CN104339098A - Solder for single-surface submerged-arc welding - Google Patents

Solder for single-surface submerged-arc welding Download PDF

Info

Publication number
CN104339098A
CN104339098A CN201410383924.4A CN201410383924A CN104339098A CN 104339098 A CN104339098 A CN 104339098A CN 201410383924 A CN201410383924 A CN 201410383924A CN 104339098 A CN104339098 A CN 104339098A
Authority
CN
China
Prior art keywords
quality
content
tio
solder flux
cao
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
Application number
CN201410383924.4A
Other languages
Chinese (zh)
Other versions
CN104339098B (en
Inventor
堀口元宏
岛本正树
石田齐
村西良昌
太田诚
幸村正晴
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Kobe Steel Ltd
Original Assignee
Kobe Steel Ltd
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Kobe Steel Ltd filed Critical Kobe Steel Ltd
Publication of CN104339098A publication Critical patent/CN104339098A/en
Application granted granted Critical
Publication of CN104339098B publication Critical patent/CN104339098B/en
Expired - Fee Related legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/36—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
    • B23K35/362—Selection of compositions of fluxes

Landscapes

  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Nonmetallic Welding Materials (AREA)

Abstract

The invention provides a solder for single-surface submerged-arc welding for obtaining right surface welding channel shape and mechanical property. The solder comprises the following components by mass: 6-12% of Si, Si alloy and Si oxide (SiO2 equivalent value), 3-9% of CaO, 15-35% of MgO, 5-23% of TiO2, 2-10% of CaF2, 5-23% of Al2O3, 2-9% of CO2, 0.5-3% of Na2O, 0.1-1% of B2O3, 0.2-1% of Mo, 10-30% of Fe powder, less than 0.9% of Mn, less than 1% of Ti and less than 3% of Al, which satisfy the equations (I)-(III). 0.1<=A<=1.7 (I), when A>=0.7, A>=-0.25*{([Al2O3]+[MgO]+[TiO2])/[T.SiO2]}+2.03 (II), and when A<0.7, A<=0.52*{([Al2O3]+[MgO]+[TiO2])/[T.SiO2]}-2.07 (III).

Description

One side solder flux used for submerged arc welding
Technical field
The solder flux that the one side submerged-arc welding that the electrode that the present invention relates to more than use 1 or 2 carries out is used.In more detail, the welding bead appearance investigation technology of the one side solder flux used for submerged arc welding containing iron powder is related to.
Background technology
In one side submerged-arc welding, usually, in order to ensure deposition amount, can weld at large line and still realize stable welding bead formation, and use the solder flux being added with iron powder (for example, referring to patent document 1,2.)。But in such containing in the existing one side solder flux used for submerged arc welding of iron powder described in patent document 1, easily there is the such problem of small abrasive grit thrust in the surface having top layer welding bead.In addition, even if when forming as the solder flux described in patent document 2, can not fully suppress abrasive grit thrust.
The thrust on such welding bead surface, top layer, becomes obstacle in coating process.Such as in shipbuilding field, object is turned to the long lifetime of hull and easy-maintaining, by International Maritime Organization (International Maritime Organization), the coating standard that to have revised with the dual shipboard portion of the ballast box of whole boats and ships and bulk freighter be object, such as, although the splashing occurred when determining welding and welding bead surface blot hinder coating like this, the important document removed can be implemented.Therefore, in the construction process of boats and ships, in order to remove abrasive grit thrust, having to cross over welding bead and carrying out polishing process completely.
Therefore, up to now, in one side solder flux used for submerged arc welding, the technology of the generation had for suppressing abrasive grit thrust is proposed (with reference to patent document 3,4.)。Such as, the solder flux used for submerged arc welding of the one side described in patent document 3, by making particle diameter and apparent density be in specific scope, to realize soundization of welding bead.In addition, in the bonded flux used for submerged arc welding described in patent document 4, in order to suppress the generation of abrasive grit projection, the content of Fe composition is limited in below 5 quality %.
[patent document]
[patent document 1] Japanese Unexamined Patent Publication 11-267883 publication
[patent document 2] Japanese Unexamined Patent Publication 2000-107885 publication
[patent document 3] Japanese Unexamined Patent Publication 6-277878 publication
[patent document 4] Japanese Unexamined Patent Publication 2006-272348 publication
But the technology as described in patent document 3, only by particle diameter and the apparent density of restriction solder flux, the generation inhibition for abrasive grit projection is little.In addition, the bonded flux used for submerged arc welding as described in patent document 4, if restriction Fe content, be then difficult to guarantee sufficient deposition amount in the splice joint of slab, during this external large line can weld, weld bead shape deterioration.So, under existing welding bead appearance investigation technology, in one side submerged-arc welding, not yet reach and maintain iron powder to the additive effect in solder flux, while suppress the generation of abrasive grit projection, make the level of perfecting of welding bead outward appearance.
Summary of the invention
Therefore, the present invention is its main purpose is, provide the one side solder flux used for submerged arc welding of the performance of a kind of top layer weld bead shape that can obtain perfecting and machinery.
The present inventors, in order to solve aforesaid problem, in the one side submerged-arc welding of electrode employing more than 1 or 2, experimental study has with keen determination been carried out in order to ensure the viability of top layer welding bead, it found that, in the generation suppressing abrasive grit projection, effectively suppresses the SiO making to contain in solder flux 2amount, and for CaO amount and TiO 2the ratio of amount, specific MgO amount, Al 2o 3amount, TiO 2amount and SiO 2the relation of amount, thus reached the present invention.
That is, one side of the present invention solder flux used for submerged arc welding, containing at least one (SiO selected from the group that Si, Si alloy and Si oxide are formed 2scaled value): add up to 6 ~ 12 quality %; CaO:3 ~ 9 quality %; MgO:15 ~ 35 quality %; TiO 2: 5 ~ 23 quality %; CaF 2: 2 ~ 10 quality %; Al 2o 3: 5 ~ 23 quality %; CO 2: 2 ~ 9 quality %; Na 2o:0.5 ~ 3 quality %; B 2o 3: 0.1 ~ 1 quality %; Mo:0.2 ~ 1 quality %; Iron powder: 10 ~ 30 quality %, and Mn: limit below 0.9 quality %, Ti: limit below 1 quality %, Al: limit below 3 quality %, if the content of CaO (quality %) is [CaO], TiO 2content (quality %) be [TiO 2], Al 2o 3content (quality %) be [Al 2o 3], the content (quality %) of MgO is the SiO of [MgO], the total content of Si, Si alloy and Si oxide 2scaled value (quality %) is [T.SiO 2] time, the content of CaO and TiO 2ratio A (=[CaO]/[TiO of content 2]) meet following formula 1 ~ 3.
[formula 1]
0.1≤A≤1.7
[formula 2]
During A >=0.7,
A≥－0.25×{([Al 2O 3]+[MgO]+[TiO 2])/[T.SiO 2]}+2.03
[formula 3]
During A < 0.7,
A≤0.52×{([Al 2O 3]+[MgO]+[TiO 2])/[T.SiO 2]}－2.07
In one side of the present invention solder flux used for submerged arc welding, by CaO content and TiO 2ratio A (=[CaO]/[TiO of content 2]) be in specific scope, and according to the value of A, specific A and Al 2o 3content, content of MgO, TiO 2the relation of the total content of content and Si, Si alloy and Si oxide.Thereby, it is possible to suppress to generate CaTi system oxide in slag in the process of solidifying at slag, at the temperature field that weld seam solidifies, MgAlTi system oxide can be generated energetically in slag.If MgAlTi system oxide generates in slag, then the abrasive grit in slag is just combined with this oxide before being deposited in the welding bead surface of solidifying, and the generation to the microvillus on welding bead surface is suppressed.
This solder flux also can contain Ti in the scope of 0.1 ~ 1 quality %.
In addition, also Mn can be contained in the scope of 0.1 ~ 0.9 quality %.
According to the present invention, because specific flux constituent and content thereof, even if so employing in single electrode or multielectrode one side submerged-arc welding, no matter pad structure, the performance of weld bead shape and the machinery perfected can both be obtained.
Accompanying drawing explanation
Fig. 1 is the supposition figure of the abrasive grit generation movement in one side submerged arc welding process.
Fig. 2 is the profile of the bevel shape representing the steel plate used in embodiments of the invention.
Fig. 3 is the figure becoming to be grouped into the relation occurred with abrasive grit projection representing embodiment and each solder flux of comparative example.
Symbol description
1,10 mother metals
2 weld metals
2a welding bead surface
The solder flux of 3 non-meltings
Solder flux (slag) in 4 melting and solidifications
5 iron powders
The aggegation of 6 iron powders
7 aggegation iron powders (abrasive grit)
Detailed description of the invention
Below, be just described in detail for implementing mode of the present invention.Further, the present invention does not limit by the embodiment of following explanation.
Fig. 1 is the supposition figure of the abrasive grit generation movement in one side submerged arc welding process.As shown in Figure 1, in one side submerged-arc welding, if use the existing solder flux 3 containing iron powder 5, then in the solder flux (slag) 4 in melting/solidify, iron powder 5 aggegation (aggegation 6 of iron powder), this aggegation iron powder (abrasive grit) 7 sedimentation, the surface (welding bead surface 2a) of the weld metal 2 that the weld part being attached to mother metal 1 is formed, infers that having small thrust occurs.Therefore, the present inventors, want the characteristic by improving solder flux, solve the problem that abrasive grit projection occurs.
Specifically, the solder flux of embodiments of the present invention is used for one side submerged-arc welding, at least has following composition: contain with specified quantitative select the group formed from Si, Si alloy and Si oxide at least one, CaO, MgO, TiO 2, CaF 2, Al 2o 3, CO 2, Na 2o, B 2o 3, Mo and iron powder, and Mn, Ti and Al are limited in below specified quantitative.
In this solder flux, make content and the TiO of CaO 2the ratio A of content be in 0.1 ~ 1.7 scope.And, when A is more than 0.7, adjust CaO content, TiO in the mode meeting following formula 4 2content, Al 2o 3content, content of MgO, the total content of Si, Si alloy and Si oxide, A lower than 0.7 time, to meet the mode of following formula 5, adjustment CaO content, TiO 2content, Al 2o 3content, content of MgO, the total content of Si, Si alloy and Si oxide.Further, in following formula 4,5, the content (quality %) that [CaO] is CaO, [TiO 2] be TiO 2content (quality %), [Al 2o 3] be Al 2o 3content (quality %), the content (quality %) that [MgO] is MgO, [T.SiO 2] be the total content (quality %) of Si, Si alloy and Si oxide.
[formula 4]
A≥－0.25×{([Al 2O 3]+[MgO]+[TiO 2])/[T.SiO 2]}+2.03
[formula 5]
A≤0.52×{([Al 2O 3]+[MgO]+[TiO 2])/[T.SiO 2]}－2.07
Below, the composition restriction reason for the solder flux of present embodiment is described.
[total content of Si, Si alloy and Si oxide: 6 ~ 12 quality %]
The Si alloy of Si and Fe-Si etc., has deoxidation, reacts and generate SiO with the oxygen in weld metal 2, this SiO 2play a role as binding agent and slag slag former.In addition, Si oxide too, plays a role as slag slag former.
But the total content of Si, Si alloy and Si oxide is with SiO 2if convert more than 12 quality %, then the viscosity of liquid slag entirety increases, and the mobility of slag reduces.So when the submerged-arc welding of high speed one side, top layer weld width cannot launch, and become unstable, therefore easily undercut occurs.In addition, abrasive grit easily occurs.On the other hand, the total content of Si, Si alloy and Si oxide is with SiO 2convert when lower than 6 quality %, the setting temperature of liquid slag becomes too high, therefore can not get good top layer weld bead shape.
Therefore, the total content of Si, Si alloy and Si oxide, with SiO 2be scaled 6 ~ 12 quality %.Further, in the solder flux of present embodiment, containing at least one among Si, Si alloy and Si oxide.
[CaO:3 ~ 9 quality %]
CaO makes the viscosity of liquid slag reduce, and improves the mobility of slag, has the effect of expansion top layer weld width.But if CaO content is more than 9 quality %, then the setting temperature of liquid slag becomes too high, and top layer weld bead shape is impaired.On the other hand, when CaO content is lower than 3 quality %, the mobility that can not get liquid slag improves effect, and top layer weld width is not enough, therefore easily undercut occurs.Therefore, CaO content is 3 ~ 9 quality %.
[MgO:15 ~ 35 quality %]
MgO is the same with aforesaid CaO, and the viscosity of liquid slag is reduced, and improves the mobility of slag, has the effect of expansion top layer weld width.But when the content of MgO is lower than 15 quality %, the mobility that can not get liquid slag improves effect, and top layer weld width is not enough, easily undercut occurs.
On the other hand, because MgO is dystectic composition, if so add more than 35 quality %, then the meltbility of solder flux entirety is impaired, can not guarantee stable welding bead, easily becomes convexity welding bead.At this, so-called " convexity welding bead " is relative to welding direction, top layer welding bead central portion welding bead convexly, is one of bad essential factor of application.Therefore, in the solder flux of present embodiment, content of MgO is 15 ~ 35 quality %.
Further, content of MgO is preferably more than 20 quality %, thereby, it is possible to improve the mobility of liquid slag, makes top layer weld bead shape more soundization.
[TiO 2: 5 ~ 23 quality %]
TiO 2it the improvement of single fillet welded slag fissility is effective especially composition.But if its content is more than 23 quality %, then the weld ripples of top layer welding bead is thicker.In addition, TiO 2when content is lower than 5 quality %, can not get the improvement effect of aforesaid slag fissility, abrasive grit easily occurs in addition.Therefore, TiO 2content is 5 ~ 23 quality %.
[Al 2o 3: 5 ~ 23 quality %]
Al 2o 3being neutral compound, is the viscosity for adjustment slag and the effective composition of setting temperature.But, Al 2o 3when content is lower than 5 quality %, the viscosity of slag and setting temperature reduce, and weld width becomes irregular.On the other hand, if add Al 2o 3more than 23 quality %, then the setting temperature of slag becomes too high, and welding bead is difficult to expansion, and weld bead shape becomes convex.Therefore, Al 2o 3content is 5 ~ 23 quality %.
[CaF 2: 2 ~ 10 quality %]
CaF 2be the composition making the meltbility of solder flux entirety good, particularly as one side submerged-arc welding, solder flux must be melted at short notice, generate in the welding method of slag, composition integral especially.But, if CaF 2content is more than 10 quality %, then arc stability deterioration, easily current interruption occurs.On the other hand, CaF 2when content is lower than 2 quality %, the meltbility that can not get solder flux improves effect, and welding bead crawls generation.Therefore, CaF 2content is 2 ~ 10 quality %.
[CO 2: 2 ~ 9 quality %]
CO 2suppressing nitrogen to be effective composition in the intrusion of weld metal and minimizing diffusivity hydrogen amount, add in solder flux as metal carbonate.But, CO 2when content is lower than 2 quality %, the diffusivity hydrogen amount in weld metal uprises, low temperature resistant anti-thread breakage deterioration.On the other hand, if CO 2content is more than 9 quality %, then gas generating capacity is excessive, in top layer welding bead generation pit.Therefore, CO 2content is 2 ~ 9 quality %.
[Na 2o:0.5 ~ 3 quality %]
Na 2o is the composition for guaranteeing arc stability.Specifically, Na 2when O content is lower than 0.5 quality %, arc electrode is unstable, and current interruption occurs, weld bead shape and fusion penetration uneven.On the other hand, if Na 2o content is more than 3 quality %, then resistance to hygroscopicity reduces, low temperature resistant anti-thread breakage deterioration.Therefore, Na 2o content is 0.5 ~ 3 quality %.
[B 2o 3: 0.1 ~ 1 quality %]
B 2o 3be reduced in welding, in weld metal as B exist, for toughness guarantee effectively play a role.But, B 2o 3when content is lower than 0.1 quality %, this effect cannot play fully, toughness deterioration.On the other hand, if B 2o 3content is more than 1 quality %, then intensity is excessive, and heat cracking occurs.Therefore, B 2o 3content is 0.1 ~ 1 quality %.
[Mo:0.2 ~ 1 quality %]
Mo improves effective composition to hardenability, except Mo monomer, also adds in solder flux with the form of the alloy of Fe-Mo etc.But, when Mo content is lower than 0.2 quality %, weld metal organize coarsening, toughness deterioration.On the other hand, if add Mo more than 1 quality %, then the intensity of weld metal is excessive, and heat cracking occurs.Therefore, Mo content is 0.2 ~ 1 quality %.
[iron powder: 10 ~ 30 quality %]
Iron powder had been once necessary adding ingredient in the one side submerged-arc welding needing a large amount of deposited metals.And, when iron content is lower than 10 quality %, can not get the effect making up deposited metal amount, and the apparent density of solder flux diminishes, therefore anti-blowing property deterioration.On the other hand, if make iron powder contain more than 30 quality %, then, in the solder flux in melting/solidify, the easy aggegation of iron powder, the quantitative change of aggegation iron powder sedimentation is many, and abrasive grit is easily attached to welding bead surface.And the apparent density of solder flux uprises, weld width can not be guaranteed.Therefore, the content of iron powder is 10 ~ 30 quality %.
[A(＝CaO/TiO 2)：0.1～1.7]
As aforementioned, CaO and TiO 2effective composition for the mobility of slag and the raising of slag fissility, but CaO content (quality %) and TiO 2ratio A (=[CaO]/[TiO of content (quality %) 2]) lower than 0.1 time, electric arc is unstable, and welding bead easily occurs concavo-convex.On the other hand, if A is more than 1.7, then welding bead crawls.Therefore, in the solder flux of present embodiment, in order to make CaO content and TiO 2content is in aforesaid scope, and in order to guarantee good welding operation under large-line energy, makes CaO content and TiO 2the ratio A of content is in the scope of 0.1 ~ 1.7.
[below Ti:1 quality %]
Ti is same with aforesaid Si, Si alloy, is the effective composition of oxygen amount for reducing in weld metal, but this effect fully can be reached by the interpolation of Si and/or Si alloy etc., and therefore in the solder flux of present embodiment, Ti is composition not necessarily.In addition, if Ti content is more than 1 quality %, then slag heating adheres to welding bead surface, the deterioration of slag fissility.Therefore, Ti content is limited in below 1 quality %.
On the other hand, if Ti contains more than 0.1 quality %, then the deoxidation effect of weld metal realizes further, can realize the raising of toughness.Therefore, in the solder flux of present embodiment, as required, Ti can be contained in the scope of 0.1 ~ 1 quality %.Further, Ti, except Ti monomer, also adds in solder flux with the form of the alloy of Fe-Ti etc.
[below Mn:0.9 quality %]
Mn is same with aforesaid Mo, has the effect that hardenability is improved, and the raising of intensity and toughness is effective composition, if but Mn content more than 0.9 quality %, then slag heating adheres to welding bead surface, the deterioration of slag fissility.In addition, in the solder flux of present embodiment, because by adding Mo, the effect of hardenability can be obtained thus, so Mn content is limited in below 0.9 quality %.
On the other hand, if reach more than 0.1 quality % containing Mn, then can realize the further raising of hardenability, toughness is improved.Therefore, in the solder flux of present embodiment, as required, Mn can be contained in the scope of 0.0 ~ 0.9 quality %.Further, Mn, except Mn monomer, also adds in solder flux with the form of the alloy of Fe-Mn etc.
[below Al:3 quality %]
Al makes organizing of weld metal fine, is to the effective composition of the raising of toughness.But this effect fully can be reached by adding other compositions, and therefore in the solder flux of present embodiment, Al is composition not necessarily.In addition, if Al content is more than 3 quality %, then overquenching, intensity rises, and low-temperature cracks occurs.Therefore, Al content is limited in below 3 quality %.Further, Al is inevitable impurity, but as aforementioned, owing to having the effect organizing miniaturization making weld metal, so allow containing below 3 quality %.
[CaO content, TiO 2content, Al 2o 3content, content of MgO, the relation of the total content of Si, Si alloy and Si oxide]
In the solder flux of present embodiment, the content of each composition is made to be in aforesaid scope, and to meet the mode of above-mentioned formula 4 or formula 5, adjustment CaO content, TiO 2content, Al 2o 3content, content of MgO, and the total content of Si, Si alloy and Si oxide.Thus, in the process that slag solidifies, the generation of the CaTi system oxide in slag can be suppressed, and at temperature near the temperature of solidifying at weld seam, MgAlTi system oxide can be generated energetically energetically in slag.
At the neighborhood of the setting temperature of weld seam, if there is MgAlTi system oxide to generate in slag, then the abrasive grit in slag can be made to rest in slag before falling welding bead surface, therefore, it is possible to suppress the generation of the microvillus on welding bead surface.Further, MgAlTi system oxide is not defined as single-phase, can generate by complex phase yet.
In addition, the CaTi system oxide generated in slag, mainly CaTiO 3(perovskite), the CaO amount in solder flux and TiO 2amount, with mol ratio (=CaO/TiO 2) count about 1, mass ratio (=CaO/TiO 2) when when being about 0.7, have the tendency the most easily generated.In the CaTi system oxide of perovskite etc., because do not make abrasive grit rest on effect in slag, so suppress its generation very important.
Therefore, in the solder flux of present embodiment, by CaO and TiO 2ratio (=CaO/TiO 2) be benchmark when being 0.7 by quality ratio, when the generation of perovskite is many, the growing amount (ratio relative to the total content of Si, Si alloy and Si oxide) of MgAlTi system oxide is increased, suppress the generation of abrasive grit defect.Specifically, CaO content (quality %) and TiO 2ratio A (=[CaO]/[TiO of content (quality %) 2]) when being more than 0.7, meet above-mentioned formula 4, A lower than 0.7 time, meet above-mentioned formula 5, so the blending amount of each composition of adjustment.
Further, CaO content, TiO 2content, Al 2o 3content, content of MgO, and the total content of Si, Si alloy and Si oxide, when not meeting above-mentioned formula 4 or formula 5, that is, CaO content (quality %) and TiO 2ratio A (=[CaO]/[TiO of content (quality %) 2]) be 0.7≤A <-0.25 × { ([A1 2o 3]+[MgO]+[TiO 2])/[T.SiO 2]+2.03, or, 0.52 × { ([A1 2o 3]+[MgO]+[TiO 2])/[T.SiO 2]-2.07 < A < 0.7 time, during welding in slag CaTi system oxide growing amount increase, the generation of MgAlTi system oxide is suppressed.Consequently, at the setting temperature neighborhood of weld seam, the abrasive grit in slag falls the welding bead surface of solidifying, and microvillus occurs.
[other composition]
Composition other than the above in the solder flux of present embodiment is FeO, ZrO 2and K 2o etc.
As described in detail above, the solder flux of present embodiment, carry out intention from the genesis mechanism of microvillus to prepare, with the specific flux constituent of new viewpoint and content, therefore single electrode or multielectrode one side submerged-arc welding is being employed, no matter pad structure, the performance of sound weld bead shape and machinery can both be obtained.
Specifically, make 6 ~ 12 quality % that the total content of Si, Si alloy and Si oxide becomes few than ever, and CaO content (quality %) and TiO 2ratio A (=[CaO]/[TiO of content (quality %) 2]) when being more than 0.7, be A>=-0.25 × { ([A1 2o 3]+[MgO]+[TiO 2])/[T.SiO 2]+2.03, A lower than 0.7 time, be A≤0.52 × { ([A1 2o 3]+[MgO]+[TiO 2])/[T.SiO 2]-2.07, the aggegation of iron powder in the solder flux that this can suppress in melting and solidification and the abrasive grit of generation are to the attachment of top layer welding bead.Thus, in one side submerged-arc welding, the excellent of machinery can be formed, there is no the sound top layer welding bead of abrasive grit projection.
Also have, the solder flux of present embodiment, mainly use in one side submerged-arc welding method, but about its pad approach, be not particularly limited, with the flux copper-gasket method that solder flux and copper are gasket material, be only the solder flux liner method of gasket material with solder flux, use any one methods such as the liner method of solid flux to be suitable for.In addition, about liner solder flux, be also not particularly limited, can directly apply existing solder flux.
[embodiment]
Below, enumerate examples and comparative examples of the present invention, effect of the present invention is illustrated particularly.In the present embodiment, use the welding wire shown in the steel plate shown in following table 1 and table 2, the bevel shape of the welding condition according to following table 3 and the steel plate shown in Fig. 2 (mother metal 10), implements one side submerged-arc welding, the performance of each solder flux of Evaluation operation example and comparative example.Further, in the present embodiment, Blend Stocks makes it to become the composition shown in following table 4 and table 5, after mixing together with adhesive (waterglass), carry out granulation, re-use rotary kiln and burn till with 400 ~ 650 DEG C, obtain by whole grain the solder flux that particle diameter is below 2.5mm.
[table 1]
[table 2]
[table 3]
[table 4]
[table 5]
Further, the surplus of the steel plate composition shown in above-mentioned table 1 and the composition of the welding wire shown in above-mentioned table 2 is Fe and inevitable impurity.In addition, " A " shown in above-mentioned table 4 and table 5 is CaO content (quality %) and TiO 2ratio ([CaO]/[TiO of content (quality %) 2]), " AMT/T.S " is Al 2o 3, MgO and TiO 2total content and the ratio (([A1 of total content of Si, Si alloy and Si oxide 2o 3]+[MgO]+[TiO 2])/[T.SiO 2]).
The evaluation of each solder flux of embodiment and comparative example, by welding operation (welding bead outward appearance, undercut etc.), carry out according to the ultrasonic examination (UT) test (having flawless, slag inclusion etc.) of JIS Z3060 and the pendulum impact test of foundation JIS Z2242.These evaluation results are presented in following table 6.
[table 6]
Further, in the evaluation of the welding operation shown in above-mentioned table 6, so-called " abrasive grit projection ", is iron powder melting aggegation contained in solder flux and is attached to the part on welding bead surface, becoming one of bad reason of application.In the present embodiment, by welding bead surface observation, when the abrasive grit that particle diameter is more than 200 μm exists more than 100 in the every 1m of welding bead length, be considered as " having abrasive grit projection ".
In addition, so-called " convexity welding bead ", be relative to welding bead direction, top layer welding bead central portion becomes convex, becomes one of bad essential factor of application.So-called " slag heating adhesion ", be that slag heating after welding bead adheres on welding bead and is difficult to peel off, the welding bead appearance degradation after stripping, therefore becomes one of bad reason of application.So-called " undercut " is mother metal has been dug along the tape edge of welding bead, and deposited metal does not fill up and becomes the part that groove remains, and is the one of welding bead defect.
So-called " weld ripples is thick ", refers to that the combined length of connection 5 spacing is more than 40mm, because welding bead appearance degradation, so become one of bad reason of application.So-called " welding bead is irregular ", refers to that the place of the difference of the welding bead Breadth Maximum that arbitrary 50mm is wide and minimum widith more than 5.0mm is more than the situation at a place, because welding bead appearance degradation, so become one of bad reason of application.Further, about the details of " undercut ", " weld ripples is thick " and " welding bead is irregular ", describe in " the whether qualified of outward appearance test judges guide " formulated by (society) Japanese welding association in March nineteen eighty-three.
On the other hand, pendulum impact test, it can (vE-20 DEG C) be qualified at more than 50J that pendulum at test temperature-20 DEG C absorbs, and lower than 50J is defective.
As shown in table 6, the solder flux of the embodiment 1 ~ 18 made within the scope of the invention, welding operation, ultrasonic examination (UT) test and toughness (vE-20 DEG C) are all good.
In contrast, the solder flux of comparative example 1, because the total content of Si, Si alloy and Si oxide is lower than the lower limit of the scope of the invention, so convexity welding bead occurs.On the other hand, the solder flux of comparative example 2, because the total content of Si, Si alloy and Si oxide exceedes the upper limit of the scope of the invention, so undercut and abrasive grit projection occur.In addition, the solder flux of comparative example 3, because CaO content is lower than the lower limit of the scope of the invention, so undercut occurs.On the other hand, the solder flux of comparative example 4, because CaO content exceedes the upper limit of the scope of the invention, so welding bead is convex.
The solder flux of comparative example 5, because the content of the MgO in solder flux is lower than the lower limit of the scope of the invention, so undercut occurs.On the other hand, the solder flux of comparative example 6, because the content of MgO exceedes the upper limit of the scope of the invention, so convexity welding bead occurs.In addition, the solder flux of comparative example 7, because TiO 2content is lower than the lower limit of the scope of the invention, so abrasive grit projection occurs, in addition, because Mn content exceedes scope of the present invention, slag heating adhesion occurs.On the other hand, the solder flux of comparative example 8, because TiO 2content exceedes the upper limit of the scope of the invention, so the weld ripples of welding bead is thick.
The solder flux of comparative example 9, because Al 2o 3content is lower than the lower limit of the scope of the invention, so the alignment of weld width is bad.On the other hand, the solder flux of comparative example 10, because Al 2o 3content exceedes the upper limit of the scope of the invention, so welding bead is convex.
The solder flux of comparative example 11 ~ 14, CaO content and TiO 2ratio A (=[CaO]/[TiO of content 2]), with Al 2o 3content, content of MgO, TiO 2the relation of the total content of content and Si, Si alloy and Si oxide departs from the scope of the present invention.Specifically, comparative example 11 and comparative example 14, although A is more than 0.7, do not meet A>=-0.25 × { ([A1 2o 3]+[MgO]+[TiO 2])/[T.SiO 2]+2.03, comparative example 12 and comparative example 13, although A is lower than 0.7, do not meet A≤0.52 × { ([A1 2o 3]+[MgO]+[TiO 2])/[T.SiO 2]-2.07.Therefore, all there is abrasive grit projection on welding bead surface in the solder flux of comparative example 11 ~ 14.
The solder flux of comparative example 15, because CaO content and TiO 2ratio A (=[CaO]/[TiO of content 2]) exceed the upper limit of the scope of the invention, so welding bead is irregular.On the other hand, the solder flux of comparative example 16, because A is lower than the lower limit of the scope of the invention, so convexity welding bead occurs.
Fig. 3 is the figure that the one-tenth of each solder flux representing embodiment and comparative example is grouped into the relation occurred with abrasive grit projection.As shown in Figure 3, at CaO content and TiO 2ratio A (=[CaO]/[TiO of content 2]), with Al 2o 3content, content of MgO, TiO 2in the solder flux that the relation of the total content of content and Si, Si alloy and Si oxide departs from the scope of the present invention, confirm abrasive grit projection and occur.
Also have, the evaluation of each solder flux of aforesaid embodiment and comparative example, use the liner material generated by solid flux to implement one side submerged-arc welding, but do not using flux copper-gasket method and the copper coin of copper coin and liner solder flux, but liner solder flux is solidified while in the solder flux liner method of carrying out, also roughly the same result can be obtained.In addition, the result of three electrode weldings is shown in table 4 and table 5, but also have in four electrode weldings at other single electrodes, bipolar electrode, because the melting/process of setting of the solder flux after welding does not have difference, so can obtain the result same with the situation of three electrode weldings shown in table 4 and table 5 yet.
According to above result, the solder flux of the application of the invention, in single electrode or multielectrode one side submerged-arc welding, confirms the top layer weld bead shape and mechanical property that can obtain perfecting.

Claims (3)

1. an one side solder flux used for submerged arc welding, wherein, at least one containing selecting from the group that Si, Si alloy and Si oxide are formed: with SiO 2scaled value meter adds up to 6 ~ 12 quality %, CaO:3 ~ 9 quality %, MgO:15 ~ 35 quality %, TiO 2: 5 ~ 23 quality %, CaF 2: 2 ~ 10 quality %, Al 2o 3: 5 ~ 23 quality %, CO 2: 2 ~ 9 quality %, Na 2o:0.5 ~ 3 quality %, B 2o 3: 0.1 ~ 1 quality %, Mo:0.2 ~ 1 quality %, iron powder: 10 ~ 30 quality %, and, Mn: be limited in below 0.9 quality %, Ti: be limited in below 1 quality %, Al: be limited in below 3 quality %,
Further, setting the mass percentage content of CaO as [CaO], TiO 2mass percentage content be [TiO 2], Al 2o 3mass percentage content be [Al 2o 3], the mass percentage content of MgO is [MgO], the SiO of the mass percent total content of Si, Si alloy and Si oxide 2scaled value is [T.SiO 2] time, the mass percentage content of CaO and TiO 2ratio A=[CaO]/[TiO of mass percentage content 2] meet following formula (I) ~ (III),
0.1≤A≤1.7…(I)
During A>=0.7, A>=-0.25 × { ([Al 2o 3]+[MgO]+[TiO 2])/[T.SiO 2]+2.03 ... (II)
During A < 0.7, A≤0.52 × { ([Al 2o 3]+[MgO]+[TiO 2])/[T.SiO 2]-2.07 ... (III).
2. one side according to claim 1 solder flux used for submerged arc welding wherein, is 0.1 ~ 1 quality % containing Ti.
3. one side according to claim 1 and 2 solder flux used for submerged arc welding wherein, is 0.1 ~ 0.9 quality % containing Mn.
CN201410383924.4A 2013-08-07 2014-08-06 One side solder flux used for submerged arc welding Expired - Fee Related CN104339098B (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2013164192A JP6071797B2 (en) 2013-08-07 2013-08-07 Flux for single-sided submerged arc welding
JP2013-164192 2013-08-07

Publications (2)

Publication Number Publication Date
CN104339098A true CN104339098A (en) 2015-02-11
CN104339098B CN104339098B (en) 2017-06-30

Family

ID=52496003

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201410383924.4A Expired - Fee Related CN104339098B (en) 2013-08-07 2014-08-06 One side solder flux used for submerged arc welding

Country Status (2)

Country Link
JP (1) JP6071797B2 (en)
CN (1) CN104339098B (en)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108145343A (en) * 2016-12-05 2018-06-12 株式会社神户制钢所 Solder flux used for submerged arc welding

Families Citing this family (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
KR20190047388A (en) * 2017-10-27 2019-05-08 현대종합금속 주식회사 Extra low silicon welding consumable having excellent porosity resistance and electro coating, and weld metal

Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1608791A (en) * 2003-10-22 2005-04-27 株式会社神户制钢所 Melt flux for submerged-arc welding
CN1853845A (en) * 2005-04-28 2006-11-01 株式会社神户制钢所 Hidden arc welding used smelting solder
CN101966630A (en) * 2009-07-27 2011-02-09 株式会社神户制钢所 Material and method for submerged arc welding of 9% Ni steel
CN103223562A (en) * 2012-01-27 2013-07-31 株式会社神户制钢所 Solder for single-surface submerged-arc welding
CN103223563A (en) * 2012-01-27 2013-07-31 株式会社神户制钢所 Solder for single-surface submerged-arc welding

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2860060B2 (en) * 1994-09-30 1999-02-24 株式会社神戸製鋼所 Single-sided submerged arc welding method
JP3617605B2 (en) * 1998-10-01 2005-02-09 株式会社神戸製鋼所 Bond flux for submerged arc welding
JP2002018595A (en) * 2000-07-03 2002-01-22 Nippon Steel Corp One side submerged arc welding method for steel for low temperature use
JP3747321B2 (en) * 2003-03-12 2006-02-22 株式会社神戸製鋼所 Slag regeneration flux
JP4537310B2 (en) * 2005-12-01 2010-09-01 日鐵住金溶接工業株式会社 Low temperature steel single-sided submerged arc welding method and weld metal
JP5766500B2 (en) * 2011-05-06 2015-08-19 株式会社神戸製鋼所 Submerged arc welding material and submerged arc welding method

Patent Citations (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1608791A (en) * 2003-10-22 2005-04-27 株式会社神户制钢所 Melt flux for submerged-arc welding
CN1853845A (en) * 2005-04-28 2006-11-01 株式会社神户制钢所 Hidden arc welding used smelting solder
CN101966630A (en) * 2009-07-27 2011-02-09 株式会社神户制钢所 Material and method for submerged arc welding of 9% Ni steel
CN103223562A (en) * 2012-01-27 2013-07-31 株式会社神户制钢所 Solder for single-surface submerged-arc welding
CN103223563A (en) * 2012-01-27 2013-07-31 株式会社神户制钢所 Solder for single-surface submerged-arc welding

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN108145343A (en) * 2016-12-05 2018-06-12 株式会社神户制钢所 Solder flux used for submerged arc welding
CN108145343B (en) * 2016-12-05 2020-08-25 株式会社神户制钢所 Flux for submerged arc welding

Also Published As

Publication number Publication date
JP6071797B2 (en) 2017-02-01
JP2015033700A (en) 2015-02-19
CN104339098B (en) 2017-06-30

Similar Documents

Publication Publication Date Title
US4149063A (en) Flux cored wire for welding Ni-Cr-Fe alloys
CN103223562B (en) One side solder flux used for submerged arc welding
JP4986563B2 (en) Flux-cored wire for electrogas arc welding and 2-electrode electrogas arc welding method
CN103223563B (en) Solder for single-surface submerged-arc welding
EP3208030B1 (en) Flux-cored wire for arc welding of duplex stainless steel
JP2007160314A (en) Flux cored wire for welding high-strength stainless steel
KR20090012045A (en) Weld metal and titania-based flux cored wire
KR20190038412A (en) Aluminum-containing welding electrode
JP2008149341A (en) Flux cored wire for gas-shielded arc welding
JP2003019595A (en) Flux cored wire for gas-shielded arc welding for low alloy heat resistant steel
KR20190019020A (en) Electrodes for forming austenitic and duplex steel weld metal
JP2011245519A (en) Weld metal excellent in hot crack resistance
JP3787104B2 (en) Flux-cored wire for gas shielded arc welding
CN104339098A (en) Solder for single-surface submerged-arc welding
CN104339100B (en) One side solder flux used for submerged arc welding
KR102675635B1 (en) Flux Cored Wire and Welding Methods
KR102456990B1 (en) Flux-cored wire for gas shielded arc welding of low temperature steel
CN104339101B (en) One side solder flux used for submerged arc welding
JP2009018337A (en) Flux cored wire for gas-shielded arc welding
JP7252051B2 (en) Solid wire and weld joints for electroslag welding
JP2524774B2 (en) Submerged arc welding method for stainless steel
JPS5877790A (en) Sintered flux for submerged arc welding
JPS6045996B2 (en) Flux-cored wire for self-shield arc welding
JP6071834B2 (en) Flux for single-sided submerged arc welding
JPH0122080B2 (en)

Legal Events

Date Code Title Description
C06 Publication
PB01 Publication
C10 Entry into substantive examination
SE01 Entry into force of request for substantive examination
GR01 Patent grant
GR01 Patent grant
CF01 Termination of patent right due to non-payment of annual fee

Granted publication date: 20170630

Termination date: 20200806

CF01 Termination of patent right due to non-payment of annual fee