CN103223562A - Solder for single-surface submerged-arc welding - Google Patents
Solder for single-surface submerged-arc welding Download PDFInfo
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- CN103223562A CN103223562A CN2012105518639A CN201210551863A CN103223562A CN 103223562 A CN103223562 A CN 103223562A CN 2012105518639 A CN2012105518639 A CN 2012105518639A CN 201210551863 A CN201210551863 A CN 201210551863A CN 103223562 A CN103223562 A CN 103223562A
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Abstract
The invention provides a solder for single-surface submerged-arc welding for obtaining right surface welding channel shape and mechanical property. The product comprises the following components by mass: 10-30% of SiO2, 3-9% of CaO, 15-35% of MgO, 4-20% of TiO2, 2-9% of CaF2, 5-20% of Al2O3, 2-9% of Co2, 1-3% of Na2O, 0.1-1% of B2O3, 0.2-1% of Mo, 10-30% of Fe powder, less than 2% of Si, less than 1.5% of Mn, less than 1% of Ti and less than 3% of Al. 0.7-3% of Al is added into the product.
Description
Technical field
The employed solder flux of single face submerged-arc welding that the present invention relates to use one or more electrode to carry out.In more detail, relate to contain the welding bead outward appearance improvement technology of the single face used for submerged arc welding solder flux of iron powder.
Background technology
In single face submerged-arc welding, usually,, realize still that in the large-line energy welding stable welding bead forms, and is added with the solder flux of iron powder (for example, with reference to patent documentation 1 and use in order to ensure deposited amount.)。But the patent documentation 1 described this existing single face used for submerged arc welding solder flux that contains iron powder has on the surface of cap bead the small such problem of abrasive grit thrust takes place easily.The thrust on such cap bead surface becomes obstacle in coating process, therefore for example in the shipbuilding field, for the new coating standard of corresponding construction process, remove the abrasive grit thrust, has to relate to welding bead and polishes processing completely.
Therefore, in single face used for submerged arc welding solder flux, proposed to be useful on the technology of the generation that suppresses the abrasive grit thrust (with reference to patent documentation 2,3 in the past.)。For example, in patent documentation 2 described single face used for submerged arc welding solder flux, be in specific scope, realize soundization of welding bead by making particle diameter and apparent density.In addition, in patent documentation 3 described used for submerged arc welding bonded fluxes, in order to suppress the generation of abrasive grit projection, the content of Fe composition is limited in below the 5 quality %.
[look-ahead technique document]
[patent documentation]
[patent documentation 1] spy opens flat 11-267883 communique
[patent documentation 2] spy opens flat 6-277878 communique
[patent documentation 3] spy opens the 2006-272348 communique
But, as patent documentation 2 described technology, just limiting the particle diameter and the apparent density of solder flux, the effect that suppresses for the generation of abrasive grit projection is little.In addition, as patent documentation 3 described used for submerged arc welding bonded fluxes, if restriction Fe content then is difficult to guarantee sufficient deposited amount in the jigsaw butt welding of slab, weld bead shape deterioration in this external large-line energy welding.So, existing welding bead outward appearance is improved technology in single face submerged-arc welding, keeps the effect that iron powder adds solder flux to Yi Bian also can't reach, Yi Bian suppress the generation of abrasive grit projection, and make soundization of welding bead outward appearance.
Summary of the invention
Therefore, main purpose of the present invention is, a kind of single face used for submerged arc welding solder flux that can access the performance of sound cap bead shape and machinery is provided.
Present inventors are in order to solve aforesaid problem, in the single face submerged-arc welding of the electrode that has used one or more, carried out experimental study with keen determination in order to ensure the viability of cap bead, it found that, in the suppressing of abrasive grit projection, it is effective to add metal A l at solder flux, thereby has finished the present invention.
That is, single face used for submerged arc welding solder flux of the present invention has following composition: contain SiO
2: 10～30 quality %, CaO:3～9 quality %, MgO:15～35 quality %, TiO
2: 4～20 quality %, CaF
2: 2～9 quality %, Al
2O
3: 14～20 quality %, CO
2: 2～9 quality %, Na
2O:1～3 quality %, B
2O
3: 0.1～1 quality %, Mo:0.2～1 quality %, Al:0.7～3 quality %, iron powder: 10～30 quality %, and below the restriction Si:2 quality %, below the Mn:1.5 quality %, below the Ti:1 quality %.
In single face used for submerged arc welding solder flux of the present invention, because blending has iron powder, so the excellent in stability of the weld bead shape of large-line energy welding.In addition, because contain the Al of specified quantitative,, in single face submerged-arc welding, can access the sound cap bead that does not have the abrasive grit projection so be difficult to adhere to abrasive grit on the cap bead.
This single face used for submerged arc welding solder flux also can contain Si:0.5～2 quality % and/or Ti:0.3～1 quality %.
In addition, also can contain Mn is 0.5～1.5 quality %.
According to the present invention, because the composition of specific solder flux and content thereof, so in having used single electrode or multielectrode single face submerged-arc welding, no matter liner is constructed, the performance of weld bead shape that can both obtain perfecting and machinery.
Description of drawings
Fig. 1 is the imaginary drawing of abrasive grit generation movement in the single face submerged arc welding process.
Fig. 2 is the profile of the groove shape of the steel plate that uses in the embodiments of the invention of expression.
Symbol description
1,10 mother metals
2 weld metals
2a welding bead surface
3 solder flux that do not dissolve
4 solder flux (slag) in dissolving/solidifying
5 iron powders
The aggegation of 6 iron powders
7 aggegation iron powders (abrasive grit)
The specific embodiment
Below, be elaborated for being used to implement mode of the present invention.Also have, the present invention is not defined as the embodiment of following explanation.
Fig. 1 is the imaginary drawing of the abrasive grit generation movement of single face submerged arc welding process.As shown in Figure 1, suppose in single face submerged-arc welding, when use contains the solder flux 3 of existing iron powder 5, in the solder flux (slag) 4 of fusion/in solidifying, iron powder 5 aggegations (aggegation 6 of iron powder) are arranged, these aggegation iron powder (abrasive grit) 7 depositions, attached to the surface (welding bead surface 2a) of the weld metal 2 of the weld part that is formed at mother metal 1, small thrust takes place.Therefore, present inventors determine to improve the characteristic of solder flux, thereby solve the problem that the abrasive grit projection takes place.
Specifically, the solder flux of embodiments of the present invention is used for single face submerged-arc welding, and specified quantitative contains SiO at least
2, CaO, MgO, TiO
2, CaF
2, Al
2O
3, CO
2, Na
2O, B
2O
3And Mo, and contain the Al of iron powder 10～30 quality % and 0.7～3 quality %.In addition, in the solder flux of present embodiment, respectively Si content is limited in below the 2 quality %, Mn content is limited in below the 1.5 quality %, and Ti content is limited in below the 1 quality %.Below, limit reason for the composition of the solder flux of present embodiment and describe.
[SiO
2: 10～30 quality %]
SiO
2Be the vitrifying composition, but if its content surpasses 30 quality %, then the viscosity of liquid slag integral body increases, the flowability of slag reduces.And under the situation of high speed single face submerged-arc welding, the cap bead width can't be expanded, and becomes unstable, and therefore undercut takes place easily.On the other hand, SiO
2When content was lower than 10 quality %, the setting temperature of liquid slag became too high, therefore can not get the surface of good weld bead shape.Therefore, SiO
2Content is 10～30 quality %.
[CaO:3～9 quality %]
CaO has the viscosity that makes liquid slag to be reduced, and improves the flowability of slag, the effect of extended surface weld width.But if CaO content surpasses 9 quality %, then the setting temperature of liquid slag becomes too high, and the cap bead shape is impaired.On the other hand, when CaO content is lower than 3 quality % and less than the effect of the flowability that improves liquid slag, therefore undercut takes place in cap bead width deficiency easily.Therefore, CaO content is 3～9 quality %.
[MgO:15～35 quality %]
MgO and aforesaid CaO are same, have the viscosity that makes liquid slag and reduce, and improve the flowability of slag, the effect of extended surface weld width.But, when the content of MgO is lower than 15 quality %, can not get improving the effect of the flowability of liquid slag, cap bead width deficiency, undercut takes place easily.On the other hand, because MgO is dystectic composition,, particularly during the high speed single face submerged-arc welding of the thin plate under being in little heat input, can not guarantee stable welding bead so if add and surpass 35 quality %, then the meltbility of solder flux integral body is impaired.Therefore, MgO content is 15～35 quality %.
[TiO
2: 4～20 quality %]
TiO
2For improving single fillet welded slag fissility is effective especially composition.But if its content surpasses 20 quality %, the then ripple chap of cap bead in addition, when being lower than 4 quality %, can not get the effect of improving of aforesaid slag fissility.Therefore, TiO
2Content is 4～20 quality %.
[CaF
2: 2～9 quality %]
CaF
2Being the good composition of meltbility that makes solder flux integral body, especially must making solder melts at short notice as single face submerged-arc welding and generate in the welding method of slag, is indispensable composition.But, if CaF
2Content surpasses 9 quality %, and current interruption takes place the arc stability deterioration easily.On the other hand, CaF
2When content was lower than 2 quality %, the meltbility that can not get solder flux was improved effect, and the welding bead that crawls takes place.Therefore, CaF
2Content is 2～9 quality %.
[Al
2O
3: 14～20 quality %]
Al
2O
3Being neutral compound, is the effective composition of adjustment for the viscosity and the setting temperature of slag.But, Al
2O
3When content was lower than 14 quality %, the viscosity of slag and setting temperature reduced, and weld width is inconsistent.On the other hand, if add Al
2O
3Surpass 20 quality %, then the setting temperature of slag becomes too high, and welding bead is difficult to launch, and weld bead shape becomes convex.Therefore, Al
2O
3Content is 14～20 quality %.
[CO
2: 2～9 quality %]
CO
2Be for suppressing intrusion and the reduction diffusivity hydrogen amount effective composition of nitrogen, adding in the solder flux as metal carbonate to weld metal.But, CO
2When content is lower than 2 quality %, the diffusivity hydrogen quantitative change height in the weld metal, low temperature resistant crackle deterioration.On the other hand, if CO
2Content surpasses 9 quality %, and the gas generating capacity is excessive, at cap bead generation pitted skin.Therefore, CO
2Content is 2～9 quality %.
[Na
2O:1～3 quality %]
Na
2O is used to guarantee the arc stability desirable ingredients.Specifically, Na
2When O content was lower than 1 quality %, electric arc was extremely unstable, and current interruption takes place, and weld bead shape and fusion penetration are inhomogeneous.On the other hand, if Na
2O content surpasses 3 quality %, and then anti-hygroscopicity reduces, low temperature resistant crackle deterioration.
[B
2O
3: 0.1～1 quality %]
B
2O
3In welding, be reduced, in weld metal, exist, for guaranteeing that toughness plays a role effectively as B.But, B
2O
3When content was lower than 0.1 quality %, its effect was not in full use, the toughness deterioration.On the other hand, if B
2O
3Content surpasses 1 quality %, and then intensity is excessive, and heat cracking takes place.Therefore, B
2O
3Content is 0.1～1 quality %.
[Mo:0.2～1 quality %]
Mo improves effective composition to hardenability, except that the Mo monomer, also adds with the form of Fe-Mo etc.But, when Mo content is lower than 0.2 quality %, weld metal organize thickization, toughness deterioration.On the other hand, surpass 1 quality % if add Mo, then the intensity of weld metal is excessive, and heat cracking takes place.
[Al:0.7～3 quality %]
Deoxidation when Al is generally considered to be for welding and the miniaturization effective elements of austenite particle diameter, but present inventors further play a role Al, are conceived to the heating functioin that brings with the anti-ying of the aluminothermy of oxide.Specifically, utilize the heating functioin add the Al in the solder flux to exactly, the solder flux (slag) of heating fusion when welding and reaching a high temperature, thus convection current is produced, allow abrasive grit be difficult to attached on the cap bead.In order to obtain this effect, need to add the above Al of 0.7 quality %.On the other hand, surpass 3 quality %, then form top bainite structure, the toughness deterioration of weld metal in weld metal portion if the Al surplus is contained.Also have, Al can also add with the form of Fe-Al and Al-Mg etc. except the Al monomer.
[iron powder: 10～30 quality %]
Iron powder is necessary adding ingredient in the single face submerged-arc welding that once needs a large amount of deposited metals.So, when iron content is lower than 10 quality %, can not get replenishing the effect of deposited metal amount, and the apparent density of solder flux diminishes, therefore anti-blowing afloat property deterioration.On the other hand, if iron powder is contained surpass 30 quality %, then in the solder flux of fusion/in solidifying, the easy aggegation of iron powder, the quantitative change of aggegation iron powder deposition is many, and abrasive grit is easily attached to the welding bead surface.And the apparent density of solder flux uprises, and can not guarantee weld width.Therefore, the content of iron powder is 10～30 quality %.
[Si:2 quality % is following]
Surpass 2 quality % if contain Si, then the easy sintering of slag is on the welding bead surface, the fissility deterioration of slag, so Si content is limited in below the 2 quality %.On the other hand, Si also is for the effective composition of oxygen amount that reduces in the weld metal, therefore if Si is contained more than the 0.5 quality %, then also can show deoxidation effect, tough property improvement.Therefore, in the solder flux of present embodiment, as required, add Si in the scope of 0.5～2 quality %.Also have, Si also can add with the form of Fe-Si etc. except the Si monomer.
[Ti:1 quality % is following]
Ti and aforesaid Si are same, are for the effective composition of oxygen amount that reduces in the weld metal, but interpolation that this effect can be by Si etc. and fully reaching, therefore in the solder flux of present embodiment, Ti is composition not necessarily.In addition, if Ti content surpasses 1 quality %, then the slag sintering is on the welding bead surface, slag fissility deterioration.Therefore, Ti content is limited in below the 1 quality %.On the other hand, if Ti contains more than the 0.3 quality %, then the deoxidation effect of weld metal is further realized, can realize the raising of toughness.Therefore, in the solder flux of present embodiment, as required, add Ti in the scope of 0.3～1 quality %.Also have, Ti can also add with the form of Fe-Ti etc. except adding with the Ti monomer form.
[Mn:1.5 quality % is following]
Mn and aforesaid Mo are same, have the effect that the hardenability of making improves, and are for the effective composition of the raising of intensity and toughness, but if Mn content surpasses 1.5 quality %, and then the slag sintering is on the welding bead surface, slag fissility deterioration.In addition, in the solder flux of present embodiment,, obtain the effect of hardenability thus, Mn content is limited in below the 1.5 quality % in order to add Mo.On the other hand, if Mn contains more than the 0.5 quality %, then hardenability further improves realization, tough property improvement.Therefore, in the solder flux of present embodiment, as required, add Mn in the scope of 0.5～1.5 quality %.Also have, Mn can also add with the form of Fe-Mn etc. except the Mn monomer.
[other composition]
The above-mentioned composition in addition of the solder flux of present embodiment for example has FeO, ZrO
2, K
2O etc.
As described in detail above, the solder flux of present embodiment makes iron content be in specific scope, and adds the Al of specified quantitative, therefore can resist the aggegation of the iron powder in the solder flux of inhibition fusion/in solidifying and abrasive grit the adhering to cap bead of generation.Consequently, in single face submerged-arc welding, can form the excellent performance of machinery, not have the sound cap bead of abrasive grit projection.
Also have, the solder flux of present embodiment, mainly in single face submerged-arc welding method, use, but about its pad approach, be not particularly limited, with solder flux and copper be the flux copper-gasket method of liner material, only with the solder flux be the liner material solder flux liner method, use any one methods such as liner method of solid shape solder flux to be suitable for.In addition,, also be not particularly limited, can directly use existing solder flux about the liner solder flux.
[embodiment]
Below, enumerate embodiments of the invention and comparative example, specifically be illustrated for effect of the present invention.In the present embodiment, use the welding wire shown in steel plate shown in the following table 1 and the table 2,, implement single face submerged-arc welding, estimate the performance of each solder flux of embodiment and comparative example according to the groove shape of welding condition shown in the following table 3 and steel plate (mother metal 10) shown in Figure 2.Also have, the surplus that the welding wire shown in steel plate composition shown in the following table 1 and the following table 2 is formed is Fe and unavoidable impurities.
[table 1]
[table 2]
[table 3]
The evaluation of each solder flux of embodiment and comparative example is by welding operation (welding bead outward appearance, undercut etc.), carry out according to the ultrasonic examination (UT) of JISZ3060 test (flawless, slag inclusion etc. are arranged) with according to the pendulum impact test of JISZ2242.In addition, pendulum impact test, the pendulum under test temperature-20 ℃ absorb can (vE-20 ℃) more than 50J, be qualified, what be lower than 50J is defective.Each solder flux composition of these evaluation results and embodiment and comparative example is presented in following table 4 and the table 5.
[table 4]
[table 5]
As shown in table 4, the solder flux of the embodiment 1～31 of Zhi Zuoing within the scope of the invention, welding operation, ultrasonic examination (UT) test and toughness (vE-20 ℃) are all not well.
With respect to this, as shown in table 5, the solder flux of comparative example 1 because the content of the MgO in the solder flux, is lower than the lower limit of the scope of the invention, so undercut takes place.On the other hand, the solder flux of comparative example 2 is because the content of MgO surpasses the upper limit of the scope of the invention, so overlap takes place.The solder flux of comparative example 3 takes place so reinforcement is not enough because Fe content is lower than the lower limit of the scope of the invention.The solder flux of comparative example 4 is because Fe content surpasses the upper limit of the scope of the invention, so abrasive grit takes place on the welding bead surface.
The solder flux of comparative example 5 is because SiO
2Content is lower than the lower limit of the scope of the invention, so overlap takes place.On the other hand, the solder flux of comparative example 6 is because SiO
2Content surpasses the upper limit of the scope of the invention, so undercut takes place.In addition, the solder flux of comparative example 7 is because Al
2O
3Content is lower than the lower limit of the scope of the invention, so weld width is inconsistent.On the other hand, the solder flux of comparative example 8 is because Al
2O
3Content surpasses the upper limit of the scope of the invention, so welding bead becomes convex.
The solder flux of comparative example 9 is because TiO
2Content is lower than the lower limit of the scope of the invention, so slag fissility deterioration.On the other hand, the solder flux of comparative example 10 is because TiO
2Content surpasses the upper limit of the scope of the invention, so the ripple chap of welding bead.In addition, the solder flux of comparative example 11 is because CaO content is lower than the lower limit of the scope of the invention, so undercut takes place.On the other hand, the solder flux of comparative example 12 is because CaO content surpasses the upper limit of the scope of the invention, so welding bead becomes convex.
The solder flux of comparative example 13 is because CO
2Content is lower than the lower limit of the scope of the invention, so the diffusivity hydrogen quantitative change height in the weld metal, the low temperature crackle takes place.On the other hand, the solder flux of comparative example 14 is because CO
2Content surpasses the upper limit of the scope of the invention, so on the welding bead surface pitted skin takes place.In addition, the solder flux of comparative example 15 is because CaF
2Content is lower than the lower limit of the scope of the invention, so the welding bead that crawls takes place.On the other hand, the solder flux of comparative example 16 is because CaF
2Content surpasses the upper limit of the scope of the invention, so current interruption takes place frequently.
The solder flux of comparative example 17 is because Na
2O content is lower than the lower limit of the scope of the invention, so the welding bead that crawls takes place.On the other hand, the solder flux of comparative example 18 is because Na
2O content surpasses the upper limit of the scope of the invention, so the low temperature crackle takes place.In addition, the solder flux of comparative example 19 is because Si content surpasses the upper limit of the scope of the invention, so the toughness deterioration takes place the slag sintering.In addition, the solder flux of comparative example 20 is because Mn content surpasses the upper limit of the scope of the invention, so slag fissility deterioration.In addition, the solder flux of comparative example 21 is because Ti content surpasses the upper limit of the scope of the invention, so slag fissility deterioration.
The solder flux of comparative example 22 is because Mo content is lower than the lower limit of the scope of the invention, so the toughness deterioration.On the other hand, the solder flux of comparative example 23 is because Mo content surpasses the upper limit of the scope of the invention, so heat cracking takes place in weld metal.In addition, the solder flux of comparative example 24 is because B
2O
3Content is lower than the lower limit of the scope of the invention, so the toughness deterioration.On the other hand, the solder flux of comparative example 25 is because B
2O
3Content surpasses the upper limit of the scope of the invention, so heat cracking takes place in weld metal.In addition, the solder flux of comparative example 26 is because Al content is lower than the lower limit of the scope of the invention, so have abrasive grit to take place on the welding bead surface.On the other hand, the solder flux of comparative example 27 is because Al content surpasses the upper limit of the scope of the invention, so the toughness deterioration.
Also have, the evaluation of each solder flux of aforesaid embodiment and comparative example, implement the evaluation of single face submerged-arc welding with the flux copper-gasket method, promptly on copper coin with certain thickness scattering liner solder flux, it is crimped on the method that steel plate back side face welds, and do not use copper coin, and while in the liner method of solder flux liner method that the curing of liner solder flux is carried out and the solid shape solder flux of use, also can access roughly same result.In addition, the result who shows the welding of three electrodes in table 4 and the table 5, but in addition in single electrode, bipolar electrode also have four electrodes welding, the dissolving of the solder flux after the welding/process of setting does not have difference yet, therefore can access the same result of situation with the three electrodes welding shown in table 4 and the table 5.
According to above results verification, the solder flux of the application of the invention in single electrode or multielectrode single face submerged-arc welding, can access sound cap bead shape and mechanical property.
Claims (3)
1. a single face used for submerged arc welding solder flux is characterized in that, contains SiO
2: 10～30 quality %, CaO:3～9 quality %, MgO:15～35 quality %, TiO
2: 4～20 quality %, CaF
2: 2～9 quality %, Al
2O
3: 14～20 quality %, CO
2: 2～9 quality %, Na
2O:1～3 quality %, B
2O
3: 0.1～1 quality %, Mo:0.2～1 quality %, Al:0.7～3 quality %, iron powder: 10～30 quality %, and, limit below the Si:2 quality %, below the Mn:1.5 quality %, below the Ti:1 quality %.
2. single face used for submerged arc welding solder flux according to claim 1 is characterized in that, contains Si:0.5～2 quality % and/or Ti:0.3～1 quality %.
3. single face used for submerged arc welding solder flux according to claim 1 and 2 is characterized in that, contains Mn:0.5～1.5 quality %.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2012015543A JP2013154363A (en) | 2012-01-27 | 2012-01-27 | Flux for one side submerged arc welding |
| JP2012-015543 | 2012-01-27 |
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|---|---|
| CN103223562A true CN103223562A (en) | 2013-07-31 |
| CN103223562B CN103223562B (en) | 2016-02-10 |
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|---|---|---|---|
| CN201210551863.9A Active CN103223562B (en) | 2012-01-27 | 2012-12-18 | One side solder flux used for submerged arc welding |
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| CN104339100A (en) * | 2013-08-07 | 2015-02-11 | 株式会社神户制钢所 | Welding flux for one-side submerged-arc welding |
| CN104339098A (en) * | 2013-08-07 | 2015-02-11 | 株式会社神户制钢所 | Solder for single-surface submerged-arc welding |
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| CN104339100A (en) * | 2013-08-07 | 2015-02-11 | 株式会社神户制钢所 | Welding flux for one-side submerged-arc welding |
| CN104339098A (en) * | 2013-08-07 | 2015-02-11 | 株式会社神户制钢所 | Solder for single-surface submerged-arc welding |
| CN104339101A (en) * | 2013-08-07 | 2015-02-11 | 株式会社神户制钢所 | Welding flux for one-side submerged-arc welding |
| CN104400256A (en) * | 2014-10-31 | 2015-03-11 | 天津市宏远钛铁有限公司 | Low-hygroscopicity submerged-arc welding sintered flux and preparation method thereof |
| CN105081615A (en) * | 2015-09-11 | 2015-11-25 | 武汉铁锚焊接材料股份有限公司 | High tenacity and low hydrogen type agglomerated flux for ocean engineering and preparation method thereof |
| CN105081615B (en) * | 2015-09-11 | 2017-04-05 | 武汉铁锚焊接材料股份有限公司 | A kind of ocean engineering high tenacity low hydrogen type sintered flux and preparation method thereof |
| CN108274157A (en) * | 2017-01-05 | 2018-07-13 | 株式会社神户制钢所 | Pad solder flux |
| CN112621016A (en) * | 2019-10-08 | 2021-04-09 | 株式会社神户制钢所 | Welding material, welding metal, and electroslag welding method |
| CN112621016B (en) * | 2019-10-08 | 2022-06-28 | 株式会社神户制钢所 | Welding material, weld metal, and electroslag welding method |
| CN113695789A (en) * | 2021-10-28 | 2021-11-26 | 东北大学 | Sintered flux for welding HSLA steel and preparation method thereof |
| CN113695789B (en) * | 2021-10-28 | 2022-02-22 | 东北大学 | Sintered flux for welding HSLA steel and preparation method thereof |
Also Published As
| Publication number | Publication date |
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| CN103223562B (en) | 2016-02-10 |
| JP2013154363A (en) | 2013-08-15 |
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