TWI357369B - - Google Patents

Description

1357369 IX. INSTRUCTIONS OF THE INVENTION [Technical Field] The present invention relates to a solid electrode for carbon dioxide gas welding used for carbon steel gas shielded arc welding of mild steel or 490 to 5 20 N/mm2 high tensile steel, in particular, The welding is performed with high efficiency, and a solid electrode for arc welding of the carbon dioxide gas of the welded metal having good mechanical properties can be obtained. [Prior Art] Recently, in the field of building reinforcement, the gas shielding arc welding method using CO 2 as a shielding gas mainly adopts this method because of its high efficiency. In the past, the gas shielded arc welding method almost always uses an artificial semi-automatic welding method. However, in order to save manpower and reduce the cost, and to further improve the welding efficiency by utilizing nighttime or holiday unmanned operation, automatic welding using robots has also begun to spread. On the other hand, in order to improve the performance of the welded joints, in order to improve the performance of the welded joint portion, in the JASS6 revision of 1997 and the revision of the Building Standard Act of 1999, heat supply during welding is performed. The upper temperature of the interlayer temperature is managed. Affected by this trend, welding rods corresponding to high heating and high-rise temperatures have been developed for welded electrodes, which allow up to 40kJ/cm of maximum heating and 3 50°C of interlayer temperature for 490N/mm2 grade carbon steel sheets. The 520N/mm2 grade carbon steel plate allows up to 30kJ/cm of maximum heating and 250°C of interlayer temperature. In 1999, it was JIS in the form of 540N/mm2 = YGW18. Up to now, it has been able to obtain better mechanical properties than conventional welding rods at high heating and high-rise temperatures. -4- 1357369 540N/mm2 grade welding rods have rapidly spread. In addition, the grade electrode has been popularized at a low level for heat supply and interlayer temperature. In recent years, the number of fully self-welding 540N/mm2 electrodes in the robot has begun to increase. In the electrode corresponding to the temperature of the carbon dioxide gas shielding welding, the content of Si, Mn, and Ti is more than that of the conventional electrode as a whole, and I, Al, Nb, V, Ni, and the like are added as needed. In this way, the hardenability of the steel is improved, and the toughness due to the grain refinement is increased, and the precipitation hardening action is added to increase the strength. However, the actual situation of these conventional electrodes is that they do not take into account the welding applied to the robot. Conventional and high-temperature electrodes have the disadvantage of excessive slag generation. Since the slag is insulative, the accumulated slag is likely to be defective, which causes defects such as insufficient penetration of the weld and contamination of the slag. In addition, as long as the unnatural peeling of the slag occurs slightly, even if the arcing position is changed and the re-arcing is attempted, the error will still be wrong. Therefore, the welding robot will judge the error and stop the maximum strength of the person to save the manpower, but the arc is caused in a short time. In the case of destabilization, it is necessary to frequently enter the industry manually, or to start the arcing part in order to repair the arcing error, so that the advantages cannot be exerted. Therefore, in order to solve the problem of providing a welded electrode, it is necessary to use a large current, a high-rise, etc. in the 540N/mm2 automatic welding in the 540N/mm2 automatic welding under the conditions of maximum heating of 40kJ/cm and 35°C. The deoxidizing component ports Mo, B, and Cr, which are combined and solid solution hardened, all correspond to large currents at the time of design, and the peeling property is poor to prevent the arc from being stable, and the welding robot continues to generate the arcing industry. The welding machine slag is deposited to remove the slag from the slag removal. This problem is expected to have the highest interlaminar temperature mechanical properties, 1357369, and the amount of slag generated is small, the peelability is also good, and the continuous stacking height is large and the efficiency is high. In response to this expectation, the electrode described in JP-A-2006-88187, JP-A-2006-305605, and JP-A-2006-15 〇 437 has been developed as an electrode for improving slag removability. In addition, the welding rod which is improved in the slag-removing property and the slag-forming property is also disclosed in Japanese Laid-Open Patent Publication No. 2004-122170, No. 2006-26643. Significant evolution. Therefore, narrow groove formation with a groove angle of 30° has been achieved. That is to say, the conventional groove angle is based on 3 5 °, but in order to reduce the groove area to reduce the number of layers and shorten the welding time, reduce the amount of welding electrode used, reduce the thermal strain, and in order to reduce the rise in interlayer temperature to improve The mechanical properties of the welded metal such as strength and toughness have been able to achieve a narrow groove of about 30° for this purpose. When the groove angle is so small, since the torch tip easily interferes with the grooved surface, the distance from the tip end of the torch to the bottom surface of the groove is inevitably long, and the so-called electrode protrusion length is often long, and the weld penetration is likely to be poor due to the reduction of the arc force. . Further, since the protruding length becomes long, the gas shielding property is deteriorated, and nitrogen tends to be mixed into the welded metal from the atmosphere, and the toughness tends to decrease. In the past, there has been no development of a technique for preventing splice penetration failure in terms of a welded electrode. Further, there is no welding electrode which can achieve the excellent mechanical properties such as excellent slag releasability and slag amount, and excellent strength and toughness. Therefore, it has been desired to develop an optimum welding electrode which can prevent welding -6-1357369 poor penetration and has excellent mechanical properties and can correspond to narrow groove construction using a robot for multilayer welding. The present invention has been developed in view of the above problems, and its object is to provide a solid electrode for carbon dioxide gas welding, which can obtain sufficient welding paint penetration even in a narrow grooved construction, and can obtain strength and edge A fusion metal that is excellent in mechanical properties such as properties. The solid electrode for carbon dioxide gas fusion of the present invention contains C: • 0 03 to 010% by mass, si: 0.67 to 1_0% by mass, Mn: K8U.50% by mass, S: 0.006-0.018% by mass, Ti: 〇_ 1〇〇~0.150% by mass, B: 0.0015 to 0.0070% by mass, cu: 0.10 to 0.45 mass% including the plating component, and the balance is Fe and unavoidable impurities, and the parameter Pbs represented by the following formulas '1 and 2 And Pmt is in accordance with PBS$10, Ρμτ$32, and is limited to P: 0.020 mass% or less, Nb: 〇·〇4 mass% or less, V: 0.04 mass% or less, and Α1: 0.04 mass% or less. [Equation 1] • Pbs=[B]x[S]x105 [Equation 2] Ρμτ = [Μιι]χ[Τϊ]χ102. Here, [] represents the content (% by mass) of the element in the electrode. In the solid electrode for welding carbon dioxide gas, at least one selected from the group consisting of Mo: 0.25 mass% or less, Cr: 0.25 mass% or less, and Ni: 0.25% by mass or less is preferably contained. Further, it is preferable that there is 0.01 to 1. 〇〇g of MOS2 per 10 kg of the electrode on the surface of the electrode. 1357369 [Embodiment] The inventors of the present invention conducted a study on the relationship between the protruding length of the electrode, the transition pattern of the droplet, and the penetration depth of the welding, and as a result, the following matters were clarified. When the feed amount of the welding rod is constant, if the protruding length becomes long, the electric resistance from the tip end of the welding rod to the energization point in the chip rises, and the melting is easily caused by the temperature rise, so the welding current supplied from the fusion splicer is lowered. , but the welding voltage rises. Under the condition that the welding current is reduced and the welding voltage is increased, since the arc reaction force is small and the traveling space (arc length) is long, the droplets which are melted at the tip end of the electrode and fall to the welded portion are likely to become a completely spherical droplet transfer of the large particles. The directivity of the arc is weakened, and the area of the concentric drop-shaped drop region centered on the electrode is enlarged. Further, the transition period is also lengthened, the arc force applied to the base material is weak, and the penetration depth of the fusion is small. In order to avoid this phenomenon, it is most effective to prevent complete spherical droplet transfer, and the inventors have found that it is necessary to suppress the factor that causes the droplet to grow substantially. The most important influence on the size of the droplet is Ti, and the Ti content in the electrode. The smaller the amount, the more the droplet growth can be suppressed, and the short-circuit transition occurs, the concentration of the arc increases, the area of the droplet drop region decreases, and the penetration depth of the weld increases. In Fig. 1, the horizontal axis represents the length of the electrode protrusion (mm), and the vertical axis represents the penetration depth (mm) of the weld, and represents the relationship between the Ti content, the length of the electrode protrusion, and the penetration depth of the weld. Among them, the feed amount of the electrode is l〇m/min. As shown in Fig. 1, the longer the protruding length of the welding rod, the smaller the penetration depth of the welding, but the smaller the Ti content, the smaller the penetration depth of the welding. Further, the oxide of Ti is a source of slag, and the amount of Ti is made smaller than in the related art, and problems caused by slag deposition can be alleviated. -8 - 1357369 —The reduction, the gold: the reach: the • 05 The tolerance is poor and the arc is left when the melt is missing. On the other hand, Ti has a strong affinity with nitrogen, which will prevent nitrogen from binding when it is poorly shielded. The occurrence of pores has the effect of preventing metal embrittlement. The fact that less Ti causes the occurrence of pores and metal embrittlement occurs. Therefore, in order to reduce the penetration depth of the weld due to the reduction of Ti and the problem of occurrence of porosity and embrittlement, the contents of Μη and B are optimized. Hereinafter, the reasons for the addition of the solid electrode component for carbon dioxide gas welding of the present invention and the reasons for the composition limitation will be described.

"C : 0 · 0 3 ~ 0 . 1 0 mass % " C is an important additive element for ensuring strength. However, when it is not 0.03 mass%, the strength required for high heat supply and high-temperature temperature welding cannot be ensured. . Therefore, C is 0.03 mass% or more, preferably 〇 mass% or more. On the other hand, if C is excessively added, high temperature cracks are likely to occur. Further, if C is excessively added, in the arc atmosphere, the CO image appears to cause an increase in the amount of spatter generated, and the arc stability is changed. Further, if the C content is large, the strength of the welded metal is too large, and the toughness is inversely lowered. If the C content exceeds 0.10% by mass, these effects become apparent, so the upper limit is made 0.10% by mass. "Si: 0 _ 6 7 ~ 1 _ 0 0 mass % ”

Si is mainly added to ensure strength and prevent stomata trapping due to deoxidation. Further, the addition of Si increases the amount of slag, but the slag releasability is improved. These effects are effective at a Si content of 0.67 mass% or more. When the Si content is less than 0.67 mass%, the slag peeling property is poor and the electric power is destabilized. The lower limit 更 of Si is more preferably 0.75 mass%. On the other hand, when Si is excessively added and exceeds 1.00% by mass, the amount of slag exceeds 1,357,369, the arc stability is deteriorated, and the toughness 値 is lowered. Therefore, the upper limit Si of Si is 1.0% by mass. "Mn: 1.8 to 2.50% by mass" Μη has a deoxidizing effect of the weld metal, and the strength of the weld metal is increased, and the effect of obtaining a weld metal having high toughness is obtained. In a robot system with a narrow slot corresponding function, the maximum electrode projection length is set to be long, and the occurrence of porosity and toughness due to shielding failure are likely to occur. Therefore, as the robot electrode, a large amount of Μη is added to prevent these disadvantages. Therefore, the Μη content must be added at least 1.81% by mass or more. On the other hand, when the Μη content exceeds 2.50% by mass, the amount of slag increases, and the slag releasability is lowered, and as a result, the arc stability is also deteriorated. Further, as will be described later, the upper limit Μ of Μη must be suppressed to be lower depending on the relationship with the amount of Ti. "S : 0 · 0 0 6 〜 0 · 0 1 8% by mass" By adding S, the surface tension of the molten pool is lowered, the physical unevenness at the time of solidification is reduced, and the surface of the welded metal is smoothed. . Thereby, the slag peelability can be improved. When S is less than 0.006 mass%, the effect is not exhibited, and the arc stability is deteriorated due to poor peelability. On the other hand, even if S is added in an amount exceeding 0.018 mass%, not only the surface shape improving effect of the welded metal is saturated, but also high temperature cracking is likely to occur. Further, the form of the slag is granulated, the arc is prevented from being melted, and local arc instability is caused, and the toughness is also lowered. Therefore, the upper limit S of S is 0.018% by mass. Further, as will be described later, the upper limit of S is not required to be suppressed to be lower depending on the relationship with the amount of enthalpy. "Ti : 0· 1 00~0· 1 50 mass %" -10- 1357369

Ti has an effect of improving the arc stability in a high current range. In other words, there are many electrodes in which Ti is added at about 0.20% by mass. One of the characteristics of the composition of the present electrode is that the Ti content is more than that of a general electrode. When Ti is less than 0.100% by mass, the arc stability is poor and the spatter property is increased. Therefore, T i must be added 〇 · 1 〇 〇 by mass or more. On the other hand, if the Ti content is increased, the penetration depth of the weld is reduced due to the change in the above-described droplet transfer mode, and the penetration defect is likely to occur when the electrode has a long protruding length. When the Ti content exceeds 0.150% by mass, the molten droplets are completely migrated and the fusion penetration is poor, so the upper limit is 0.150% by mass. Further, as will be described later, the upper limit of the content according to the relationship with the Μη content is not required to be suppressed to be lower. In the case where the robot is welded, the optimum voltage and the welding speed can be set at all times, so even if Ti is contained, the arc stability does not deteriorate. "B : 0 0 0 1 5 - 0 · 0 0 7 0 Mass 0 / 〇 " By adding a small amount of B, the crystal grains of the weld metal can be made fine, and thus the strength and toughness are improved. When the B content is less than 0% by mass, the effect of improving the strength and toughness of the welded metal cannot be insufficient. Therefore, B is 0.0015 mass% as the lower limit. On the other hand, if B is excessively added and more than 0.0070 mass% exceeds, high temperature cracking is likely to occur. Therefore, the B content is 0.0070% by mass. Also, the upper limit of the B content is not required to be lower depending on its relationship with the amount of S. “ C u : 0 _ 1 0 ～ 0 · 4 5 mass % ”

Cu tends to cause high temperature cracks when it is excessively added, and is generally low. The amount of surface is measured, and the fusion is connected to the world. Due to the low amount of Ti, 0015 is now, 値. Then, the tolerance 値 is changed to the properties of the slag -11 - 1357369 to deteriorate the peelability. As a result, the arc stability is deteriorated. It is not necessary to actively add Cu to the electrode wire, and in most cases, it is to improve conductivity, rust resistance, linearity, and aesthetics, and it is added in the state of Cu component in copper plating performed on the surface of the electrode. . When the amount of Cu is 0.10% by mass or less, the film thickness of the plating film is too small, resulting in poor conductivity, arc instability, and spatter. On the other hand, when the Cu content exceeds 0.45 mass%, high temperature cracks and slag peeling properties are a problem, so the upper limit of Cu is 0.45 mass%. Further, Cu is a combination of the amount contained in the wire and the copper plating component. “PbsS 1〇(Pbs = [B]x[S]x1〇5)” Both B and S are elements that cause high temperature cracks. In addition to separately specifying the contents of B and S, the two elements must be correlated with each other. Ways to limit 'to prevent high temperature cracks. That is, since high temperature cracks are likely to occur in the welding of narrow slots, it is necessary to pay more attention to the prevention of cracks than before, in addition to separately specifying the contents of B and S, the two elements must be interconnected. limit. In Fig. 2, the horizontal axis represents the S content, and the vertical axis represents the b content, which indicates the relationship between the occurrence of cracks and the contents of S and B. As shown in Fig. 2, it has been found from the results of experiments by the inventors of the present invention that in the range of pBS > 1 , even if both B and S are within the scope of the present invention, both elements are at a high content. Range, so cracks will occur. Therefore, when the relevant parameter Pbs is defined as Pbs = [B]x[S]x105 ([B], [S] respectively represent the B content (% by mass) and the S content (% by mass) in the electrode), the pBS must For i 〇 the following. -12- 1357369 *' Ρμτ ^ 3 2 (Ρμτ = [Μπ]χ[Τϊ]χ1 Ο2)" Μη and Ti are the main generating elements of slag, in addition to separately specifying the contents of Μη and Ti, respectively The two elements are constrained in a cross-correlation manner to prevent excess slag from occurring. In Fig. 3, the horizontal axis represents the Μη content, and the vertical axis represents the Ti content, which indicates the relationship between the slag content and the like, and the content of Μη and Ti. The present inventors have found that, as shown in Fig. 3, in the range of PMT > 32, even if both Μη and Ti are within the prescribed range of the present invention, since the content of both elements is high, the amount of slag formation is large. The slag removability also deteriorates, so the stability of the arc is poor. Further, if the amount of slag is increased, slag removal must be frequently performed, and the operation efficiency is lowered. Therefore, when the relevant parameter pMT is defined as PMT=[Mn]x [Ti]xl02, ([Μη], [Ti] respectively represent the Μη content (% by mass) and the Ti content (% by mass) in the electrode), which ΡΜΤ Must be below 32. “ Ρ : 0 · 0 2 0% by mass or less Ρ Ρ is one of the main elements that cause high temperature cracks, and there is no need to actively add bismuth. Therefore, the upper limit 値 which does not constitute a problem as a high temperature crack is set to 0.020% by mass. "Nb : 0.04 mass% or less, V: 0.04 mass% or less, Α1 : 0.04 mass% or less"

Nb, V, and A1 reduce the toughness of the weld metal under low heat welding conditions. Therefore, it is necessary to avoid the positive addition of these elements as the upper limit of the allowable range in which the toughness can be neglected, and the upper limit 値 of these elements is set to 0.04% by mass. “Mo : 0.25 mass% or less, Cr: 0.25 mass% or less, Ni: -13-1357369 0.2 5 mass% ”

Mo and Cr 'Ni increase the hardenability of the weld metal and increase the strength, and it is preferable to add it positively. Mo, Cr, and Ni maintain moderate strength even at higher heating and interlayer temperatures. The addition of these elements does not require a lower limit, but as long as at least one of Mo, Cr, and Ni is added in an amount of 5% by mass or more, the effect is remarkable. On the other hand, if the amount of these elements added exceeds 〇 _25 mass%, the microstructure of the fused metal will be ironed in the field and the toughness will be lowered. Therefore, these elements are each set to be 0.25 mass% or less at the time of addition. “MoS2 on the surface of the electrode: 每.〇1~l.〇〇g per 10kg of electrode” The feedability of the electrode has a great influence on the slag removability. Stable feed of the electrode will stabilize the formation of the molten pool, the thickness of the generated slag will be uniform, and the strain of heat shrinkage will uniformly function, thereby facilitating the overall peeling. The Mo S 2 on the surface of the electrode reduces the fusion of the feed point between the tip and the electrode, which contributes to the improved feedability of the electrode. In the conventional method for improving the feedability of the electrode, there is a method of excessively oxidizing along the grain boundary on the surface of the electrode. In this method, the amount of slag is increased due to excessive amount of ruthenium. On the other hand, since the application of MoS2 does not increase the amount of melting compared with the other feedability lifting method, it is suitable for the method of improving the electrode feedability of the electrode of the present invention. This effect is effective in attaching 1 〇 32 above O.Olg per 10 kg of the electrode. On the other hand, if MoS2 is attached to more than 1.00g per 10kg of welding rod, it will start to build up in the feeding system. As the Mo S 2 is blocked, it will cause poor feeding, which will affect the slag property and make the stripping property. reduce. As a result, the arc stability is deteriorated. Therefore, it is preferable that 'in every 1 〇kg of the electrode, there is -14 to 1357369 0.01 to 1.0 g of m〇s2 on the surface of the electrode. [Examples] Hereinafter, in order to explain the effects of the present invention, the present invention is included in the present invention. The electrode of the embodiment of the range and the electrode of the comparative example which deviated from the scope of the present invention describe the results of the fusion test. Figs. 4(a) to 4(C) are views showing the shape of the welded test piece and the shape of the groove. Fig. 4(a) is a cross-sectional view showing the grooved portion in an enlarged manner, Fig. 4(b) is a front view of the test body, and Fig. 4(c) is a side view. The diaphragms 1 are vertically arranged, and the shaft of the circular steel pipe 3 is horizontally arranged, and the end faces of the circular steel pipes 3 are opposed to the partition plates 1. The end face of the circular steel pipe 3 is chamfered to form a grooved groove with the separator 1. Further, a cylindrical spacer 2 is placed on the inner surface of the circular steel pipe 3. Then, the grooved portion is subjected to circumferential seam welding by the welding torch 4. Table 1 below shows the welding conditions. Further, Table 2 below shows combinations of the steel sheets of the separator 1, the steel pipe 3, and the gasket 2, and Table 3 shows the composition (% by mass) of the separator 1, the steel pipe 3, and the gasket 2. The welded test piece shown in Fig. 4 was welded using a commercially available rebar system for reinforcing steel construction using the welding conditions shown in Table 1. Further, the separator 1 and the steel pipe 3 are blast furnace materials, and the gasket 2 is a commercially available electric furnace material, and the gasket 2 has a very high nitrogen content and poor weldability. The groove angle is generally 35°, and the root gap is 7 mm. However, in the welding test, a narrow groove construction with a groove angle of 30° and a root gap of 5 mm was performed. Then, the peeling property of the slag after the completion of the welding was calculated by digital image processing, and the amount of slag was measured. The strength and toughness of the welded metal were measured by a tensile test and a Charpy impact test. In addition, the stability of the arc and the amount of spatter generated in the fusion -15-1357369 were also recorded. In addition, ultrasonic flaw detection tests were conducted to investigate whether weld penetration and high temperature cracks occurred. Table 4 below shows the composition (% by mass) of the electrodes of the examples and the comparative examples. In addition, Table 5 below shows the test results of the fusion test. Further, in the composition of Table 4, "<0·***" is shown, and the analysis result of the composition is 値 which does not reach the lower limit of the general analysis accuracy, and is not industrially contained. The evaluation methods of the respective characteristics shown in Table 5 are as follows. Regarding the slag peeling property evaluation method, the evaluation of the peeling property and the slag amount was carried out only under the condition 1 (see Table 2) in which the thickness of the steel pipe was thin. Further, it was confirmed that the welded electrode having good slag removability under Condition 1 was also good under Condition 2. At the welding start point, when the welding is completed to the final layer, the photograph is taken at a position of 90 mm from the front of the welding rod, and a total of 200 mm is taken (see Figures 4(b) and (c)). . Next, the appearance of the bead is dilated into (a) a portion where the slag is naturally peeled off and (b) a portion where the slag adheres, and the distribution thereof is obtained. The total amount of each pixel is calculated by the image analysis software, and the slag peeling rate (%) is obtained by (a) / ((a) + (b)) xl00. The slag peeling rate was 15% or more, and it was judged that the slag removability was good. Next, regarding the amount of slag, all the slag was recovered (including the natural peeling after the photograph of the appearance of the bead), and the weight was measured. When the amount of the slag was 12 g or less, it was judged that the amount of slag was good. The tensile test and the Charpy impact test of the welded metal were carried out under the condition 2 (refer to Table 2), and the A2 No. (parallel diameter 6 mm) of the jis Z 3111 was taken from the positions shown in Figs. 5 and 6 respectively. Standard test pieces (l〇mm square) are available for testing. Also, the tensile test is at 20%. (: At room temperature, Charpy Chong-16-1357369 hit test is 〇 ° C, with 3 averages as evaluation 値. Tensile strength is above 490N/mm2, and Charpy impact test average is more than 70J. The sex is judged to be good according to the sensory evaluation in the welding, and the slag does not interfere with the occurrence of the disturbing arc. Also, the case where the arc is unstable due to the poor feeding of the electrode is also unacceptable. After the welding of Condition 1 (refer to Table 2) was completed, the spatter attached to the shield nozzle was collected and the weight was measured. The amount of spatter generated was 6 g or less, and it was judged to be good. [Table 1] Welding machine type steel bar Welding robot welding power supply, polar DC machine, reverse polarity shielding gas C〇2, flow rate 25 liters/min welding rod diameter 1.2mm heating maximum 40kJ/cm interlayer temperature maximum 350°C posture downward welding rod protruding length 27 to 35mm slag removal Condition 1: None, Condition 2: Spatter removal and cleaning conditions with tip attachment 1 : None, Condition 2: Yes [Table 2] Partition steel pipe gasket condition 1 (thin plate) SN490C plate 25mmx450mm square STKN490B wall thickness 16mmx outer diameter 350mm SN490A wall thickness 9mmx outer diameter 334mm condition 2 (thick plate) SN490C plate thickness 75mmx800mm square STKN490B wall thickness 00mmx outer diameter 700mm SN490A wall thickness 9mmx outer diameter 640mm -17- 1357369 [Table 3] /Steel type C Si Μη Ρ SN Partition / SN490C 0.15 0.35 1.45 0.010 0.003 0.0029 Steel pipe / STKN490B 0.09 0.12 1.02 0.010 0.003 0.0035 Liner / SN490A 0.11 0.13 0.46 0.017 0.022 0.0125

[Table 4-1] No Electrochemical composition of electrode (% by mass) C Si Μη Ti S Ρ Cu B Pbs Pmt Example 1 0.06 0.80 1.85 0.15 0.009 0.011 0.20 0.0030 2.7 27.8 2 0.09 0.90 2.00 0.14 0.010 0.012 0.23 0.0020 2.0 28.0 3 0.04 0.95 2.35 0.12 0.008 0.010 0.27 0.0054 4.3 28.2 4 0.05 0.75 1.89 0.15 0.006 0.009 0.25 0.0045 2.7 28.4 5 0.07 0.70 2.45 0.13 0.008 0.015 0.17 0.0040 3.2 31.9 6 0.03 0.88 1.95 0.15 0.012 0.007 0.30 0.0060 7.2 29.3 7 0.10 0.85 1.84 0.14 0.018 0.013 0.21 0.0055 9.9 25.8 8 0.06 0.67 1.90 0.15 0.007 0.008 0.15 0.0070 4.9 28.5 9 0.05 1.00 1.85 0.11 0.008 0.005 0.45 0.0040 3.2 20.4 10 0.07 0.90 1.81 0.15 0.008 0.010 0.20 0.0035 2.8 27.2 11 0.06 0.75 1.88 0.10 0.016 0.010 0.28 0.0050 8.0 18.8 12 0.07 0.90 1.90 0.14 0.010 0.012 0.10 0.0025 2.5 26.6 13 0.06 0.80 2.10 0.14 0.009 0.011 0.20 0.0015 1.4 29.4 14 0.06 0.69 1.82 0.13 0.010 0.008 0.40 0.0046 4.6 23.7 15 0.08 0.90 1.90 0.11 0.011 0.011 0.25 0.0018 2.0 20.9 16 0.05 0.82 1.87 0.13 0.007 0.012 0.17 0.0040 2.8 24.3 17 0.05 0.85 1.97 0.14 0.006 0.007 0.25 0.0035 2.1 27.6 18 0.06 0.80 2.20 0.14 0.010 0.020 0.20 0.0044 4.4 30.8 -18- 1357369

[Table 4-2] No Electrochemical composition of the electrode (% by mass) M0S2 g / electrode l〇Ks Nb V A1 Mo Cr Ni 1 < 0.005 < 0.005 < 0.005 < 0.005 0.010 < 0.005 < 0.01 2 < 0.005 <0.005 <0.005 0.20 < 0.005 < 0.005 0.20 3 < 0.005 < 0.005 < 0.005 0.02 < 0.005 < 0.005 < 0.01 4 < 0.005 < 0.005 < 0.005 0.15 0.010 < 0.005 <0.01 5 < 0.005 < 0.005 < 0.005 < 0.005 < 0.005 < 0.005 < 0.01 6 < 0.005 < 0.005 < 0.005 0.22 0.060 < 0.005 0.18 7 < 0.005 < 0.005 < 0.005 0.06 0.020 <0.005 0.54 8 0.04 <0.005 <0.005 0.13 0.010 <0.005 <0.01 Real 9 <0.005 <0.005 <0.005 0.01 0.23 <0.005 <0.01 Apply 10 <0.005 0.04 0.011 0.25 <0.005 0.10 0.29 Example 11 0.050 < 0.005 < 0.005 0.03 0.200 0.25 < 0.01 12 < 0.005 0.050 < 0.005 < 0.005 < 0.005 0.020 0.77 13 0.009 < 0.005 0.04 < 0.005 0.030 0.050 0.98 14 &lt ;0.005 <0.005 <0.005 0.15 <0.005 0.010 <0.01 15 <0.005 <0.005 <0.005 ≪ 0.005 0.010 < 0.005 < 0.01 16 < 0.005 < 0.005 < 0.005 0.10 < 0.005 < 0.005 0.03 17 0.01 < 0.005 < 0.005 < 0.005 0.030 < 0.005 < 0.01 18 < 0.005 0.01 0.02 0.20 0.15 0.15 0.30 -19- 1357369

[Table 4-3] No. C Si Μη Ti SP Cu B Pbs Pmt Comparative Example 19 0.02 0.75 1.85 0.13 0.008 0.006 0.25 0.0040 3.2 24.1 20 0.11 0.92 2.30 0.13 0.008 0.010 0.19 0.0030 2.4 29.9 21 0.05 0.66 1.85 0.15 0.010 0.015 0.25 0.0020 2.0 27.8 22 0.08 1.02 2.10 0.14 0.015 0.011 0.28 0.0050 7.5 29.4 23 0.09 0.82 1.80 0.12 0.010 0.016 0.18 0.0035 3.5 21.6 24 0.08 0.75 2.52 0.11 0.009 0.010 0.20 0.0044 4.0 27.7 25 0.04 0.80 1.99 0.09 0.014 0.008 0.15 0.0040 5.6 17.9 26 0.06 0.85 1.82 0.16 0.011 0.007 0.29 0.0045 5.0 29.1 27 0.07 0.95 2.00 0.17 0.013 0.012 0.21 0.0018 2.3 34.0 28 0.06 0.80 2.30 0.14 0.009 0.009 0.20 0.0048 4.3 32.2 29 0.08 0.81 1.90 0.12 0.005 0.007 0.22 0.0025 1.3 22.8 30 0.03 0.90 1.98 0.14 0.019 0.016 0.23 0.0030 5.7 27.7 31 0.06 0.86 1.87 0.13 0.016 0.013 0.30 0.0064 10.2 24.3 32 0.07 0.90 1.82 0.15 0.009 0.021 0.25 0.0016 1.4 27.3 33 0.05 0.83 2.05 0.14 0.008 0.005 0.08 0.0026 2.1 28.7 34 0.05 0.77 1.87 0.14 0.013 0.009 0.47 0.0063 8.2 26.2 35 0.06 0.88 1.87 0.15 0 .009 0.015 0.40 0.0013 1.2 28.1 36 0.10 0.69 1.95 0.14 0.012 0.011 0.20 0.0072 8.6 27.3 37 0.03 0.80 2.40 0.15 0.018 0.008 0.26 0.0058 10.4 36.0 38 0.04 0.70 1.87 0.12 0.015 0.012 0.19 0.0030 4.5 22.4 39 0.08 0.81 1.84 0.15 0.006 0.010 0.15 0.0041 2.5 27.6 40 0.07 0.88 1.95 0.14 0.007 0.006 0.26 0.0055 3.9 27.3 41 0.09 0.90 1.83 0.13 0.009 0.008 0.19 0.0045 4.1 23.8 42 0.07 0.86 1.85 0.15 0.009 0.013 0.26 0.0039 3.5 27.8 43 0.08 0.77 1.99 0.12 0.009 0.010 0.20 0.0025 2.3 23.9 44 0.06 0.89 1.90 0.14 0.011 0.010 0.18 0.0066 7.3 26.6 45 0.07 0.90 1.95 0.23 0.003 0.012 0.25 <0.0001 0.0 44.9 46 0.08 0.79 1.72 0.19 0.005 0.019 0.17 0.0043 2.2 32.7 47 0.11 0.80 1.45 <0.01 0.012 0.010 0.25 0.0001 0.1 0.0 48 0.06 0.50 2.00 0.18 0.004 0.012 0.20 0.0019 0.8 36.0 49 0.07 1.10 1.82 0.05 0.025 0.006 0.20 <0.0001 0.0 9.1 50 0.06 0.25 1.95 0.15 0.015 0.010 0.25 0.0101 15.2 29.3 -20- 1357369

[Table 4-4] No Nb V A1 Mo Cr Ni M〇S2 19 < 0.005 < 0.005 < 0.005 0.15 < 0.005 < 0.005 0.05 20 < 0.005 < 0.005 < 0.005 < 0.005 < 0.005 <0.005 <0.01 21 <0.005 < 0.005 < 0.005 0.22 < 0.005 < 0.005 0.15 22 < 0.005 < 0.005 < 0.005 0.16 < 0.005 < 0.005 0.25 23 < 0.005 < 0.005 <; 0.005 0.13 0.005 < 0.005 0.50 24 < 0.005 < 0.005 < 0.005 < 0.005 < 0.005 < 0.005 0.78 25 < 0.005 < 0.005 < 0.005 < 0.005 < 0.005 < 0.005 0.35 26 <; 0.005 < 0.005 < 0.005 0.17 < 0.005 0.010 0.45 27 < 0.005 < 0.005 < 0.005 < 0.005 < 0.005 < 0.005 0.90 28 < 0.005 < 0.005 < 0.005 0.13 < 0.005 0.020 <; 0.01 29 < 0.005 < 0.005 < 0.005 < 0.005 < 0.005 0.010 0.10 30 < 0.005 < 0.005 < 0.005 < 0.005 < 0.005 < 0.005 < 0.01 31 < 0.005 < 0.005 <;0.005<0.005<0.005<0.005<0.01 32 <0.005 <0.005 <0.005 0.10 <0.005 <0.005 <0.01 33 <; 0.005 < 0.005 < 0.005 < 0.005 < 0.005 < 0.005 < 0.01 ratio 34 0.080 < 0.005 0.010 0.005 < 0.005 < 0.005 < 0.01 to 35 < 0.005 < 0.005 < 0.005 < 0.005 <0.005 <0.005 <0.01 Example 36 <0.005 < 0.005 < 0.005 < 0.005 < 0.005 < 0.005 0.50 37 < 0.005 < 0.005 < 0.005 < 0.005 < 0.005 < 0.005 <0.005 < 0.005 <<0.005< 0.005 < 0.005 0.27 < 0.005 < 0.005 < 0.01 42 < 0.005 < 0.005 < 0.005 0.010 0.28 < 0.005 < 0.01 43 0.010 < 0.005 0.010 < 0.005 0.020 0.27 0.05 44 <0.005 0.006 <0.005 < 0.005 < 0.005 0.15 1.10 45 < 0.005 < 0.005 < 0.005 < 0.005 0.150 0.010 < 0.01 46 < 0.005 < 0.005 0.01 0.20 0.010 0.010 < 0.01 47 < 0.005 <0.005 <0.005 <0.005 <0.005 <0.005 <0.01 48 0.010 0.010 0. 010 0.40 0.050 0.020 0.12 49 <0.005 <0.005 <0.005 <0.005 <0.005 <0.005 0.02 50 <0.005 <0.005 <0.005 0.18 0.09 0.01 0.10 -21 - 1357369

[Table 5-1] No Welding penetration poor peeling rate % Slag halo tensile strength Mpa Absorption energy J Arc stability Spatter amount g Cracked pores 1 Μ 〆,, 22〇8.4〇572〇146〇〇4.0〇Μ • Frrt II1 it /η, 2 Μ /ι\\ 24〇9_2〇600〇164〇◎ 3.7〇4nr 1 i 11 and 3 te JiW 20〇10.60 536〇155〇〇4.5〇 dirty y» \\ 4 cars 150 10.50 608〇174〇〇4.6〇无无5 te 16〇11.8〇575〇110〇〇4.9〇1/1 \\ No 6 SE /«,, 29〇9.0〇496〇122〇◎ 3.5〇v\ ΤΤΤΓ Real 7 4E 22〇10.30 595〇73〇◎ 5.8〇无/rrr .iIIL /»w Shi 8 No 150 11.2〇556〇74〇〇4·3〇 No Case 9 Charm 19〇11.6〇599〇72〇〇5.3 〇Μ /1 Μ /»»\ 10 No 20〇10.0〇628〇73〇◎ 3.7〇无无11 No 21〇7.5〇605〇75〇〇5.9〇无Μ 12 and /\ \\ 20〇8.5〇555 〇145〇〇5.0〇 Μ y»%\ 13 ΑίΤΤ III' 19〇9.6〇588〇71〇◎ 4.5〇Μ •/ιι Γ 1Μ ι >ι,, 14 No 21〇8.0 〇598〇124〇〇4.6〇无无15和/» \N 22〇8_4〇574〇150〇〇4.2〇Μ «t,, «μ,, 16 No 18〇7.7〇560〇123〇◎ 4.9〇Μ y»>> Μ 17 and 15〇9.0〇555〇167〇〇4.2〇细;n\ /ι,·》 18 Μ yt νν 17〇10.2〇581〇1〇〇〇◎ 5.0〇组/1 &gt ;> Μ /1 >\ -22- 1357369

[Table 5-2] No Weld penetration poor peeling rate % Slag amount Tensile strength Mpa Absorption energy j Arc stability Spatter amount g Crack hole 19 Μ /w\ 20〇8.5〇485x 132〇◎ 4.7〇4τττ 1ΙΤΓ 20 Μ 17〇10.40 615〇65x X 6.6x with or without 21 ίΚ ^ t \\ 14x 7.5〇486x 144〇X 5.1〇Μ There are 22 ΛΕ , , 28〇12.2x 604〇63x X 5.5〇Μ /1 s\ Μ 23 VnT Μ ί /\\\ 25〇6.2〇542〇66x 〇5.70 川川,有24•^* 12x 12.6x 629〇1190 X 5.1〇无和J\ \\ 25 M. 27〇5.8〇555〇91〇X 6.4 x Μ Jtw No 26 There are 15〇11.5〇587〇135〇◎ 3.9〇无/» 27 There are 15〇11.3〇-596〇139〇〇4.4〇Μ and, 28 Μ /\SS 14x 12.4x 610〇124〇 X 4.9〇无A\ i'll 11. 29 No 14x 10.70 576〇160〇X 3.8〇No 30 and J\S\ 20〇9.1〇535〇67x X 5.1〇有31 4fff JXW 17〇8.3〇546〇 75〇〇5_4〇有Μ 32 ^fH: / « »N 22〇9.0〇524〇76x 〇5.2〇 with or without 33 and 19〇10.00 600〇142〇X 6.4x None Ratio 34 M 14χ 9.1〇561〇83〇X 5.2〇 γηγ Compared with 35 No 17〇8.5〇485x 65x 〇4_2〇Μ /w\ Μ Example 36 No 20〇9.2〇602〇1500 ◎ 4.4〇有37 ffi y» \\ 13x 12'5x 641〇89〇X 4_1〇有38 Sister/»>> 21〇7.9〇572〇68x ◎ 5.2〇无无39 No 19〇8.7〇598〇64x ◎ 5.0〇Μ >1 /»,, 40 18〇9.5〇609〇65x ◎ 5.2〇无41 No 22〇8.1〇660〇68x 〇4.8〇•^11: te 42 Μ jw\ 21〇8.2〇638〇66x 〇4.9〇无无43 And /»,, 18〇9.1〇614〇69x ◎ 4.4〇Μ JSW 44 No 14x 8.5〇599〇129〇X 5.7〇AndΜ /UN 45 Yes 5x 11.00 484x 66x X 5_2〇No 46 There are llx 11.2〇486x 64x X 4.3〇无47 w 20〇4.5〇480x 42x X 12.5x There are 48 9x 1〇.4〇625〇60x X 3.9〇dirty 49 no 28〇12.3x 479x 49x X 9.8x has 50 and/ »>% 7x 10.10 488x 155〇X 5.1〇有-23- 1357369 As shown in Table 5, the composition range of each component of the present invention is 1 to 18. In the range defined by the present invention, the slag removability, the amount of slag, the strength of the weld metal, the toughness, the arc stability, the low spatter property, the weld penetration property, and the crack resistance are all good, and excellent weldability can be obtained. Excellent mechanical properties with welded metals. On the other hand, Comparative Examples 19 to 50 deviated from the scope of the present invention, in which Comparative Example 19 had too little C and the strength of the welded metal was insufficient. In Comparative Example 20, C was excessive, and high-temperature cracks occurred in the welded metal, and the strength was excessive and the toughness was low. In addition, there are many spatters and the arc stability is poor, so the continuous weldability is also deteriorated. In Comparative Example 21, Si was too small, the strength of the weld metal was insufficient, and the slag removability was also poor, and the slag interference caused the arc to be unstable and the continuous weldability was poor. In addition, pores also occur due to insufficient deoxygenation. In Comparative Example 22, Si was excessive, the toughness of the welded metal was insufficient, the amount of molten slag was excessive and interference was caused, the arc was unstable, and the continuous weldability was poor. In Comparative Example 23, the enthalpy η was too small, the toughness was low, and pores were generated due to insufficient deoxidation. In Comparative Example 24, the Μη was excessive, the amount of slag was large, and the peeling property was also poor. In addition, slag interference makes the arc unstable and has poor continuous weldability. In Comparative Example 25, the amount of spatter was too small, the amount of spatter generated was large, the arc stability was poor, and the tip was likely to be clogged, so that the continuous weldability was poor. In Comparative Examples 26 and 27, Ti was excessive, and the droplet transfer became a complete spherical droplet transfer, so that a large number of poor penetration of the weld occurred. In Comparative Example 28, although the respective components of Mn and Ti were each in compliance with the predetermined range, the parameter PMT was too large, so that the amount of slag was large and the peeling property was also poor. In addition, the slag interferes to make the arc unstable and the continuous fusion property is poor. In Comparative Example 29, the S was too small, the slag had poor peelability, the slag was disturbed, the arc was unstable, and the continuous weldability was poor. Comparative Example 3 0 has an excess of S, -24-1357369 has low toughness, and high temperature cracks also occur. Although the slag has good peelability, the deposit is granulated and the thickness is increased to impair the stability of the arc. As a result, the continuous weldability is poor. In Comparative Example 31, although the respective components of S and B were in compliance with the scope of the present invention, the parameter PBS was too large, so that the crack resistance was poor and cracking occurred. Comparative Example 3 2 had a P excess, low toughness, and high temperature cracking also occurred. In Comparative Example 33, the Cu was too small, and the thickness of the copper plating layer was thin, so that the conductivity was poor. A small amount of fusion occurs in a large amount to make the arc unstable and the spatter increases. In Comparative Example 34, Cu was excessive, high-temperature cracks occurred, and slag removability was also poor, and slag interference caused arc instability and poor continuous weldability. In Comparative Example 35, B was insufficient and strength and toughness were insufficient. Comparative Example 3 6 has a B excess and a high temperature crack occurs. In Comparative Example 37, each of the Mn, Ti, B, and S elements was individually within the prescribed range of the present invention, but the parameters Pmt and PBS were outside the scope of the present invention. Therefore, the amount of slag is large, and the slag removability is also poor. In addition, the slag interference makes the arc unstable, the continuous weldability is poor, and high temperature cracks occur. In Comparative Examples 38 to 40, Nb, V, and A1 were excessive, and the toughness was lowered. In Comparative Example 4, 1 to 4, respectively, Mo, Cr, and Ni were excessive, and although the strength was increased, the strength became excessive, and the toughness was lowered. In Comparative Example 4, the amount of 〇 2 S 2 was excessive, and MoS2 accumulation clogging occurred in a feed system such as a conduit liner, and the electrode feeding was extremely unstable. As a result, the arc stability is deteriorated, the slag distribution is uneven, and adverse effects are caused, and the slag removability is lowered. As a result, the slag interferes and the continuous weldability deteriorates. In Comparative Example 45, Ti was excessive, and S was too small, and B was not added. Therefore, the excess of Ti from -25 to 1357369 causes the droplet to migrate into a complete spherical droplet transfer, so that a large number of poor penetration of the weld occurs. In addition, since s is too small, the slag removability is also poor. In addition, slag interference makes the arc unstable and has poor continuous weldability. In addition, since B is not added, strength and toughness are insufficient. In Comparative Example 46, Ti was excessive, and S and Μη were too small. Since the excess of Ti causes the droplet transfer to become a complete spherical droplet transfer, a large number of poor penetration of the weld occurs. In addition, since S is too small, the peelability is also poor. The slag interference makes the arc unstable and the continuous fusion is poor. Since Μη is too small, strength and toughness are insufficient, and pores are also generated due to insufficient deoxidation. In Comparative Example 47, C excess 'Μη was insufficient, and Ti and Β were not added. Therefore, due to insufficient Μη and no enthalpy added, the strength and toughness are insufficient, and pores are also generated due to insufficient deoxidation. High temperature cracks occur due to excess C, and no Ti is added to the mixture, resulting in a large amount of spatter and poor arc stability. In Comparative Example 48, Ti, PMT, and Mo were excessive but Si and S were insufficient. Therefore, since the excess of Ti causes the droplet transfer to become a complete spherical droplet transfer, a large number of poor weld penetration occurs. In addition, since the Si and S are too small, the slag removability is also poor. The slag interference makes the arc unstable and the continuous weldability is poor. In addition, excess Mo leads to insufficient toughness. In addition, insufficient oxygen is caused by insufficient Si, and pores also occur. In Comparative Example 49, Si and S were excessive, Ti was insufficient, and B was not added. Since B is not added, the toughness is lowered and the strength is also low. Since Si and S are excessive, the amount of slag is large and granulated to impair arc stability. As a result, the continuous weldability is poor. In addition, a large amount of flying spatter occurs due to insufficient Ti. Because of the excess of S, high temperature cracks also occur. In Comparative Example 50, Si was insufficient, B was excessive, and PBS was too large. Insufficient Si causes welding -26-1357369 The strength of the metal is insufficient 'The slag removability is also poor' The slag interference makes the arc unstable and the continuous weldability is poor. Porosity also occurs due to insufficient deoxidation due to insufficient Si. In addition, because Pbs are too large, high temperature cracks can also occur. BRIEF DESCRIPTION OF THE DRAWINGS Fig. 1 is a graph showing the influence of the amount of Ti in the composition of the electrode and the protruding length of the electrode on the penetration depth of the weld. φ Fig. 2 is a view showing ranges of B and S in the present invention. Fig. 3 is a view showing the range of Μη and Ti in the present invention. The fourth (a), (b) and (c) drawings show the shape of the welded test piece and the shape of the groove. 'Fig. 5 is the position where the welded metal tensile test piece is taken. • Figure 6 shows the position of the welded metal Charpy impact test piece. [Main component symbol description] 1 : spacer • 2 : gasket 3 : steel pipe 4 : welding torch -27-

Claims (1)

1357369 Patent Application No. 097145201 Patent Revision of Chinese Patent Application Revision of the Republic of China on September 14, 100 A solid electrode for carbon dioxide gas welding, comprising: C: 0.03 to 0.10% by mass, Si: 0.67 to 1.00% by mass, Μη: 1.81 to 2.50% by mass, S: 0.006 to 0.018% by mass, Ti: 0.100 ~0.150% by mass, B: 0.0015 to 0.0070% by mass, Cu including a plating component: 0.10 to 0.45 mass%, and the balance is Fe and unavoidable impurities; the parameters Pbs and Pmt represented by the following formula correspond to PbsSIO, Ρμτ$32, And P: 0.020% by mass or less, Nb: less than 0.005 mass%, V: less than 0.005 mass%, A1: less than 0.005 mass%, Pbs=[B]x[S]x105 ΡΜτ=[Μη]χ[ Τΐ]χ1 02 Here, [] represents the content (% by mass) of the element in the electrode. 2. The solid electrode for carbon dioxide gas welding according to the first aspect of the invention, which further comprises at least one selected from the group consisting of Cr: 0.25 mass% or less and Ni: 0.25 mass% or less. 3. The solid electrode for carbon dioxide gas welding according to claim 1 or 2, wherein 0.01 to 1.00 g of MoS2 is present on the surface of the electrode per 10 kg of the electrode.