KR101153572B1 - Flux cored wire - Google Patents

Abstract

An object of the present invention is to provide a flux-embedded wire excellent in high temperature crack resistance, welding workability, and mechanical properties of a weld metal.
The flux-embedded wire is filled with flux in a steel outer sheath, the flux filling rate relative to the total mass of the wire is 10 to 25% by mass, C: 0.03 to 0.08% by mass, Si: 0.10 to 1.00% by mass, Mn: 2.4 to 3.7 mass%, Ti: 0.15 to 1.00 mass%, TiO ₂ : 5.0 to 8.0 mass%, Al: 0.20 to 0.50 mass%, Al ₂ O ₃ : 0.05 to 0.50 mass%, B: 0.003 to 0.020 mass %, The remainder being made of Fe and unavoidable impurities, and satisfying the relational formula of (4 x Ti + 10 x Al-3 x Si)> 1.0, wherein (Ti) represents Ti and TiO Ti amount is calculated from only _two of the Ti.

Description

Flux built-in wire {FLUX CORED WIRE}

The present invention relates to a flux-embedded wire applied to gas shielded arc welding of a steel sheet made of mild steel, high tensile strength steel, or the like.

Conventionally, what has the following structures is proposed for the flux built-in wire applied to the gas shield arc welding of a steel plate. For example, Patent Document 1 discloses a predetermined amount of TiO ₂ , SiO ₂ , ZrO ₂ , CaO, Na ₂ O, K ₂ O, F, C, Si, Mn, Al, in mass% relative to the total mass of the wire. Proposed flux-cored wire for gas shielded arc welding containing Mg, P, S, B, Bi, the remainder being made of Fe and unavoidable impurities, and Na ₂ O + K ₂ O, Mn / Si, Al + Mg It is.

Japanese Patent Application Publication No. 2006-289404

However, since the wire described in Patent Document 1 does not contain Ti and has a small content of Mn, there is a problem that high temperature cracking occurs in the first layer welded portion in the one-sided butt welded joint of the steel sheet. In addition, since the wire does not contain Al ₂ O ₃ , the welding operation in all posture welding, such as bead deterioration in horizontal fillet welding, or bead dripping in upright welding, occurs. There is a problem that sex is degraded. Moreover, since the amount of Mn and B of a wire is small, there also exists a problem that the mechanical property (toughness) of a weld metal deteriorates.

This invention is made | formed in view of the said subject, and an object of this invention is to provide the flux-cored wire which was excellent in high temperature crack resistance, welding workability, and the mechanical property of a weld metal.

In order to solve the said subject, the flux-cored wire which concerns on this invention is a flux-cored wire in which the flux was filled in the steel outer sheath, the flux filling rate with respect to the wire total mass is 10-25 mass%, and with respect to the wire total mass, C : 0.03 to 0.08 mass%, Si (total amount of Si calculated from all Si sources contained in the wire): 0.10 to 1.00 mass%, Mn (total amount of Mn amount calculated from all Mn sources contained in the wire): 2.4 To 3.7% by mass, Ti: 0.15 to 1.00% by mass, TiO ₂ : 5.0 to 8.0% by mass, Al: 0.20 to 0.50% by mass, Al ₂ O ₃ : 0.05 to 0.50% by mass, B: 0.003-0.020% by mass And the remainder is made of Fe and unavoidable impurities, and satisfies a relational formula of (4 x Ti + 10 x Al-3 x Si)> 1.0, wherein (Ti) is the Ti contained in the wire and ryangin that Ti which is calculated from only the Ti of the TiO ₂ And a gong.

According to the above structure, the flux filling rate with respect to the total mass of the wire is a predetermined amount, and welding is carried out by containing a predetermined amount of C, Si, Mn, Ti, TiO ₂ , Al, Al ₂ O ₃ and B with respect to the total mass of the wire. At the time, spatter generation and fume generation are suppressed, slag peelability is improved, mechanical properties of the weld joint (welding metal) are improved, and high temperature cracking at the superlayer weld is suppressed. In addition, Ti amount, Al amount, and Si amount satisfy a predetermined relationship, that is, (4 x Ti + 10 x Al-3 x Si)> 1.0, so that Ti contributes to the deoxidation reaction during welding and is produced in the weld metal. The composition of the inclusions can be controlled by a Ti-based oxide composition effective for promoting nucleation. As a result, the solidification structure of a weld metal can be refined | miniaturized and the suppression effect of a high temperature crack improves.

According to the flux-cored wire according to the present invention, the flux filling rate is a predetermined amount, contains a predetermined amount of C, Si, Mn, Ti, TiO ₂ , Al, Al ₂ O ₃ , B, and is contained in the flux-embedded wire. By satisfy | filling a predetermined relationship with Ti amount, Al amount, and Si amount, it is excellent in the high temperature crack resistance in the first layer welding part of a single side butt-weld joint, and welding workability (including a bead appearance) in all posture welding, and The mechanical properties of the weld metal become excellent. As a result, it is possible to provide a welded product of excellent quality.

1 (a) to 1 (d) are cross-sectional views showing the configuration of the flux-cored wire according to the present invention.
2 is a cross-sectional view showing an improved shape of a weld base metal used for evaluation of high temperature crack resistance.

The flux-embedded wire which concerns on this invention is demonstrated in detail. (A)-(d) is sectional drawing which shows the structure of a flux built-in wire.

As shown to Fig.1 (a)-(d), the flux-cored wire (henceforth a wire) 1 is the steel outer shell 2 formed in the cylindrical shape, and the flux 3 filled in the cylinder. ) In addition, the wire 1 is a seamless type in which the flux 3 is filled in the seamless casing 2 of the steel outer shell 2 as shown in FIG. 1A, FIGS. 1B to 1D. Any form of seam type in which the flux 3 is filled in the container of the steel outer sheath 2 with the seam 4 as shown in FIG.

The wire 1 has a flux filling rate of a predetermined amount, contains a predetermined amount of C, Si, Mn, Ti, TiO ₂ , Al, Al ₂ O ₃ and B, and the remainder is made of Fe and unavoidable impurities. In addition, the Ti amount, Al amount and Si amount satisfy predetermined relations (specifically, (4 × Ti + 10 × Al-3 × Si) is equal to or larger than a predetermined value).

Below, the numerical range of a wire component (flux filling rate and component amount) is described with the reason for limitation. The flux filling rate defines the mass of the flux 3 to be filled in the steel sheath 2 as a ratio with respect to the total mass of the wire 1 (steel sheath 2 + flux 3). In addition, the component amount is represented by the sum total of the component amounts in the steel outer shell 2 and the flux 3, and the mass of each component contained in the wire 1 (steel outer shell 2 + flux 3) is wired. It is prescribed by the ratio with respect to the total mass of (1). In addition, among the components constituting the wire 1, C, Si, Mn, Ti, TiO ₂ , Al, Al ₂ O ₃ and B are specifically added from the steel shell 2 or from the flux 3. It does not matter, what is necessary is just to be added to at least one of the steel outer shell 2 and the flux 3.

(Flux filling rate: 10-25 mass%)

If the flux filling rate is less than 10% by mass, the stability of the arc deteriorates, the amount of spatter generated increases, and the workability of welding decreases. Moreover, when the flux filling rate exceeds 25 mass%, the disconnection of the wire 1, etc. generate | occur | produce, and productivity falls remarkably.

(C: 0.03-0.08 mass%)

C is added in order to ensure the hardenability of a weld part. When the amount of C is less than 0.03 mass%, the strength (tensile strength) and toughness (absorption energy) of the welded portion are insufficient due to lack of hardenability. Moreover, high temperature crack generate | occur | produces in a weld part (superlayer weld part) by low C amount. When the amount of C exceeds 0.08 mass%, the amount of spatters generated or the amount of fumes generated at the time of welding increases, and welding workability falls. Moreover, when there is much C amount of the steel material which is a to-be-welded material, C amount of a weld part (welding metal) increases. When C is a region causing a peritectic reaction, hot cracking tends to occur in the welded portion (superlayer welded portion). As the C source, for example, steel shell, alloy powder such as Fe-Mn, iron powder, or the like is used.

(Si: 0.10 to 1.00 mass%)

Si is added in order to ensure the ductility of a weld part, and to maintain bead shape. If the amount of Si is less than 0.10 mass%, the ductility (stretching) of a weld part will run short. In addition, the shape of the beads deteriorates, particularly, the beads flow in the upwardly advanced welding, and the welding workability is lowered. If the amount of Si exceeds 1.00 mass%, a high temperature crack will generate | occur | produce in a weld part (superlayer weld part). Here, the amount of Si is the sum total of the amount of Si computed from all the Si sources contained in the wire 1. As the Si source, for example, an alloy such as steel shell, Fe-Si, Fe-Si-Mn, fluorides such as K ₂ SiF ₆ , oxides such as zircon sand, silica sand, feldspar and the like are used.

(Mn: 2.4 to 3.7 mass%)

Mn is added in order to ensure the hardenability of a weld part. If Mn amount is less than 2.4 mass%, the hardenability of a weld part will run short and toughness will fall. Moreover, since the amount of MnS obtained by combining with S contained as an unavoidable impurity also becomes small, the suppression effect of the high temperature crack by MnS becomes small, and a high temperature crack arises in a weld part (superlayer weld part). When Mn amount exceeds 3.7 mass%, the intensity | strength of a weld part will become excessive and a toughness will become short. In addition, low temperature cracking occurs in the welded portion. Here, the amount of Mn is the sum of the amount of Mn calculated from all Mn sources contained in the wire 1. As the Mn source, for example, alloys such as steel sheath, Mn metal powder, Fe-Mn, and Fe-Si-Mn are used.

(Ti: 0.15 to 1.00 mass%, preferably 0.20 to 1.00 mass%)

Ti (metal Ti) is added in order to improve high temperature crack resistance of a welded part (superlayer welded part). Ti (metal Ti) contributes to the deoxidation reaction during welding, and the inclusion in the weld metal can be controlled by the Ti-based oxide composition, and as a result, the solidification structure of the weld (welding metal) can be made fine, and the weld (superlayer) The high temperature crack suppression effect of the weld portion is improved. When Ti amount (metal Ti) is less than 0.15 mass%, high temperature crack generate | occur | produces in a weld part (superlayer weld part). When Ti amount (metal Ti) exceeds 1.00 mass%, a weld metal reheating part will become hard and brittle bainite and martensite easily, and toughness will fall. Moreover, the spatter generation amount at the time of welding increases, and welding workability falls. In addition, as Ti source, alloy powders, such as a steel outer shell and Fe-Ti, are used, for example.

(TiO ₂ : 5.0 to 8.0 mass%)

TiO ₂ (Ti oxide) is added to ensure all posture weldability. In the TiO ₂ amount (Ti oxide) is less than 5.0% by mass, down to the bead is flowing from iphyang upward welding, the welding operability deteriorates. If the TiO ₂ amount (Ti oxide) is more than 8.0% by mass, the slag removability during welding away, the welding operability deteriorates. Moreover, the volume specific gravity of the flux 3 becomes small, and productivity falls. As the TiO ₂ source, for example, rutile or the like is used.

(Al: 0.20 to 0.50% by mass, preferably 0.20 to 0.40% by mass)

Al is a strong deoxidizer, and from the inclusions generated in the weld joint (welding metal), SiO ₂ made of Si, which is weaker in deoxidation than Al, is reduced, and the composition of the inclusion is a Ti-based oxide composition effective for promoting nucleation. Can be controlled. As a result, the solidification structure of a weld metal can be made fine. In addition, the amount of oxygen in the weld metal is lowered, the yield of Mn is stabilized, the high temperature crack suppression effect of the welded portion (superlayer welded portion) is improved, and the toughness is also stabilized. If Al amount is less than 0.20 mass%, deoxidation is not enough and a high temperature crack will generate | occur | produce in a weld part (superlayer weld part). Moreover, toughness also falls. When Al amount exceeds 0.50 mass%, the amount of spatters at the time of welding will increase, and welding workability will fall. As the Al source, for example, an alloy powder such as steel shell, Al metal powder, Fe-Al, Al-Mg, or the like is used.

(Al ₂ O ₃ : 0.05 to 0.50% by mass, preferably 0.05 to 0.40% by mass)

Al ₂ O ₃ is added to prevent beads from flowing in the bead shape in the horizontal fillet attitude and in the upright attitude. When the amount of Al ₂ O ₃ is less than 0.05% by mass, the bead shape (affinity) in the horizontal fillet welding is bad, and the bead flow down occurs in the upwardly advanced welding, and the welding workability is lowered. When the amount of Al ₂ O ₃ exceeds 0.50% by mass, the slag removability during welding away, the welding operability deteriorates. As the Al ₂ O ₃ source, for example, complex oxides such as alumina and feldspar are used.

(B: 0.003-0.020 mass%)

Among B, dissolved B segregates at γ grain boundaries and has an effect of suppressing formation of cornerstone ferrite and is effective for improving the toughness of a weld metal. If the amount of B is less than 0.003 mass%, most B will be immobilized with nitride as BN, and there will be no effect which suppresses formation of a cornerstone ferrite, and a toughness improvement effect is not obtained. When the amount of B exceeds 0.020 mass%, the high temperature crack of a weld metal will generate | occur | produce easily. As the B source, for example, alloys such as Fe-B and atomized B are used.

[(4 × Ti + 10 × Al-3 × Si) ≥1.0]

By controlling the Ti amount (metal Ti) contained in the wire 1 within a predetermined range, Ti (metal Ti) contributes to the deoxidation reaction during welding, and nucleation of the composition of inclusions generated in the weld joint (welding metal). It can control with the inclusion of the Ti type oxide composition effective for promotion. As a result, the solidification structure of a weld metal can be made fine and a high temperature crack suppression effect can be remarkably improved. In addition, it is preferable that Ti-type oxide which is effective for promoting nucleation does not contain SiO ₂ which lowers the melting point of inclusions. In addition, Al is a strong deoxidizing agent, and has an effect of reducing SiO ₂ made of Si having a weaker deoxidizing power than Al, thereby controlling the composition of the inclusions as inclusions having a Ti-based oxide composition effective for promoting nucleation. Therefore, by defining the relationship between Ti amount (metal Ti), Al amount, and Si amount contained in the wire 1, the Ti-based oxide composition can be controlled to an effective composition by miniaturization of the solidification structure, and thus the solidification structure of the weld metal can be controlled. In the improvement of a high temperature crack suppression effect, it becomes controllable as a thing preferable.

If (4xTi + 10xAl-3xSi) <1.0, the solidification structure of a weld joint will not be refined. Therefore, (4xTi + 10xAl-3xSi) ≥1.0.

Here, Ti is an amount of Ti calculated only from the Ti (metal Ti) of the Ti and TiO ₂ contained in the wire 1, and is calculated from the TiO ₂ (Ti oxide) contained in the wire 1. Ti amount (converted) is not included.

In addition, (Si) is the sum total of the amount of Si computed from all the said Si sources contained in the wire 1. Further, the SiO ₂ is contained in the oxide, such as, for example, zircon sand, silica sand, feldspar is used as an Si source.

(Fe)

The remaining amount of Fe corresponds to Fe constituting the steel sheath 2 and / or Fe in the iron powder and the alloy powder added to the flux 3.

(Inevitable impurities)

S, P, Ni, O, Zr etc. are mentioned as an unavoidable impurity of a remainder, It is acceptable to contain in the range which does not prevent the effect of this invention. The amount of S, P, Ni, O, and Zr are preferably 0.050 mass% or less, respectively, and are the sum of the amounts of each component in the steel jacket 2 and the flux 3.

In addition, the steel outer shell 2 and the flux 3 select each component (amount of each component) of the steel outer shell 2 and the flux 3 so that the said wire component (component amount) may be in the said range at the time of wire manufacture. .

Moreover, Cu plating can also be given to the surface of the wire 1, and 0.35 mass% or less Cu may be contained with respect to the wire total mass.

[Example]

The flux-embedded wire according to the present invention will be specifically described by comparing an example that satisfies the requirements of the present invention with a comparative example that does not satisfy the requirements of the present invention.

Steel outer shell (steel contains C: 0.03% by mass, Si: 0.02% by mass, Mn: 0.25% by mass, P: 0.010% by mass, and S: 0.007% by mass, and uses a remainder containing Fe and unavoidable impurities ) And the wire 1 (Examples: No. 1 to 19, comparative example shown in FIG. 1 (b) of the wire diameter 1.2mm which consists of the wire component shown in Table 1, Table 2) by filling a flux inside : No. 20 to 40) were produced.

In addition, the wire component was measured and calculated by the following measuring methods.

The amount of C was measured by the "infrared absorption method". The amount of Si, the amount of Mn, and the amount of B melt | dissolve the whole wire quantity and measured by "ICP emission spectroscopy."

TiO ₂ amount (present as TiO ₂ and the like, Fe-Ti, etc. is not included) is measured by the "acid decomposition". The solvent used for the acid decomposition method melt | dissolved wire whole quantity using aqua regia. As a result, Ti source (Ti-Fe, etc.) contained in the wire (1), but is dissolved in aqua regia, TiO ₂ source (TiO _2, etc.) because it is insoluble for aqua regia, and remains dissolved. This solution was filtered using a filter (filter is 5C eye fineness), the filter residue was transferred to a nickel crucible and heated and gasified by a gas burner. Subsequently, an alkali flux (a mixture of sodium hydroxide and sodium peroxide) was added, and the residue was further heated by a gas burner to melt the residue. Next, after 18 mass% hydrochloric acid was added and the melt was liquefied, it transferred to the measuring flask, the pure water was further added, and the volume was made up, and the analysis liquid was obtained. Ti concentration in the analysis solution was measured by "ICP emission spectrometry". In terms of the Ti concentration of the TiO ₂ amount it was calculated the amount of TiO _2.

Ti amount (exists as Fe-Ti and the like, TiO ₂ and the like is not contained), the entire wire is dissolved in aqua regia by the "acid decomposition method", and the insoluble TiO ₂ source (TiO ₂ and the like) is filtered out, Since the solution can be made into Ti source (Fe-Ti etc.) contained in the wire 1, presence was calculated | required as Ti amount (Fe-Ti etc.) using "ICP emission spectroscopy."

The amount of Al ₂ O ₃ (exists as a composite oxide such as alumina or feldspar and does not include alloy powder such as Al metal powder) is measured by the "acid decomposition method". The solvent used for the acid decomposition method melt | dissolved wire whole quantity using aqua regia. As a result, although dissolution in the Al source is aqua regia (alloy powder, such as Al metal powder) contained in the wire (1), Al ₂ O ₃ source (the composite oxide, such as alumina or feldspar) is so insoluble for aqua regia, dissolution and Remains. This solution was filtered using a filter (filter is 5C eye fineness), the filter residue was transferred to a nickel crucible and heated and gasified by a gas burner. Subsequently, an alkali flux (a mixture of sodium hydroxide and sodium peroxide) was added, and the residue was further heated by a gas burner to melt the residue. Next, after 18 mass% hydrochloric acid was added and the melt was liquefied, it transferred to the measuring flask, the pure water was further added, and the volume was made up, and the analysis liquid was obtained. Al concentration in the analysis solution was measured by "ICP emission spectrometry". In terms of the Al concentration of the Al ₂ O ₃ amount, and it calculates the amount of Al ₂ O _3.

Al amount (exists as an alloy powder such as Al metal powder and does not include a composite oxide such as alumina or feldspar) is the Al ₂ O ₃ source (which was insoluble by dissolving the whole wire in the aqua regia by the acid decomposition method). Composite oxides such as alumina and feldspar) can be filtered and the solution can be made into an Al source (alloy powder such as Al metal powder) contained in the wire 1, thereby utilizing Al by using the "ICP Emission Spectroscopy". Presence was calculated | required as quantity (alloy powder, such as Al metal powder).

Using the produced wire 1, it evaluated about high temperature crack resistance, mechanical properties (tensile strength, absorbed energy), and welding workability by the method shown below. Based on the evaluation result, comprehensive evaluation of the wire 1 of an Example and a comparative example was performed.

(High Temperature Cracking Resistance)

Welding base material which consists of JIS G3106 SM400B steel (C: 0.12 mass%, Si: 0.2 mass%, Mn: 1.1 mass%, P: 0.008 mass%, S: 0.003 mass%, and remainder Fe and an unavoidable impurity) Was welded on one side under the welding conditions shown in Table 3 (downward butt welding).

It is sectional drawing which shows the improved shape of the welding base material used for evaluation of high temperature crack resistance. As shown in FIG. 2, the welding base material 11 has a V shape improvement, and the backing material which consists of a refractory material 12 made of ceramics, aluminum tape 13, etc. on the back surface of this V shape improvement is carried out. material is placed. And the improvement angle was 35 degrees, and the root spacing of the part in which the backing material is arrange | positioned was 4 mm.

After the completion of the welding, the first-layer welded portion (excluding the crater portion) was checked for the presence of internal cracks in the X-ray transmission test (JIS Z3104), the total length of the crack-producing portion was measured, and the crack ratio was calculated. Here, a crack ratio is computed by crack ratio W = (total length of a crack generation part) / [superlayer weld part length (except crater part)] x100. The high temperature crack resistance was evaluated by the crack rate. The results are shown in Tables 4 and 5.

The evaluation criteria are "excellent:" when the cracking rate is 0% at the welding current 240A and the cracking rate is 0% at the welding current 260A, and the cracking rate is 0% at the welding current 240A, and the cracking rate 10% at the welding current 260A. It was set as "good | favorableness: (circle)" and a crack at the welding current 240A, and a "fall: x" when there was a crack at the welding current 260A when below.

(Mechanical properties)

According to JIS Z3313, the tensile strength and 0 degreeC absorption energy (toughness) were evaluated. The results are shown in Tables 4 and 5.

In addition, the evaluation criteria of tensile strength were made into "excellent:" when it is 490 Mpa or more and 640 Mpa or less, and "falling: x" when it is less than 490 Mpa or more than 640 Mpa. In addition, the evaluation criteria of 0 degreeC absorption energy were made into "excellent: (circle)" when 60J or more, and "falling: x" when less than 60J. In addition, when evaluating an elongation rate according to JIS Z3313, the evaluation criteria were made into "excellent:" when it is 22% or more, and "falling: x" when it was less than 22%.

(Welding workability)

Using the same welding base material as the high temperature crack resistance, four types of welding were performed: downward fillet welding, horizontal fillet welding, upward-filled fillet welding, and downward-filled fillet welding. Here, the welding conditions of the downward fillet welding test, the horizontal fillet welding test, and the oriented welding test were made the same as the said high temperature crack resistance (refer Table 3). The welding conditions of the grain growth fillet welding test were welding currents of 200 to 220 A and arc voltages of 24 to 27 V. The results are shown in Tables 4 and 5.

The evaluation criteria were &quot; excellent: &quot; when no welding defects such as spatter generation, fume generation, bead dripping and bead appearance occurred, and &quot; falling: × &quot; when welding defects occurred.

(General evaluation)

The evaluation criteria of the comprehensive evaluation are "excellent: ◎" when the high temperature crack resistance is "◎" and the mechanical property and the welding workability are "○" among the above evaluation items, and the high temperature crack resistance is "○" and mechanical properties. And "good:" when the welding workability was "o", and "falling: x" when at least one of said evaluation items was "x". The results are shown in Tables 4 and 5.

As shown in Table 1 and Table 4, Examples (Nos. 1 to 19) are excellent in all of high temperature crack resistance, mechanical properties, and welding workability because all wire components satisfy the scope of the present invention (or It was good) and was excellent (or good) also in comprehensive evaluation.

As shown in Table 2 and Table 5, since the amount of C was less than a lower limit in Comparative Example (No. 20), high temperature crack resistance and mechanical properties were inferior, and comprehensive evaluation was also inferior. In the comparative example (No. 21), since the amount of C exceeded the upper limit, high temperature crack resistance and weldability were inferior, and comprehensive evaluation was also inferior. Since the amount of Si was less than a lower limit in Comparative Example (No. 22), welding workability and mechanical properties (stretching) were inferior, and comprehensive evaluation was also inferior. In Comparative Example (No. 23), since the amount of Si exceeded the upper limit, the high temperature crack resistance was inferior and overall evaluation was also poor.

Since the amount of Mn was less than a lower limit in Comparative Example (No. 24), high temperature crack resistance and mechanical properties were inferior, and overall evaluation was also inferior. In the comparative example (No. 25), since the Mn amount exceeded the upper limit, mechanical properties and welding workability were inferior, and overall evaluation was also inferior. Since the amount of Ti was less than a lower limit in Comparative Example (No. 26), high temperature crack resistance was inferior, and comprehensive evaluation was also inferior. In the comparative example (No. 27), since the Ti amount exceeded the upper limit, mechanical properties and welding workability were inferior, and overall evaluation was also inferior.

In Comparative Example (No. 28), since the TiO ₂ amount was less than the lower limit, welding workability was inferior, and comprehensive evaluation was also poor. Comparative Example (No.29) is, since the amount of TiO ₂ exceeds the upper limit, poor welding workability, was also off assessment. Since the amount of Al was less than a lower limit in Comparative Example (No. 30), high temperature crack resistance and mechanical properties were inferior, and overall evaluation was also inferior. Since the amount of Al exceeded the upper limit in the comparative example (No. 31), weldability was inferior and comprehensive evaluation was also inferior.

In the comparative example (No. 32), since the Al ₂ O ₃ amount was less than the lower limit, welding workability was inferior, and overall evaluation was also inferior. In the comparative example (No. 33), since the Al ₂ O ₃ amount exceeded the upper limit, welding workability was inferior and overall evaluation was also inferior. In Comparative Example (No. 34), since the amount of B was less than the lower limit, mechanical properties were inferior, and comprehensive evaluation was also inferior. In the comparative example (No. 35), since the amount of B exceeded the upper limit, high temperature crack resistance was inferior and comprehensive evaluation was also inferior. In Comparative Examples (Nos. 36 to 38), since (4xTi + 10xAl-3xSi) was less than the lower limit, high temperature crack resistance was inferior, and comprehensive evaluation was also poor. Since the flux filling rate of the comparative example (No. 39) was less than a lower limit, welding workability was inferior and comprehensive evaluation was also inferior. In the comparative example (No. 40), since the flux filling rate exceeded the upper limit, disconnection occurred during wire production, and was poor as a comprehensive evaluation.

From the above results, it was confirmed that Examples (Nos. 1 to 19) were superior as the flux-embedded wires 1 as compared to Comparative Examples (Nos. 20 to 40).

1: Flux embedded wire (wire)
2: forced shell
3: flux
4: seam
11: welding base material
12: refractory
13: aluminum tape

Claims (1)

Flux-embedded wire filled with flux in a steel sheath,
The flux filling rate with respect to the wire total mass is 10-25 mass%,
For the total mass of the wire,
C: 0.03-0.08 mass%,
Si (total amount of Si calculated from all Si sources contained in the wire): 0.10 to 1.00 mass%,
Mn (total amount of Mn calculated from all Mn sources contained in the wire): 2.4 to 3.7% by mass,
Ti: 0.15 to 1.00 mass%,
TiO ₂ : 5.0-8.0 mass%,
Al: 0.20-0.50 mass%,
Al ₂ O ₃ : 0.05 to 0.50% by mass,
B: 0.003-0.020 mass%
Containing, the remainder being made from Fe and unavoidable impurities,
In addition, (4 x Ti + 10 x Al-3 x Si) ≥ 1.0 is satisfied, and in the relation, (Ti) is an amount of Ti calculated only from the Ti among the Ti and TiO ₂ contained in the wire. Flux built-in wire, characterized in that.

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