JP4625415B2 - Solid wire for gas shielded arc welding - Google Patents

Solid wire for gas shielded arc welding Download PDF

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JP4625415B2
JP4625415B2 JP2006077030A JP2006077030A JP4625415B2 JP 4625415 B2 JP4625415 B2 JP 4625415B2 JP 2006077030 A JP2006077030 A JP 2006077030A JP 2006077030 A JP2006077030 A JP 2006077030A JP 4625415 B2 JP4625415 B2 JP 4625415B2
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JP2007253163A (en
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茂 大北
勇 木本
浩一 磯部
修 高木
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新日本製鐵株式会社
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Description

The present invention relates to a solid wire for gas shielded arc welding mainly used for gas shielded arc welding of high strength steel having a tensile strength of 490 to 780 N / mm 2 grade. The present invention relates to a solid wire for gas shielded arc welding that can stably ensure the toughness and strength of a weld metal even if multilayer welding is performed under conditions of high heat input and high-pass temperature, and has good welding workability.

  In general, gas shielded arc welding is frequently used in various industrial fields as a highly efficient welding method. In recent years, for the purpose of further improving the efficiency of gas shielded arc welding, continuous welding by increasing the current and heat input per welding pass and shortening the time between each welding pass has been required. Under such high current, high heat input, and welding conditions in which the temperature between the high passes increases due to the shortening of the time between weld passes, the toughness of the weld metal is reduced. It has been a conventional technical problem to improve toughness while maintaining it.

  Therefore, conventionally, a Ti-B welding wire is used as a welding wire for maintaining good strength and toughness of the weld metal when performing gas shielded arc welding under conditions of high current, high heat input, and high temperature between welding passes. Have been studied and some proposals have been made (for example, see Patent Documents 1 to 5).

For example, Patent Document 1 discloses that C, Si, Mn, Ti, and B are used for the purpose of improving low temperature toughness when gas shield arc welding is performed under conditions where the welding current is 600 A or more and the welding heat input is 20 to 60 kJ / cm. A high-efficiency gas shielded arc welding wire has been proposed in which the content is specified and the parameter Pa (= Ti × B × 10 4 ) determined based on the Ti and B content is limited to 1 to 25.

Patent Document 2 discloses a heat treatment (PWHT) after welding high-tensile steel of 588 N class (60 kgf class) steel or higher by gas shielded arc welding using a mixed gas such as Ar—CO 2 as a shielding gas. The content of C, Si, Mn, Ti and B is specified in order to suppress a decrease in low temperature toughness that sometimes occurs, and in order to further improve the strength and toughness, any one or more of Ni, Cr and Mo A Ti-B high strength steel melt wire excellent in low temperature toughness containing a low amount of these elements has been proposed. Furthermore, in Patent Document 3, the content of C, Si, Mn, B, O, S, and N is specified, and a welding steel wire containing Ti and / or Mo in order to improve low-temperature toughness. Has been proposed.

On the other hand, Patent Document 4 defines the contents of C, Si, Mn, Ti, Mo, O, S, P and N, and further contains one or more elements of B, Al and N. A low alloy steel wire for gas shielded arc welding is disclosed. Further, Patent Document 5 discloses C, Si, Mn, Ti, B and S as carbon dioxide welding wires for welding under conditions of high heat input and high pass temperature of mild steel or 490 N / mm grade 2 high strength steel. The parameter P BT (= [B] × 10 3 / [Ti]) consisting of the relationship between the Ti and B contents, and the P BS consisting of the relationship between the Ti and B contents (= [B] × [S] × 10 5 ) and a wire for gas shielded arc welding in which the contents of Al, Cr, Mo, Cu, and P, which reduce toughness among inevitable components, are limited. Yes. Thus, conventionally, various welding wires have been developed and proposed for the purpose of improving the toughness of weld metal under high heat input welding conditions in gas shielded arc welding.

JP 54-40250 A JP-A 63-157795 JP 55-149797 Japanese Patent Publication No. 4-20720 JP-A-10-230387

  However, the conventional welding wires such as the welding wires described in Patent Documents 1 to 5 described above have a problem that the effect cannot be obtained sufficiently stably depending on the welding conditions. In particular, when multi-pass welding is performed under conditions of high current, high heat input, and high pass temperature by gas shielded arc welding, the strength and toughness of the weld metal can be stably and sufficiently improved with conventional welding wires. It is difficult.

The present invention has been made in view of the above problems, and has a high current, a high heat input, a high pass when gas-shielded arc welding is performed on a high strength steel having a tensile strength of 490 to 780 N / mm 2 grade. To provide a solid wire for gas shielded arc welding that can stably secure a weld metal with excellent toughness and strength, and that has good welding workability even when performing at high efficiency under welding conditions at intermediate temperatures. Objective.

  The solid wire for gas shielded arc welding according to the present invention is, in mass%, C: 0.02 to 0.14%, Si: 0.4 to 1.5%, Mn: 1.0 to 2.5%, Ti: 0.05-0.4%, Mg: 0.0003-0.010% and B: 0.0005-0.010%, and one or more selected from the group consisting of Al and Zr The total content of two or more elements is 0.005 to 0.050%, N is limited to 0.005% or less, the balance is Fe and inevitable impurities, and the total content of Si and Mn is 1. It is 5 to 3.5%, and the ratio (Mn / Si) of Mn content (%) and Si content (%) is 0.85 or more.

  This solid wire for gas shielded arc welding is further, in mass%, Cu: 0.3-1.5%, Ni: 0.3-3.0%, Cr: 0.1-1.5% and Mo : One or two or more elements selected from the group consisting of 0.1 to 1.5% may be contained in total of 5.0% or less.

  According to the present invention, when performing gas shielded arc welding under welding conditions of high current, high heat input, and high pass temperature, it is possible to obtain a weld metal having excellent workability and excellent tensile strength and stable toughness. Therefore, it is possible to improve the efficiency of welding and improve the quality of the welded portion.

  Hereinafter, the best mode for carrying out the present invention will be described in detail. When gas shielded arc welding is performed under welding conditions of high current, high heat input, and high pass temperature, the most important issue in maintaining the quality of the weld metal is to suppress the deterioration of toughness due to coarsening of the weld metal structure. It is to be. Therefore, in the solid wire for gas shielded arc welding according to the present invention, the coarsening of the weld metal structure under such welding conditions is suppressed, and a toughness of 70 J or more is secured with Charpy absorbed energy at 0 ° C. And by regulating the content of Mg, the total content of Si and Mn, and the ratio of the Mn content to the Si content, the weld metal is sufficiently deoxidized and the formation of coarse ferrite is suppressed. In addition, the first technical idea is to generate fine acicular ferrite with a fine oxide of Ti as a nucleus in the crystal grains.

  In particular, the solid wire for gas shielded arc welding of the present invention is characterized in that it contains a predetermined amount of Mg. Since Mg has a low melting point and is easy to vaporize during welding, it hardly remains in the weld metal and does not affect the properties of the weld metal. It is added to the filler in the flux cored wire and the bond type flux for submerged arc welding.

  On the other hand, when Mg is added to the solid wire, the wire drawing workability of the steel material is lowered, so conventionally Mg has not been included in the solid wire. However, as a result of earnest experiments, the present inventor has found that a trace amount of Mg remaining in the weld metal is not obtained under the conditions of deoxidation and composition control of the weld metal by Ti, Si and Mn contained in the wire. A fine oxide is formed at high temperature, and this fine oxide serves as a nucleus to form a fine composite oxide containing Al, Ti, Si, etc., and fine acicular ferrite is formed in the crystal grains of the weld metal. It was confirmed that the refinement of the microstructure was promoted. Further, the present inventor suppresses the consumption due to oxidation of B by promoting the formation of fine oxides by Mg as described above, and improves the hardenability by B and the effects of suppressing coarse ferrite harmful to the toughness at the grain boundaries. Has also been confirmed to improve.

  In addition, when gas shielded arc welding is performed under the conditions of high current, high heat input, and high pass temperature described above, the molten pool at the time of welding becomes large due to heating. Nitrogen penetrates into the molten metal and causes a reduction in the toughness of the weld metal. For fixing N in this weld metal, B, which has a large diffusion coefficient in the metal, exhibits the most excellent effect. As described above, self-oxidation of Mg, Ti, Al and Zr prevents oxidation of B. The content of B effective for fixing N can be ensured.

  The solid wire for gas shielded arc welding of the present invention regulates the content of Al and / or Zr having a nitrogen fixing action in the same manner as Ti in order to suppress toughness deterioration due to nitrogen penetration into the weld metal. By fixing nitrogen in the weld metal as a nitride, the amount of solute N in the weld metal can be sufficiently reduced even under the above-described welding conditions, and toughness can be improved. This is the second technical idea.

Furthermore, in the solid wire for gas shielded arc welding according to the present invention, from the viewpoint of ensuring stable strength and toughness of the weld metal, an appropriate amount of Cu, Ni, Cr and Mo should be contained as a hardenable element. You can also. Thereby, when welding 490-780 N / mm 2 grade steel on the welding conditions mentioned above, favorable toughness can be ensured more stably, maintaining the tensile strength of a weld metal.

The solid wire for gas shielded arc welding of the present invention has been made based on the above knowledge and technical idea, and gas shielded from 490 to 780 N / mm grade 2 steel under welding conditions of high current, high heat input, and high pass temperature. When arc welding is performed, a weld metal having good toughness having a tensile strength of 4490 to 780 N / mm 2 and a Charpy absorbed energy at 0 ° C. of 70 J or more can be obtained.

  Hereinafter, the component composition of the solid wire for gas shielded arc welding of the present invention and the reasons for limitation of each component element will be described in detail. In the following description, “%” means “mass%” unless otherwise specified.

(C: 0.02-0.14%)
C is an element necessary for improving the strength of the weld metal by solid solution strengthening, but this effect cannot be obtained when the C content in the wire is less than 0.02%. On the other hand, if the C content exceeds 0.14%, the toughness of the weld metal is impaired in multi-layer arc welding with high current, high heat input, and high interpass temperature. In particular, when welding high-tensile steel such as 490 to 780 N / mm grade 2 steel, if the C content exceeds 0.14%, a phase harmful to toughness such as high carbon martensite is formed as the second phase. Or the tendency of martensite to harden in a low heat input weld such as tacking becomes strong. Therefore, the C content is 0.02 to 0.14%.

(Si: 0.4-1.5%)
Si is a main deoxidizer and is an element necessary for reducing the oxygen content of weld metal and improving toughness. In particular, since the consumption of Si is large in a high welding current region, a higher addition than usual is required. Specifically, when the Si content is less than 0.4%, deoxidation is insufficient, and a sound weld metal cannot be obtained, so that toughness is reduced and strength is reduced. On the other hand, when the Si content exceeds 1.5%, the strength of the weld metal is increased, coarse ferrite is generated in the weld metal, the microstructure of the weld metal is coarse ferrite, and the toughness is lowered. Moreover, when Si is contained excessively, the arc becomes unstable, the amount of spatter generated increases, and welding workability deteriorates. Therefore, the Si content is set to 0.4 to 1.5%.

(Mn: 1.0-2.5%)
Mn is a major deoxidizer like Si, and is an element that has the effect of ensuring the strength of the weld metal and further stabilizing the formation of austenite to improve the toughness of the weld metal. Mn also has the effect of stabilizing the arc, reducing the amount of spatter generated, and improving the welding workability. However, Mn, like Si, needs to consider oxidation consumption under high welding current conditions. Specifically, if the Mn content is less than 1.0%, the strength and toughness of the weld metal cannot be sufficiently secured. On the other hand, if the Mn content exceeds 2.5%, the strength of the weld metal is increased, and the weld metal is tempered and embrittled during multi-layer welding at a high heat input / high pass temperature, resulting in a decrease in toughness. Therefore, the Mn content is 1.0 to 2.5%.

(Si + Mn: 1.5-3.5%)
As described above, in arc welding under high current, high heat input, and high pass temperature conditions, the oxidation consumption of Si and Mn is large, so if these total contents are less than 1.5%, deoxidation is insufficient. And the strength and toughness of the weld metal are reduced. Moreover, since the arc state during welding becomes unstable, the amount of spatter generated increases and the welding workability deteriorates. On the other hand, if the total content of Si and Mn exceeds 3.5%, a hardened phase is generated in the weld metal part, the strength becomes too high, and the toughness decreases. Therefore, the total content of Si and Mn is 1.5 to 3.5%.

(Mn / Si: 0.85 or more)
When the ratio of the Mn content (%) to the Si content (%) is less than 0.85, the content of Si as a ferrite forming element is excessive as compared with the content of Mn as an austenite forming element. For this reason, coarse ferrite is generated in the microstructure of the weld metal, resulting in insufficient strength and toughness. Therefore, in order to ensure good strength and toughness of the weld metal, the ratio of Mn content to Si content (Mn / Si) is 0.85 or more.

(Ti: 0.05-0.4%)
Ti is a deoxidizer, and it produces a fine oxide of Ti in the weld metal, and uses this as a nucleus to produce fine acicular ferrite in the crystal grains, thereby improving the toughness of the weld metal. It is an important element. In multi-layered arc welding with high current, high heat input, and high pass temperature, in order to promote the formation of fine Ti oxide in weld metal and fine acicular ferrite, Mn, Si, etc. It is necessary to control the oxygen content of the weld metal to be low by a deoxidizing element other than Ti, and to contain 0.05% or more Ti. On the other hand, when the Ti content exceeds 0.4%, solid solution Ti remains in the weld metal, the weld metal is significantly hardened, and the toughness is significantly reduced. Therefore, the Ti content is set to 0.05 to 0.4%.

(Mg: 0.0003 to 0.010%)
Mg is an element having a deoxidizing action, like Si, Mn and Ti described above, and acts as a particularly strong deoxidizing agent among the deoxidizing elements. For this reason, a large molten pool is generated and oxygen penetration is increased, so even during multi-layer gas shielded arc welding with high current, high heat input, and high pass temperature, the weld metal is sufficiently deoxidized and toughness is improved. There is an effect to. In addition, Mg has a low melting point, so it hardly remains in the weld metal. However, under conditions where the weld metal is deoxidized and the composition is controlled by Ti, Si and Mn contained in the wire, If a very small amount of Mg remains, the Mg forms a fine oxide at a high temperature, and a fine composite oxide containing Al, Ti, Si and the like is formed using the fine oxide as a nucleus. Thereby, fine acicular ferrite is generated in the crystal grains of the weld metal, and the refinement of the microstructure is promoted. Further, since the consumption of B due to oxidation is suppressed by promoting the formation of fine oxides by Mg, the effects of improving hardenability by B and suppressing coarse ferrite harmful to toughness at grain boundaries are improved. However, when the Mg content is less than 0.0003%, these effects cannot be obtained sufficiently. On the other hand, if the Mg content exceeds 0.010%, the arc stability during welding decreases. Therefore, the Mg content is set to 0.0003 to 0.010%.

(Al, Zr: 1 type or 2 types in total 0.005 to 0.050%)
In multi-layer gas shielded arc welding under the welding conditions of high current, high heat input, and high pass temperature, the molten pool becomes large and sufficient shielding properties cannot be obtained. It easily penetrates and deteriorates the toughness of the weld metal. Both Al and Zr have the effect of binding to N in the weld metal to form nitrides and suppressing toughness degradation due to solute N in the weld metal. Moreover, both Al and Zr are deoxidizing elements having a strong affinity for oxygen, and also have the effect of reducing the amount of oxygen in the weld metal. Furthermore, when Al and Zr are contained in the weld metal, N and oxygen in the weld metal are reduced by the action of denitrification and deoxidation, and B consumption due to oxidation or nitridation is suppressed. Therefore, effects such as improvement of hardenability by B and suppression of coarse ferrite harmful to toughness at grain boundaries are improved. These effects become remarkable when one or two elements of Al and Zr are contained in total of 0.005% or more. On the other hand, if one or two elements of Al and Zr are contained in total exceeding 0.050%, the weld metal is hardened and the toughness is lowered. For these reasons, Al and / or Zr is made 0.005 to 0.050% in total.

(N: 0.005% or less)
N is an unavoidable impurity. In order to stably improve the toughness of the weld metal, it is essential to reduce the solid solution N in the weld metal. Specifically, when the N content exceeds 0.005%, the toughness of the weld metal decreases. Therefore, the N content is restricted to 0.005% or less.

(B: 0.0005 to 0.010%)
B is an element that contributes to improving the toughness of the weld metal by refining the weld metal structure by complex addition with Ti. In addition, B improves the hardenability of the weld metal when multi-layer gas shielded arc welding is performed on high-strength steel of 490 to 780 N / mm class 2 under conditions of high current, high heat input, and high pass temperature, It has the effect of suppressing the formation of coarse ferrite that is detrimental to toughness at grain boundaries. However, when the B content is less than 0.0005%, such an effect cannot be sufficiently obtained. On the other hand, when the B content in the weld metal is excessively high, specifically, when the B content exceeds 0.010%, the weld metal is hardened to cause a decrease in toughness. Cause. Therefore, the B content is set to 0.0005 to 0.010%. In addition, when welding 490 to 540 N / mm grade 2 high strength steel with relatively low strength, the hardenability of the weld metal may be lowered, and coarse ferrite is likely to be generated at the grain boundaries. The content is preferably 0.002% or more. Moreover, in order to suppress hardening of the weld metal by B, it is preferable to make B content 0.005% or less.

  The solid wire for gas shielded arc welding of the present invention may contain one or more elements selected from the group consisting of Cu, Ni, Cr and Mo in addition to the above components. Good.

(Cu: 0.3-1.5%)
Cu is an element effective for improving the strength by reducing the transformation temperature and making the structure finer, especially when welding high-strength steel, as well as extreme high current, high heat input, and high interpass temperature conditions. It also works effectively to improve toughness when welding with. However, when the Cu content is less than 0.3%, these effects cannot be obtained sufficiently. On the other hand, if the Cu content exceeds 1.5%, precipitation embrittlement occurs as in the case of Cr and Mo, and weld metal hot cracking occurs. Therefore, when adding Cu, the content is made 0.3 to 1.5%. For rust prevention, Cu plating may be applied to the surface of the wire in a range of about 0.2 to 0.3% with respect to the total mass of the wire. It is contained in Cu content in.

(Ni: 0.3-3.0%)
Ni is an element that lowers the transformation temperature to refine the structure and increases the strength without dissolving in the weld metal and lowering the toughness, and is generally used to obtain a high-strength weld metal. Element. However, when the Ni content is less than 0.3%, the effect of preventing the strength and toughness from being lowered cannot be sufficiently obtained during welding of high-strength steel or welding at high heat input / high pass temperature. On the other hand, if the Ni content exceeds 3%, the solidification temperature decreases at the solidification segregation part of the weld metal, and welding hot cracks occur. Therefore, when adding Ni, the content is made 0.3 to 3.0%.

(Cr: 0.1-1.5%)
Similar to Cu, Cr has the effect of reducing the transformation temperature to refine the structure and improve the strength. In particular, it effectively works to improve toughness when welding high-strength steel and when welding under conditions of extreme high current, high heat input, and high pass temperature. However, when the Cr content is less than 0.1%, these effects cannot be obtained sufficiently. On the other hand, when Cr is added alone and the content thereof exceeds 1.5%, the weld metal is hardened, resulting in an adverse effect on toughness. Therefore, when adding Cr, the content is made 0.1 to 1.5%.

(Mo: 0.1-1.5%)
Mo, like Cu and Cr, is an element effective in improving toughness by lowering the transformation temperature and refining the structure. In particular, when welding high-strength steel, and when welding under conditions of extreme high current, high heat input, and high pass temperature, it has softening resistance and effectively acts to improve toughness. However, when the Mo content is less than 0.1%, the effect cannot be sufficiently obtained. On the other hand, when Mo is added alone and the content exceeds 1.5%, the weld metal is hardened, resulting in an adverse effect on toughness. Therefore, when adding Mo, the content is made 0.1 to 1.5%.

(Cu, Ni, Cr, Mo: 1 type or 2 types or more in total of 5.0% or less)
When the content of one or more elements selected from the group consisting of Cu, Ni, Cr and Mo exceeds 5.0% in total, the weld metal is markedly hardened and the toughness is greatly reduced. For this reason, when adding Cu, Ni, Cr and / or Mo, while making content of each element into the above-mentioned range, the total content of these elements is regulated to 5.0% or less.

  Furthermore, the components other than those described above in the solid wire for gas shielded arc welding of the present invention, that is, the balance, are Fe and inevitable impurities. Among these inevitable impurities, P is preferable to have a content of 0.015% or less in order to reduce the toughness of the weld metal. Moreover, although S has the effect | action which improves the slag peelability of a welding part, in order to reduce the toughness of a weld metal, it is preferable to make the content into 0.020% or less.

  In addition, in the solid wire for gas shielded arc welding of the present invention, it is allowed that the wire contains a metal component other than the components described above, as long as the characteristics of the weld metal targeted by the present invention are not impaired. The For example, for the purpose of adjusting the strength and toughness of the weld metal, V and Nb can be added in the range of 0.005% or less, respectively.

  Hereinafter, the effects of the present invention will be described in detail by way of examples of the present invention. In this example, first, various raw steels were vacuum-melted and forged so as to have the compositions shown in Tables 1 to 3, and then rolled and drawn, and a 1.4 mm diameter 20 kg spool was wound. A wire was made. In addition, the remainder in the wire composition shown to the following Tables 1-3 is Fe and an unavoidable impurity. Moreover, the underline in the following Tables 1-3 shows that it is outside the scope of the present invention.

Next, using the wires of the examples and comparative examples shown in Tables 1 to 3 above, gas shield arc welding was performed on a 490 N / mm 2 grade steel plate with a plate thickness of 25 mm under the conditions shown in Table 4 below. Then, a weld metal test (groove shape and specimen collection position conforming to JIS Z3111) was performed.

In addition, as an evaluation of the strength and toughness of the weld metal, a test piece cut out from a weld metal of a joint obtained by gas shield arc welding of a 490 N / mm grade 2 steel plate having a thickness of 25 mm under the conditions shown in Table 4 above was used. A tensile test and a Charpy impact test at 0 ° C. were performed. As a result, the case where the tensile strength was 490 N / mm 2 or more and the minimum value of the absorbed energy was repeated 70 times or more in each Charpy impact test at 0 ° C. was determined to be acceptable (good).

  Further, the welding workability was evaluated from the amount of spatter generated and the arc stability. Specifically, the amount of spatter generated during welding was bead-on-plate welding using a copper collection box separately from the weld metal test, and was welded three times under the conditions shown in Table 4 above (one welding time) 1.5 minutes), the amount of spatter collected when converted to 1 minute was evaluated in terms of the amount generated for 1 minute. Further, the arc stability was determined to be good when the spatter generation amount was 2 g / min or less and the arc was stable. The above evaluation results are summarized in Table 5 and Table 6 below.

  No. shown in Table 1, Table 2 and Table 5 above. W1-No. W37 is a wire of an example within the scope of the present invention, and No. W shown in Tables 3 and 6 above. Z1-No. Z19 is a comparative wire outside the scope of the present invention. As shown in Table 5 above, Example No. W1-No. Since the wire composition of W37 is appropriate, the strength and absorbed energy of the weld metal are good, the amount of spatter generated during welding is small, the arc is stable, and satisfactory results are obtained.

  On the other hand, as shown in Table 6 above, Z1 and No. The Z2 wire is a comparative example in which the C content is outside the scope of the present invention. Comparative Example No. The Z1 wire has low Charpy absorbed energy because the C content exceeds the range of the present invention. Comparative Example No. Since the Z content of the wire of Z2 is less than the range of the present invention, the tensile strength of the weld metal was insufficient. No. Z3 and No. The Z4 wire is a comparative example in which the Si content is outside the scope of the present invention. Comparative Example No. The Z3 wire had a low absorbed energy because the Si content exceeded the range of the present invention. Comparative Example No. Since the Z content of the Z4 wire was less than the range of the present invention, the amount of spatter was large, and defects were generated due to insufficient deoxidation.

  No. Z5 and No. The wire of Z6 is a comparative example in which the Mn content is out of the scope of the present invention. Comparative Example No. Since the Mn content of the Z5 wire exceeded the range of the present invention, the toughness was lowered. Comparative Example No. The wire of Z6 was insufficient in hardenability because the Mn content was less than the range of the present invention, and the strength and toughness were lowered. No. Z7 and No. The Z8 wire is a comparative example in which the total content of Al and Zr is out of the scope of the present invention. All of these wires are insufficient in refinement of the weld metal structure and lack in toughness. It was. Furthermore, no. Z9 and No. The wire of Z10 is a comparative example in which the ratio of Mn content to Si content (Mn / Si) is less than 0.85, and these wires have a coarse weld metal structure and reduced toughness. Furthermore, no. Z11 and No. The Z12 wire is a comparative example in which the Ti content is outside the scope of the present invention. Comparative Example No. Since the Ti content of the Z11 wire exceeded the range of the present invention, the weld metal was hardened and the toughness was lowered. Comparative Example No. Since the Z content of the wire of Z12 is less than the range of the present invention, the microstructure becomes rough and the toughness decreases.

  No. Z13 and No. The Z14 wire is a comparative example in which the Mg content is outside the scope of the present invention. No. Since the Z13 wire has an Mg content exceeding the range of the present invention, the amount of spatter increases, the arc is disturbed, and as a result, the toughness also deteriorates. No. Since the Z14 wire had an Mg content less than the range of the present invention, the hardenability was insufficient, and as a result, the toughness was insufficient. Comparative Example No. The Z15 wire was insufficient in toughness because the N content exceeded the range of the present invention. Furthermore, no. Z16 and No. The Z17 wire is a comparative example in which the total content of Si and Mn is out of the scope of the present invention. Comparative Example No. Since the total content of Si and Mn was less than the range of the present invention, the Z16 wire was insufficient in hardenability and as a result, lacked toughness. Comparative Example No. Since the total content of Si and Mn exceeded the range of the present invention, the toughness of the Z17 wire was lowered. No. Z18 and No. The wire of Z19 is a comparative example in which the B content is out of the scope of the present invention. Comparative Example No. Since the Z content of the Z18 wire was less than the range of the present invention, a large amount of grain boundary ferrite was generated and the toughness was insufficient. Comparative Example No. Since the Z content of the wire of Z19 exceeded the range of the present invention, the strength was satisfied, but the weld metal was cracked at high temperature, and the toughness was greatly varied. As a result, the minimum value was not satisfied. It was.

Claims (2)

  1. % By mass
    C: 0.02-0.14%,
    Si: 0.4 to 1.5%,
    Mn: 1.0 to 2.5%
    Ti: 0.05 to 0.4%,
    Mg: 0.0003-0.010% and B: 0.0005-0.010%,
    Furthermore, while containing 0.005 to 0.050% in total of one or more elements selected from the group consisting of Al and Zr,
    N: limited to 0.005% or less,
    The balance consists of Fe and inevitable impurities,
    The total content of Si and Mn is 1.5-3.5%,
    And the ratio (Mn / Si) of Mn content (%) and Si content (%) is 0.85 or more, The solid wire for gas shielded arc welding characterized by the above-mentioned.
  2.   Furthermore, in mass%, Cu: 0.3-1.5%, Ni: 0.3-3.0%, Cr: 0.1-1.5% and Mo: 0.1-1.5% 2. The solid wire for gas shielded arc welding according to claim 1, comprising one or more elements selected from the group consisting of 5.0% or less in total.
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CN103170762A (en) * 2013-01-23 2013-06-26 中广核工程有限公司 Solder wire special for nuclear power 20-control chrome steel

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JP5337665B2 (en) * 2008-10-21 2013-11-06 株式会社神戸製鋼所 Solid wire for MAG welding
JP5670305B2 (en) * 2011-12-14 2015-02-18 日鐵住金溶接工業株式会社 Solid wire for gas shielded arc welding of high strength steel sheet

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JP2006000868A (en) * 2004-06-15 2006-01-05 Nippon Steel Corp Solid wire for gas shielded arc welding for primary build-up welding

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JPH09225680A (en) * 1996-02-22 1997-09-02 Nippon Steel Corp Welding wire for ferritic stainless steel
JPH1190678A (en) * 1997-09-25 1999-04-06 Nippon Steel Weld Prod & Eng Co Ltd Solid wire for carbon dioxide gas shielded arc welding
JP3545193B2 (en) * 1998-02-25 2004-07-21 日鐵住金溶接工業株式会社 Solid wire for carbon dioxide shielded arc welding and welding method thereof

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JP2006000868A (en) * 2004-06-15 2006-01-05 Nippon Steel Corp Solid wire for gas shielded arc welding for primary build-up welding

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103170762A (en) * 2013-01-23 2013-06-26 中广核工程有限公司 Solder wire special for nuclear power 20-control chrome steel
CN103170762B (en) * 2013-01-23 2015-06-17 中广核工程有限公司 Solder wire special for nuclear power 20-control chrome steel

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