CN115338558B - Slag-gas joint protection flux-cored wire and postweld heat treatment method thereof - Google Patents
Slag-gas joint protection flux-cored wire and postweld heat treatment method thereof Download PDFInfo
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- 238000010438 heat treatment Methods 0.000 title claims abstract description 25
- 238000003466 welding Methods 0.000 claims abstract description 69
- 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 39
- 239000002893 slag Substances 0.000 claims abstract description 36
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 22
- 239000010959 steel Substances 0.000 claims abstract description 22
- 239000003795 chemical substances by application Substances 0.000 claims abstract description 19
- 238000005275 alloying Methods 0.000 claims abstract description 12
- 239000003381 stabilizer Substances 0.000 claims abstract description 10
- 238000005496 tempering Methods 0.000 claims abstract description 8
- 229910045601 alloy Inorganic materials 0.000 claims description 15
- 239000000956 alloy Substances 0.000 claims description 15
- 239000011572 manganese Substances 0.000 claims description 12
- 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
- 229910002115 bismuth titanate Inorganic materials 0.000 claims description 7
- 150000002910 rare earth metals Chemical class 0.000 claims description 7
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 6
- 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
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 4
- 229910052796 boron 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
- 229910052720 vanadium Inorganic materials 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
- 229910016036 BaF 2 Inorganic materials 0.000 claims description 3
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 claims description 3
- 229910019589 Cr—Fe Inorganic materials 0.000 claims description 3
- 229910052691 Erbium 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
- 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
- 229910002091 carbon monoxide Inorganic materials 0.000 claims description 2
- 238000002156 mixing Methods 0.000 claims description 2
- 230000004907 flux Effects 0.000 claims 1
- 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
- 239000001257 hydrogen Substances 0.000 abstract description 14
- 229910052739 hydrogen Inorganic materials 0.000 abstract description 14
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 abstract description 13
- 238000009792 diffusion process Methods 0.000 abstract description 9
- QSHDDOUJBYECFT-UHFFFAOYSA-N mercury Chemical compound [Hg] QSHDDOUJBYECFT-UHFFFAOYSA-N 0.000 abstract description 6
- 229910052753 mercury Inorganic materials 0.000 abstract description 6
- 230000008569 process Effects 0.000 description 20
- 230000007704 transition Effects 0.000 description 18
- 229910001566 austenite Inorganic materials 0.000 description 15
- 230000009466 transformation Effects 0.000 description 10
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- 238000013461 design Methods 0.000 description 6
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- 238000001816 cooling Methods 0.000 description 5
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- 238000010276 construction Methods 0.000 description 4
- 239000001301 oxygen Substances 0.000 description 4
- 229910052760 oxygen Inorganic materials 0.000 description 4
- KRHYYFGTRYWZRS-UHFFFAOYSA-M Fluoride anion Chemical compound [F-] KRHYYFGTRYWZRS-UHFFFAOYSA-M 0.000 description 3
- 229910004298 SiO 2 Inorganic materials 0.000 description 3
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 238000002360 preparation method Methods 0.000 description 3
- VTYYLEPIZMXCLO-UHFFFAOYSA-L Calcium carbonate Chemical compound [Ca+2].[O-]C([O-])=O VTYYLEPIZMXCLO-UHFFFAOYSA-L 0.000 description 2
- BVKZGUZCCUSVTD-UHFFFAOYSA-L Carbonate Chemical compound [O-]C([O-])=O BVKZGUZCCUSVTD-UHFFFAOYSA-L 0.000 description 2
- 229910010413 TiO 2 Inorganic materials 0.000 description 2
- 239000011324 bead Substances 0.000 description 2
- 229910052804 chromium Inorganic materials 0.000 description 2
- 238000011161 development Methods 0.000 description 2
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- 229910052500 inorganic mineral Inorganic materials 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
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- 239000011707 mineral Substances 0.000 description 2
- 229910052750 molybdenum Inorganic materials 0.000 description 2
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- 239000007787 solid Substances 0.000 description 2
- 239000006104 solid solution 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
- KRHYYFGTRYWZRS-UHFFFAOYSA-N Fluorane Chemical group F KRHYYFGTRYWZRS-UHFFFAOYSA-N 0.000 description 1
- 229910018643 Mn—Si Inorganic materials 0.000 description 1
- 125000004429 atom Chemical group 0.000 description 1
- 230000000903 blocking effect Effects 0.000 description 1
- 229910000019 calcium carbonate Inorganic materials 0.000 description 1
- 150000005323 carbonate salts Chemical class 0.000 description 1
- 150000004649 carbonic acid derivatives Chemical class 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 230000009194 climbing Effects 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000026058 directional locomotion Effects 0.000 description 1
- 239000006185 dispersion Substances 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 150000002431 hydrogen Chemical class 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
- 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
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000006213 oxygenation reaction Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
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- 230000008023 solidification Effects 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000000126 substance Substances 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 joint 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 slag former, 1.5-2% of gas former, 1.5-2% of arc stabilizer, 25.5-55.5% of alloying agent and the balance of Fe powder according to mass percentage. By adopting the gas protection O-shaped slag gas joint protection flux-cored wire with the diameter of 1.4mm, the welding heat input is improved from 10kJ/cm to 30kJ/cm, and the welding deposited metal has the tensile strength of 1000-1020MPa, the yield ratio of 0.82-0.85, the strength-plastic product is more than or equal to 15GPa, and the diffusion hydrogen is less than or equal to 4ml/100g (mercury method) after specific post-welding tempering heat treatment (480-580 ℃ for 2-4 h).
Description
Technical Field
The invention belongs to the technical field of welding material development, and particularly relates to a gas protection O-shaped flux-cored wire, in particular to a slag gas joint protection flux-cored wire, a preparation method thereof and a postweld heat treatment method thereof, so that the advantages of low yield ratio, high strength-plastic product, ji Paji and ultra-low hydrogen of a welded seam part metal structure welded by the flux-cored wire can be achieved through postweld heat treatment.
Background
In recent years, high-strength steel for (heavy) engineering construction is advancing toward light weight and high reinforcement, and particularly, when bearing dynamic load components 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 components. At present, the application of 1GPa (Jipa) high-strength steel has entered substantial design links in key welded structures such as commercial vehicle bearing beam frames, lifting booms, hydroelectric spiral cases and the like. With the improvement of future steel plate service grade and the further rigor of service working conditions, higher requirements are also put on the safety margin of the high-strength steel welded joint.
At present, domestic welding engineering construction is often limited by construction environments and construction periods, and welding materials are expected to adapt to field environment large heat input welding, so that the welding efficiency of large structural members is improved. From the viewpoint of welding equipment and technology, manual arc welding and gas shielded welding can conveniently realize field welding, but the welding efficiency of manual arc welding is lower. Although gas shielded welding of solid welding wires has advantages over manual arc welding in terms of improving welding efficiency, it cannot realize slag-gas combined protection of a molten pool, and cannot guarantee oxygenation of a welding line in a high-efficiency welding process. In particular, from the viewpoint of welding heat input, the welding heat input range is 10-20kJ/cm in both manual arc welding and solid gas shielded welding, and once the welding heat input is more than 20kJ/cm, various problems such as large residual stress, low toughness storage, poor strength and plasticity are brought to a welding joint, particularly a high-strength steel welding joint, and the structural safety of a 1 GPa-level high-strength steel welding part is seriously affected.
Therefore, development and design of a flux-cored wire are needed, the welding efficiency is improved, a welding pool is effectively protected, and the safety margin of the 1 GPa-grade high-strength steel weld joint under the condition of high heat input is also improved.
Disclosure of Invention
The invention aims to provide a slag gas joint protection flux-cored wire of a gas protection O type, which improves welding efficiency and heat input application range, and a super-strong steel metal structure welded by using the flux-cored wire can have the advantages of low yield ratio, ultra-low hydrogen with high plastic product and Gippa grade after heat treatment after welding, and particularly, the welding structure can realize that deposited metal tensile strength is more than or equal to 1000MPa, yield ratio is less than or equal to 0.85, strength-plastic product is more than or equal to 15GPa and diffusion hydrogen is less than or equal to 4ml/100g (mercury method) at room temperature through tempering heat treatment (480-580 ℃ for 2-4 h) under the condition that heat input is improved to 30 kJ/cm.
To achieve the above object, the present invention provides:
the invention provides a giga grade slag-gas joint protection flux-cored wire for realizing low yield ratio and high strength-plastic product 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 slag former, 1.5-2% of gas former, 1.5-2% of arc stabilizer, 25.5-55.5% of alloying agent and the balance of Fe powder according to mass percentage.
Further preferably, the 4Ni steel sheath has a C content of 0.02% or less, a Si content of 0.02% or less, a Mn content of 0.1% or less, a S+P content of 0.002% or less, a Ni content of about 4.0% by mass, and the balance being Fe.
Further preferably, the slag former comprises marble, fluorite, rutile, zircon sand, er 2 O 3 And bismuth titanate, wherein the respective addition amounts of the bismuth titanate are sequentially as follows in percentage by mass of the total mass of the powder core: 16% -18%,8% -9%,2% -3%, 1% -3% and 0.5% -1% of the above-mentioned components 2 -TiO 2 -ZrO 2 -SiO 2 -Er 4 S 3 Is mainly designed for slag system.
Further preferably, the gas-forming agent further contains Na in addition to marble in the above-mentioned slag-forming agent 2 CO 3 、K 2 CO 3 And BaCO 3 At least 2 of (2).
Further preferably, the arc stabilizer removes Na in the gas generating agent 2 CO 3 、K 2 CO 3 In addition, naF, KF and BaF are contained 2 At least 2 of (2).
Further preferably, the 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, 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, thereby obtaining the deposited metal composition, in mass percent: 0.08 percent or less of C is less than or equal to 0.1 percent, 0.4 percent or less of Si is less than or equal to 0.5 percent, 1.8 percent or less of Mn is less than or equal to 1.9 percent, S+P is less than or equal to 0.02 percent, 0.5 percent or less of Cr is less than or equal to 0.6 percent, 0.5 percent or less of Mo is less than or equal to 0.6 percent, 4 percent or less of Ni is less than or equal to 8 percent, 0.2 percent or less of Cu is less than or equal to 0.3 percent, other alloying elements are less than 0.06 percent, and the balance is Fe. The other alloy elements comprise vanadium, boron, rare earth erbium and other elements.
The invention also provides a preparation method of the slag-gas joint protection flux-cored wire, which is characterized by comprising the following steps of:
after the 4Ni steel sheath is rolled and formed, filling the powder, and obtaining the slag-gas joint protection flux-cored wire after roll closure and multi-pass drawing; wherein,
the 4Ni steel skin is subjected to the procedures of absolute alcohol cleaning and drying for 2-3 times before being rolled and formed;
and baking the components of the medicinal powder before mixing.
Further 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 joint protection flux-cored wire, which is characterized by comprising the following steps of:
arc welding is carried out under the atmosphere of mixed gas of 80 percent Ar and 20 percent CO2 to obtain welding deposited metal, and tempering heat treatment is carried out for 2 to 4 hours at the temperature of 480 to 580 ℃.
By adopting the O-shaped flux-cored wire with the specification of 1.4mm in diameter, even if the heat input is improved from 10kJ/cm to 30kJ/cm, the tensile strength of the welding deposited metal is up to 1000-1020MPa at room temperature through specific post-welding tempering heat treatment (480-580 ℃ for 2-4 h), the yield ratio is 0.82-0.85, the strong plastic product is more than or equal to 15GPa, and the diffusion hydrogen is less than or equal to 4ml/100g (mercury method).
Detailed Description
In order to realize the above summary, the specific embodiments adopted by the present invention are:
o-shaped 80% Ar+20% CO with diameter of 1.4mm 2 The mixed gas shielding gas slag joint protection 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 weight percentage of C in the 4Ni steel sheath is less than or equal to 0.02%, the weight percentage of Si is less than or equal to 0.02%, the weight percentage of Mn is less than or equal to 0.1%, the weight percentage of S+P is less than or equal to 0.002%, the weight percentage of Ni is about 4.0%, 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 greasy dirt, the 4Ni steel skin is subjected to the processes of absolute alcohol cleaning and drying for 2-3 times.
The components of the powder core consist of slag former, gas former, arc stabilizer, alloy agent and Fe powder.
Marble, fluorite, rutile, zircon sand and rare earth element oxide Er in slag former 2 O 3 The adding amount of the bismuth titanate is sequentially as follows in percentage by mass of the total mass of the powder core: 16% -18%,8% -9%,2% -3%, 1% -3% and 0.5% -1% of the above-mentioned components 2 -TiO 2 -ZrO 2 -SiO 2 -Er 4 S 3 Is mainly designed for slag system.
The gas-making agent contains Na in addition to marble in the slag-making agent 2 CO 3 、K 2 CO 3 And BaCO 3 At least 2 kinds of carbonate are added, the total addition amount is not more than 2% of the total mass percentage of the powder core, and the content is not less than 1.5% for exerting the effect.
Arc stabilizer for removing Na in said gas-making agent 2 CO 3 And K 2 CO 3 Besides NaF, KF and BaF 2 The total addition amount of fluoride is at least 2 and not more than 2% by mass of the powder core, and the content should not be less than 1.5% for exerting its effect.
The 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, 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 for transition into the deposited metal, thereby ensuring that the deposited metal composition (mass%) is obtained: 0.08 percent or less of C is less than or equal to 0.1 percent, 0.4 percent or less of Si is less than or equal to 0.5 percent, 1.8 percent or less of Mn is less than or equal to 1.9 percent, S+P is less than or equal to 0.02 percent, 0.5 percent or less of Cr is less than or equal to 0.6 percent, 0.5 percent or less of Mo is less than or equal to 0.6 percent, 4 percent or less of Ni is less than or equal to 8 percent, 0.2 percent or less of Cu is less than or equal to 0.3 percent, other alloying elements are less than 0.06 percent, and the balance of Fe. The other alloying elements include vanadium, boron, and rare earth erbium. Except Fe powder, the alloy agent accounts for 25.5% -55.5% of the total mass of the powder core.
In order to obtain the ultra-low hydrogen flux-cored wire, the marble, fluorite, bismuth titanate, gas former, arc stabilizer and other carbonates, fluoride mineral powder and alloying agents in the slag former are baked for 3-4 hours at 300-350 ℃.
Likewise, the oxides Er of rutile, zircon sand and rare earth elements in the slag former 2 O 3 And the rest mineral powder is baked for 2 to 3 hours at the temperature of 180 to 220 ℃.
After the components in the powder core are fully and uniformly mixed, the O-shaped flux-cored wire is prepared according to the filling rate (the powder core accounts for the total weight of the flux-cored wire) of 18-20 percent. The preparation process comprises the steps of Ni steel sheath roll forming, powder filling, roll closing and multipass drawing, and finally preparing the O-shaped flux-cored wire with the diameter of 1.4 mm.
In order to ensure that the O-shaped flux-cored wire designed by the invention realizes low yield ratio of deposited metal, and simultaneously ensures that the strength grade of the deposited metal reaches the GPa grade, namely the tensile strength is required to reach more than 1000MPa, a certain amount of austenite expanding elements such as C, mn, ni and the like are required to be added, so that the heat treatment temperature of 480-580 ℃ is in a two-phase region, the austenite expanding elements are redistributed for 2-4 hours, and the structural characteristics of hard phase and soft phase are obtained under the air cooling condition, thereby realizing the preferential yielding of the soft phase in the material stretching process and achieving the purpose of low yield strength.
In the heat treatment process at 400-580 ℃, a large amount of austenite expanding elements are enriched in a hard phase, wherein the diffusion of C is more uniform, but a brittle hard phase is easy to form in the cooling process, so that the O-shaped flux-cored wire adopts a low-carbon design when an alloying agent is designed, and the mass percentage of C in deposited metal is higher than 0.1 percent, which is unfavorable for toughness. Mn is also an austenitizing element, but because of larger atomic radius and lower diffusion migration rate than C, mn-Fe intermetallic compounds are easy to form in the temperature range of 100-200 ℃ in the cooling process, and the toughness is also unfavorable, but Mn and Si are combined to be a main deoxidizing mode of weld metal, so that the weld is oxygen increased due to too low Mn content, and the comprehensive mechanical property after welding is unfavorable, therefore, the mass percentage of Mn in deposited metal is designed to be 1.8-1.9%. Considering the combined deoxidizing capability of Mn-Si and the influence of Mn/Si ratio on the fluidity of a welding pool, and simultaneously, in order to improve the escape of gas, particularly hydrogen, in a welding seam, the fluidity and calm of the welding pool are better, wherein the Mn/Si ratio is set between 3.6 and 4.75, so that the mass percent of Si in deposited metal is preferably between 0.4 and 0.5 percent. The main function of Cr and Mo in deposited metal is to improve hardenability, ensure that the Jipa grade welding material has certain yield strength, but the effect is not obvious when the content is too low, carbide is easily formed with C element when the content is too high, and impact toughness is deteriorated, so that the mass percentage range of Cr and Mo in deposited metal is between 0.5% and 0.6%. Ni is a main alloy element for realizing low yield ratio, and can obviously reduce the phase transition point of the heat treatment deposited metal component and lower the temperature window of the two-phase region. After the Ni content reaches 4%, the tempering heat treatment temperature reaches 480 ℃ and can enter a two-phase region, reverse transformation austenite enriched with austenitizing enlarging element Ni at room temperature is formed, the tensile strength is improved, and the yield ratio is reduced. However, when the Ni content exceeds 8% and the tempering temperature is higher than 580 ℃, the tensile strength of the welding material deposited metal is lowered due to excessive austenite structure, so that the reasonable Ni composition range is 4% -8%.
In order to improve the uniform elongation in the drawing process after the heat treatment of the deposited metal, 0.2-0.3% of Cu is added into the deposited metal besides the reverse transformation 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 insufficient to remarkably expand the austenite region, and the main purpose of the Cu is to realize element distribution in the heat treatment process of deposited metal, stabilize reverse transformation austenite, and dissolve in the reverse transformation austenite in a solid solution in the cooling process, and the Cu is characterized in that: the deposited metal after heat treatment is subjected to plastic deformation preferentially due to the existence of reverse transformed austenite in the stretching process, so that the yield strength is reduced; however, cu atoms in the reverse transformation austenite can be gradually and uniformly separated out to form epsilon-Cu phase and be precipitated in the deformed reverse transformation austenite in the deformation process, so that the uniform elongation in the tensile deformation process is further improved; with the increase of the deformation process, the epsilon-Cu phase plays a role in blocking the slippage and climbing of dislocation in the reverse transformation austenite, and induces the reverse transformation austenite to generate martensitic transformation in the stretching process, so that the tensile strength is further improved, and the strong plastic product of the final heat treatment deposited metal stretching process is remarkably improved.
Other alloying elements with the total content not exceeding 0.06 percent comprise V, B elements, rare earth Er elements and the like. Micro-nano V can be separated out in the cooling stage of weld metal by micro-addition of metal V x C y The precipitated phase and the following element B are combined for refining the grain sizes of BCC and FCC structural phases, and play a role in dispersion precipitation strengthening, and the mass percentage of V in deposited metal is controlled to be between 0.02 and 0.03 percent, if the content is too low, the element V is mostly in a solid solution form, and the element V is x C y Less precipitated phase, no function of grain refinement, excessively high content, severe solidification of C element, reduced weld metal strength, and V x C y The precipitated phase is easy to be coarse and deviated to the polycrystalline boundary, and embrittle weld metal. The main purpose of adding the nonmetallic B element is to improve the hardenability of the deposited metal, and the mass percentage of B in the deposited metal is controlled to be between 0.0015 and 0.002 percent, if the content is too low, the B can not effectively inhibit the formation of a first eutectoid high temperature phase under the welded state structure of the deposited metal, and the toughness improvement of the deposited metal under the welded state is unfavorable; the content is excessive, the yield of Mn and Si can be improved in the molten pool metallurgy process, and the deposited metal in a welding state is embrittled. The rare earth Er element is added by adding Er oxide Er 2 O 3 Realized by the method. The mass percentage of Er in the deposited metal is controlled to be between 0.02 and 0.028 percent. Er added in slag former 2 O 3 At the high temperature of the welding arc (arc column region temperatures up to 5000-30000K) it is sufficient to promote the following reaction to the right: the formed rare earth Er element has higher surface activity, is easy to adsorb molten drops, reduces the surface tension of the molten drops, and obviously reduces welding spatter of short circuit transition. In addition, rare earth Er element preferentially reacts with S in a molten pool to form a product mostly containing Er 4 S 3 The form of the alloy is in a slag system, a small part of the alloy is reserved in weld metal to form fine inclusions, the fine inclusions are combined with B to inhibit pro-eutectoid ferrite nucleation in the subsequent weld solid-state transformation process, acicular ferrite nucleation is promoted, and the alloy plays a role in improving toughness while reducing S element as an impurity. The oxygen element part formed forms CO with the carbon element in the weld joint, and then forms CO with the oxygen element in the electric arc secondarily 2 Part of which forms SiO with Si 2 And into 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
SiO in the slag system 2 In addition to the sources involved in the metallurgical deoxidization of the weld, siO is also present in the slag former of the present invention 2 The components have the functions of regulating the pH value of the slag system and improving the activity of slag.
TiO in slag system 2 Slag formation can be realized, the covering performance and slag removing performance of welding slag are improved, the arc stability is improved, and splashing is reduced.
ZrO in slag system 2 Slag formation can also be realized, and the melting point is high, and the slag forming device is mainly used for properly adjusting the melting point of slag.
CaO in the slag system is mainly obtained by decomposing calcium carbonate in marble and is mainly used for slagging.
CaF in slag system 2 Mainly from fluorite and other fluoride, is mainly used for slagging and regulating pH value, and has excessive consumption and severely deteriorated welding arc stability.
The bismuth titanate (Bi) is added in a trace amount into the powder core 4 Ti 3 O 12 ) The slag loosening capability is provided, and the slag loosening capability is improved, the brightness of a welding bead is improved, but excessive addition can increase the hot cracking tendency of the welding bead.
In order to fully protect the welding pool from oxidation, besides marble, na is added into the gas-making agent 2 CO 3 、K 2 CO 3 And BaCO 3 At least 2 of the carbonate salts. Carbonate is decomposed to form CO in the arc column region 2 And the low-oxygen environment of a welding pool is ensured together with the welding protective atmosphere.
To ensure the stability of the electric arc, the arc stabilizer removes Na in the gas-making agent 2 CO 3 And K 2 CO 3 Besides NaF, KF and BaF 2 At least 2 of the above-mentioned substances can be ionized to obtain K + ，Na + The plasma promotes electron directional motion, thereby improving arc stability.
To ensure low diffusion of hydrogen in the deposited metal, naF, KF and BaF in the arc stabilizer 2 The fluoride forms F-after ionization, can effectively and effectively mix with [ H ] in deposited metal]The HF gas is formed and overflowed, thereby reducing the [ H ] in the deposited metal]The content further ensures the design of low diffusion hydrogen of deposited metal.
The invention has the advantages that the O-shaped gas slag combined protection flux-cored wire obtains deposited metal with low diffusion hydrogen under the condition that the welding heat input is improved 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 strength-plastic product is more than or equal to 15GPa, and the diffusion hydrogen is less than or equal to 4ml/100g (mercury method) through tempering heat treatment after welding (480-580 ℃ for 2-4 h).
Examples:
the invention will be further illustrated with reference to specific examples.
When the flux-cored wire controls the average welding heat input 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 results of the composition, the heat treatment process, the yield ratio, the compressive strength and the products of strength and plastic are as follows:
further, when the average welding heat input of the flux-cored wire is controlled to be 30kJ/cm under the conditions of welding current of 240-260A, welding voltage of 23-25V and welding speed of 2mm/s, the hydrogen content of deposited metal is 3.6-4.0ml/100g (mercury method), and the composition, heat treatment process, yield ratio, compressive strength and products of strength and plastic are as shown in the following examples.
As can be seen from the examples below, when the content of the deposited metal alloy is measured, the protection extremum of the patent shows that only the yield ratio, the tensile strength and the products of strength and plasticity in the corresponding heat treatment process window (480-580 ℃ and 2-4 h) are in the range meeting the requirements of the invention. The above data are only for illustrating technical effects of the present invention.
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The above embodiments are only for illustrating the technical idea and implementation features of the present invention, and are intended to enable those skilled in the art to understand the technical idea of the present invention, not to limit the scope of the present invention, and all embodiments that simulate the component proportions of the flux-cored wire of the present invention and achieve substantial application effects, or make equivalent evolution and modification in the technology of the present invention shall be included in the scope of the present invention, so as to be specifically stated.
Claims (4)
1. The utility model provides a slag gas allies oneself with guarantor flux cored wire which 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 slag former, 1.5-2% of gas former, 1.5-2% of arc stabilizer, 25.5-55.5% of alloying agent and the balance of Fe powder according to mass percentage; the slag former comprises marble, fluorite, rutile, zircon sand and Er 2 O 3 And bismuth titanate, wherein the respective addition amounts of the bismuth titanate are sequentially as follows in percentage by mass of the total mass of the powder core: 16% -18%,8% -9%,2% -3%, 1% -3% and 0.5% -1%; the gas-making agent contains Na 2 CO 3 、K 2 CO 3 And BaCO 3 At least 2 of (2); the arc stabilizer contains NaF, KF and BaF 2 At least 2 of (2); the alloying agent consists of graphite, 75% of Si-Fe alloy, atomized manganese powder, 50% of Cr-Fe alloy, 59% of Mo-Fe alloy, ni powder, cu powder, 50% of V-Fe alloy and 20% of B-Fe alloy, and is used for transitional C, si, mn, cr, mo, ni, cu and Fe elements in deposited metal, so that the following deposited metal components are obtained according to mass percent: 0.08 percent or less of C is less than or equal to 0.1 percent, 0.4 percent or less of Si is less than or equal to 0.5 percent, 1.8 percent or less of Mn is less than or equal to 1.9 percent, S+P is less than or equal to 0.02 percent, 0.5 percent or less of Cr is less than or equal to 0.6 percent, 0.5 percent or less of Mo is less than or equal to 0.6 percent, 4 percent or less of Ni is less than or equal to 8 percent, 0.2 percent or less of Cu is less than or equal to 0.3 percent, other alloy elements are less than 0.06 percent, and the balance is Fe, wherein the other alloy elements comprise vanadium, boron and rare earth erbium elements.
2. A method for preparing the slag-gas joint insurance flux-cored wire of claim 1, which is characterized in that:
after the 4Ni steel sheath is rolled and formed, filling the powder, and obtaining the slag-gas joint protection flux-cored wire after roll closure and multi-pass drawing; wherein,
the 4Ni steel skin is subjected to the procedures of absolute alcohol cleaning and drying for 2-3 times before being rolled and formed;
and baking the components of the medicinal powder before mixing.
3. The method for preparing the slag-gas joint insurance flux-cored wire, which is characterized by comprising the following steps of: and finally preparing the O-shaped flux-cored wire with the diameter of 1.4mm after the multi-pass drawing.
4. A method for gas shielded welding by using the slag-gas joint protection flux-cored wire of claim 1, which is characterized in that:
in 80% Ar+20% CO 2 And (3) arc welding is carried out under the mixed gas protection atmosphere to obtain welding deposited metal, and tempering heat treatment is carried out for 2-4h at the temperature of 480-580 ℃.
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