JP5869066B2 - Bond flux for multi-electrode single-sided submerged arc welding - Google Patents

Description

  The present invention relates to a bond flux for multi-electrode single-sided submerged arc welding used for large plate joints such as shipbuilding, and more particularly to a multi-electrode single-sided submerged arc suitable for obtaining a stable bead shape and forming a weld metal with excellent mechanical performance. The present invention relates to a welding bond flux.

  In submerged arc welding, a granular flux is dispersed in advance along the welding line, and an electrode wire is continuously supplied therein, and an arc is generated between the tip of the electrode wire and the base material to perform welding. Is a method of continuously performing. According to this submerged arc welding method, high efficiency and stable welding workability and mechanical performance of weld metal can be obtained, so a wide range of fields such as shipbuilding, steel frames, pipes, bridges, vehicles, etc. Has been applied.

  In recent years, with the development of the energy industry, high strength and high toughness of steel materials have been studied, and the increase in the thickness of structures due to the increase in size of structures has been studied. doing. Therefore, in submerged arc welding, further quality improvement is required in order to improve productivity and ensure safety and durability in welding construction. Among them, in particular, higher efficiency of welding and higher welding metal are required. There is a great demand for toughness.

  Especially in the shipbuilding industry, the number of large-scale bulk carriers, tankers, container carriers, etc. is increasing year by year, and in order to improve productivity and secure safety and durability in these constructions, further increase the efficiency of welding. There is a great demand for higher toughness of welds.

  The large plate joint, which is the main axis of the shipbuilding construction process, is frequently used the flux copper backing single-sided submerged arc welding method (hereinafter referred to as FCuB method) shown in FIG. In this FCuB method, about 4 to 7 mm of back flux 2 is sprayed on the backing copper plate 1, air is injected into the air hose 3, and this is pressed against the groove back surface 4 a corresponding to the back side of the steel plate 4 to be welded. And the front bead and the back bead are formed simultaneously by spraying the front flux 6 from the front side using 2 to 4 wires 5 and welding one layer. In this welding method, since the back flux 2 adheres closely to the groove back surface 4a, the backing hits well, and the back copper bead 1 under the back flux 2 suppresses the height of the back bead. Even if it is constructed under welding conditions, a beautiful back bead with no welding defects can be obtained. For this reason, the FCuB method is widely applied from a thin plate to a thick plate.

  Submerged arc welding has higher welding heat input and higher base metal dilution ratio than clad arc welding and gas shielded arc welding, so welding workability and weld metal performance are almost determined by the composition of flux and wire. The Among the submerged arc welding, the above-described single-sided submerged arc welding method is characterized by a high amount of welding heat input and a large base material dilution rate.

  In this single-sided submerged arc welding method, bond flux which is a calcined flux is mainly applied. Bond flux is made by adding water glass to various raw materials, granulated, and fired at about 500 ° C. It can be used to adjust the chemical composition of the weld metal freely and can add iron powder. There is an excellent feature that efficiency can be increased.

  However, in high-speed single-sided submerged arc welding, iron grain protrusions are likely to occur on the surface bead surface, and slag tends to stick. In particular, the number of wire electrodes tends to be more prominent with 4 electrodes than with 3 electrodes, and it has been confirmed that this depends on the welding speed. That is, if the number of wire electrodes is increased, the welding speed can be increased. Therefore, the speed of the four electrodes is increased, and iron grain protrusions and slag sticking on the surface bead surface are likely to occur.

  In consideration of these points, a flux for submerged arc welding and a single-sided welding method that can obtain good welding workability and weld metal mechanical performance have been proposed.

  For example, Patent Document 1 discloses a basic technique related to a high-speed single-sided submerged arc welding method using four electrodes. In order to obtain a weld metal free of sound defects in high-speed single-sided submerged arc welding, the wire diameter, welding current, welding speed, distance between electrodes, flux and wire components are limited and improved. However, although the technique described in Patent Document 1 can obtain a weld metal without a sound defect, it cannot improve the iron grain protrusion and slag sticking on the surface bead surface, and a deoxidizer in the flux, The addition of the alloying agent is not limited. For this reason, there is a problem that stable welding workability and good weld metal mechanical performance cannot be obtained because the tensile strength of the weld metal is lowered and the toughness is further lowered when the thick plate is subjected to high heat input welding.

  Patent Document 2 discloses a technique relating to a high-speed single-sided submerged arc welding flux using three or more electrodes and a welding method. This limits the components of the flux, further limits the particle size configuration and bulk density of the flux, and aims to improve sound front and back beads. However, since the particles having a particle size exceeding 840 μm are less than 20% by weight in the particle size configuration, the particle size of the entire flux becomes fine. As a result, the arc state during welding is finely dispersed, and the arc is difficult to spread, the bead shape becomes convex, the outgassing becomes worse and welding defects such as pits and pock marks occur, so it is healthy and stable. There is a problem that the front and back beads cannot be obtained.

  Patent Document 3 discloses a technique for obtaining a sound back bead by using three or more electrodes, limiting the wire diameter, welding current, distance between electrodes, and electrode torch angle. Although the technology described in Patent Document 3 can obtain a healthy back bead even at high speed by single-sided submerged arc welding, it cannot improve the iron grain protrusion and slag sticking on the surface bead surface. I can't get it.

  Patent Document 4 discloses a technique related to a single-sided submerged arc welding method using a single electrode. According to this method, by optimizing the welding speed and welding heat input, it is possible to obtain a sound and stable bead shape and appearance for both the front and back beads. There is a problem that the efficiency is lowered and the production efficiency is remarkably lowered.

  Patent Document 5 discloses a technique related to a bond flux for multi-electrode high-speed single-sided submerged arc welding. This disclosed technique aims to improve iron grain protrusions and undercuts on the surface bead surface in high-speed single-sided submerged arc welding. According to the technique described in Patent Document 5, the composition of the flux composition is limited, and as a result of iron powder (Fe), which is considered to be the cause of the generation of iron grain protrusions, being 5% or less, the generation of iron grain protrusions is reduced. Can do. However, in high-speed single-sided welding, Fe in the flux is an essential component for obtaining a stable back bead shape and penetration, and can be expected to improve the welding efficiency. For this reason, as in the technique described in Patent Document 5, if the addition amount is 5% or less, a stable back bead shape cannot be obtained, and the welding efficiency is also lowered, so that welding workability and production efficiency are remarkably deteriorated. There is a problem.

  Patent Document 6 also discloses a technique for improving iron grain protrusions and welding defects on the surface bead surface related to the bond flux for multi-electrode high-speed single-sided submerged arc welding. In the technique described in Patent Document 6, the components of the flux composition are limited in a manner similar to the technique described in Patent Document 5, and in particular, iron powder (Fe), which is considered to be the cause of the generation of iron grain protrusions, is 5% or less, and is further subjected to welding. The joint plate thickness is 16 mm or less. However, in the technology disclosed in Patent Document 6, as described above, even when the applied joint plate thickness is 16 mm or less, a stable back bead shape cannot be obtained if the Fe addition amount in the flux is 5% or less, and the welding efficiency is also low. Therefore, there is a problem that welding workability and production efficiency are remarkably deteriorated.

  In addition, the present applicant has proposed a technique related to bond flux for multi-electrode high-speed single-sided submerged arc welding, in which a weld metal with improved iron grain protrusions and welding defects on the surface bead surface and excellent mechanical performance can be obtained. The technology described in Patent Document 7 limits the components of the flux composition and further improves the iron grain protrusions on the surface bead surface by adjusting the particle size of the flux, but only by limiting the components of the flux composition and adjusting the flux particle size The generation of iron grain protrusions cannot be completely eliminated, and there is another problem that the bead shape becomes convex when welding thick steel plates.

Japanese Patent Laid-Open No. 5-337651 JP-A-6-277878 JP-A-8-99178 JP 2004-154841 A JP 2006-272348 A JP 2007-136516 A JP 2012-218053 A

  Therefore, the present invention has been devised in view of the above-described problems, and particularly suppresses the occurrence of iron grain protrusions on the surface bead surface even in multi-electrode high-speed single-sided submerged arc welding of three or more thick steel plates. Multi-electrode single-sided submerging that can form a healthy weld metal free of weld defects, can obtain a stable bead shape and bead appearance on both the front and back beads, and can provide a weld metal with superior mechanical performance. An object is to provide a bond flux for arc welding.

  In order to solve the above problems, the present inventors have studied the chemical composition of the bond flux and the particle size of the iron powder raw material used for the Fe component. As a result, by limiting the chemical composition of the bond flux and further limiting the particle size of the iron powder raw material used for the Fe component, iron is also applied to the surface bead surface in multi-electrode high-speed single-sided submerged arc welding of 3 or more thick steel plates. It is possible to suppress the occurrence of grain protrusions, to form a sound weld metal with no welding defects, and to obtain a stable bead shape and bead appearance on both the front and back beads, and welding with superior mechanical performance. It has been found that a metal can be obtained.

That is, the present multi-electrode submerged arc welding bonded flux according to the first invention, in _{mass%, SiO 2: 5~24%,} MgO: 12~30%, CaO: 3~15%, Al 2 O 3: 5 ˜17%, CaF ₂ : 7 to 19%, ZrO ₂ : 0.5 to 5%, B ₂ O ₃ : 0.1 to 3%, CaCO ₃ and MgCO ₃ as one or two kinds of CO ₂ conversion values Total: 2-7%, Fe: 10-35%, Si: 0.3-4%, Mn: 0.3-1%, Mo: 0.1-3%, Ti: 0.1-3% The others are characterized by comprising an alkali metal oxide and inevitable impurities.

  Moreover, the bond flux for multi-electrode submerged arc welding according to the second invention of the present application is characterized by further containing Al: 0.05 to 0.5% in the first invention of the present application.

The bond flux for multi-electrode submerged arc welding according to the third invention of the present application is characterized in that, in the first or second invention of the present application, TiO ₂ : 1.5% or less.

  Furthermore, the bond flux for multi-electrode submerged arc welding according to the fourth invention of the present application is characterized in that, in the first to third inventions of the present application, the average particle diameter of the iron powder raw material used for the Fe component is 150 μm or less.

  According to the bond flux for multi-electrode single-sided submerged arc welding to which the present invention is applied, it is possible to further suppress generation of iron grain protrusions on the surface bead surface even in multi-electrode high-speed single-sided submerged arc welding of three or more electrodes of a thick steel plate. It is possible to form a sound weld metal free of welding defects, to obtain a stable bead shape and bead appearance on both the front and back beads, and to obtain a weld metal with excellent mechanical performance with high efficiency. .

It is sectional drawing which shows the flux copper backing single-sided submerged arc welding method used in the Example of this invention. It is a figure which shows the groove shape of the steel plate used in the Example of this invention.

  In the multi-electrode single-sided submerged arc welding of a thick steel plate having a thickness of 8 mm or more, the present inventors can maintain good weld metal mechanical performance and can further suppress the occurrence of iron grain protrusions on the surface bead surface. In order to obtain excellent front and back bead shapes without weld defects, the chemical composition of the bond flux and the particle size of the iron powder raw material used for the Fe component were examined in detail.

  Multi-electrode high-speed single-sided submerged arc welding, which is applied to large plate joints for shipbuilding, has a wide range of plate thicknesses from 8 mm to 40 mm, and the heat input increases as the plate thickness increases. Therefore, to obtain excellent weld metal mechanical performance even in high heat input welding, it is necessary to add a deoxidizer, an alloying agent, etc. in the bond flux to keep the oxygen content of the weld metal low and to improve the hardenability. is there. However, if a deoxidizer and an alloying agent are added excessively, the hardenability of the weld metal becomes excessive, the strength increases, and the toughness decreases. Therefore, as a result of examining various deoxidizers and alloying agents in order to develop bond fluxes corresponding to changes in welding heat input at various plate thicknesses, by adding appropriate amounts of Si, Mn and Mo, good results are obtained. It has been found that the tensile strength and toughness of the weld metal can be obtained.

  It has also been found that by adding an appropriate amount of Al, a good weld metal toughness can be obtained even in the case of welding with a large steel plate and a large heat input.

  Next, the improvement in welding workability is the improvement of iron grain protrusions on the surface bead surface, which is currently considered the most important issue of single-sided submerged arc welding applied to large plate joints in shipbuilding. If iron grain protrusions occur on the front bead, a large amount of paint adheres to the iron grain protrusions in the shipbuilding coating process, and depending on the shape of the iron grain protrusions, it may be easy to peel off. Rust is easy to progress, and corrosion resistance is remarkably lowered. Therefore, the current shipyard removes the iron grain protrusions on the surface bead surface with a grinder, shot blasting, or the like, which raises a problem of cost increase due to a decrease in productivity.

  In order to improve the above problems, the chemical composition of bond flux was examined. The cause of the iron grain protrusion is the iron powder (Fe) added to the bond flux. The weld metal during welding and the iron powder added to the bond flux during the slag solidification process are in a semi-molten state. It melts on the metal surface and remains on the surface when it is not completely melted.

  Therefore, as a result of removing the iron powder in the bond flux, there was no iron grain protrusion on the front bead surface, but the back bead shape was unstable and welding defects such as poor penetration and undercut occurred. Since the welding efficiency is reduced by removing the, the productivity is remarkably reduced as the welding speed is reduced. From the above, it has been found that iron powder in the bond flux is an essential component and cannot be removed in order to obtain a stable back bead shape, penetration and high welding efficiency in high-speed single-side welding.

Therefore the results of investigations of the bonded flux chemical composition assuming bonded flux of iron powder added type, by optimizing _{TiO 2, SiO 2, MgO,} CaO, Al 2 O 3, the slag composition such as CaF ₂ We succeeded in reducing iron grain protrusions. However, only by optimizing these slag compositions, the iron grain protrusions could not be completely eliminated, and the slag composition was further examined.

As a result, it was found that when TiO ₂ is contained in the slag composition, the slag tends to stick to the bead surface and the generation of iron grain protrusions is promoted. Therefore, in order not to contain TiO _2, we succeeded in significantly reducing iron grain protrusions by applying raw materials not containing TiO ₂ as much as possible.

However, TiO ₂ is an essential component for welding materials as a component for maintaining arc stability and bead smoothness. By removing TiO ₂ , iron grain protrusions decreased, but arc stability deteriorated. In addition, a tendency to disturb the bead shape was observed. In addition, TiO ₂ is an important nucleation site that generates Ti oxide and the like in the form of weld metal structure and generates fine crystal grain acicular ferrite effective in improving strength and toughness. Therefore, the removal of TiO ₂ eliminated the nucleation site for generating acicular ferrite, and the tendency for weld metal toughness to decrease was recognized.

In order to solve these problems, the slag composition was further examined by adding ZrO ₂ and metal Ti. ZrO ₂ is similar to TiO _{2 in} that it has the effect of improving arc stability and bead smoothness, and no slag sticking is observed, and the bead heel end is well adapted and slag peelability is good. It was recognized that

  Nucleation for generating acicular ferrite was made possible by adding a small amount of metal Ti, and it was found that weld metal toughness was improved.

  By optimizing the above flux chemical composition, the iron grain protrusions on the surface bead surface were greatly reduced, and it became possible to obtain excellent weld metal mechanical performance. In welding, the iron grain protrusion on the surface bead surface could not be completely eliminated.

  Therefore, the present inventors paid attention to the particle size of the iron powder raw material used for the Fe component of the bond flux as a further improvement of the iron particle protrusion, and by adjusting the particle size of the iron powder raw material, It was found that a good front bead shape and appearance can be obtained.

Furthermore, it became clear that the shape of a surface bead became convex when the plate | board thickness of a steel plate became thick, and further examination was performed. As a result, it was found that by adjusting the amounts of MgO, Al ₂ O ₃ and SiO ₂ , the surface bead shape is improved even in the welding of thick steel plates.

That is, multi-electrode submerged arc welding bonded flux according to the present invention, in _{mass%, SiO 2: 5~24%,} MgO: 12~30%, CaO: 3~15%, Al 2 O 3: 5~ 17%, CaF ₂ : 7 to 19%, ZrO ₂ : 0.5 to 5%, B ₂ O ₃ : 0.1 to 3%, CaCO ₃ and MgCO ₃ of one or two kinds of CO ₂ conversion value Total: 2-7%, Fe: 10-35%, Si: 0.3-4%, Mn: 0.3-1%, Mo: 0.1-3%, Ti: 0.1-3% Others are composed of alkali metal oxides and inevitable impurities. At this time, it may further contain Al: 0.05 to 0.5% by mass%. In addition mass%, TiO _2: may be 1.5% or less, an average particle size of the iron powder raw materials used in the Fe component may be a 150μm or less.

  The reasons for limiting the flux component composition of the bond flux for multi-electrode single-sided submerged arc welding to which the present invention is applied and the particle size configuration of the iron powder raw material used for the Fe component will be described below. The content of each component is expressed by mass% with respect to the total mass of the bond flux for multi-electrode single-sided submerged arc welding, and when expressing the mass%, it is simply expressed as%.

(SiO _2: 5~24%)
SiO ₂ using silica sand, zircon sand, wollastonite, water glass (sodium silicate, potassium silicate), etc. as a raw material is an important component for forming a good weld bead. The amount increases and the toughness deteriorates. If the SiO ₂ content is less than 5%, the fit of the bead heel ends is deteriorated, the slag peelability is deteriorated, and undercutting also occurs particularly in high-speed single-side welding. On the other hand, if SiO ₂ exceeds 24%, the oxygen content of the weld metal increases and the toughness decreases. Thus, SiO ₂ is set to 5-24%.

(MgO: 12-30%)
MgO using magnesia clinker, magnesium carbonate, or the like as a raw material has the effect of improving the fire resistance and basicity of the slag and reducing the oxygen content of the weld metal. When MgO is less than 12%, the basicity of the flux is lowered, the amount of oxygen in the weld metal is increased, and the toughness is lowered. On the other hand, if MgO exceeds 30%, the softening and melting point of the flux becomes high, the waviness of the bead surface becomes rough, and the slag peelability and bead appearance become poor. Therefore, MgO is 12-30%.

(CaO: 3 to 15%)
CaO using wollastonite, calcium carbonate or the like as a raw material is an important component for adjusting the melting point and fluidity of slag. If the CaO content is less than 3%, the bead collar will not fit well and the bead appearance will be poor, and undercut will also occur in high-speed single-sided welding. On the other hand, if CaO exceeds 15%, the slag fluidity becomes poor, the bead height is uneven, and the slag peelability becomes poor. Therefore, CaO is 3 to 15%.

(Al ₂ O ₃ : 5 to 17%)
Al ₂ O ₃ mainly composed of alumina is an extremely important component for obtaining good slag removability and bead appearance by high-speed single-side welding. It also has the effect of improving the arc stability. If Al ₂ O ₃ is less than 5%, the effect cannot be obtained. On the other hand, if Al ₂ O ₃ exceeds 17%, it becomes a convex bead and the slag peelability becomes poor. Accordingly, Al ₂ O ₃ is set to 5 to 17%.

(CaF ₂ : 7 to 19%)
CaF ₂ using fluorite as a raw material is effective in improving toughness, but since the melting point is low, if it is excessive, the smoothness of the beads is impaired. When CaF ₂ is less than 7%, there is no effect of improving toughness, and when it exceeds 19%, the bead appearance becomes poor. Therefore, CaF ₂ is set to 7-19%.

(ZrO ₂ : 0.5 to 5%)
ZrO ₂ using zircon sand, zircon oxide, or the like as a raw material is an extremely important component for obtaining arc stability, good bead shape / appearance, and slag peelability by high-speed single-side welding. If ZrO ₂ is less than 0.5%, the effect cannot be obtained. On the other hand, if ZrO ₂ exceeds 5%, the oxygen content of the weld metal increases and the toughness deteriorates. Therefore, ZrO ₂ is 0.5 to 5%.

(B ₂ O ₃ : 0.1 to 3%)
B ₂ O ₃ made from boron oxide, borax or the like is effective in improving toughness. If B ₂ O ₃ is less than 0.1%, the effect of improving toughness cannot be obtained, and if it exceeds 3%, the weld metal is hardened and the toughness is lowered. Therefore, B ₂ O ₃ is 0.1 to 3%.

(Total of one or two kinds of CO ₂ converted values of CaCO ₃ and MgCO ₃ : 2 to 7%)
CO ₂ from CaCO ₃ (calcium carbonate) and MgCO ₃ (magnesium carbonate) is an important element for stabilizing the arc and improving the toughness of the weld metal. During welding, CaCO ₃ and MgCO ₃ are decomposed to produce CO 2. Alternatively, the CO ₂ gas stabilizes the arc and lowers the nitrogen partial pressure in the arc atmosphere, thereby reducing the amount of nitrogen in the weld metal. If the total of one or two types of CO ₂ equivalents of CaCO ₃ and MgCO ₃ is less than 2%, the arc is unstable and the shape and appearance of the front bead are particularly poor, and the nitrogen of the weld metal is increased and the toughness is increased. descend. On the other hand, if the total of one or two kinds of CO ₂ converted values of CaCO ₃ and MgCO ₃ exceeds 7%, CO or CO ₂ gas becomes excessive and a pock mark is generated on the bead surface. Therefore, the total of one or two CO ₂ converted values of CaCO ₃ and MgCO ₃ is 2 to 7%.

(Fe: 10 to 35%)
Fe using iron powder and iron alloys such as Fe-Si, Fe-Mn, and Fe-Mo as raw materials is effective in improving welding efficiency and arc concentration. If Fe is less than 10%, the welding efficiency is lowered and the arc concentration is inferior, so that the bead shape of the back bead becomes unstable. On the other hand, if the Fe content exceeds 35%, iron grain protrusions are generated on the bead surface, the slag sticks and the slag peelability becomes poor. Therefore, Fe is 10 to 35%.

(Average particle size of iron powder raw material used for Fe component: 150 μm or less)
The particle size of the iron powder raw material used for the Fe component is an important factor for completely eliminating iron grain protrusions on the bead surface in high-speed and continuous long-time welding. In order not to generate iron grain protrusions on the bead surface, it is necessary to make the iron powder melt into the molten metal at an early stage of welding, and it is improved to some extent by limiting the overall particle size of the flux to the optimum configuration However, it is preferable to apply a finer particle size of the iron powder raw material to be applied, and the average particle size is desirably 150 μm or less. However, in the present invention, it is not essential that the average particle diameter of the iron powder raw material is 150 μm or less, and even if it exceeds this, the desired effect is exhibited.

(Si: 0.3-4%)
Si using metal Si, Fe-Si, Fe-Si-Mn, or the like as a raw material is a deoxidizing element and reduces the oxygen content of the weld metal. If Si is less than 0.3%, the deoxidation effect cannot be obtained, and the toughness decreases. On the other hand, when Si exceeds 4%, the yield is excessively increased in the weld metal, the strength is increased, and the toughness is lowered. Therefore, Si is 0.3 to 4%.

(Mn: 0.3 to 1%)
Mn using metal Mn, Fe—Mn, Fe—Si—Mn, or the like as a raw material is a deoxidizing element like Si, and reduces the oxygen content of the weld metal. If Mn is less than 0.3%, the deoxidizing effect cannot be obtained and the toughness is lowered. On the other hand, if Mn exceeds 1%, the yield is excessively increased in the weld metal, the strength is increased, and the toughness is lowered. Therefore, Mn is set to 0.3 to 1%.

(Mo: 0.1 to 3%)
Mo made of metal Mo and Fe—Mo is an important component as an element for increasing the hardenability of weld metal. If Mo is less than 0.1%, the strength of the weld metal is lowered and there is no effect in improving toughness. On the other hand, if Mo exceeds 3%, the hardenability of the weld metal becomes excessive, the strength increases, and the toughness decreases. Therefore, Mo is 0.1 to 3%.

(Ti: 0.1-3%)
Ti using metal Ti, Fe-Ti, etc. as a raw material is important to generate Ti oxides and the like in the weld metal microstructure, and to produce fine crystalline acicular ferrite effective in improving strength and toughness. It becomes a nucleation site. If Ti is less than 0.1%, acicular ferrite effective for improving toughness cannot be produced, and the toughness decreases. On the other hand, if Ti exceeds 3%, the strength of the weld metal increases and the toughness decreases. Therefore, Ti is 0.1 to 3%.

(Al: 0.05-0.5%)
Al is a strong deoxidizer, and the thickness of the steel plate to be welded is thick, and the toughness of the weld metal can be ensured in welding with high heat input. If Al is less than 0.05%, the effect of securing toughness during welding with high heat input cannot be obtained. On the other hand, if Al exceeds 0.5%, it excessively remains in the weld metal as an oxide and lowers the toughness of the weld metal. Therefore, Al is desirably 0.05 to 0.5%. However, in the present invention, it is not essential that the Al content is 0.05 to 0.5%, and even if it deviates from this, the desired effect can be obtained.

(TiO ₂ : 1.5% or less)
TiO ₂ is an effective component for maintaining arc stability and bead smoothness, but it is also a component that facilitates slag sticking to the bead surface and promotes the generation of iron grain protrusions. Therefore, the content of TiO ₂ as an impurity in each raw material is preferably as low as possible, and the content is desirably 1.5% or less. However, in the present invention, it is not essential that the content of TiO ₂ is 1.5% or less, and even if it exceeds this, the desired effect can be obtained.

Others are alkali metal oxides such as K ₂ O and Na ₂ O from water glass: 5% or less and inevitable impurities such as P and S. Both P and S produce a low melting point compound to improve toughness. Since it reduces, it is preferable that it is as low as possible.

  In the single-side welding using the bond flux for multi-electrode single-sided submerged arc welding according to the present invention, the wire diameter to be combined is 4 in order to perform welding that enables stable arc, wire feedability, and improved welding efficiency. 0 to 6.4 mm, and applied to multi-electrode single-sided submerged arc welding with 3 or more electrodes.

  Hereinafter, the effect of the present invention will be described in more detail with reference to examples.

  Table 4 shows the bond flux adjusted for the particle size of the iron powder raw material applied to the various flux components and Fe components shown in Table 1, the back flux of the chemical composition shown in Table 2, and the wire of the chemical composition shown in Table 3. A steel plate symbol A having a thickness of 25 mm having a chemical composition was processed into a groove shape having a groove angle of 50 ° and a root face of 5 mm as shown in FIG. 1 (3 electrodes) or condition no. The FCuB single-sided submerged arc welding test shown in FIG. 1 was carried out under welding conditions of 2 (4 electrodes).

  In this FCuB single-sided submerged arc welding test, about 4 to 7 mm of back flux having the composition shown in Table 2 is sprayed on the backing copper plate, air is sucked into the air hose 3, and this is the back side of the steel plate 4 to be welded. Press against the groove back surface 4a. And the front bead and the back bead are formed simultaneously by spraying the front flux 6 from the front side using 2 to 4 wires 5 and welding one layer.

  The bond flux shown in Table 1 was granulated with water glass as a fixing agent, then baked at 400 to 550 ° C. for 2 hours, and sized to 1.4 × 0.15 mm.

  In addition, the wires shown in Table 3 were used by drawing the raw wires to 4.8 mm and 6.4 mm diameters by reducing the diameter, annealing, pickling, and copper plating to form the strands.

  Each prototype bond flux was evaluated under the condition no. 1 or condition no. Investigate the arc stability during single-sided submerged arc welding according to 2, the slag peelability after welding, the presence or absence of undercut, the presence of iron grain protrusions and slag sticking on the surface bead surface, the bead appearance and shape, and the tension of the weld metal The strength, toughness and weld metal oxygen content were investigated.

  The mechanical performance evaluation of the weld metal was performed by taking a Charpy impact test piece (JIS Z2242 V-notch test piece) and a tensile test piece (JIS Z2241 No. 10) around the center of the thickness of the steel plate of the weld specimen. Carried out. The toughness was evaluated by a Charpy impact test at −20 ° C., and evaluated by the average of 3 repetitions. The absorbed energy in the Charpy impact test was 80 J or more. Evaluation of tensile strength made 490-690 MPa favorable. The results of these surveys are summarized in Table 6.

Flux symbols F1 to F10 in Tables 1 and 6 are examples of the present invention, and flux symbols F11 to F24 are comparative examples. Flux symbols F1, F2, F4 to F6, F8, and F9, which are examples of the present invention, are suitable in terms of the average particle size of the flux component and the iron powder raw material, so that the arc stability is achieved in either one-sided submerged arc welding with three electrodes or four electrodes. And the slag peelability was good, there was no iron grain protrusion and slag sticking on the front bead surface, both the front bead and the back bead had good bead shape and appearance, and the mechanical performance of the weld metal was also excellent, which was a very satisfactory result. . In addition, the flux symbols F3 and F7 had some iron powder protrusions because the average particle diameter of the iron powder raw material was large. In addition, since the flux symbol F10 has a large amount of TiO ₂ , iron grain protrusions and sticking slightly occurred on the surface bead surface, but there was no problem in practical use.

In the comparative example, the flux symbol F11 has a small amount of SiO ₂ , so that the conformity of the bead toe portion is poor and the slag peelability is poor and the undercut occurs. Moreover, since there is much Ti, the tensile strength of a weld metal became high and the absorbed energy was a low value.

Flux code F12, since SiO ₂ is large, amount of oxygen in the weld metal is large and the absorbed energy were low. Further, since TiO ₂ is large, slag little sticking to the bead surface was also slightly generated iron particle projection.

  Flux symbol F13 has a small amount of MgO, so the amount of oxygen in the weld metal is large and the absorbed energy is low. Moreover, since the average particle diameter of the iron powder raw material was large, some iron grain protrusions were generated on the surface bead.

  Since the flux symbol F14 has a large amount of MgO, the wavy surface of the bead surface becomes rough, and the slag peelability and the bead appearance deteriorate. Further, since the amount of Si was small, the amount of oxygen in the weld metal was large and the absorbed energy was low.

  Flux symbol F15 has a small amount of CaO, so that the familiarity of the toe end of the bead is poor and the bead appearance is poor and undercutting occurs. Moreover, since there is much Si, the tensile strength of a weld metal became high and the absorbed energy was a low value. Since the flux symbol F16 contains a large amount of CaO, the bead appearance and slag peelability were poor. Further, since Mn is small, the amount of oxygen in the weld metal is large and the absorbed energy is low.

Flux symbol F17 had little Al ₂ O ₃ , so the arc became unstable, and the slag peelability and bead appearance were poor. Moreover, since there was much Mn, the tensile strength of the weld metal became high and the absorbed energy was low.

Since the flux symbol F18 has a large amount of Al ₂ O ₃ , the bead shape and slag removability were poor. Moreover, since there is little Mo, the tensile strength and absorbed energy of the weld metal were low values.

Flux code F19, because CaF ₂ is small, the absorbed energy of the weld metal was low. Further, since the amount of Fe was small, the amount of welding was small, the front bead shape was poor, and the arc concentration was poor, so the bead shape of the back bead was also unstable. Flux symbol F20 had a poor bead shape because of the large amount of CaF ₂ . Moreover, since there is much Mo, the tensile strength of the weld metal was high and the absorbed energy was low.

Flux symbol F21 had low ZrO ₂ , so the arc was unstable and the bead shape / appearance and slag peelability were poor. Further, since Ti is small, the absorbed energy of the weld metal was low.

Since the flux symbol F22 has a large amount of ZrO ₂ , the amount of oxygen in the weld metal is large and the absorbed energy is low. Further, since the total of one or two kinds of CO ₂ converted values of CaCO ₃ and MgCO ₃ was small, the arc was unstable and the bead shape / appearance was poor.

Since the flux symbol F23 has a small amount of B ₂ O ₃ , the absorbed energy of the weld metal was low. Further, since the total of one or two kinds of CO ₂ converted values of CaCO ₃ and MgCO ₃ was large, a pock mark was generated on the bead surface, and the shape and appearance of the front bead were poor.

Since the flux symbol F24 has a large amount of B ₂ O ₃ , the tensile strength of the weld metal was high and the absorbed energy was low. Moreover, since there was much Fe, the iron particle protrusion generate | occur | produced on the bead surface, slag stuck, and slag peelability was also unsatisfactory.

  Table 4 shows the bond flux adjusted in particle size of the iron powder raw material applied to the various flux components and Fe components shown in Table 7, the back flux of the chemical composition shown in Table 2, and the wire of the chemical composition shown in Table 3. A steel plate symbol B having a thickness of 40 mm having a chemical composition was processed into a groove shape having a groove angle of 50 ° and a root face of 5 mm as shown in FIG. The FCuB single-sided submerged arc welding test shown in FIG. 1 was performed under the welding conditions of 3 (4 electrodes). The details of the FCuB single-sided submerged arc welding test method are the same as in Example 1.

  Each prototype bond flux was evaluated under the condition no. Investigate arc stability during single-sided submerged arc welding according to No. 3, slag peelability after welding, presence of undercut, presence of iron grain protrusions and slag sticking on the surface bead surface, bead appearance and shape, and tensile of weld metal The strength, toughness and weld metal oxygen content were investigated.

  The mechanical performance evaluation of the weld metal was performed by taking a Charpy impact test piece (JIS Z2242 V-notch test piece) and a tensile test piece (JIS Z2241 No. 10) around the center of the thickness of the steel plate of the weld specimen. Carried out. The toughness was evaluated by a Charpy impact test at −20 ° C., and evaluated by the average of 3 repetitions. The absorbed energy in the Charpy impact test was 80 J or more. Evaluation of tensile strength made 490-690 MPa favorable. These survey results are summarized in Table 8.

  Flux symbols F25 to F28 in Tables 7 and 8 are examples of the present invention, and flux symbols F29 to F32 are comparative examples. Since the flux symbols F25 to F28, which are examples of the present invention, have an appropriate average particle size of the flux component and the iron powder raw material, arc stability and slag peelability are good in single-sided submerged arc welding with four electrodes with large heat input. There was no iron grain protrusion and slag sticking on the surface of the front bead, both the front bead and the back bead had good bead shape and appearance, and the mechanical performance of the weld metal was excellent, which was a very satisfactory result.

  Since flux symbol F29 in the comparative example does not contain Al, the absorbed energy of the weld metal was low.

  Since the flux symbol F30 has a large amount of Al, the absorbed energy of the weld metal was low.

Since the flux symbol F31 has a large amount of TiO ₂ , the slag sticks a little on the bead surface, and a few iron grain protrusions are generated. Moreover, since there is little Al, the absorbed energy of the weld metal was low.

  In the flux symbol F32, since the average particle diameter of the iron powder raw material is large, some iron grain protrusions were generated on the front bead. Moreover, since there is much Al, the absorbed energy of the weld metal was low.

1 Back copper plate 2 Back flux 3 Air hose 4 Welded steel plate 4a Groove back 5 Wire 6 Front flux

Claims (4)

% By mass
SiO ₂ : 5 to 24%,
MgO: 12-30%,
CaO: 3 to 15%,
Al ₂ O ₃ : 5 to 17%,
CaF ₂ : 7 to 19%,
ZrO ₂ : 0.5 to 5%,
B ₂ O ₃ : 0.1 to 3%,
Sum of 1 or 2 types of CO ₂ converted values of CaCO ₃ and MgCO ₃ : 2 to 7%,
Fe: 10 to 35%,
Si: 0.3 to 4%
Mn: 0.3 to 1%
Mo: 0.1 to 3%,
A bond flux for multi-electrode single-sided submerged arc welding characterized by containing Ti: 0.1 to 3% and the other consisting of an alkali metal oxide and inevitable impurities. % By mass
The bond flux for multi-electrode single-sided submerged arc welding according to claim 1, further comprising Al: 0.05 to 0.5%. % By mass
TiO _2: 1.5% claim 1 or 2 multielectrode sided submerged arc welding bonded flux, wherein the less.   4. The bond flux for multi-electrode single-sided submerged arc welding according to claim 1, wherein an average particle diameter of the iron powder raw material used for the Fe component is 150 μm or less. 5.

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