the non-metal B element is to improve the hardenability of the deposited metal, the mass percent of B in the deposited metal is preferably controlled to be 0.0015-0.002%, if the content is too low, B can not effectively inhibit the formation of a eutectoid high-temperature phase under the welding state structure of the deposited metal, and the toughness of the deposited metal in the welding state is not favorably improved; the excessive content can improve the yield of Mn and Si in the molten pool metallurgy process, and also embrittle the deposited metal in a welding state. The rare earth Er element is added by adding Er oxide Er 2 O 3 And (4) realizing. The mass percent of Er in the deposited metal is controlled to be between 0.02 and 0.028 percent. Er added in slagging agent 2 O 3 Under the action of the high temperature of the welding arc (the temperature of the arc column reaches 5000-30000K), the following reaction formula is promoted to be carried out to the right: the formed rare earth Er element has higher surface activity, is easy to absorb molten drops and reduce the surface tension thereof, and obviously reduces the welding spatter in short circuit transition. In addition, the rare earth Er element preferentially reacts with S in the molten pool to form a product with most Er 4 S 3 The form of the (B) is in a slag system, a small part of the (B) is remained in weld metal to form fine inclusions, and the (B) and B are combined to inhibit proeutectoid ferrite nucleation in the subsequent weld solid phase transformation process, so that acicular ferrite nucleation is promoted, and the (S) impurity element is reduced, and meanwhile, the toughness is improved. The formed oxygen element part forms CO with carbon element in the welding seam, and then forms CO with oxygen element in the electric arc secondarily 2 Partial formation of SiO with Si 2 And enters the slag system.
Er 2 O 3 →2Er(g)+3O(g)
4Er+3S→Er 4 S 3
C+O→CO
CO+[O]→CO 2 (g)
Si+2O→SiO 2
In the slag system, siO 2 The source of the slag-forming agent not only participates in the metallurgical deoxidation of the welding seam, but also contains SiO 2 The components have the functions of regulating the pH value of the slag system and improving the activity of the slag.
TiO in slag system 2 Can realize thatSlagging, improving the covering performance and slag detachability of the welding slag, improving the stability of the electric arc and reducing splashing.
ZrO in slag systems 2 Can also realize slag formation, has high melting point and is mainly used for properly adjusting the melting point of slag.
The CaO in the slag system is mainly obtained by decomposing calcium carbonate in the marble and is mainly used for slagging.
CaF in slag system 2 The fluoride mainly comes from fluorite and the like, is mainly used for slagging and adjusting the pH value, has excessive dosage and seriously deteriorates the stability of the welding arc.
Adding bismuth titanate (Bi) in small amount into the medicinal powder core 4 Ti 3 O 12 ) The slag loosening capacity is certain, and the auxiliary effect is achieved on improving the slag removing performance and improving the welding bead brightness, but the excessive addition can increase the hot cracking tendency of the welding bead.
In order to fully protect the welding pool from being oxidized, na is required to be added into the gas-forming agent besides the marble 2 CO 3 、K 2 CO 3 And BaCO 3 And at least 2 kinds of carbonate. In the arc column region, carbonate is decomposed to form CO 2 And the low-oxygen environment of a welding pool is ensured together with the welding protective atmosphere.
In order to ensure the stability of the electric arc, the arc stabilizer removes Na in the gas generating agent 2 CO 3 And K 2 CO 3 In addition, naF, KF and BaF 2 At least 2 kinds of isofluorides, the purpose being that the above-mentioned substances can be ionized to obtain K + ，Na + The plasma promotes the directional movement of electrons, thereby improving the stability of the arc.
To ensure low diffusible hydrogen in the deposited metal, naF, KF and BaF in the arc stabilizer 2 When fluoride is ionized, F-is formed, and H in deposited metal can be effectively bonded]The HF gas is formed and then overflows, thereby reducing the [ H ] in the deposited metal]And the content further ensures the low-diffusibility hydrogen design of the deposited metal.
The O-shaped gas slag joint protection flux-cored wire has the using effects that deposited metal with low diffusibility hydrogen is obtained by using the O-shaped gas slag joint protection flux-cored wire under the condition that the welding heat input is increased from 10kJ/cm to 30kJ/cm, and the tensile strength is more than or equal to 1000MPa, the yield ratio is less than or equal to 0.85, the product of strength and elongation is more than or equal to 15 GPa%, and the diffusibility hydrogen is less than or equal to 4ml/100g (a mercury method) through tempering heat treatment (480-580 ℃ and 2-4 h) after welding.
The embodiment is as follows:
the present invention will be further described with reference to the following specific examples.
When the average welding heat input of the flux-cored wire is controlled to be 10kJ/cm under the parameters of 240-260A of welding current, 23-25V of welding voltage and 6mm/s of welding speed, the hydrogen content of deposited metal is 3.2-3.5ml/100g (mercury method), and the components, the heat treatment process, the yield ratio, the compressive strength and the product of strength and elongation of the flux-cored wire are shown in the following examples:
further, when the average welding heat input of the flux-cored wire is controlled to 30kJ/cm under the conditions of 240-260A of welding current, 23-25V of welding voltage and 2mm/s of welding speed, the hydrogen content of deposited metal is 3.6-4.0ml/100g (mercury method), and the composition, the heat treatment process, the yield ratio, the compressive strength and the product of strength and elongation are shown in the following examples.
As can be seen from the following examples, when the content of the deposited metal alloy is measured according to the protection extreme value of the patent, only the yield ratio, the tensile strength and the product of strength and elongation in the corresponding heat treatment process window (480 ℃ -580 ℃,2h-4 h) are in the range of the requirement of the invention. The above data are merely intended to illustrate the technical effects of the present invention.
The above embodiments are merely illustrative of the technical ideas and implementation features of the present invention, and are not intended to limit the scope of the present invention, and all the embodiments that imitate the distribution ratio of the flux cored wire and achieve the substantial application effect of the present invention, or make equivalent evolution and modification on the technology of the present invention should be included in the scope of the present invention.
Claims (9)
1. A slag gas combined protection flux-cored wire is characterized in that: the flux-cored wire comprises a 4Ni steel sheath and a powder core, wherein the powder core accounts for 18-20% of the total weight of the flux-cored wire; the powder core consists of 28.5-37.0% of slagging agent, 1.5-2% of gas making agent, 1.5-2% of arc stabilizer, 25.5-55.5% of alloying agent and the balance of Fe powder by mass percentage.
2. The slag gas combined protection flux-cored wire of claim 1, wherein: the mass percentage of C in the 4Ni steel outer skin is less than or equal to 0.02%, the mass percentage of Si is less than or equal to 0.02%, the mass percentage of Mn is less than or equal to 0.1%, the mass percentage of S + P is less than or equal to 0.002%, the mass percentage of Ni is about 4.0%, and the balance is Fe.
3. The slag gas combined protection flux-cored wire of claim 1, wherein: the slagging agent contains marble, fluorite, rutile, zircon sand and Er 2 O 3 And bismuth titanate, the respective addition amounts of which account for the total mass of the medicine powder core are as follows: 16% -18%,8% -9%,2% -3%, 1% -3% and 0.5% -1%, which form CaO-CaF 2 -TiO 2 -ZrO 2 -SiO 2 -Er 4 S 3 Mainly designed for slag system.
4. The flux-cored wire for slag-gas joint protection according to claim 1, wherein: the gas generating agent contains Na 2 CO 3 、K 2 CO 3 And BaCO 3 At least 2 of (a).
5. The flux-cored wire for slag-gas joint protection according to claim 1, wherein: the arc stabilizer contains NaF, KF and BaF 2 At least 2 of (a).
6. The slag gas combined protection flux-cored wire of claim 1, wherein: the alloying agent consists of graphite, 75% Si-Fe alloy, atomized manganese powder, 50% Cr-Fe alloy, 59% Mo-Fe alloy, ni powder, cu powder, 50% V-Fe alloy, 20% B-Fe alloy, elements C, si, mn, cr, mo, ni, cu and Fe for transition into deposited metal, whereby the following deposited metal compositions are obtained in mass percent: c is more than or equal to 0.08 percent and less than or equal to 0.1 percent, si is more than or equal to 0.5 percent and less than or equal to 0.5 percent, mn is more than or equal to 1.8 percent and less than or equal to 1.9 percent, S + P is less than or equal to 0.02 percent, cr is more than or equal to 0.5 percent and less than or equal to 0.6 percent, mo is more than or equal to 0.5 percent and less than or equal to 0.6 percent, ni is more than or equal to 4 percent and less than or equal to 8 percent, cu is more than or equal to 0.2 percent and less than or equal to 0.3 percent, other alloy elements are less than 0.06 percent, and the balance is Fe. The other alloying elements include vanadium, boron, and rare earth erbium elements.
7. A method for preparing the slag gas combined protection flux-cored wire of any one of claims 1 to 6, which is characterized by comprising the following steps:
rolling and forming a 4Ni steel sheath, filling medicinal powder, and performing roller type closing and multi-pass drawing to obtain the slag-gas combined protection flux-cored wire; wherein, the first and the second end of the pipe are connected with each other,
the 4Ni steel outer skin is subjected to the working procedure treatment of absolute alcohol cleaning and drying for 2-3 times before being rolled and formed;
baking the components of the medicinal powder before mixing.
8. The slag gas combined protection flux-cored wire of claim 7, wherein: and finally obtaining the O-shaped flux-cored wire with the diameter of 1.4mm after the multi-pass drawing.
9. A welding method for performing gas protection by using the slag gas combined protection flux-cored wire of any one of claims 1 to 6, which is characterized by comprising the following steps:
at 80% Ar +20% CO 2 Arc welding is carried out under the atmosphere of mixed gas protection to obtain welding deposited metal, and then tempering heat treatment is carried out for 2-4h at the temperature of 480-580 ℃.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210966092.3A CN115338558B (en) | 2022-08-12 | 2022-08-12 | Slag-gas joint protection flux-cored wire and postweld heat treatment method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210966092.3A CN115338558B (en) | 2022-08-12 | 2022-08-12 | Slag-gas joint protection flux-cored wire and postweld heat treatment method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN115338558A true CN115338558A (en) | 2022-11-15 |
| CN115338558B CN115338558B (en) | 2023-11-07 |
Family
ID=83952303
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202210966092.3A Active CN115338558B (en) | 2022-08-12 | 2022-08-12 | Slag-gas joint protection flux-cored wire and postweld heat treatment method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN115338558B (en) |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103817465A (en) * | 2012-11-16 | 2014-05-28 | 李彬 | Fluoride welding rod |
| CN105755389A (en) * | 2016-05-06 | 2016-07-13 | 江苏金源腾峰换热设备有限公司 | Treatment technology of corrosion-resistant material for heat exchanger |
| CN107252992A (en) * | 2017-05-09 | 2017-10-17 | 安徽飞弧焊业股份有限公司 | A kind of pipe line steel self-protection flux-cored wire |
| CN108544141A (en) * | 2018-03-15 | 2018-09-18 | 西安理工大学 | WH80 and 20Mn23Al self-protection flux-cored wires and preparation method thereof |
| JP2021090975A (en) * | 2019-12-06 | 2021-06-17 | 日本製鉄株式会社 | Weld material for ferritic heat-resistant steel, and method for producing weld joint of ferritic heat-resistant steel |
-
2022
- 2022-08-12 CN CN202210966092.3A patent/CN115338558B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103817465A (en) * | 2012-11-16 | 2014-05-28 | 李彬 | Fluoride welding rod |
| CN105755389A (en) * | 2016-05-06 | 2016-07-13 | 江苏金源腾峰换热设备有限公司 | Treatment technology of corrosion-resistant material for heat exchanger |
| CN107252992A (en) * | 2017-05-09 | 2017-10-17 | 安徽飞弧焊业股份有限公司 | A kind of pipe line steel self-protection flux-cored wire |
| CN108544141A (en) * | 2018-03-15 | 2018-09-18 | 西安理工大学 | WH80 and 20Mn23Al self-protection flux-cored wires and preparation method thereof |
| JP2021090975A (en) * | 2019-12-06 | 2021-06-17 | 日本製鉄株式会社 | Weld material for ferritic heat-resistant steel, and method for producing weld joint of ferritic heat-resistant steel |
Non-Patent Citations (1)
| Title |
|---|
| 张楠等: "SG90T-9C高强韧性渣气联保药芯焊材的研发", 机械工程材料, vol. 44, no. 12, pages 53 - 61 * |
Also Published As
| Publication number | Publication date |
|---|---|
| CN115338558B (en) | 2023-11-07 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN100469513C (en) | High-strength gas-defended welding wire material | |
| CN102658442B (en) | Low-alloy steel welding electrode with Cr control capacity and FAC resisting capacity of weld metal of basic slag system | |
| CN102489902B (en) | Metal powder type flux-cored wire used for welding high-impact-toughness steel | |
| JP4958872B2 (en) | Large heat input electroslag welding method | |
| JP2011212691A (en) | Flux-cored welding wire for small diameter multi-electrode submerged arc welding | |
| CN109128573B (en) | Large-heat-input electro-gas welding gas-shielded flux-cored wire based on grain refinement mechanism | |
| CN111235350B (en) | Strengthening method for adding vanadium-titanium balls in construction steel bar smelting process | |
| CN109158796B (en) | Flux-cored wire matched with bridge steel Q690qE | |
| CN113714682B (en) | Super duplex stainless steel self-protection flux-cored wire and preparation method thereof | |
| CN101509099A (en) | High-strength Q420C level steel tower corner iron and production process | |
| JP4896691B2 (en) | Solid wire for gas shielded arc welding | |
| CN115338558B (en) | Slag-gas joint protection flux-cored wire and postweld heat treatment method thereof | |
| CN111745325A (en) | Self-protection flux-cored wire for X70 pipeline steel | |
| CN110253172A (en) | A kind of high-strength steel Ar-CO2Metal powder core solder wire used for gas shield welding | |
| JP2007253163A (en) | Solid wire for gas shielded arc welding | |
| JPH08325635A (en) | Production of high strength and high toughness steel excellent in hic resistance | |
| CN114248040A (en) | High-strength anti-crack metal powder cored flux-cored wire for engineering machinery | |
| JP3718323B2 (en) | Flux-cored wire for multi-electrode vertical electrogas arc welding for extra heavy steel | |
| JP2011206828A (en) | Flux-cored welding wire for fine diameter wire multiple electrode submerged arc welding | |
| CN109128585B (en) | Large-heat-input electro-gas welding gas-shielded flux-cored wire based on organization homogenization mechanism | |
| JP3203527B2 (en) | Flux-cored wire for gas shielded arc welding | |
| JPH033555B2 (en) | ||
| CN114161024B (en) | Metal powder type flux-cored wire and preparation method and application thereof | |
| CN114769938B (en) | Metal flux-cored wire and preparation method and application thereof | |
| CN115091077B (en) | Austenitic stainless steel welding wire resistant to liquid lead and bismuth corrosion |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |