CN102000925B - Low-alloy welding wire for high-titanium low-molybdenum high-strength and high-toughness twin-wire submerged arc welding - Google Patents
Low-alloy welding wire for high-titanium low-molybdenum high-strength and high-toughness twin-wire submerged arc welding Download PDFInfo
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- CN102000925B CN102000925B CN2010105928206A CN201010592820A CN102000925B CN 102000925 B CN102000925 B CN 102000925B CN 2010105928206 A CN2010105928206 A CN 2010105928206A CN 201010592820 A CN201010592820 A CN 201010592820A CN 102000925 B CN102000925 B CN 102000925B
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Abstract
The invention relates to a low-alloy welding wire for high-titanium low-molybdenum high-strength and high-toughness twin-wire submerged arc welding, which comprises the following chemical constituents in weight percent: 0.05-0.10% of C, not greater than 0.25% of Si, 0.90-1.40% of Mn, not greater than 0.010% of S, not greater than 0.015% of P, 1.20-2.20% of Ni, 0.25-0.70% of Cr, 0.10-0.20% of Ti, 0.01-0.05% of Mo and the balance of Fe. The welding wire is matched with WF802 sintered flux, and the weld metal has qualified strength, good manufacturability and outstanding low-temperature toughness; the yielding strength Rp0.2 of the weld metal is 460-520 MPa, KV2 reaches 110-140 J at 40 DEG C below zero, and the dynamic tearing energy at 20 DEG C below zero is 500 J; no preheating before welding and no after heating after welding can be realized, the twin-wire submerged arc welding with various process requirements can be adapted, and efficiency is increased.
Description
Technical field
The present invention relates to a kind of welding wire, the low molybdenum high-strength tenacity double wire hidden arc welding of particularly a kind of high titanium is used the low-alloy welding wire.
Background technology
Ni-Cr-Mo is that steel alloy is that high strength important in the shipbuilding is used steel, in fields such as pipeline, offshore oil platform, engineering machinery extensive application is arranged also.For improving welding efficiency, reducing construction cost; Mariages or multiplewire submerged arc welding technology are used widely; But for Ni-Cr-Mo is domestic correlative study, the alternative double wire hidden arc welding welding wire that is not complementary with it of also not carrying out of Double Wire Welding technology of steel alloy.Its main cause is that this steel has the higher strength and toughness requirement, and requires welding point to have good resistance to corrosion seawater and welding crack resistance.If will carry out the double wire hidden arc welding welding with this steel coupling, also there is following problem in existing submerged-arc welding wire:
(1) though can satisfy the requirement of intensity, toughness is not enough;
(2) the welding crack resistance can not satisfy the technique of double wire hidden arc welding requirement;
(3) matching of component of weld wire and steel is bad, influences the welding point serviceability.
Both at home and abroad the submerged-arc welding wire document shows, Mo content is all higher in the welding wire of most patents, mainly is to utilize the solution strengthening of Mo to improve the intensity of weld metal.Be that the Mo content of its welding wire is 0.20～0.50% in the explanation of 00114334.4 Chinese patent " high-strength and high-toughness submerged-arc welding welding wire " like application number; Application number is that its welding wire Mo content is 0.05～0.40% in 200610107016.8 Chinese patent " high-strength high-toughness low alloy steel welding wire used for submerged arc welding of the cupric " patent.Adopt the welding wire of such higher Mo content to carry out Ni-Cr-Mo when being the double wire hidden arc welding of steel, be prone in the weld seam form a large amount of granular bainites and cause impact flexibility to descend.
In the existing welding wire patent, a kind of in addition means are to adopt Ti, B synergy to improve the toughness of weld metal.It like application number 92105621 Chinese patent " low carbon micro alloyed submerged-arc welding wire " patent; 0.02～0.08% Ti and 0.001～0.008% B are arranged in the welding wire; The mechanism that its weld seam has certain low-temperature flexibility is the effect of nonmetalloid B main in the welding wire, and B depends on the proper content of content and simultaneous O, Ti, Al of N in the weld metal etc. to the effect of toughness.Adopt such welding wire to carry out Ni-Cr-Mo when being the double wire hidden arc welding of steel, the matching of its composition and steel is bad, and resistance to corrosion seawater is relatively poor.
Summary of the invention
Technical problem to be solved by this invention provides the low molybdenum high-strength tenacity double wire hidden arc welding of a kind of high titanium and uses the low-alloy welding wire; Thereby overcome the problem that exists in the prior art; To Ni-Cr-Mo is steel alloy composition and technique of double wire hidden arc welding characteristics, satisfies this high-strength steel technique of double wire hidden arc welding peculiar to vessel welding requirements.
For the purpose that realizes solving the problems of the technologies described above, the present invention has adopted following technical scheme:
The low molybdenum high-strength tenacity double wire hidden arc welding of a kind of high titanium of the present invention is used the low-alloy welding wire, and its chemical composition consists of (wt%): C:0.05～0.10; Si≤0.25; Mn:0.90～1.40; S≤0.010; P≤0.015; Ni:1.20～2.20; Cr:0.25～0.70; Ti:0.10～0.20; Mo:0.01～0.05; Surplus is Fe.
Further, the low molybdenum high-strength tenacity double wire hidden arc welding of a kind of high titanium of the present invention is used the low-alloy welding wire, and its chemical composition consists of (wt%): C:0.05～0.09; Si≤0.25; Mn:1.0～1.40; S≤0.010; P≤0.015; Ni:1.50～2.20; Cr:0.25～0.70; Ti:0.13～0.18; Mo:0.01～0.42; Surplus is Fe.
The smelting production process and the process of described welding wire are identical with solid wire, must adopt vacuum induction to smelt, and use the pure iron prepurging before the charging in the smelting process, will accomplish clean dry to casting system, and guarantee that the ingot mould inwall is level and smooth; All raw material must carry out baking processing before using, to remove moisture.Whole fusion process is forbidden vacuum breaker, prevents to inhale nitrogen; Processing process is: vacuum induction furnace smelting-casting-annealing-forging is become a useful person-heat treatment and drawing.
Make weld metal that higher intensity and good toughness arranged, key is to add suitable alloying element and impels a certain amount of acicular ferrite structure of formation in the weld seam.C, Mn, Ni, Mo element all have the ability that promotes that acicular ferrite forms within the specific limits, and Ti, B element have bigger facilitation to the formation of acicular ferrite.The Strengthening and Toughening of weld metal can be achieved through adding these elements, but the strength and toughness of weld seam is not only considered in the selection of soldering wire alloy system, also will consider the working environment and quilt weldering chemical composition of steel and Performance Match of welding point.The emphasis of this welding wire development is the obdurability coupling and composition coupling that solves welding point.
Welding wire of the present invention adopt with Ni-Cr-Mo be the close alloy system of steel alloy, guaranteeing the composition coupling of welding point, on basis, carry out the adjustment of constituent content to the analysis of each element interaction, confirmed the ultimate constituent of welding wire through a large amount of welding wires trial-productions.
Though the C content of weld seam increases the amount that can improve the amount of acicular ferrite in the weld seam and reduce pro-eutectoid ferrite, too much C element has promoted bainite even martensitic formation, and is unfavorable for the cold-crack resistance ability of weld seam.Therefore, the C content in the welding wire must be controlled at reduced levels.
The Mn element can make the abundant deoxidation of weld metal on the one hand, crystal grain thinning solution strengthening, the tensile strength of raising weld metal; Also can increase the stability of overcooling austenite on the other hand, make austenite phase transformation shift to lower temperature, can suppress separating out of pro-eutectoid ferrite and ferrite side plate, improve the content of acicular ferrite.Therefore the Mn in the welding wire will arrive certain level.But when Mn was too high, Mn can have a negative impact to toughness to more serious segregation taking place and forming tissues such as retained austenite, bainite or martensite in the segregation territory in process of setting, and the Mn in the welding wire is controlled between 0.90～1.40%.
The Cr element has bigger retardation function to bainite transformation, can reduce austenite and ferritic free energy difference, reduces the driving force of phase transformation.Cr and Mn can also hinder the carbon diffusion, so it is very strong to postpone the effect of bainite transformation.The Ni element not only reduces γ → α phase transition temperature; Reduce the proeutectoid ferrite body burden; And the frictional resistance and the pinning constant of weld metal when reducing low temperature, increasing stacking fault energy, screw dislocation is handed over slippage when promoting low temperature; Thereby crackle expansion consumed work is increased, and then can obtain higher low-temperature flexibility.In the welding wire suitably Ni, Cr content for guarantee the weld seam obdurability and with reach the purpose that is complementary with the mother metal composition.
In the Ti element butt welded seam metal acicular ferrite be formed with remarkable effect, the Ti element forms TiN, TiO, Ti
2O
3The field trash that equidimension varies in size, these field trashes become the particle of acicular ferrite nucleating.Thereby adding Ti is the effective measures that improve the weld seam obdurability.But work as Ti content (as＞0.20%) more for a long time; Oxide and nitride particles alligatoring, and separate out on ferrite lath border and inside thereof, the adhesion between ferrite lath reduced; Ferrite hardness rising plasticity is reduced, though the higher toughness of intensity that organize this moment is very poor; In addition, also can form more TiC, TiS when Ti content is high, these particles will be separated out from matrix when solidifying, and cause toughness obviously to descend.Ti content crosses that (as＜0.10%) is not enough to form effective acicular ferrite nucleating particle when low, and other element also is prone to oxidization burning loss.Therefore in this welding wire, Ti is controlled in 0.10～0.20 scope.
Mo element butt welded seam tissue influence is very big.Austenite belongs to diffusion-type transition to the transformation of pro-eutectoid ferrite, the influence that the forming core of α phase is grown up and changed by γ → α, the velocity effect that spread out from the α phase surface of growing up by carbon.When containing Mo in the weld seam, along with the increase of the mass fraction of Mo, the diffusion activation energy of carbon in austenite increases, thereby makes the diffusion coefficient of carbon reduce.Simultaneously, Mo can reduce the diffusivity of carbide former, thereby hinders the formation of carbide, postpones the precipitation process of carbide.Therefore, Mo hinders separating out of pro-eutectoid ferrite and growth process strongly.Mo element and Ti element interact can promote that acicular ferrite forms in a large number.So Mo element an amount of in the welding wire can arrive the purpose that is complementary with mother metal, can play the purpose of restraining pro-eutectoid ferrite and promoting acicular ferrite formation again.(as＜0.01%) effect is not obvious when Mo content is low, more pro-eutectoid ferrite and ferrite side plate can occur in the weld seam, and toughness is relatively poor; And Mo content is greater than 0.05% o'clock, and seam organization is upper bainite or granular bainite, and toughness obviously descends.For this reason, it is more suitable Mo content to be controlled at 0.01～0.05% scope.
Controlling lower Si content also is in order to improve the toughness of weld seam; Strict control S, P content in order that improve the degree of purity of material, reduce welding hot crack tendency.
The key of this welding wire invention is the reasonable control to elemental composition scopes such as Mn, Cr, Ni, Ti and Mo; Under the acting in conjunction of several kinds of alloying elements, suppressed the appearance of separating out and prevented upper bainite and granular bainite of pro-eutectoid ferrite; Its seam organization is main with acicular ferrite, and making weld metal have high strength has high toughness simultaneously.
Through adopting technique scheme, the present invention has following beneficial effect:
Adopt the result of the test of welding wire of the present invention to show that when being complementary with the WF802 sintered flux, weld metal intensity is qualified, manufacturability is good, and low-temperature flexibility is particularly outstanding: weld metal yield strength R
P0.2Be 460～520MPa ,-40 ℃ of KV
2Reach 110～140J ,-20 ℃ dynamic tear energy is 500J.And the result of the test of existing other submerged-arc welding wire shows weld metal-40 ℃ KV
2Be 28～36J ,-20 ℃ dynamic tear energy is 100～120J.
Compared with prior art; Welding wire of the present invention has the excellent comprehensive performance; Not only have higher intensity and good low-temperature flexibility, and also have anti-preferably hydrogen induced cracking performance, not preheating before can realizing welding, not after heat of postwelding; Can adapt to the double wire hidden arc welding welding that single or multiple lift, single welding or welding by both sides kinds of processes require, significantly improve welding efficiency.
The specific embodiment
With embodiment the present invention is made further detailed description below, but the present invention is not limited to these embodiment.The smelting of welding wire is produced and is adopted vacuum induction to smelt, and uses the pure iron prepurging before the charging in the smelting process; All raw material must carry out baking processing before using, to remove moisture; Processing process is: vacuum induction furnace smelting-casting-annealing-forging is become a useful person-heat treatment and drawing.
The chemical composition of used embodiment welding wire is as shown in table 1.
Weld according to following experimental condition:
Welding wire specification: φ 3.0mm
Solder flux: WF802 sintered flux (weld and cured in preceding 400 ℃, 2 hours)
Welding procedure: preceding silk is a dc reverse connection, electric current 600～620A, voltage 31～32V; The back silk is for exchanging electric current 520～540A, voltage 34～36V; Mariages spacing 25mm welds fast 75 cm/min; Temperature is 80～120 ℃ between the road, not preheating before the welding, not after heat of postwelding.
The chemical composition of table 1 welding wire (wt%)
| ? | C | Si | Mn | Ni | Cr | Ti | Mo | S | P | Fe |
| Embodiment 1 | 0.05 | 0.03 | 0.90 | 1.20 | 0.36 | 0.10 | 0.010 | 0.003 | 0.004 | Surplus |
| Embodiment 2 | 0.072 | ＜0.005 | 1.25 | 1.56 | 0.25 | 0.16 | 0.015 | 0.006 | 0.010 | Surplus |
| Embodiment 3 | 0.082 | 0.25 | 1.40 | 1.78 | 0.54 | 0.18 | 0.027 | 0.005 | 0.006 | Surplus |
| Embodiment 4 | 0.056 | 0.12 | 1.02 | 2.20 | 0.70 | 0.13 | 0.042 | 0.010 | 0.008 | Surplus |
| Embodiment 5 | 0.10 | 0.21 | 1.32 | 2.05 | 0.37 | 0.20 | 0.050 | 0.005 | 0.004 | Surplus |
Test butt welded seam institutional framework is analyzed, and the weld seam metallographic structure of several kinds of embodiment is identical, all is to be master+little granular bainite and a small amount of pro-eutectoid ferrite with the acicular ferrite.
The deposited metal mechanical property test has been carried out in test, the joint toughness test is restrained the weld crack test with window shape, and the result is as shown in table 2.
Table 2 experimental test result
| Pilot project | The weld metal mechanical property | ? | ? | ? | The joint toughness test | ? | Cracking test under the 0 ℃+80%RH environment, crackle rate/% |
| ? | R p0.2/MP | R m/MP | A/% | Z/% | -40 ℃ of ballistic work KV 2 /J | -20 ℃ of dynamic tear energy/J | ? |
| Embodiment 1 | 465 | 580 | 25.5 | 72.5 | 167,166,162，165 | 510 | 0.0 |
| Embodiment 2 | 470 | 585 | 26.0 | 71.5 | 187,166,172，175 | 530 | 0.0 |
| Embodiment 3 | 480 | 590 | 25.5 | 72.0 | 157,150,152，153 | 500 | 0.0 |
| Embodiment 4 | 498 | 610 | 25.0 | 70.0 | 122,170,110，134 | 495 | 0.0 |
| Embodiment 5 | 460 | 585 | 27.0 | 73.0 | 173,174,166，171 | 515 | 0.0 |
Annotate: cracking test adopts the window shape of 20mm steel plate to restrain the weld crack test, and-40 ℃ of ballistic work numerical value are three test values and an average.
Claims (1)
1. the low molybdenum high-strength tenacity double wire hidden arc welding of high titanium is used the low-alloy welding wire, and it is characterized in that: the percentage by weight of welding wire chemical composition consists of: C:0.05～0.10; Si≤0.25; Mn:0.90～1.40; S≤0.010; P≤0.015; Ni:1.20～2.20; Cr:0.25～0.70; Ti:0.10～0.20; Mo:0.01～0.05; Surplus is Fe.
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|---|---|---|---|
| CN2010105928206A CN102000925B (en) | 2010-12-17 | 2010-12-17 | Low-alloy welding wire for high-titanium low-molybdenum high-strength and high-toughness twin-wire submerged arc welding |
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| Application Number | Priority Date | Filing Date | Title |
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| CN2010105928206A CN102000925B (en) | 2010-12-17 | 2010-12-17 | Low-alloy welding wire for high-titanium low-molybdenum high-strength and high-toughness twin-wire submerged arc welding |
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| CN102000925B true CN102000925B (en) | 2012-08-08 |
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| CN105945453B (en) * | 2016-07-21 | 2018-06-05 | 武汉天高熔接股份有限公司 | Steel construction U-shaped floor sintered flux used for submerged arc welding |
| CN106001992A (en) * | 2016-08-22 | 2016-10-12 | 昆山中冶宝钢焊接材料有限公司 | Ultrahigh-strength low-temperature welding wire |
| CN110640277B (en) * | 2019-09-30 | 2021-08-13 | 广州黄船海洋工程有限公司 | Q420 high-strength steel thick plate non-preheating double-wire submerged-arc welding process |
| CN113319465B (en) * | 2021-06-13 | 2022-07-05 | 石家庄铁道大学 | Double-wire gas shielded welding wire for welding ultrahigh-strength steel and welding method |
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| CN1709634A (en) * | 2005-06-28 | 2005-12-21 | 武汉钢铁(集团)公司 | Submerged-arc welding wire for high-strength pipeline steel |
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| CN101288924A (en) * | 2007-04-20 | 2008-10-22 | 宝山钢铁股份有限公司 | Seawater corrosion resistance submerged arc welding wire rod, welding wire and application thereof |
| CN101288925A (en) * | 2007-04-20 | 2008-10-22 | 宝山钢铁股份有限公司 | High intensity gas shielded welding wire, wire rod and application thereof |
Family Cites Families (2)
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| JPS61119394A (en) * | 1984-11-16 | 1986-06-06 | Sumitomo Metal Ind Ltd | Submerged arc welding material |
| JP3871655B2 (en) * | 2003-05-13 | 2007-01-24 | Ｊｆｅスチール株式会社 | Double-sided single layer submerged arc welding wire for high strength steel |
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| CN1709634A (en) * | 2005-06-28 | 2005-12-21 | 武汉钢铁(集团)公司 | Submerged-arc welding wire for high-strength pipeline steel |
| CN1919524A (en) * | 2006-09-13 | 2007-02-28 | 武汉钢铁(集团)公司 | High ductility buried arc welding wire for low-alloy super-strength steel |
| CN101288924A (en) * | 2007-04-20 | 2008-10-22 | 宝山钢铁股份有限公司 | Seawater corrosion resistance submerged arc welding wire rod, welding wire and application thereof |
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| JP特开2004-337863A 2004.12.02 |
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