The application is to be September 30 calendar year 2001, application number the dividing an application for the application for a patent for invention of " method for making of large-line energy submerged arc welding joint, this joint and used welding wire and solder flux " that be 01135349.X, denomination of invention the applying date.
The specific embodiment
The inventor etc. are in order to finish above-mentioned problem, adopt the large-line energy submerged-arc welding of weld heat input more than 150kJ/cm to engage, concentrate on studies about the various factors of the toughness that influences the gained weld metal as 490~520MPa level steel of materials to be welded.Found that the toughness of the weld metal that obtains by the large-line energy submerged-arc welding of weld heat input more than 150kJ/cm is very responsive to nitrogen, sometimes because little by little variation of nitrogen content causes the remarkable deterioration of toughness.
Particularly at Ti and Nb content after a little while, owing to increasing microstructure coarsening that nitrogen content causes weld metal, remarkable deterioration a little as the steel of materials to be welded.This generally thinks because steel contain the Ti amount after a little while, can not fully supply with Ti to weld metal, is difficult to adjust due to the solid solution N content.
The inventor etc. have further launched discussion based on above-mentioned opinion, the result expects: also can obtain stable and the large-line energy submerged-arc welding seam metal of high tenacity in order to contain Ti and Nb amount in the steel as materials to be welded after a little while, when suitably adjusting the N content of welding wire, by making an amount of Ti that contains in the welding wire corresponding to N content in the welding wire, thereby also may obtain fine weld structure even carry out the large-line energy welding.
The inventor etc. have carried out stably giving large-line energy submerged-arc welding seam metal more research, the discussion of high tenacity.Originally, absorb merit, toughness value (vE with regard to grain boundary ferrite growing amount in the weld metal and Xia Bi
0) relation to adopt weld heat input the welding of the large-line energy submerged-arc welding more than 150kJ/cm Ti content below the 0.006 quality %, the weld metal of the steel gained of the thickness of slab 40mm of Nb content below 0.012 quality % investigates.Its investigation the results are shown in Fig. 4, can get following new opinion by Fig. 4: by making grain boundary ferrite growing amount in the weld metal below 15 area %, ideal situation is below the 10 area %, can stably give high tenacity.
The quality % ratio of the B/N in the weld metal and the relation of grain boundary ferrite growing amount have also been investigated.It the results are shown in Fig. 5.Fig. 5 shows, contain Mo, Nb etc. in the welding wire and add an amount of Mo, Nb etc. in weld metal, B/N quality % ratio is adjusted into desired value by making, the grain boundary ferrite growing amount of weld metal is controlled at that 15.0 area % are following, ideal situation is to be possible below the 10.0 area %.
In addition, the welding wire that the adjustment of the solid solution nitrogen content in the weld metal contains Ti and Nb as welding wire by use can have improvement to a certain degree, but uses when not containing the welding wire of Ti and Nb as welding wire, and it adjusts difficult, the remarkable deterioration of the toughness of weld metal.Use when not containing the welding wire of Ti, the toughness deterioration of weld metal is remarkable especially.
Usually for the widely-used high 490~520MPa level steel of property, Ti content below the 0.006 quality %, Nb content below 0.012 quality % to contain the few steel of Ti, Nb representative, be difficult to obtain stable in the time of most and the weld metal of high tenacity.The urgent welding of wishing to obtain being applicable to this steel, the stable and weld metal of good-toughness.
The inventor etc. are based on above-mentioned opinion, further carried out discussion, the result expects: by the Ti of welding steel material and Nb content after a little while, even use the welding wire that does not particularly contain Ti to carry out the large-line energy submerged arc welding, pass through to use the atomized iron powder of N content below 0.0030 quality % as the iron powder that adds in the solder flux, also may obtain stable and the weld metal of high tenacity.In addition, in order stably to give large-line energy submerged-arc welding seam metal higher toughness, wish to make to contain Mo, Nb etc. in the solder flux, by adding an amount of Mo and Nb etc. to weld metal, the quality % ratio of B/N is adjusted into desired value, the grain boundary ferrite growing amount in the weld metal is controlled at that 15.0 area % are following, ideal situation is to be possible below the 10.0 area %.In this occasion, effect becomes big when adding to a spot of Ti in the weld metal by solder flux.
The one-tenth of the weld metal that the large-line energy submerged-arc welding welding that more than illustrates obtains is grouped in following scope is advisable.Below quality % in composition only represent with %.
C:0.03~0.15%
C amount in the weld metal is as if less than 0.03%, and the toughness of weld metal is difficult to improve, and one surpasses 0.15%, causes weld crack easily.Thereby C content is taken as C:0.03~0.15% in the weld metal.
Si:0.10~1.00%
Si amount in the weld metal is as if less than 0.10%, and the oxygen content of weld metal uprises, and is difficult to obtain good weld metal toughness.In addition, the Si amount one in the weld metal surpasses 1.00%, then generates the island martensite body in weld metal, and the toughness of weld metal is tending towards deterioration.So to measure be 0.10~1.00% to Si in the weld metal.
Mn:0.70~2.50%
Mn amount in the weld metal is as if less than 0.70%, and then the pearlitic transformation in weld metal is suppressed, the toughness deterioration of weld metal.On the other hand, the Mn amount one in the weld metal surpasses 2.50%, then generates the island martensite body in weld metal, and the toughness of weld metal is tending towards deterioration.So to measure be 0.70~2.50% to Mn in the weld metal.
Ti:0.003~0.030%
Ti exists as oxide in weld metal, works as ferritic forming core core, and be that the ferrite refinement is necessary., its Ti content is as if less than 0.003%, and this effect is insufficient.In addition, the Ti amount one in the weld metal surpasses 0.030%, and the intensity of weld metal becomes too high, is easy to generate by the low temperature crackle due to the hardness rising of weld metal.So it is 0.003~0.030% that the Ti in the weld metal is measured.
Below the N:0.0050%
N is the element that makes the toughness deterioration of weld metal, and the present invention wishes to reduce as far as possible.Owing to contain the N amount in the weld metal once surpassing 0.0050% toughness deterioration, so be limited to below 0.0050%.Secondly, it also is possible below 0.0020% that N content is reduced to, but because the welding material cost increases, and the manufacturing expense of welding point uprises, so wish more than 0.0020%.
From Mo:0.10~0.50%, Nb:0.010~0.200%, Ni:0.05%~1.00%, select more than a kind or 2 kinds
Mo, Nb, Ni have the effect that the toughness that makes weld metal significantly improves, and the present invention can select as required, contain.Mo, Nb are suppressed at the generation of the thick grain boundary ferrite that austenite grain boundary separates out, and the toughness of weld metal is improved.This effect more than containing Mo:0.10%, to contain Nb:0.010% remarkable when above.On the other hand, content surpasses Mo:0.50%, Nb:0.200% respectively, and the tissue of weld metal becomes upper bainite easily, the toughness deterioration.Thus, preferable range is respectively Mo:0.10~0.50%, Nb:0.010~0.200%.
In addition, Ni improves the toughness of ferritic phase, and the toughness of weld metal is improved.This effect is 0.05% remarkable when above at content.On the other hand, one surpasses 1.00%, just causes the generation of low temperature crackle easily.Therefore, the Ni preferable range is 0.05%~1.00%.
Grain boundary ferrite growing amount in the weld metal: below the 15.0 area %
In order stably to give large-line energy submerged-arc welding seam metal higher toughness, not only only adjust the composition of weld metal, also be necessary to make grain boundary ferrite growing amount in the weld metal below 15.0 area %.In order more stably to obtain high tenacity, the grain boundary ferrite growing amount in the weld metal is necessary below 10.0 area %.Secondly, observe weld metal and measured grain boundary ferrite growing amount wherein.Use light microscope, electron microscope etc. in the observation, observing multiplying power is 10~500 times.To corrode by corrosive liquid behind the sightingpiston grinding and polishing, and use the image analysis treating apparatus will observe picture and carry out the image processing, obtain the grain boundary ferrite growing amount in the weld metal.The mensuration of grain boundary ferrite growing amount needn't limit especially in the weld metal, and common assay method is also applicable.
0.60≤B/N≤1.20
In order to make grain boundary ferrite growing amount in the weld metal below 10.0 area %, not only adjust the solid solution N amount of weld metal, also need in weld metal, to add an amount of Mo, Nb etc., adjust the quality % ratio of the B/N in the weld metal simultaneously.B is suppressed at the generation of the thick grain boundary ferrite that austenite grain boundary separates out, and is the element that the toughness of weld metal is improved.The quality % ratio of B/N is as if less than 0.60, and its effect is insufficient, can not stably obtain higher toughness.In addition, the quality % of B/N surpasses 1.20 than one, and toughness is with regard to deterioration.So the quality % of the B/N in the weld metal is advisable below 1.20 than with more than 0.60.
As the 1st method of the weld metal that obtains the invention described above, by limiting the method that welding wire is formed.At this moment solder flux does not need special qualification, and generally well-known sintered flux all can use.
At first, the qualification reason of forming about large-line energy submerged-arc welding wire of the present invention is illustrated.Below quality % in composition only represent with %.
C:0.03~0.10%
C is the element that increases weld metal intensity, and the present invention contains more than 0.03% in welding wire in order to ensure desirable weld metal intensity.If C content in the welding wire is difficult to obtain the weld metal intensity of defined less than 0.03%, and the CO dividing potential drop step-down in arc atmosphere during welding, worries to be involved in from atmosphere N, and the N content of weld metal increases.On the other hand, content one surpasses 0.10%, and the C content in the weld metal increases, and in the time of the toughness deterioration of weld metal, heat cracking takes place easily.Therefore, C is limited to C:0.03~0.10%.Have, ideal situation is 0.04~0.08% again.
Below the N:0.0035%
N is the element that makes the toughness deterioration of weld metal, wishes reduction as far as possible and the N too high levels that content one surpasses in 0.0035% weld metal in welding wire in the present invention, the toughness deterioration.Therefore, N is limited to below 0.0035%.Have, it also is possible below 0.0010% that N content is reduced to again, but the increase of concise cost is a high price, so wish that N content is more than 0.0010% economically.
Below the Si:0.40%
Si works as deoxidier, is the element that effectively reduces the oxygen in the weld metal.Contain but one surpasses 0.40% volume, the cementite that then suppresses weld metal generates, and when generating the island martensite body, promotes ferritic alligatoring, makes the toughness deterioration of weld metal.Therefore, Si is limited to below 0.40%.Secondly, the Si of steel or the SiO in the solder flux
2Also supply Si, the Si in the welding wire is to be advisable below 0.30%.
Mn:1.00~2.50%
Mn works as deoxidier, is the element that effectively reduces the oxygen in the weld metal.Mn improves quenching degree in addition, and thinning microstructure has the effect that the intensity of weld metal is increased by solution strengthening simultaneously.In order to obtain this effect, need to contain the Mn more than 1.00% among the present invention.If contain quantity not sufficient 1.00%, then be difficult to obtain desirable weld metal intensity, generate thick tissue, the toughness deterioration of weld metal in the weld structure easily.On the other hand, content surpasses 2.50%, and tissue thinning effect is saturated, simply hinders the diffusion of C, when generating the island martensite body, significantly hardens owing to solution strengthening makes weld metal, makes the toughness deterioration of weld metal.Therefore, Mn is limited to 1.00~2.50%.Moreover ideal situation is 1.40~2.10%.
Ti:0.030% is above, the quality % of Ti/N ratio: 15~50
Ti is owing to thinning weld metal structure, so add in welding wire in the present invention.Particularly effective after a little while as the Ti content in the steel of materials to be welded.For this weld structure of refinement, need contain more than 0.030%.If less than 0.030%, particularly as the Ti content in the steel of materials to be welded after a little while, the refinement of weld structure is insufficient.If add Ti to weld metal by solder flux, the welding bead appearance degradation is then arranged and take off problems such as slag is bad, in the present invention, add Ti to weld metal and mainly undertaken by welding wire.
Again, because the Ti fix N, adjust solid solution N amount toughness is improved, so Ti content is more than 0.030% in the present invention, and corresponding to the N content in the welding wire, the quality % ratio of Ti/N is adjusted into 15~50.The quality % ratio of Ti/N is as if less than 15, and then the tough property improvement effect of weld metal is little.On the other hand, if the quality % of Ti/N contains Ti, then the toughness deterioration of weld metal than surpassing 50 superfluously.Therefore, limit Ti more than 0.030%, and the quality % of Ti/N is than the scope that is 15~50.Have again, consider that from toughness desirable Ti is below 0.200%.Better situation is below 0.150%.
From Mo:0.10~0.60%, Nb:0.010~0.100%.Select in B:0.0005~0.0100%, Ni:0.20%~2.00% more than a kind or 2 kinds
Mo, Nb, B, Ni have the effect of the toughness that significantly improves weld metal, and the present invention can select as required, contain.Mo, Nb, B are suppressed at the generation of the thick grain boundary ferrite that austenite grain boundary separates out, and the toughness of weld metal is improved.This effect more than containing Mo:0.10%, contain more than the Nb:0.010%, to contain B:0.0005% remarkable when above.On the other hand, content surpasses Mo:0.60%, Nb:0.100%, B:0.0100% respectively, and the tissue of weld metal becomes upper bainite easily, the toughness deterioration.Thus, preferable range is respectively Mo:0.10~0.60%, Nb:0.010~0.100%, B:0.0005~0.0100%.
Again, Ni improves the toughness of ferritic phase, and the toughness of weld metal is improved.This effect is 0.20% remarkable when above at content.On the other hand, one surpasses 2.00%, causes the generation of low temperature crackle easily.Therefore, the Ni preferable range is 0.20%~2.00%.
Remainder beyond the mentioned component is Fe and unavoidable impurities.As unavoidable impurities, below the permission O:0.0050%, below the P:0.020%, below the S:0.010%.
Secondly, welding wire of the present invention is considered from raising wire feeding property, rust-preventing characteristic, is preferably implemented copper facing at welding wire surface.In addition, the low heat input submerged arc welding that welding wire of the present invention promptly is used in the not enough 150kJ/cm of heat input does not have any problem yet, can stablize the weld metal that obtains having excellent in toughness natch.
In addition, when using the welding wire of the invention described above, the solder flux of use does not need special qualification, and generally well-known sintered flux all can use, but the sintered flux of oxide that preferably contains the boron of 0.1~1.0 quality % is good.Provide B by it to weld metal, suppress the alligatoring of tissue, prevent the deterioration of toughness.Secondly, the flux constituent beyond the oxide of boron does not limit especially, but represents that with quality % ideal situation is to contain SiO
2: 15~28%, MgO:15~38%, iron powder: 15~35%, CaCO
3: 5~15%, Al
2O
3: 5~20%, TiO
2: 2~10%, CaF
2: 2~10%, the metal powder beyond the iron powder: below 8%, even the metal powder beyond the iron powder surpasses the weld metal that 8 quality % also can obtain excellent in toughness, but because the welding material cost increases, the manufacturing expense of welding point uprises, so to contain iron powder metal powder in addition: be advisable below 8%.Secondly, in the present invention, solder flux is not limited thereto, in the solder flux of JISZ3352 defined so long as the solder flux of good manufacturability can not contain iron powder.Have, when adding iron powder in solder flux, ideal situation is to use the following iron powder of N:0.0030 quality % again.The following iron powder of N:0.0030 quality % is advisable with 20~45 quality % that contain the solder flux total amount.
N content one in the iron powder surpasses 0.0030 quality %, and the N content of the weld metal that then obtains increases, and demonstrates to be difficult to the stable tendency of guaranteeing high tenacity.Have, the N content in the iron powder is preferably below 0.0025 quality % again.
Iron powder in the solder flux time helps to increase to molten bath transition, deposited speed, improves welding efficiency and reduce weld heat input in welding.The content of the iron powder that the N:0.0030 quality % in the solder flux is following is as if less than 20 quality %, and above-mentioned effect is little, and on the other hand, content one surpasses the tendency that 45 quality % then demonstrate electric arc instability, welding bead appearance degradation.Thus, the content of the iron powder that N:0.0030 quality % is following is with respect to the solder flux total amount, and preferable range is 20~45 quality %.
In addition, as the 2nd method of the weld metal that obtains the invention described above, by limiting the method that solder flux is formed.At this moment welding wire does not need special qualification, and generally well-known welding wire for submerged-arc welding all can use.
Submerged arc flux of the present invention is a sintered flux, is applicable to the large-line energy submerged arc welding of heat input more than 150kJ/cm well.At first, the reason about the composition that limits submerged arc welding flux of the present invention is illustrated.Be meant quality % when below not having special declaration with respect to the solder flux total amount.Following quality % only represents with %.
Iron powder: 20~45%
Submerged arc flux mainly is made of oxide, fluoride, contains metal powder based on iron powder at the solder flux that is used for the welding of large-line energy and high efficiency.Iron powder in the solder flux time helps to increase to molten bath transition, deposited speed in welding, improves welding efficiency.
Submerged arc flux of the present invention contains 20~45% iron powder with respect to the solder flux total amount.The content of the iron powder in the solder flux is as if less than 20%, and above-mentioned effect is little, and on the other hand, content one surpasses 45% tendency that demonstrates electric arc instability, welding bead appearance degradation.Thus, the content of iron powder is taken as 20~45% with respect to the solder flux total amount.
In the present invention, use N content at the atomized iron powder below 0.0030% as iron powder again.The contained N of iron powder in the solder flux increases the N in the weld metal, reduces the toughness of weld metal.Therefore, in the present invention, the N content of the iron powder in the solder flux is reduced to suitable as far as possible.N content one in the iron powder surpasses 0.0030%, and the N content of the weld metal that then obtains increases, and demonstrates to be difficult to the stable tendency of guaranteeing high tenacity.Therefore, in the present invention, the N content of the iron powder in the solder flux is limited to below 0.0030%.Ideal situation be N content in the iron powder below 0.0025%, consider again serving as better more than 0.0010% from economy.
As the iron powder that has reduced N content, use by molten metal favourable on economy by the atomized iron powder of atomization manufacturing.In addition, by atomized iron powder is used as the solder flux raw material, this benefit of binder amount in the time of reducing the solder flux granulation is arranged also.
Atomized iron powder is that usually the operation by dehydration-drying-pulverizing-classification-processing reduction-pulverizing-classification becomes product with after molten metal spraying, the efflorescence.The N content of common atomized iron powder is about 0.0050%, in order to become the low N atomized iron powder below 0.0030%, will reduce the N amount of molten metal certainly, but need suitably be adjusted at reduction temperature in the processing reduction operation, cooling velocity etc.
B compound: convert 0.03~0.30% with B
B transition in weld metal when welding has the thick ferritic generation that suppresses to be created on austenite grain boundary in weld metal, make the effect of the toughness raising of weld metal, and B can reach this effect at an easy rate.This effect is by containing the convert B compound more than 0.03% that surpasses the solder flux total amount and more remarkable of useful B.On the other hand, convert and account for 0.30% B compound of solder flux total amount, the tendency of weld metal toughness deterioration is then arranged if contain useful B.
(A) group and (B) group in 1 group or 2 groups
(A) group: Mo powder.In molybdenum-iron powder and the Mo compound powder more than a kind or 2 kinds: convert to add up to 0.2~2.0% with Mo
(B) group: in Nb powder, ferro-niobium powder and the Nb compound powder more than a kind or 2 kinds: convert to add up to 0.02~0.15% with Nb
(A) group is to make that to contain Mo, (B) group in the weld metal be to make the supply source that contains Nb in the weld metal.Mo, Nb all transition in weld metal when welding, in weld metal, has the thick ferritic generation that suppresses to be created on austenite grain boundary, make the effect of the toughness raising of weld metal, 1 group or 2 groups that selects can be selected, be contained to above-mentioned effect as required from (A) group, (B) group.
Above-mentioned effect converting with Mo more than a kind or 2 kinds in Mo powder, molybdenum-iron powder and the Mo compound powder of (A) group amounts to 0.2% or more, amounting to 0.02% with the Nb conversion more than a kind or 2 kinds and become remarkable when above in Nb powder, ferro-niobium powder and the Nb compound powder of (B) group.On the other hand, if excess contains respectively (A) group and (B) group, wherein (A) group: will convert to add up to surpass 2.0% with Mo more than a kind or 2 kinds in Mo powder, molybdenum-iron powder and the Mo compound powder; (B) group: with adding up to above 0.15% with the Nb conversion more than a kind or 2 kinds in Nb powder, ferro-niobium powder and the Nb compound powder, then the tissue of weld metal becomes upper bainite easily, and the tendency of the toughness deterioration of weld metal is arranged.
On the mentioned component basis also from SiO
2: 10~28%, CaCO
3: 5~15%, MgO:15~38%, Al
2O
3: 3~20%, TiO
2: 2~10%, CaF
2: 2~10%, atomized iron powder, the metal powder beyond Mo powder, molybdenum-iron powder, Nb powder and the ferro-niobium powder: select in 2~8% more than a kind or 2 kinds
Solder flux of the present invention above-mentioned iron powder (atomized iron powder), B compound powder, and Mo powder, molybdenum-iron powder, Mo compound powder in the basis more than a kind or 2 kinds more than a kind or 2 kinds, in the Nb powder, ferro-niobium powder, Nb compound powder on, ideal situation is also to contain from SiO
2, CaCO
3, MgO, Al
2O
3, TiO
2, CaF
2And select in the metal powder beyond the atomized iron powder, Mo powder, molybdenum-iron powder, Nb powder, ferro-niobium powder more than a kind or 2 kinds.
SiO
2As slag former is active ingredient, for the viscosity of adjusting slag preferably contains it.SiO
2Contain quantity not sufficient 10%, the fusing point of the slag of generation is tending towards rising, on the other hand, it is low excessively that content one surpasses 28% fusing point, the welding bead outward appearance is disorderly easily, the oxygen amount of weld metal increases in addition, the toughness of weld metal is tending towards deterioration.Therefore, SiO
2Be preferably 10~28%.
CaCO
3In welding, decompose, become CaO and CO
2By this CO
2When gas isolates weld metal in the gas from the outside, reduce the hydrogen dividing potential drop in the welding atmosphere, play effective function in the weld metal for preventing that hydrogen from dissolving in.In addition, CaO is an alkaline components, has the fusing point that improves slag, improves the effect of the toughness of weld metal.
CaCO
3Content if less than 5%, can't see as described above by CO
2The protection effect that gas brings has the tendency of anti-hydrogen induced cracking reduction.On the other hand, its content one surpasses 15%, CO
2The generating capacity of gas increases, welding procedure, figuration of bead reduction.Therefore, CaCO
3Preferable range be 5~15%.
MgO has the effect that prevents the solder flux excess flow, has the effect of the weld bead shape in the stable large-line energy welding.Again, MgO is the basicity that increases slag, reduces the oxygen content in the weld metal, improves the useful component of the toughness of weld metal.The content of MgO is if less than 15% be can't see above-mentioned effect, and on the other hand, content one surpasses 38%, then has fusing point too to rise, the tendency of welding bead appearance degradation.Therefore, the preferable range of MgO is 15~38%.
Al
2O
3Owing to not reducing the fusing point that viscosity improves slag, so be the composition of effectively adjusting the slag fusing point.Al
2O
3Content if less than 3%, can't see above-mentioned effect, on the other hand, content one surpasses 20%, then the fusing point of slag too rises, and causes the inhomogeneous and appearance degradation of weld width.Therefore, Al
2O
3Preferable range be 3~20%.
TiO
2When improving the flowability of slag, improving the slag removability of slag, in the electric arc cavity,, carry out the transition in the weld metal as Ti by partial reduction, the toughness of improving weld metal is played useful effect.TiO
2Content if less than 2%, can't see above-mentioned effect, on the other hand, content one surpasses 10%, then demonstrates the tendency of welding bead appearance degradation.Therefore, TiO
2Preferable range be 2~10%.
CaF
2Do not improve fusing point, can increase the basicity of slag, effective to the oxygen amount of adjusting weld metal.CaF
2Content if less than 2%, this effect is little, on the other hand, its content one surpasses 10%, then the viscosity of slag too reduces, the welding bead outward appearance worsens.Therefore, CaF
2Preferable range be 2~10%.
Metal powder beyond atomized iron powder, Mo powder, molybdenum-iron powder, Nb powder and the ferro-niobium powder adds as deoxidier or alloying element source, but if its content is difficult to guarantee the toughness of weld metal, the tendency that has the welding bead outward appearance to worsen simultaneously less than 2%.On the other hand, its content one surpasses 8%, and then the oxygen quantitative change of weld metal is low, because weld structure becomes bainite or martensite is the tissue of main body, so the tendency that has weld metal toughness to descend.Therefore, the preferable range of the metal powder beyond atomized iron powder, Mo powder, molybdenum-iron powder, Nb powder and the ferro-niobium powder is 2~8%.As such metal powder ferromanganese, ferrosilicon, ferrotianium, manganese, titanium etc. are arranged.Secondly, metal powder can be the form beyond the powder, can be paper tinsel shape, needle-like.
Solder flux of the present invention is to fire after above-mentioned solder flux raw material is mixed together stirring, granulation by the ormal weight of above-mentioned scope batching and binding agent.Do not limit especially as prilling process, but use rotary type comminutor, extrusion formula comminutor etc. more suitable.Carry out the whole grain of gumming dirt, pulverizing big particle etc. after the granulation and handle, the desirable average grain diameter of particle is 0.075~5mm scope.
Again, as mixed liquor of the aqueous solution, sodium silicate aqueous solution, potassium silicate aqueous solution and the sodium silicate aqueous solution and the potassium silicate aqueous solution of binding agent preferably polyethylene alcohol etc. etc.Desirable content of binder is that every solder flux raw material total amount 1kg adds about 50~300cc.In addition, the low heat input submerged arc welding that solder flux of the present invention promptly is used in the not enough 150kJ/cm of heat input does not have any problem yet, can stablize the weld metal that obtains having excellent in toughness certainly.
Again, when using the solder flux of the invention described above, the welding wire of use does not need special qualification, and generally well-known welding wire for submerged-arc welding all can use.
Manufacture method about the large-line energy submerged-arc welding welding point of weld metal zone good-toughness is illustrated below.The manufacture method of large-line energy submerged-arc welding welding point of the present invention, use the poor steel of Ti, Nb as soldered material, when carrying out solder joints, effective especially to the weld metal that obtains high tenacity by the large-line energy submerged arc welding of heat input more than 150kJ/cm.
The steel that use as soldered material be have Ti content below the 0.006 quality %, Nb content below the 0.012 quality %, the steel formed of the desirable mother metal of N content below 0.0055 quality %.As other composition with contain C:0.07~0.18%, below the Si:0.40%, Mn:1.00~1.60%, below the P:0.020%, below the S:0.010%, perhaps also contain below the Al:0.050% and be advisable.Except that mentioned component, can contain V.Secondly, said steel are meant the steel that comprise steel plate, shaped steel, steel pipe, bar steel among the present invention.
After above-mentioned steel being implemented the groove processing of defined shape, in this groove, scatter solder flux, use above-mentioned large-line energy welding wire for hidden arc welding, by the large-line energy submerged-arc welding solder bond of heat input more than 150kJ/cm.
Submerged arc welding among the present invention does not need special qualification, and comprising the generally well-known welding method that multiple electrode submerged arc welding connects can both be suitable for.In addition, welding condition does not need special qualification yet.
Combination with such materials to be welded, welding material is made welding point (Welding Structure) by the large-line energy submerged-arc welding solder joints of heat input more than 150kJ/cm.The weld metal of the welding point that obtains (Welding Structure) is the weld metal of high tenacity.
(embodiment 1)
The 490MPa grade steel plate (thickness of slab: 25mm, 40mm) that mother metal shown in the his-and-hers watches 1 is formed is implemented the groove processing of shape shown in Figure 1A, Figure 1B, has made welding point by the submerged arc welding of 1 passage.Groove during thickness of slab 25mm is shaped as レ type groove, and bevel angle is 40 °, and root face is 2mm.Again, steel plate when being 40mm thick groove be shaped as Y type groove, bevel angle is 35 °, root face is 3mm.
The bipolar electrode submerged arc welding machine is used in submerged arc welding, and the welding wire of forming shown in the use table 3 under the welding condition shown in the table 2 carries out.Again, the solder flux that uses is the commercially available iron powder sintered flux of the boron oxide that contains 0.4 quality % of the composition shown in the table 4.Secondly, the iron powder that contains in the solder flux uses with the iron powder of sponge iron as raw material.Weld heat input is 153kJ/cm at thickness of slab during for 25mm, is 270kJ/cm at thickness of slab during for 40mm.
The welding point that obtains is like this prepared sample from Fig. 2 A of the central part of welding total length, the position shown in Fig. 2 B, investigate hot strength, the toughness of weld metal.Tension test is implemented according to the regulation of JIS Z3112 according to the regulation of JIS Z3111, impact test, and the summer when having obtained hot strength TS and 0 ℃ ,-20 ℃ is than absorbing merit value vE
0, vE
-20
It the results are shown in table 5.
Example of the present invention can both obtain having the vE of weld metal
0More than 27J and the welding point of the equal good toughness of the mean level of mother metal standard.In addition, the welding point (welding point No.3, No.4, No.5) that uses the welding wire contain Mo, Nb in the scope of the invention to obtain has the vE of weld metal
-20The good toughness that surpasses 27J.
On the other hand, exceed the comparative example (welding point No.6) of the scope of the invention, the vE of weld metal for the N content of welding wire
0Not enough 27J, the toughness deterioration.Again, hang down the comparative example (welding point No.7) of scope of the present invention for the Ti content of welding wire, organize thick, the vE of weld metal
0Not enough 27J, the toughness deterioration.Hang down the comparative example (welding point No.6, No.7, No.8) of scope of the present invention, the vE of weld metal for the Ti/N of welding wire again,
0Not enough 27J, the toughness deterioration.Again, exceed the comparative example (welding point No.9) of scope of the present invention for the Ti content of welding wire, tissue becomes the tissue that upper bainite is a main body, the vE of weld metal
0Not enough 27J, the toughness deterioration.Again, for the Mn content of welding wire hang down the comparative example (welding point No.10) of scope of the present invention, the Si content of welding wire exceeds the comparative example of the scope of the invention (welding point No.11), the ferrite alligatoring of weld metal, vE
0Not enough 27J, the toughness deterioration of weld metal.
Again, quality % ratio and the grain boundary ferrite growing amount of the composition of table 6 expression weld metal, the B/N in the weld metal.Grain boundary ferrite growing amount in the weld metal of example of the present invention all is below the 15 area %, can obtain the vE of weld metal
0Welding point more than 27J with excellent in toughness.Again, use contains the Mo in the scope of the invention, the welding wire of Nb, grain boundary ferrite growing amount in the weld metal of the B/N quality % ratio welding point (welding point No.3, No.4, No.5) within the scope of the invention in the weld metal is below the 10 area %, has the vE of weld metal
-20The good toughness that surpasses 27J.
(embodiment 2)
The groove that the 490MPa grade steel plate (thickness of slab t:40mm) that mother metal shown in the his-and-hers watches 7 is formed, building structure are implemented shape shown in Figure 3 with TMCP steel plate (thickness of slab t:60mm) is processed, and has made welding point by the submerged arc welding of 1 passage.Groove is shaped as the Y type, and bevel angle is 35 °, and root face d (mm) is 2mm when thickness of slab t:40mm, is 3mm when thickness of slab t:60mm.
The bipolar electrode submerged arc welding machine is used in submerged arc welding, and the welding wire that the welding wire under the welding condition shown in the table 8 shown in the use table 9 is formed carries out.Again, use the solder flux contain boron oxide and iron powder, solder flux is to make to resemble to prepare burden forming shown in the table 10 and sodium metasilicate burns till under the condition of 500 ℃ * 15min after being mixed together stirring, granulation, and particle diameter is below the 3mm.Add the iron powder of nitrogen content shown in the iron powder use table 11 in the solder flux to again.Weld heat input is 269kJ/cm at thickness of slab during for 40mm, is 549kJ/cm at thickness of slab during for 60mm.
Same to the welding point and the embodiment 1 that obtain like this, prepare sample from Fig. 2 A, the position shown in Fig. 2 B of the central part of welding total length, investigate hot strength, the toughness of weld metal.Again and embodiment 1 same, tension test is implemented according to the regulation of JIS Z3112 according to the regulation of JIS Z3111, impact test, the summer when having obtained hot strength TS and 0 ℃ ,-20 ℃ is than absorbing merit value vE
0, vE
-20
It the results are shown in table 12.
For the welding point of welding wire that has used example of the present invention and solder flux, the vE of weld metal
0Reach more than the 100J during at thickness of slab, reach more than the 47J vE of weld metal during for 60mm at thickness of slab for 40mm
-20Reach more than the 80J during at thickness of slab, reach more than the 50J during for 60mm, can obtain having the welding point of excellent in toughness at thickness of slab for 40mm.
Again, quality % ratio and the grain boundary ferrite growing amount of the composition of table 13 expression weld metal, the B/N in the weld metal.Use welding wire of the present invention and solder flux, grain boundary ferrite growing amount in the weld metal of the B/N quality % ratio welding point (welding point No.2-1, No.2-2, No.2-3, No.2-4, No.2-5) within the scope of the invention in the weld metal is below the 10 area %, can obtain having the weld metal of very good toughness.
(embodiment 3)
The groove that the 490MPa grade steel plate (thickness of slab t:40mm) that mother metal shown in the his-and-hers watches 7 is formed, building structure are implemented shape shown in Figure 3 with TMCP steel plate (thickness of slab t:60mm) is processed, and has made welding point by the submerged arc welding of 1 passage.Groove is shaped as the Y type, and bevel angle is 35 °, and root face d (mm) is 2mm when thickness of slab t:40mm, is 3mm when thickness of slab t:60mm.
The bipolar electrode submerged arc welding machine is used in submerged arc welding, and the solder flux of forming shown in the welding wire that the welding wire under the welding condition shown in the table 14 shown in the use table 15 is formed, the table 16 carries out.
Again, (addition: the about 200cc of every 1kg solder flux) burn till under the condition of 500 ℃ * 15min after being mixed together stirring, granulation, particle diameter is below the 3mm for the such preparation raw material of solder flux composition shown in table 16 and the sodium silicate aqueous solution.Again, the chemical composition in the table 16 adds up to less than 100 quality %, but remainder is sodium metasilicate solid state component and unavoidable impurities.Again, the iron powder that adds in the solder flux is an atomized iron powder, uses the atomized iron powder of the nitrogen content shown in the table 17.Weld heat input is 269kJ/cm at thickness of slab during for 40mm, is 521kJ/cm at thickness of slab during for 60mm.
The welding point that obtains is like this prepared sample from Fig. 2 A of the central part of welding total length, the position shown in Fig. 2 B, investigate hot strength, the toughness of weld metal.Tension test prepares sample from the position of Fig. 2 A, implements according to the regulation of JIS Z3111, has obtained hot strength TS, and impact test prepares sample from the position of Fig. 2 B, implements according to the regulation of JIS Z3112, and the summer when having obtained 0 ℃ is than absorbing merit value vE
0
It the results are shown in table 18.
Example of the present invention all satisfies the vE of weld metal
0More than 27J, can obtain having the welding point of excellent in toughness.The toughness of weld metal that departs from the comparative example of the scope of the invention reduces.
Again, quality % ratio and the grain boundary ferrite growing amount of the composition of table 19 expression weld metal, the B/N in the weld metal.Having used the grain boundary ferrite growing amount in the weld metal of solder flux of example of the present invention is below the 15.0 area %, can obtain having the weld metal of excellent in toughness.Grain boundary ferrite growing amount in the weld metal of the welding point (welding point No.3-5, No.3-9, No.3-10) within the scope of the invention of the B/N quality % in the weld metal is below the 10 area %, has better toughness.
According to the present invention, when adopting the poor steel of large-line energy submerged-arc welding welding Ti, the Nb etc. of weld heat input more than 150kJ/cm, also can stablize the weld metal that obtains having excellent in toughness, can significantly improve welding efficiency, the special result on the acquisition industry.
Table 1
Steel plate No |
Grade |
Thickness of slab mm |
Chemical composition (quality %) |
C |
Si |
Mn |
P |
S |
Ti |
Nb |
N |
Al |
V |
1 |
SN-490C |
25 |
0.14 |
0.35 |
1.48 |
0.015 |
0.003 |
0.005 |
0.003 |
0.0030 |
0.030 |
- |
2 |
SN-490C |
40 |
0.13 |
0.33 |
1.36 |
0.015 |
0.003 |
0.003 |
0.008 |
0.0040 |
0.021 |
0.030 |
Table 3
Welding wire No |
Chemical composition (quality %) |
Remarks |
C |
Si |
Mn |
P |
S |
Ti |
N |
Ti/N |
Mo |
Nb |
B |
Ni |
A |
0.06 |
0.05 |
1.80 |
0.009 |
0.005 |
0.100 |
0.0022 |
45 |
- |
- |
- |
- |
Example of the present invention |
B |
0.04 |
0.35 |
2.20 |
0.015 |
0.006 |
0.080 |
0.0032 |
25 |
- |
- |
- |
- |
Example of the present invention |
C |
0.05 |
0.30 |
1.50 |
0.010 |
0.005 |
0.030 |
0.0020 |
15 |
0.50 |
- |
- |
0.5 |
Example of the present invention |
D |
0.08 |
0.03 |
1.20 |
0.009 |
0.003 |
0.080 |
0.0024 |
33 |
0.20 |
- |
0.0010 |
- |
Example of the present invention |
E |
0.07 |
0.02 |
2.40 |
0.008 |
0.002 |
0.040 |
0.0025 |
16 |
- |
0.080 |
- |
- |
Example of the present invention |
F |
0.06 |
0.01 |
1.90 |
0.016 |
0.003 |
0.050 |
0.0040 |
13
|
- |
- |
- |
- |
Comparative example |
G |
0.06 |
0.30 |
1.80 |
0.016 |
0.003 |
0.020
|
0.0030 |
7
|
- |
- |
- |
- |
Comparative example |
H |
0.07 |
0.20 |
1.80 |
0.015 |
0.003 |
0.040 |
0.0030 |
13
|
- |
- |
- |
- |
Comparative example |
I |
0.07 |
0.20 |
1.80 |
0.015 |
0.003 |
0.22
|
0.0031 |
71
|
- |
- |
- |
- |
Comparative example |
J |
0.06 |
0.02 |
0.80
|
0.012 |
0.003 |
0.040 |
0.0024 |
17 |
- |
- |
- |
- |
Comparative example |
K |
0.08 |
0.50
|
1.90 |
0.010 |
0.004 |
0.040 |
0.0025 |
16 |
- |
- |
- |
- |
Comparative example |
Table 2
Welding condition No |
Welding condition |
Remarks |
The preceding utmost point |
The back utmost point |
Speed of welding cm/min |
Heat input kJ/cm |
Gage of wire mm |
Electric current A |
Voltage V |
Gage of wire mm |
Electric current A |
Voltage V |
a |
6.4 |
1600 |
34 |
6.4 |
1160 |
42 |
39 |
153 |
Thickness of slab 25mm |
b |
6.4 |
1800 |
35 |
6.4 |
1400 |
45 |
28 |
270 |
Thickness of slab 40mm |
Table 4
Solder flux No |
Chemical composition (quality %) |
SiO
2 |
MgO |
CaCO
2 |
Al
2O
3 |
TiO
2 |
CaF
3 |
B
2O
4 |
Iron powder |
Metal powder beyond the iron powder |
FL |
|
20 |
20 |
9 |
8 |
5 |
4 |
0.4 |
25 |
5 |
Table 5
Welding point No |
The welding combination |
Toughness |
Hot strength |
Remarks |
Steel No. |
Welding wire No. |
Solder flux No |
Welding condition |
vE
0 (J)
|
vE
-20 (J)
|
TS (MPa) |
1 |
1 |
A |
FL |
a |
45 |
27 |
589 |
Example of the present invention |
2 |
2 |
B |
FL |
b |
41 |
25 |
622 |
Example of the present invention |
3 |
2 |
C | FL |
b | |
120 |
74 |
623 |
Example of the present invention |
4 |
1 |
D |
FL |
a |
81 |
53 |
577 |
Example of the present invention |
5 |
1 |
E |
FL |
a |
59 |
38 |
644 |
Example of the present invention |
6 |
1 |
F
|
FL |
a |
25 |
16 |
589 |
Comparative example |
7 |
2 |
G
|
FL |
b |
23 |
11 |
586 |
Comparative example |
8 |
2 |
H
|
FL |
b |
24 |
12 |
604 |
Comparative example |
9 |
1 |
I
|
FL |
a |
26 |
16 |
640 |
Comparative example |
10 |
1 |
J
|
FL |
a |
22 |
11 |
478 |
Comparative example |
11 |
2 |
K
|
FL |
b |
24 |
17 |
608 |
Comparative example |
Table 6
Welding point No. |
C |
Si |
Mn |
Ti |
N |
Mo |
Nb |
Ni |
B |
B/N quality % ratio in the weld metal |
Grain boundary ferrite growing amount in the weld metal (area %) |
Remarks |
1 |
0.10 |
0.31 |
1.46 |
0.030 |
0.0031 |
- |
0.002 |
- |
0.0017 |
0.55 |
13.1 |
Example of the present invention |
2 |
0.09 |
0.42 |
1.56 |
0.024 |
0.0039 |
- |
0.003 |
- |
0.0020 |
0.51 |
11.4 |
Example of the present invention |
3 |
0.09 |
0.39 |
1.38 |
0.005 |
0.0031 |
0.20 |
0.003 |
0.19 |
0.0022 |
0.71 |
7.8 |
Example of the present invention |
4 |
0.11 |
0.33 |
1.33 |
0.025 |
0.0032 |
0.09 |
0.003 |
- |
0.0026 |
0.81 |
8.2 |
Example of the present invention |
5 |
0.10 |
0.30 |
1.77 |
0.013 |
0.0030 |
- |
0.034 |
- |
0.0018 |
0.60 |
9.6 |
Example of the present invention |
6 |
0.10 |
0.28 |
1.52 |
0.010 |
0.0040 |
- |
0.002 |
- |
0.0016 |
0.40 |
18.7 |
Comparative example |
7 |
0.10 |
0.40 |
1.44 |
0.004 |
0.0036 |
- |
0.002 |
- |
0.0017 |
0.47 |
17.5 |
Comparative example |
8 |
0.11 |
0.35 |
1.39 |
0.008 |
0.0039 |
- |
0.004 |
- |
0.0019 |
0.49 |
16.8 |
Comparative example |
9 |
0.11 |
0.36 |
1.46 |
0.071 |
0.0033 |
- |
0.002 |
- |
0.0017 |
0.52 |
15.2 |
Comparative example |
10 |
0.10 |
0.30 |
1.06 |
0.011 |
0.0033 |
- |
0.002 |
- |
0.0017 |
0.52 |
23.1 |
Comparative example |
11 |
0.10 |
0.52 |
1.47 |
0.007 |
0.0034 |
- |
0.003 |
- |
0.0018 |
0.53 |
28.3 |
Comparative example |
Table 7
Steel plate No |
Grade |
Thickness of slab mm |
Chemical composition (quality %) |
C |
Si |
Mn |
P |
S |
Ti |
Nb |
N |
Al |
V |
3 |
SN-490C |
40 |
0.13 |
0.33 |
1.36 |
0.015 |
0.003 |
0.003 |
0.008 |
0.0040 |
0.021 |
0.030 |
4 |
The TMCP steel |
60 |
0.13 |
0.26 |
1.45 |
0.011 |
0.002 |
0.006 |
0.010 |
0.0032 |
0.026 |
0.002 |
Table 8
Welding condition No |
Welding condition |
Remarks |
The preceding utmost point |
The back utmost point |
Speed of welding cm/min |
Heat input kJ/cm |
Gage of wire mm |
Electric current A |
Voltage V |
Gage of wire mm |
Electric current A |
Voltage V |
c |
6.4 |
1800 |
34 |
6.4 |
1400 |
46 |
28 |
269 |
Thickness of slab 40mm |
d |
6.4 |
2300 |
38 |
6.4 |
1800 |
48 |
19 |
549 |
Thickness of slab 60mm |
Table 10
Solder flux No |
Chemical composition (quality %) |
SiO
2 |
MgO |
CaCO
3 |
Al
2O
3 |
TiO
2 |
CaF
2 |
B
2O
3 |
Iron powder * |
Metal powder beyond the iron powder |
FL-2 |
21 |
25 |
10 |
8 |
6 |
4 |
0.3 |
β:20 |
5 |
FL-3 |
19 |
21 |
10 |
7 |
6 |
4 |
0.4 |
α:23 |
5 |
FL-4 |
19 |
21 |
10 |
7 |
6 |
4 |
0.4 |
β:23 |
5 |
FL-5 |
19 |
21 |
10 |
7 |
6 |
4 |
0.4 |
γ:23 |
5 |
FL-6 |
11 |
16 |
6 |
4 |
3 |
3 |
0.6 |
β:47 |
6 |
FL-7 |
20 |
16 |
9 |
17 |
7 |
6 |
0.3 |
β:16 |
3 |
*) with reference to table 11
Table 11
Iron powder No. |
N content (quality %) |
α |
0.0020 |
β |
0.0028 |
γ |
0.0045 |
Table 9
Welding wire |
Chemical composition (quality %) |
Remarks |
No |
C |
Si |
Mn |
P |
S |
Ti |
N |
Ti/N |
Mo |
Nb |
B |
Ni |
L |
0.05 |
0.33 |
2.08 |
0.012 |
0.005 |
0.079 |
0.0032 |
25 |
- |
- |
- |
- |
Example of the present invention |
Table 13
Welding point No. |
C |
Si |
Mn |
Ti |
N |
Mo |
Nb |
Ni |
B |
B/N quality % ratio in the weld metal |
Grain boundary ferrite growing amount in the weld metal (area %) |
Remarks |
2-1 |
0.09 |
0.46 |
1.44 |
0.018 |
0.0023 |
0.25 |
0.004 |
- |
0.0018 |
0.78 |
1.2 |
Example of the present invention |
2-2 |
0.09 |
0.45 |
1.48 |
0.020 |
0.0024 |
0.26 |
0.004 |
- |
0.0025 |
1.04 |
7.9 |
Example of the present invention |
2-3 |
0.10 |
0.39 |
1.53 |
0.021 |
0.0031 |
0.12 |
0.005 |
- |
0.0020 |
0.65 |
9.0 |
Example of the present invention |
2-4 |
0.09 |
0.38 |
1.51 |
0.023 |
0.0036 |
- |
0.011 |
- |
0.0022 |
0.61 |
9.5 |
Example of the present invention |
2-5 |
0.10 |
0.41 |
1.50 |
0.021 |
0.0045 |
- |
0.005 |
0.05 |
0.0027 |
0.60 |
9.9 |
Example of the present invention |
2-6 |
0.09 |
0.48 |
1.47 |
0.019 |
0.0029 |
- |
0.004 |
- |
0.0015 |
0.52 |
14.7 |
Example of the present invention |
Table 12
Welding point No |
The welding combination |
Toughness |
Hot strength |
Remarks |
Steel No. |
Welding wire No. |
Solder flux No |
Welding condition |
vE
0 (J)
|
vE
-20 (J)
|
TS (MPa) |
2-1 |
3 |
L |
FL-2 |
c |
120 |
82 |
624 |
Example of the present invention |
2-2 |
3 |
L |
FL-3 |
c |
102 |
80 |
614 |
Example of the present invention |
2-3 |
4 |
L |
FL-4 |
d |
81 |
54 |
619 |
Example of the present invention |
2-4 |
4 |
L |
FL-5 |
d |
68 |
50 |
609 |
Example of the present invention |
2-5 |
4 |
L |
FL-6 |
d |
51 |
30 |
599 |
Example of the present invention |
2-6 |
3 |
L |
FL-7 |
c |
49 |
28 |
526 |
Example of the present invention |
Table 14
Welding condition No |
Welding condition |
Remarks |
The preceding utmost point |
The back utmost point |
Speed of welding cm/min |
Heat input kJ/cm |
Gage of wire mm |
Electric current A |
Voltage V |
Gage of wire mm |
Electric current A |
Voltage V |
e |
6.4 |
1800 |
34 |
6.4 |
1400 |
46 |
28 |
269 |
Thickness of slab 40mm |
f |
6.4 |
2300 |
38 |
6.4 |
1800 |
48 |
20 |
521 |
Thickness of slab 60mm |
[table 15] table 15
Welding wire No |
Chemical composition (quality %) |
C |
Si |
Mn |
P |
Ti |
N |
Nb |
M |
0.04 |
0.35 |
2.11 |
0.004 |
- |
0.0040 |
- |
Table 16
Solder flux No |
Chemical composition (quality %) |
Remarks |
SiO
2 |
MgO |
CaCO
3 |
Al
2O
3 |
TiO
2 |
CaF
2 |
Iron powder kind: content |
Metal powder kind beyond the iron powder: content |
B
***Kind: content
|
Mo
*Kind: content
|
Nb
*Kind: content
|
F1 |
22 |
25 |
10 |
8 |
6 |
4 |
B:13 |
Ferrosilicon: 5 |
B
2O
3:0.03
|
- |
- |
Comparative example |
F2 |
20 |
23 |
10 |
7 |
6 |
4 |
A:20 |
Ferrosilicon: 5 |
B
2O
3:0.05
|
- |
- |
Example of the present invention |
F3 |
20 |
23 |
10 |
7 |
6 |
4 |
B:20 |
Ferromanganese: 5 |
B
2O
3:0.05
|
- |
- |
Example of the present invention |
F4 |
20 |
23 |
10 |
7 |
6 |
4 |
C:20
|
Ferromanganese: 5 |
B
2O
3:0.05
|
- |
- |
Comparative example |
F5 |
15 |
20 |
9 |
4 |
10 |
4 |
B:30 |
Ferrosilicon: 3 |
B
2O
3:0.08
|
Mo powder: 1.0 |
Fe-Nb:0.1 |
Example of the present invention |
F6 |
15 |
20 |
9 |
6 |
5 |
4 |
B:30 |
Ferrosilicon: 3 |
- |
Mo powder: 1.5 |
- |
Example of the present invention |
F7 |
15 |
20 |
9 |
6 |
5 |
4 |
B:30 |
Ferrosilicon: 3 |
B
2O
3:0.11
|
- |
- |
Example of the present invention |
F8 |
15 |
20 |
9 |
6 |
5 |
4 |
B:30 |
Manganese: 3 |
B
2O
3:0.06
|
Fe-Mo:0.6 |
Fe-Nb:0.1 |
Example of the present invention |
F9 |
12 |
17 |
8 |
5 |
4 |
3 |
A:40 |
Ferromanganese: 3 |
B
2O
3:0.06
|
Fe-Mo:0.6 |
Fe-Nb:0.05 |
Example of the present invention |
F10 |
12 |
17 |
8 |
5 |
4 |
3 |
B:40 |
Ferromanganese: 3 |
B
2O
3:0.06
|
Fe-Mo:0.6 |
Nb powder: 0.05 |
Example of the present invention |
F11 |
12 |
17 |
8 |
5 |
4 |
3 |
C:40
|
Manganese: 3 |
B
2O
3:0.06
|
Fe-Mo:0.6 |
Nb powder: 0.05 |
Comparative example |
F12 |
11 |
16 |
6 |
4 |
3 |
3 |
B:
47 |
Ferromanganese: 3 |
B
2O
3:0.06
|
- |
- |
Comparative example |
F13 |
14 |
20 |
12 |
5 |
9 |
3 |
A:25 |
Ferrosilicon: 4 |
- |
Fe-Mo:1.5 |
- |
Example of the present invention |
F14 |
14 |
20 |
12 |
5 |
9 |
3 |
A:25 |
Ferrosilicon: 4 |
- |
- |
Fe-Nb:0.12 |
Example of the present invention |
*) content that converts with each element
*) B
2O
3Be to contain B
2O
3Glassy compound
Table 17
Atomized iron powder No. |
N content (quality %) |
A |
0.0019 |
B |
0.0027 |
C |
0.0040 |
Table 18
Welding point No |
Rong Jie Group closes sweet |
Toughness |
Hot strength |
The welding bead outward appearance |
Remarks |
Steel No. |
Welding wire No. |
Solder flux No |
Welding condition |
vE
0 (J)
|
TS (MPa) |
3-1 |
3 |
M |
F1
|
e | |
25 |
598 |
Fuse bad |
Comparative example |
3-2 |
F2 |
51 |
603 |
Well |
Example of the present invention |
3-3 |
F3 |
36 |
607 |
Well |
Example of the present invention |
3-4 |
F4
|
22 |
542 |
Well |
Comparative example |
3-5 |
3 |
M |
F5 |
e |
63 |
571 |
Well |
Example of the present invention |
3-6 |
3 |
M |
F6 |
e |
28 |
566 |
Well |
Example of the present invention |
3-7 |
3 |
M |
F7 |
e |
27 |
502 |
Well |
Example of the present invention |
3-8 |
3 |
M |
F8 |
e |
48 |
609 |
Well |
Example of the present invention |
3-9 |
4 |
M |
F9 |
f |
72 |
624 |
Well |
Example of the present invention |
3-10 |
F10 |
f |
48 |
620 |
Well |
Example of the present invention |
3-11 |
F11
| f | |
25 |
585 |
Well |
Comparative example |
3-12 |
F12
|
f |
19 |
538 |
The welding bead outward appearance is bad |
Comparative example |
3-13 |
F13 |
f |
29 |
596 |
Well |
Example of the present invention |
3-14 |
F14 |
f |
28 |
666 |
Well |
Example of the present invention |
Table 19
Welding point No. |
C |
Si |
Mn |
Ti |
N |
Mo |
Nb |
Ni |
B |
B/N quality % ratio in the weld metal |
Grain boundary ferrite growing amount in the weld metal (area %) |
Remarks |
3-1 |
0.09 |
0.47 |
1.29 |
0.004 |
0.0022 |
- |
0.004 |
- |
0.0009 |
0.41 |
16.3 |
Comparative example |
3-2 |
0.09 |
0.49 |
1.31 |
0.004 |
0.0022 |
- |
0.003 |
- |
0.0012 |
0.55 |
10.0 |
Example of the present invention |
3-3 |
0.10 |
0.30 |
1.56 |
0.005 |
0.0023 |
- |
0.004 |
- |
0.0012 |
0.52 |
12.7 |
Example of the present invention |
3-4 |
0.09 |
0.31 |
1.62 |
0.004 |
0.0031 |
- |
0.004 |
- |
0.0014 |
0.45 |
17.2 |
Comparative example |
3-5 |
0.09 |
0.39 |
1.32 |
0.004 |
0.0031 |
0.28 |
0.019 |
- |
0.0019 |
0.61 |
9.2 |
Example of the present invention |
3-6 |
0.10 |
0.41 |
1.32 |
0.004 |
0.0033 |
0.48 |
0.003 |
- |
- |
- |
14.5 |
Example of the present invention |
3-7 |
0.09 |
0.40 |
1.33 |
0.005 |
0.0029 |
- |
0.004 |
- |
0.0034 |
1.17 |
14.7 |
Example of the present invention |
3-8 |
0.09 |
0.32 |
1.77 |
0.004 |
0.0030 |
0.19 |
0.018 |
- |
0.0017 |
0.57 |
10.4 |
Example of the present invention |
3-9 |
0.09 |
0.30 |
1.57 |
0.005 |
0.0029 |
0.20 |
0.011 |
- |
0.0018 |
0.62 |
9.5 |
Example of the present invention |
3-10 |
0.10 |
0.31 |
1.64 |
0.006 |
0.0035 |
0.18 |
0.012 |
- |
0.0021 |
0.60 |
9.1 |
Example of the present invention |
3-11 |
0.10 |
0.29 |
1.76 |
0.005 |
0.0046 |
0.17 |
0.011 |
- |
0.0020 |
0.43 |
26.8 |
Comparative example |
3-12 |
0.09 |
0.31 |
1.59 |
0.005 |
0.0042 |
- |
0.006 |
- |
0.0019 |
0.45 |
25.0 |
Comparative example |
3-13 |
0.09 |
0.44 |
1.34 |
0.006 |
0.0026 |
0.49 |
0.005 |
- |
- |
- |
13.4 |
Example of the present invention |
3-14 |
0.10 |
0.43 |
1.30 |
0.005 |
0.0027 |
- |
0.020 |
- |
- |
- |
14.2 |
Example of the present invention |