CN103317257A - High-strength high-tenacity submerged arc welding wires for bainite steel - Google Patents
High-strength high-tenacity submerged arc welding wires for bainite steel Download PDFInfo
- Publication number
- CN103317257A CN103317257A CN2013102455242A CN201310245524A CN103317257A CN 103317257 A CN103317257 A CN 103317257A CN 2013102455242 A CN2013102455242 A CN 2013102455242A CN 201310245524 A CN201310245524 A CN 201310245524A CN 103317257 A CN103317257 A CN 103317257A
- Authority
- CN
- China
- Prior art keywords
- welding
- wire
- strength
- arc welding
- content
- 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
Images
Landscapes
- Arc Welding In General (AREA)
- Nonmetallic Welding Materials (AREA)
Abstract
The invention discloses high-strength high-tenacity submerged arc welding wires for bainite steel. The high-strength high-tenacity submerged arc welding wires for the bainite steel are formed by, based on the weight percent, 0.010 to 0.050 % of carbon, 1.800 to 2.100 % of manganese, 0.400 to 0.800 % of molybdenum, 0.150 to 0.450 % of tanium, 0.005 to 0.010 % of boron, 1.000 to 1.500 % of nickel, 0.200 to 0.300 % of copper, 0.010 to 0.020 % of silicon, 0.020 to 0.040 % of niobium, 0.100 to 0.400 % of chromium, 0.100 to 0.250 % of radium, 0.005 % of phosphorus, 0.003 % of sulphur and the abundant to be ferrum and the sum of the weight percent is 100 %. The high-strength high-tenacity submerged arc welding wires for the bainite steel have the advantages of solving the problems that a manufacturing cycle is long and the cost is high when measures such as the preheating and the postweld processing are used to weld the bainite steel in the prior art.
Description
Technical field
The invention belongs to field of welding material, be specifically related to a kind of bainitic steel high-strength and high ductility welding wire for submerged-arc welding.
Background technology
Along with the rapid growth of economy, people increase day by day to the demand of steel.High-grade bainitic steel has good intensity, toughness and welding performance and becomes desirable Industrial Steels material, and meet the sustainable development requirement and be subject to people's strong interest, obtain a wide range of applications in industries such as automobile, machine-building, electrical equipment and national defence.As everyone knows, the intensity of steel is higher, and its toughness deposit is lower.For this bainite steel product, the key technical problem that solve is exactly the weld defect problem.The prior art head it off is modal to be to take the measures such as preheating and post weld heat treatment, but the cost of these measures is to have prolonged the manufacturing cycle, has increased manufacturing cost, and has increased workman's labour intensity.
The high-strength and high ductility welding material can reduce the generation probability of weld defect to a certain extent, can also reduce requirement and the production cost of process conditions, and can obtain seam organization and the high welding point of Strengthening and Toughening of function admirable.As seen, develop a kind of high-performance solder wire material that is complementary with mother metal, and guarantee its application in industrial production, seem very important.
Summary of the invention
The purpose of this invention is to provide a kind of bainitic steel high-strength and high ductility welding wire for submerged-arc welding, solved the existing welding wire problem that the manufacturing cycle is long when the welding bainitic steel, cost is high.
The technical solution adopted in the present invention is: a kind of bainitic steel high-strength and high ductility welding wire for submerged-arc welding, composed of the following components by mass percentage: C0.010～0.050%, Mn1.800～2.100%, Mo0.400～0.800%, Ti0.150～0.450%, B0.005～0.010%, Ni1.000～1.500%, Cu0.200～0.300%, Si0.010～0.020%, Nb0.020～0.040%, Cr0.100～0.400%, Re0.100～0.250%, P＜0.005%, S＜0.003%, surplus are Fe, and above-mentioned each constituent mass percentage sum is 100%.
The invention has the beneficial effects as follows: bainitic steel of the present invention high-strength and high ductility welding wire for submerged-arc welding has solved prior art and has taked the measures such as preheating and after welding treatment to reduce the problem that the weld defect manufacturing cycle is long, cost is high when the welding bainitic steel; Welding wire and sintered flux SJ101 are used in conjunction with, and guarantee that stabilising arc is functional, the molten bath good fluidity, and the particle that splashes is tiny, and deslag after welding is easy, and slag covers evenly; Appearance of weld is careful attractive in appearance, and strength of joint is higher, toughness is good; Applicable to Large Heat Input Welding, not preheating before the weldering, postwelding is not processed, and both has been applicable to the individual layer multilayer, is applicable to the single or double welding yet; Development technology is simple, and is with low cost, is easy to suitability for industrialized production.
Description of drawings
Fig. 1 is that the welding wire that the embodiment of the invention 1 is produced welds the metallographic structure figure at rear weld seam center;
Fig. 2 is that the welding wire that the embodiment of the invention 2 is produced welds the metallographic structure figure at rear weld seam center;
Fig. 3 is that the welding wire that the embodiment of the invention 3 is produced welds the metallographic structure figure at rear weld seam center.
The specific embodiment
The present invention is described in detail below in conjunction with the drawings and specific embodiments.
A kind of bainitic steel of the present invention high-strength and high ductility welding wire for submerged-arc welding, composed of the following components by mass percentage: C0.010～0.050%, Mn1.800～2.100%, Mo0.400～0.800%, Ti0.150～0.450%, B0.005～0.010%, Ni1.000～1.500%, Cu0.200～0.300%, Si0.010～0.020%, Nb0.020～0.040%, Cr0.100～0.400%, Re0.100～0.250%, P＜0.005%, S＜0.003%, surplus are Fe, and above-mentioned each constituent mass percentage sum is 100%.
The design principle of chemical composition of the present invention is as follows:
(1) C:C content is close to zero, and the nose of bainite in the continuous cooling transformation (CCT) curve of steel will move to left, and forms bainite structure under the cooldown rate of wide range.C content raises, and the original austenite grain size increases, and the column crystal width increases, and the ratio of acicular ferrite (AF) increases, and the quantity of pro-eutectoid ferrite reduces.C content limit general control is below 0.12% in the bainitic steel weld metal, and carbon content increases, and toughness improves, but considers that steel-making increases smelting cost because of carbon drop, and C is controlled at 0.040～0.080%.Therefore to design welding wire C content be 0.010～0.050% in the present invention.
(2) Mn:Mn is austenite stabilizer element, significantly reduce the phase transition temperature that γ → α changes, the Main Function of Mn is the stability that increases overcooling austenite, make austenite phase transformation shift to lower temperature, eutectoid reaction is carried out under lower concentration of carbon, suppress its under higher temperature to polygonal ferrite (PF) phase transformation, (800～500 ℃ of common weld metal coolings, 3～30 ℃/s) time, Mn can suppress austenite to pearlitic transformation.The yield strength of weld metal and tensile strength raise with Mn content and are linear increase, every increase 0.01%Mn can make the yield strength of weld seam and tensile strength increase 10MPa, although and Mn do not increase the room temperature impact flexibility of Gao Gang, significantly reduces brittle transition temperature.The beneficial effect of Mn is that it can be combined into manganese sulfide with sulphur, makes the sulphur in the weld metal partly enter slag, play the effect of desulfurization, and residual manganese sulfide is not deposited in crystal boundary, secondly manganese refinement the tissue of weld metal.When Mn, Si exist simultaneously, along with the increase of Mn/Si content, phase transition temperature is reduced gradually, structure refinement, but Si significantly improves the pearlitic transformation temperature, forms comparatively thick carbide under higher temperature, so just impels separating out toughness of polygonal ferrite unfavorable.The present invention designs Mn content and is controlled at 1.800～2.100%.
(3) Si:Si is conducive to the deoxidation of welding pool metal, and in the low-alloy steel submerged-arc welding seam, mass fraction is that 0.15～0.3% Si content can make it reach the highest notch impact toughness.During submerged-arc welding, if ooze Si by solder flux, Si reaches as high as 0.8% in the weld metal, in this case, even Mn/Si ratio is greater than 3, nonmetallic notch impact toughness also can descend in the weld metal, this is owing to the increase along with Si content, and non-metallic inclusion (such as silicate) increases in the weld metal, remains on such as Si in 0.15～0.25% the scope, then higher Mn/Si can make the impact flexibility of weld metal obviously improve than (Mn/Si is than ﹥ 3).Therefore the present invention designs welding wire Si content range and is controlled at 0.010～0.020%.
(4) Mo:Mo can dwindle the γ phase region, forms strong carbide, and Main Function is to postpone pro-eutectoid ferrite to change and be conducive to form bainite structure, and Mo solid solution in weld seam exists in austenite or with the form of carbide, and suppresses perlitic transformation consumingly.Along with Mo content increases, tissue is the single bainite that contains bainite type ferrite and equally distributed martensite-austenite island by pearlite-bainite transformation, it can improve the toughness of Plate Welding heat affected area (HAZ), studies show that: when Mo content 0.2～0.3% the time, this improvement meeting is more obvious, and armor plate strength and low-temperature flexibility are all fine.When Mn content is 1.2%, add 0.15% Mo and can make in the weld seam acicular ferrite content be increased to 85% from 45%, and acicular ferrite crystal grain is tiny especially, but when Mn content drops to 0.8%, increase Mo and will can not change acicular ferrite content, and promote ferrite side plate to form.Mo can be used as hardening agent and uses in the bainitic steel weld seam, the adding of a small amount of Mo can improve the notch shock toughness, reduces brittle transition temperature, but general Mo content is less than 0.5%.The present invention designs the Mo content range and is controlled at 0.400～0.800%.
(5) the unlimited solid solution of Ni:Ni is the element that enlarges the γ phase region in γ-Fe.Ni can reduce dislocation motion drag and dislocation and the interstitial element reciprocation energy in the dot matrix, promotes stress relaxation, thereby reduces the brittle fracture tendency.Improve the Ni content in the bainitic steel weld metal, can guarantee to be issued to high tenacity in higher tensile strength.Simultaneously, Ni produces certain invigoration effect to the bainitic steel weld metal, and the additional mass mark is 1% Ni, and the yield strength of weld metal can improve 20～50MPa.In the Hi-Stren steel weld seam, the optimum range of Ni content is 0.8～1.6%.Therefore welding wire Ni content range of the present invention is 1.000～1.500%.
(6) Cr:Cr is the element that enlarges the γ phase region, reduces γ → α phase transformation critical-temperature, austenite is changed carry out under lower temperature, and the hardness of weld metal is cumulative with the increase of Cr content, when Cr ﹥ 0.5%, can have a negative impact to toughness.Cr content range of the present invention is controlled at 0.100～0.400%.
(7) Cu:Cu reduces γ phase transition temperature element, increases the stability of overcooling austenite, reduces martensite and begins transition point (M
s).When Cu content is in 0.03%～0.89% scope in the weld seam, along with the increase of Cu content, acicular ferrite (AF) quantity reduces, and grain boundary ferrite quantity increases, grain refinement, in fact Cu Main Function in Hi-Stren steel is to improve weather-resistant.Cu content 0.025% can improve corrosion resistance in the bainitic steel, when being higher than 0.25%, adds the corrosion resistance that more Cu can not continue to improve steel, therefore control Cu is in 0.2～0.3%.Therefore the Cu content range is controlled at 0.200～0.300% among the present invention.
(8) Ti:Ti is the element that dwindles the γ phase region, is strong deoxidier and Ti(C, N) forming element, these high melting compound particles can be used as crystallization nuclei, the refinement weld grain, and general Ti content is less than 0.003% the time, along with the increase of Ti content, acicular ferrite quantity increases.The effect of Ti in the bainitic steel weld metal is similar to vanadium, also can improve significantly the tensile strength of weld metal, and produces wholesome effect to improving the notch shock toughness, and only Ti content depends on its strength grade and the content of oxygen in the weld metal.As in the weld metal of moderate strength, best Ti content is about 0.1%, and in the high strength weld seam, and Ti content is that 0.015% weld metal toughness is best.The present invention designs the Ti content range and is controlled at 0.150～0.450%.
(9) B:B can obviously suppress the forming core of ferrite on austenite grain boundary, and the ferritic transformation curve is obviously moved to right, and makes simultaneously the bainite transformation curve become flat, just can obtain bainite structure in the larger cooling range; B also can the refinement seam organization, has strong reciprocation between B and the Ti, does not have enough Ti in the weld seam, and the Beneficial Effect of B is little, will promote upper bainite to form when B and Ti too high levels, and Ti, B again can not be too high thus.The B content range is controlled at 0.005～0.010% among the present invention.
(10) Nb: the high Nb amount that contains increases austenitic stability, make overcooling austenite to the low temperature structural transformation, but its content worsens again impact flexibility, and brittle transition temperature is raise, and should limit Nb content less than 0.05%.The present invention designs the Nb content range and is controlled at 0.020～0.040%.
(11) Re: rare earth Re rises in weld seam and purifies impurity, rotten being mingled with and Microalloying Effect, more is to be conducive to improve toughness plasticity, can comprehensively bring into play the strengthening effect of Mo, Ti, B.Re content range of the present invention is controlled at 0.100～0.250%.
The above-mentioned bainitic steel manufacturing process of high-strength and high ductility welding wire for submerged-arc welding specifically may further comprise the steps:
Selecting the pure iron of removing iron rust is welding wire steel, carries out ingot smelting in vacuum induction furnace, refining obtains smelting solder wire material; Be forged into square billet, remove the blemish such as surperficial casting skin and crackle; Billet rolling is become wire rod, carry out drawing (drawing step: wire rod-mechanical descaling-pickling derusts-dry-dry wire drawing-batch-heat treatment-dry wire drawing-batch-electroless copper-polish-batch-be wound in silk) and make welding wire.This welding wire is composed of the following components by mass percentage: C0.010～0.050%, Mn1.800～2.100%, Mo0.400～0.800%, Ti0.150～0.450%, B0.005～0.010%, Ni1.000～1.500%, Cu0.200～0.300%, Si0.010～0.020%, Nb0.020～0.040%, Cr0.100～0.400%, Re0.100～0.250%, P＜0.005%, S＜0.003%, surplus is Fe, and above-mentioned each constituent mass percentage sum is 100%.
Test piece for welding is bainitic steel, and specification is 500mm * 155mm * 15mm, and its Main Ingredients and Appearance (mass fraction %) is: 0.044C, and 0.22Si, 1.95Mn, 0.39Ni, 0.014Ti, 0.21Cu, 0.09Nb, the Fe surplus, thickness is 15mm.Its tensile strength is 868MPa, and yield strength is 745MPa, and percentage elongation is that 24.2%, 20 ℃ average Charpy impact (Charpy) absorption merit is 213J.
Adopt above-mentioned welding wire, cooperate sintered flux SJ101 as welding material, use MZ-1000 type automatic welder(welding machine) that test plate (panel) is carried out submerged-arc welding.
Bainitic steel of the present invention high-strength and high ductility welding wire for submerged-arc welding has the following advantages:
Welding wire of the present invention and sintered flux SJ101 welding wire coupling are used for domestic bainitic steel submerged-arc welding, and the tissue of weld seam is mainly the line and staff control of bainite ferrite and granular bainite, contains the black carbon compound that a small amount of disperse distributes; The tensile strength sigma of weld seam
b〉=790Mpa, impact flexibility mean value 〉=170J, percentage elongation mean value 〉=15%, the contraction percentage of area 〉=65%.Excellent combination property has guaranteed its application at industrial circle;
Welding wire of the present invention and sintered flux SJ101 welding wire coupling, have good processing performance: striking and stabilising arc are functional, and deslag performance is good, and the welding bead uniform in shaping is attractive in appearance;
The present invention is applicable to Large Heat Input Welding, not preheating before the weldering, and postwelding is not processed.Namely applicable to the individual layer multilayer, also weld applicable to single or double;
Welding wire of the present invention adopts the principle design of microalloying, and development technology is simple, and is with low cost, is fit to produce and industrialization.
Embodiment 1
Selecting the pure iron of removing iron rust is welding wire steel, carries out ingot smelting in vacuum induction furnace, refining obtains smelting solder wire material; Be forged into square billet, remove the blemish such as surperficial casting skin and crackle; Billet rolling is become wire rod, carry out drawing (drawing step: wire rod-mechanical descaling-pickling derusts-dry-dry wire drawing-batch-heat treatment-dry wire drawing-batch-electroless copper-polish-batch-be wound in silk) and make welding wire.This welding wire is composed of the following components by mass percentage: C0.010%, Mn1.800%, Mo0.400%, Ti0.150%, B0.006%, Ni1.200%, Cu0.200%, Si0.012%, Nb0.030%, Cr0.400%, Re0.200%, P0.003%, S0.002%, surplus is Fe, and above-mentioned each constituent mass percentage sum is 100%.
The test piece for welding groove adopts I type groove, adopts above-mentioned welding wire, cooperates sintered flux SJ101 as welding material, uses MZ-1000 type automatic welder(welding machine) that it is docked double-submerged arc, and welding condition is as shown in table 1.
Table 1 welding condition
The mechanical property of Welded Joints is tested, the result is as shown in table 2, and Welded Joints carries out the metallographic experiment, the metallographic structure of weld seam center as shown in Figure 1, the tissue at bainitic steel weld seam center is mainly acicular ferrite (AF) and granular bainite (GB), and acicular ferrite presents specific admixture distribution form and a fine microstructures.This random tiny slip bundle that is interspersed each other can improve its obdurability effectively, and the disperse of tiny granular bainite distributes and further strengthened again its performance.
The mechanical property of table 2 welding point
Embodiment 2
Selecting the pure iron of removing iron rust is that welding wire steel carries out ingot smelting in vacuum induction furnace, refining obtains smelting solder wire material; Be forged into square billet, remove the blemish such as surperficial casting skin and crackle; Billet rolling is become wire rod, carry out drawing (drawing step: wire rod-mechanical descaling-pickling derusts-dry-dry wire drawing-batch-heat treatment-dry wire drawing-batch-electroless copper-polish-batch-be wound in silk) and make welding wire.This welding wire is composed of the following components by mass percentage: C0.040%, Mn2.000%, Mo0.700%, Ti0.300%, B0.007%, Ni1.500%, Cu0.250%, Si0.010%, Nb0.020%, Cr0.100%, Re0.200%, P0.004%, S0.001%, surplus is Fe, and above-mentioned each constituent mass percentage sum is 100%.
The test piece for welding groove adopts I type groove, adopts above-mentioned welding wire, cooperates sintered flux SJ101 as welding material, uses MZ-1000 type automatic welder(welding machine) that it is docked double-submerged arc, and welding condition is as shown in table 3.
Table 3 welding condition
The mechanical property of Welded Joints is tested, the result is as shown in table 4, and Welded Joints carries out metallographic experiment, and the metallographic structure of weld seam center as shown in Figure 2, the microscopic structure of weld seam is mainly acicular ferrite (AF) and granular bainite (GB), the black carbon compound that has a small amount of disperse to distribute.Acicular ferrite distribution interlaced with each other, tiny granular bainite is uniformly distributed on its matrix, has increased the resistance that dislocation moves, and can effectively improve its obdurability.
The mechanical property of table 4 welding point
Embodiment 3
Selecting the pure iron of removing iron rust is that welding wire steel carries out ingot smelting in vacuum induction furnace, refining obtains smelting solder wire material; Be forged into square billet, remove the blemish such as surperficial casting skin and crackle; Billet rolling is become wire rod, carry out drawing (drawing step: wire rod-mechanical descaling-pickling derusts-dry-dry wire drawing-batch-heat treatment-dry wire drawing-batch-electroless copper-polish-batch-be wound in silk) and make welding wire.This welding wire is composed of the following components by mass percentage: C0.030%, Mn2.100%, Mo0.600%, Ti0.450%, B0.005%, Ni1.000%, Cu0.200%, Si0.015%, Nb0.040%, Cr0.300%, Re0.100%, P0.002%, S0.001%, surplus is Fe, and above-mentioned each constituent mass percentage sum is 100%.
The test piece for welding groove adopts Y type groove (60 ± 3 ° of grooves), adopts above-mentioned welding wire, cooperates sintered flux SJ101 as welding material, uses MZ-1000 type automatic welder(welding machine) that it is docked double-submerged arc, and welding condition is as shown in table 5.
Table 5 welding condition
The mechanical property of Welded Joints is tested, the result is as shown in table 6, and Welded Joints carries out the metallographic experiment, the metallographic structure of weld seam center as shown in Figure 3, the tissue at weld seam center is mainly acicular ferrite (AF) and granular bainite (GB), and acicular ferrite is with the existence of " basketry woollen yarn knitting " state, and tiny granular bainite is distributed on its matrix, can effectively hinder the expansion of crackle, improve its obdurability.
The mechanical property of table 6 welding point
Embodiment 4
Selecting the pure iron of removing iron rust is that welding wire steel carries out ingot smelting in vacuum induction furnace, refining obtains smelting solder wire material; Be forged into square billet, remove the blemish such as surperficial casting skin and crackle; Billet rolling is become wire rod, carry out drawing (drawing step: wire rod-mechanical descaling-pickling derusts-dry-dry wire drawing-batch-heat treatment-dry wire drawing-batch-electroless copper-polish-batch-be wound in silk) and make welding wire.This welding wire is composed of the following components by mass percentage: C0.040%, Mn1.900%, Mo0.800%, Ti0.400%, B0.008%, Ni1.400%, Cu0.300%, Si0.010%, Nb0.030%, Cr0.400%, Re0.250%, P0.003%, S0.001%, surplus is Fe, and above-mentioned each constituent mass percentage sum is 100%.
The test piece for welding groove adopts I type groove (60 ± 3 ° of grooves), adopts above-mentioned welding wire, cooperates sintered flux SJ101 as welding material, uses MZ-1000 type automatic welder(welding machine) that it is docked double-submerged arc, and welding condition is as shown in table 7.
Table 7 welding condition
The mechanical property of Welded Joints is tested, and the result is as shown in table 8.
The mechanical property of table 8 welding point
Embodiment 5
Selecting the pure iron of removing iron rust is that welding wire steel carries out ingot smelting in vacuum induction furnace, refining obtains smelting solder wire material; Be forged into square billet, remove the blemish such as surperficial casting skin and crackle; Billet rolling is become wire rod, carry out drawing (drawing step: wire rod-mechanical descaling-pickling derusts-dry-dry wire drawing-batch-heat treatment-dry wire drawing-batch-electroless copper-polish-batch-be wound in silk) and make welding wire.This welding wire is composed of the following components by mass percentage: C0.050%, Mn1.900%, Mo0.600%, Ti0.300%, B0.010%, Ni1.300%, Cu0.200%, Si0.020%, Nb0.020%, Cr0.100%, Re0.200%, P0.004%, S0.002%, surplus is Fe, and above-mentioned each constituent mass percentage sum is 100%.
The test piece for welding groove adopts Y type groove (60 ± 3 ° of grooves), adopts above-mentioned welding wire, cooperates sintered flux SJ101 as welding material, uses MZ-1000 type automatic welder(welding machine) that it is docked double-submerged arc, and welding condition is as shown in table 9.
Table 9 welding condition
The mechanical property of Welded Joints is tested, and the result is as shown in table 10.
The mechanical property of table 10 welding point
Present stage, H08C welding wire and H03Mn welding wire are mainly adopted in submerged-arc welding, and when itself and sintered flux SJ101 coupling was carried out the submerged arc welding bainitic steel, the average mechanical property of welding point was shown in Table 11.Welding wire mechanical property of the present invention is compared with result shown in the table 11, remaining basically stable aspect percentage elongation and the contraction percentage of area, the weld seam average tensile strength that adopts welding wire of the present invention to weld is minimum to be 793Mpa, average notched bar impact strength minimum is 174J, and the average tensile strength that adopts H08C welding wire and the welding of H03Mn welding wire to obtain is respectively 763Mpa, 792Mpa, impact flexibility is for Wei not 113J, 137J, as seen during welding wire submerged arc welding bainitic steel of the present invention, have excellent combination property, can guarantee that it is in the application of industrial circle.
The mechanical property of the existing welding wire for submerged-arc welding welding point of table 11
Claims (1)
1. bainitic steel high-strength and high ductility welding wire for submerged-arc welding, it is characterized in that, composed of the following components by mass percentage: C0.010～0.050%, Mn1.800～2.100%, Mo0.400～0.800%, Ti0.150～0.450%, B0.005～0.010%, Ni1.000～1.500%, Cu0.200～0.300%, Si0.010～0.020%, Nb0.020～0.040%, Cr0.100～0.400%, Re0.100～0.250%, P＜0.005%, S＜0.003%, surplus is Fe, and above-mentioned each constituent mass percentage sum is 100%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201310245524.2A CN103317257B (en) | 2013-06-20 | 2013-06-20 | High-strength high-tenacity submerged arc welding wires for bainite steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201310245524.2A CN103317257B (en) | 2013-06-20 | 2013-06-20 | High-strength high-tenacity submerged arc welding wires for bainite steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN103317257A true CN103317257A (en) | 2013-09-25 |
| CN103317257B CN103317257B (en) | 2015-04-22 |
Family
ID=49186459
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201310245524.2A Expired - Fee Related CN103317257B (en) | 2013-06-20 | 2013-06-20 | High-strength high-tenacity submerged arc welding wires for bainite steel |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN103317257B (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103600178A (en) * | 2013-11-27 | 2014-02-26 | 南车眉山车辆有限公司 | High-strength solid wire made of weathering resistant steel through gas shielded welding |
| CN104722949A (en) * | 2015-02-02 | 2015-06-24 | 温州大学 | Solid-core welding wire for reducing welding residual stress of high-strength steel |
| WO2015188427A1 (en) * | 2014-06-11 | 2015-12-17 | 江苏省沙钢钢铁研究院有限公司 | Submerged arc welding wire and welding method |
| CN105414799A (en) * | 2015-12-23 | 2016-03-23 | 宜昌猴王焊丝有限公司 | Solid cored welding wire of low-alloy and high-strength steel and application of solid cored welding wire |
| CN107900555A (en) * | 2017-12-18 | 2018-04-13 | 武汉钢铁有限公司 | A kind of welding wire for 630MPa grades high Nb steel two pass submerged-arc welding |
| CN111673313A (en) * | 2020-06-04 | 2020-09-18 | 江苏省沙钢钢铁研究院有限公司 | Gas shielded welding wire with fire-resistant and weather-resistant characteristics |
Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6188037B1 (en) * | 1997-03-26 | 2001-02-13 | Sumitomo Metal Industries, Ltd. | Welded high-strength steel structures and method of manufacturing the same |
| CN1623719A (en) * | 2004-12-06 | 2005-06-08 | 西安理工大学 | Solder wire material of submerged-arc welding for high grade 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 |
| CN101116930A (en) * | 2007-09-12 | 2008-02-06 | 钢铁研究总院 | High-strength gas-defended welding wire material |
| CN101549443A (en) * | 2009-05-08 | 2009-10-07 | 西安理工大学 | Submerged arc welding wire material for X80 pipeline steel and preparing method thereof |
| CN101905392A (en) * | 2010-08-26 | 2010-12-08 | 宜昌猴王焊丝有限公司 | High-toughness low-alloy solid welding wire |
| CN102019516A (en) * | 2010-11-01 | 2011-04-20 | 西安理工大学 | Solder wire for submerged arc welding of X100 pipeline steel and preparation method thereof |
| CN103056550A (en) * | 2012-12-25 | 2013-04-24 | 中国船舶重工集团公司第七二五研究所 | Gas shielded welding solder wire with 900-MPa yield strength |
-
2013
- 2013-06-20 CN CN201310245524.2A patent/CN103317257B/en not_active Expired - Fee Related
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6188037B1 (en) * | 1997-03-26 | 2001-02-13 | Sumitomo Metal Industries, Ltd. | Welded high-strength steel structures and method of manufacturing the same |
| CN1623719A (en) * | 2004-12-06 | 2005-06-08 | 西安理工大学 | Solder wire material of submerged-arc welding for high grade 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 |
| CN101116930A (en) * | 2007-09-12 | 2008-02-06 | 钢铁研究总院 | High-strength gas-defended welding wire material |
| CN101549443A (en) * | 2009-05-08 | 2009-10-07 | 西安理工大学 | Submerged arc welding wire material for X80 pipeline steel and preparing method thereof |
| CN101905392A (en) * | 2010-08-26 | 2010-12-08 | 宜昌猴王焊丝有限公司 | High-toughness low-alloy solid welding wire |
| CN102019516A (en) * | 2010-11-01 | 2011-04-20 | 西安理工大学 | Solder wire for submerged arc welding of X100 pipeline steel and preparation method thereof |
| CN103056550A (en) * | 2012-12-25 | 2013-04-24 | 中国船舶重工集团公司第七二五研究所 | Gas shielded welding solder wire with 900-MPa yield strength |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103600178A (en) * | 2013-11-27 | 2014-02-26 | 南车眉山车辆有限公司 | High-strength solid wire made of weathering resistant steel through gas shielded welding |
| CN103600178B (en) * | 2013-11-27 | 2016-08-17 | 中车眉山车辆有限公司 | A kind of high-strength weathering steel gas shield solid core welding wire |
| WO2015188427A1 (en) * | 2014-06-11 | 2015-12-17 | 江苏省沙钢钢铁研究院有限公司 | Submerged arc welding wire and welding method |
| JP2017523046A (en) * | 2014-06-11 | 2017-08-17 | 江▲蘇▼省沙▲鋼鋼鉄▼研究院有限公司Ｉｎｓｔｉｔｕｔｅ Ｏｆ Ｒｅｓｅａｒｃｈ Ｏｆ Ｉｒｏｎ Ａｎｄ Ｓｔｅｅｌ， Ｊｉａｎｇｓｕ Ｐｒｏｖｉｎｃｅ／Ｓｈａ−Ｓｔｅｅｌ， Ｃｏ．Ｌｔｄ | Submerged arc welding wire and welding method |
| KR101923948B1 (en) | 2014-06-11 | 2018-11-30 | 인스티튜트 오브 리서치 오브 아이론 앤드 스틸, 지앙수 프로빈스/샤-스틸, 씨오. 엘티디 (중국) | Submerged arc welding wire and weldling method |
| CN104722949A (en) * | 2015-02-02 | 2015-06-24 | 温州大学 | Solid-core welding wire for reducing welding residual stress of high-strength steel |
| CN105414799A (en) * | 2015-12-23 | 2016-03-23 | 宜昌猴王焊丝有限公司 | Solid cored welding wire of low-alloy and high-strength steel and application of solid cored welding wire |
| CN107900555A (en) * | 2017-12-18 | 2018-04-13 | 武汉钢铁有限公司 | A kind of welding wire for 630MPa grades high Nb steel two pass submerged-arc welding |
| CN107900555B (en) * | 2017-12-18 | 2020-04-21 | 武汉钢铁有限公司 | Welding wire for 630MPa grade high Nb steel double-channel submerged arc welding |
| CN111673313A (en) * | 2020-06-04 | 2020-09-18 | 江苏省沙钢钢铁研究院有限公司 | Gas shielded welding wire with fire-resistant and weather-resistant characteristics |
Also Published As
| Publication number | Publication date |
|---|---|
| CN103317257B (en) | 2015-04-22 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN100441364C (en) | High ductility buried arc welding wire for low-alloy super-strength steel | |
| CN104227265B (en) | Ultrahigh-intensity all-austenite stainless steel welding wire | |
| CN103317257B (en) | High-strength high-tenacity submerged arc welding wires for bainite steel | |
| CN100469513C (en) | High-strength gas-defended welding wire material | |
| CN101733580B (en) | 800MPa-grade high-strength high-tenacity gas shielded welding wire | |
| CN106312372B (en) | A kind of welding of 1000MPa high-strength steel gas shielded solid welding wire and its preparation and welding method | |
| CN101628366A (en) | Gas shielded welding wire for high-grade oil pipeline steel and preparation method thereof | |
| CN103495815B (en) | Welding material, its application and welding method | |
| CN101722382A (en) | High-strength welding wires of gas shielded welding needing thermal refining after welding | |
| CN103194688A (en) | Wear-resistant steel pipe and manufacture method thereof | |
| CN103317256A (en) | Austenitic stainless steel submerged-arc welding wire with excellent high-temperature strength | |
| CN107984112A (en) | A kind of high-strength submerged-arc welding wire with good low-temperature toughness | |
| CN112247399A (en) | 700 MPa-level annealing-free drawing high-strength steel gas protection solid welding wire | |
| CN101462207A (en) | High-ductility submerged arc welding wire for pipeline steel | |
| CN1321777C (en) | Niobium-titanium-boron microalloy high-strength gas protecting welding wire | |
| CN102011061A (en) | High-performance Cu-containing steel and heat processing process thereof | |
| CN101619419B (en) | Steel plate for low-carbon high-niobium high strength welding structure and method for manufacturing same | |
| CN102658440A (en) | High corrosion resistant type weather-resistant submerged arc welding wire and wire rod for railway vehicles | |
| CN102756219A (en) | Welding wire and wire rod as well as application thereof | |
| CN104988388B (en) | Economical L485Q seamless pipeline pipe and preparation method thereof | |
| CN103451570A (en) | Spiral submerged-arc welded pipe for oil and gas transmission suitable for low temperatures and manufacturing method thereof | |
| CN102267021B (en) | Submerged arc welding wire for pipe line steel and method for manufacturing submerged arc welding wire | |
| CN103184391B (en) | Annular plate steel used for top cover of million-kilowatt-level large-scale hydraulic turbine and manufacturing method thereof | |
| CN102962601B (en) | A kind of welding wire | |
| CN105695858A (en) | High-carbon super-high-silicon bainite steel for railway frogs and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20150422 Termination date: 20200620 |
|
| CF01 | Termination of patent right due to non-payment of annual fee |