method for the production of weld joints

专利摘要:
METHOD FOR WELDING JOINT PRODUCTION. The method for producing a weld joint according to the present invention involves subjecting a steel sheet with a predetermined Vickers HV hardness, a sheet thickness, a C content, and a CEN to a gas shielded arc welding , using a lined wire, in which an outer sheath made of steel is filled with a flux, in which: at the time of said gas-protected arc welding, no preheating operation is performed in cases where the plate temperature steel is 10 ° C or higher, and, in cases where the steel sheet temperature is below 10 ° C, the preheating operation is performed, so that the steel sheet temperature is increased to 10 ° C or higher; the weld metal of the weld joint has a predetermined chemical composition; the weld metal has a CEN of 0.20 to 0.58% by weight; and the average Vickers HV hardness at a depth of 1 mm below the weld metal surface is 337 to 440.
公开号:BR112015029349B1
申请号:R112015029349-2
申请日:2014-08-07
公开日:2020-12-08
发明作者:Tatsuya Kumagai；Shuichi Nakamura
申请人:Nippon Steel Corporation；
IPC主号:

专利说明:

[TECHNICAL FIELD OF THE INVENTION]
[001] The present invention relates to a method for the production of a weld joint having a weld metal that has high hardness and excellent abrasion resistance and does not cause cold cracking easily when a steel sheet of high hardness which has excellent abrasion resistance and is used in the field of construction machinery and industrial machinery is welded.
[002] The priority was claimed in International Application No. PCT / JP2013 / 080242, filed on November 8, 2013, the content of which is hereby incorporated by reference. [RELATED TECHNIQUE]
[003] In many cases, a steel plate used in a construction machine for excavating mines or civil engineering works needs to be replaced due to wear. To prolong the life of the steel plate, an abrasion resistant steel is used to increase the hardness of the steel plate. The hardness of the steel sheet can vary depending on the environment of use or the purpose and, in general, abrasion resistant steel sheets of grade HB400 (from HB360 to HB440 in terms of standard Brinell hardness value, and from HV380 to HV469 in standard terms of Vickers hardness), grade HB450 (from HB410 to HB490 in terms of standard value of Brinell hardness, and from HV435 to HV533 in terms of standard value of Vickers hardness), grade HB500 (from HB450 to HB550 in Brinell hardness standard value, and from HV478 to HV585 in terms of Vickers hardness standard value), and HB600 degree (from HB550 to HB650 in terms of Brinell hardness standard value, and from HV585 to HV693 in terms of value hardness standard) are widely used.
[004] Most types of abrasion resistant steel are welded, and weld metals may also require abrasion resistance close to that of base metals (abrasion resistant steel). To increase the abrasion resistance of the weld metal, it is also necessary to increase its hardness. However, when the hardness of the weld metal is increased, it is very likely that cold cracking caused by the hydrogen that infiltrates during welding is very likely. In addition, as abrasion-resistant steel having a high hardness is used as the base metal, an increase in bond strength is also a cause of the easy occurrence of cold cracking.
[005] In order to avoid such cold cracking, preheating is usually carried out before welding. However, the hardness of abrasion-resistant steel is reduced by heating more easily than that of a typical steel and, therefore, it is not necessary to employ a high preheating temperature.
[006] It is preferable that the hardness of the weld metal is the same level as that of the base metal. For example, in the case where abrasion resistant steel of grade HB400 or grade HB500 is used as the base metal, it is preferable that the hardness of the weld metal is at least HV337 (HB320) or more, or HV380 (HB360 ) or more if possible.
[007] In addition, the hardness close to the surface is important for a weld metal zone from the point of view of abrasion resistance. During multilayer welding, the weld metal to a lower layer is reheated in a subsequent pass and, therefore, its hardness is slightly reduced. However, the weld metal for the outermost layer in the case of multilayer welding or the weld metal in the case of a single pass weld must have sufficient hardness close to the weld metal surface.
[008] Therefore, it is believed that a weld metal forming welding method that has a surface hardness of HV337 or more and HV533 or less and sufficient abrasion resistance and does not cause cold cracking even when preheating does not is performed, or a weld metal forming welding method that has a surface hardness of HV380 or more and HV533 or less and sufficient abrasion resistance and does not cause cold cracking even when preheating is not carried out, is extremely useful on a weld joint using an abrasion resistant steel having a surface hardness of HV380 or more and HV693 or less as the base metal.
[009] As a technique to suppress the cold cracking caused by hydrogen that occurs in a high-strength weld metal, for example, the methods of Patent Documents 1 to 5 are proposed.
[0010] In Patent Document 1, the occurrence of cold cracking is prevented by allowing austenite retained in a steel plate used for a high-strength steel tube or similar to function as a hydrogen trapping site. In Parental Document 2, the occurrence of cold cracking is also prevented by allowing the oxides in a steel plate used for a high-strength steel tube or similar to function as a hydrogen trapping site.
[0011] Patent Document 3 discloses a technique to prevent the occurrence of cold cracking by allowing Mo carbides in steel having a tensile strength of 800 MPa to 1150 MPa to function as a trapping site. Patent Document 4 discloses a technique for improving the cold cracking strength of steel having a tensile strength of 880 MPa to 1180 MPa by appropriately mixing Mg with the material covered with a protected metal arc welding material and therefore reducing the amount of diffusible hydrogen in the weld metal immediately after welding to about 3.0 ml / 100 g to 4.0 ml / 100 g. Patent Document 5 discloses a technique for suppressing cold cracking by limiting the amount of hydrogen contained in a flux-cored metallic wire for gas arc welding with gas protection.
[0012] The techniques are applied to base metals and weld metals having a strength of less than 1200 MPa and are not techniques capable of improving the cold cracking properties of the weld metal having a hardness of HV380 (about 1200 MPa in terms of tensile strength) and abrasion resistance.
[0013] Furthermore, in general, when an austenitic stainless steel welding material is used, the hydrogen infiltration into the weld metal is significantly reduced and, therefore, the sensitivity to cold cracking can also be reduced. Furthermore, as the material has an austenitic structure, cracking is less likely due to reduced ductility. However, the weld metal using the auspicious stainless steel welding material cannot easily increase the strength, that is, the hardness, and therefore abrasion resistance cannot be expected.
[0014] Therefore, there is a demand for formation, in a weld joint that uses an abrasion resistant steel having a high hardness of HV380 or more and HV693 or less as the base metal, of a weld metal that has a surface hardness of HV337 or more and HV533 or less and excellent abrasion resistance and does not cause cold cracking easily, or a weld metal that has a surface hardness of HV380 or more and HV533 or less and excellent abrasion resistance and does not cause cold cracking with ease through electric arc welding with gas protection. [BACKGROUND DOCUMENTS] [PATENTARY DOCUMENT]
[0015] [Patent Document 1] Unexamined Japanese Patent Application, First Publication No. 2012-176434
[0016] [Patent Document 2] Unexamined Japanese Patent Application, First Publication No. 2012-218034
[0017] [Patent Document 3] Unexamined Japanese Patent Application, First Publication No. 2005-40816
[0018] [Patent Document 4] Unexamined Japanese Patent Application, First Publication No. H11-147196
[0019] [Patent Document 5] Unexamined Japanese Patent Application, First Publication No. 2009-255168 [DESCRIPTION OF THE INVENTION] [PROBLEMS TO BE SOLVED BY THE INVENTION]
[0020] It is an object of the present invention to offer a method for the production of a weld joint that uses a steel plate of high hardness having a high C content and a surface hardness of HV380 or more and HV693 or less as a metal base, and having a weld metal that has a surface hardness of HV337 or more and HV533 or less and excellent abrasion resistance and does not cause cold cracking easily, or a weld metal that has a surface hardness of HV380 or more and HV533 or less and excellent abrasion resistance and does not easily cause cold cracking. [MEANS TO SOLVE THE PROBLEM]
[0021] For abrasion resistant steel according to the related technique, a preheat temperature during welding was important to prevent cold cracking. Therefore, in general, welding was carried out using a welding material for mild steel with a preheating temperature as the main priority. Therefore, the hardness of the weld metal zone was low and wear was very likely to occur. This was considered a problem. In the present invention, it has recently been discovered that, when the hardness of the weld metal zone is increased, on the contrary, it is quite likely that cracking does not occur in the heat-affected zone of the base metal, but in the weld metal itself. Therefore, the relationship between the CEN of the weld metal and cracking is examined, and then an appropriate range of the CEN of the weld metal is obtained.
[0022] The cold cracking that occurs in the weld metal during welding is affected by the resistance of the weld metal, the joint restrictive force, and the amount of diffusible hydrogen in the weld metal. The inventors have examined several methods to reliably suppress cold cracking using high hardness weld metal having a surface hardness of HV337 or more and HV533 or less, or high hardness weld metal having a surface hardness of HV380 or more and HV533 or less. As a result, it was concluded that the most reliable method is to sufficiently reduce the amount of diffusible hydrogen in the weld metal and to establish a specific CEN with alloy components in the weld metal ranging from 0.20% by mass to 0.58% in pasta.
[0023] FIG. 1 shows the results of a y-groove weld cracking test specified in JIS Z 3158 performed on various welding materials that varied in terms of steel plates and flux compositions under various conditions. Various weld metals in which the hardness of the weld metals vary and the amounts of diffusible hydrogen in the weld metals vary are produced, and limits of the preheating temperature at which the spreading is suppressed are obtained. In FIG. 1, the relationship between the amount of diffusible hydrogen in the weld metal and the preheating temperature limit at which cracking is suppressed is plotted according to the hardness levels of the weld metals.
[0024] Here, as a cold crack test, a test based on the JIS Z 3158 standard (y-groove cold crack test method in 1993) was performed at room temperature (25 ° C), and the absence cracking on surfaces and sections was assessed as approved. A test to measure the amount of diffusible hydrogen was carried out according to a gas chromatography method based on the JIS Z 3118 standard (method to measure the amount of hydrogen released from steel welds in 2007).
[0025] As illustrated in FIG. 1, when the amount of diffusible hydrogen in the weld metal immediately after welding is lower than 1.0 ml / 100 g, the preheating temperature limit for preventing low temperature cracking does not depend significantly on the hardness of the metal soldering. Therefore, by allowing the amount of diffusible hydrogen to be lower than 1.0 ml / 100 g, the sensitivity of the weld metal having a hardness of HV337 or more and HV533 or less and of the weld metal having a hardness of HV380 or more and HV533 or less when cold cracking can be significantly reduced.
[0026] However, reducing the amount of diffusible hydrogen in the weld metal immediately after welding to such a level is not easily accomplished in the related technique. The inventors have repeated several analyzes, and have recently found that the amount of diffusible hydrogen in the weld metal can be stably reduced to a level that is not easily obtained in the related technique by improving the flux composition of a flux-cored metallic wire. Specifically, it was found that allowing a certain amount of fluorides including CaF2 to be contained in the flux components, adjusting the amount of oxides, and allowing the mixing ratios of fluorides and oxides to be within predetermined ranges. , the amount of diffusible hydrogen in the weld metal can be stably suppressed to be less than 1.0 ml / 100 g.
[0027] The sensitivity of the weld metal to cold cracking depends significantly on the hardness of the weld metal and is also affected by the alloying elements. The inventors have examined the relationship between various alloy compositions and cold cracking sensitivity (crack suppression preheat temperature) for weld metals having a hardness of HV337 or more and HV533 or less and weld metals having a hardness HV380 or more and HV533 or less. As a cold crack test, a test based on the JIS Z 3158 standard (y-groove cold crack test method in 1993) was performed at variable preheat temperatures, and the lowest preheat temperature which cold cracking has not occurred is indicated as a preheat temperature limit to prevent cracking. During welding, the metal fluxing solder wires of the present invention described below are used, and all amounts of diffusible hydrogen in the weld metals are less than 1.0 ml / 100 g.
[0028] As a result, as shown in FIG. 2, it was found that when a CEN calculated by Expression 1 (see Welding book selections 10. "Welding of iron and steel materials" published by Sanpo Publications Incorporated. (1999), p. 163) is equal to 0.58% by mass or less, the preheating temperature limit for crack prevention can be less than or equal to room temperature (25 ° C), and the occurrence of cold cracking can be suppressed without preheating. CEN = [C] + (0.75 + 0.25xtanh (20x ([C] - 0.12))) x ([Si] / 24 + [Mn] / 6 + [Cu] / 15 + [Ni] / 20 + ([ Cr] + [Mo] + [Nb] + [V]) / 5 + 5x [B]) (Expression 1)
[0029] Here, elements with [] represent the quantities (% by mass) of the corresponding elements. In the case where there are no elements added, [] is replaced by zero.
[0030] The present invention was made based on the findings, and a summary of it is as follows.
[0031] (1) According to a first aspect, a method is offered for the production of a solder joint by performing an arc welding with gaseous protection, using a melting core metallic wire filled with flux in a sheath. steel, on any of a steel plate having a Vickers HV hardness of 380 or more and 514 or less, a plate thickness from 20 mm to 100 mm, a C content of 0.120% by weight to 0.300% by weight, and a CEN calculated by Expression 1 below 0.20% by weight to 0.75% by weight, a steel sheet having a Vickers HV hardness of more than 514 and 565 or less, a sheet thickness from 12 mm to 100 mm , a C content of 0.120 wt% to 0.300 wt%, and a CEN calculated by Expression 1 after 0.20 wt% to 0.75 wt%, and a steel plate having a Vickers HV hardness of more than 565 and 693 or less, a plate thickness from 6 mm to 12 mm, a C content of 0.350% by weight to 0.450% by weight, and a CEN calculated by Expression 1 below 0.20% by mass at 0.85% by mass, the method including:
[0032] (a) during electric arc welding with gas protection, do not perform a preheating operation in the case where the temperature of the steel plate is 10 ° C or more, and in the case where the temperature of the steel sheet is lower than 10 ° C, perform the preheating operation so that the temperature of the steel sheet is 10 ° C or more,
[0033] (b) where the melting core metal wire contains one or more of CaF2, BaF2, SrF2, and MgF2, and when the sum of the amounts of these is β or β relative to the total mass of the melting core metal wire ranges from 3.3% to 8.0% in terms of mass%,
[0034] the metal fluxing core wire contains one or more of Ti oxides, Si oxides, Mg oxides, and Al oxides, and when the sum of their quantities is β o β in relation to the total mass of the wire melting core metal ranges from 0.10% to 1.50% in terms of% by mass,
[0035] a sum of the amounts of CaCO3, BaCO3, SrCO3, and MgCO3 in relation to the total mass of the melting core wire is less than 0.60% in terms of% by mass,
[0036] an amount of iron powder in the flux in relation to the total mass of the metallic flux wire is less than 10.0% in terms of% by mass,
[0037] a ratio of the amount of CaF2 to β is 0.90 or more,
[0038] a ratio of β to β is 3.0 or more and 80.0 or less,
[0039] an amount of CaO in relation to the total mass of the molten core metal wire is less than 0.20% in terms of% by mass,
[0040] the metal melting core wire includes chemical components excluding metal fluorides, metal oxides, and metal carbonates, in relation to the total mass of the metal melting core wire, in terms of% by mass:
[0041] C: 0.010% to less than 0.060%;
[0042] Si: 0.05% to 1.80%;
[0043] Mn: 0.50% to 4.00%;
[0044] P: 0.050% or less;
[0045] S: 0.020% or less;
[0046] Al: 0.005% to 0.150%;
[0047] Cu: 0% to 0.75%;
[0048] Ni: 0% less than 1.00%;
[0049] Cr: 0% to 3.50%;
[0050] Mo: 0% to 1.50%;
[0051] Ti: 0% to 0.150%;
[0052] Nb: 0% to 0.15%;
[0053] V: 0% to 0.45%;
[0054] B: 0% to 0.0500%;
[0055] Mg: 0% to 2.0%;
[0056] Ca: 0% to 2.0%;
[0057] REM: 0% to 0.0150%; and
[0058] the rest: Fe and impurities,
[0059] (c) where a weld metal of the weld joint includes as the chemical composition, in terms of% by mass:
[0060] C: 0.100% to 0.170%;
[0061] Si: 0.05% to 0.80%;
[0062] Mn: 0.20% to 2.50%;
[0063] Al: 0.0050% to 0.1000%;
[0064] P: 0.050% or less;
[0065] S: 0.020% or less;
[0066] N: 0.015% or less;
[0067] Cu: 0% to 0.50%;
[0068] Ni: 0% to less than 0.70%;
[0069] Cr: 0% to 2.50%;
[0070] Mo: 0% to 1.00%;
[0071] Ti: 0% to 0.100%;
[0072] Nb: 0% to 0.100%;
[0073] V: 0% to 0.30%;
[0074] B: 0% to 0.0100%;
[0075] O: 0% to 0.100%;
[0076] Mg: 0% to 0.100%;
[0077] Ca: 0% to 0.100%;
[0078] REM: 0% to 0.0100%; and
[0079] the rest: Fe and impurities,
[0080] the CEN of the weld metal calculated by Expression 1 below ranges from 0.20% by mass to 0.58% by mass,
[0081] the average Vickers HV hardness of the weld metal calculated at 1 mm from outside to inside from a weld metal surface ranges from 337 to 440, and
[0082] all items (a) to (c) are satisfied. CEN = [C] + (0.75 + 0.25xtanh (20x ([C] - 0.12))) x ([Si] / 24 + [Mn] / 6 + [Cu] / 15 + [Ni] / 20 + ([ Cr] + [Mo] + [Nb] + [V]) / 5 + 5x [B]) ... (Expression 1)
[0083] where the elements with [] represent the quantities (% by mass) of the corresponding elements.
[0084] (2) According to a second aspect of the invention, a method is offered for the production of a solder joint by performing an arc welding with gaseous protection, using a metal wire with a fluxing core filled with flux in a steel sheath, on any of a steel sheet having a Vickers HV hardness of 380 or more and 514 or less, a sheet thickness of 20 mm to 100 mm, a C content of 0.120% by weight at 0.300% by weight mass, and a CEN calculated by Expression 1 from 0.20% by mass to 0.75% by mass, a steel sheet having a Vickers HV hardness of more than 514 and 565 or less, a sheet thickness of 12 mm to 100 mm, a C content of 0.120 wt% to 0.300 wt%, and a CEN calculated by Expression 1 after 0.20 wt% to 0.75 wt%, and a steel plate having a Vickers HV hardness of more than 565 and 693 or less, a plate thickness from 6 mm to 12 mm, a C content of 0.350 wt% to 0.450 wt%, and a CEN calculated by Expression 1 below range from 0.20% by mass to 0.85% by mass, the method including:
[0085] (a) during electric arc welding with gas protection, do not perform a preheating operation in the case where the temperature of the steel plate is 10 ° C or more, and in the case where the temperature of the steel sheet is lower than 10 ° C, perform the preheating operation so that the temperature of the steel sheet is 10 ° C or more,
[0086] (b) where the metal melting core wire contains one or more of CaF2, BaF2, SrF2, and MgF2, and when the sum of the quantities of these is β or β relative to the total mass of the metal melting core wire ranges from 3.3% to 8.0% in terms of mass%,
[0087] the metal fluxing core wire contains one or more of Ti oxides, Si oxides, Mg oxides, and Al oxides, and when the sum of their quantities is β o β in relation to the total mass of the wire melting core metal ranges from 0.10% to 1.50% in terms of% by mass,
[0088] a sum of the amounts of CaCO3, BaCO3, SrCO3, and MgCO3 in relation to the total mass of the melting core wire is less than 0.60% in terms of% by mass,
[0089] an amount of iron powder in the flux in relation to the total mass of the metallic flux wire is less than 10.0% in terms of% by mass,
[0090] a ratio of the amount of CaF2 to β is 0.90 or more,
[0091] a ratio of β to β is 3.0 or more and 80.0 or less,
[0092] an amount of CaO in relation to the total mass of the molten core metal wire is less than 0.20% in terms of% by mass,
[0093] the metal melting core wire includes chemical components excluding metal fluorides, metal oxides, and metal carbonates, in relation to the total mass of the metal melting core wire, in terms of% by mass:
[0094] C: 0.060% to 0.350%;
[0095] Si: 0.05% to 1.80%;
[0096] Mn: 0.50% to 4.00%;
[0097] P: 0.050% or less;
[0098] S: 0.020% or less;
[0099] Al: 0.005% to 0.150%;
[00100] Cu: 0% to 0.75%;
[00101] Ni: 0% less than 1.00%;
[00102] Cr: 0% to 3.50%;
[00103] Mo: 0% to 1.50%;
[00104] Ti: 0% to 0.150%;
[00105] Nb: 0% to 0.15%;
[00106] V: 0% to 0.45%;
[00107] B: 0% to 0.0500%;
[00108] Mg: 0% to 2.0%;
[00109] Ca: 0% to 2.0%;
[00110] REM: 0% to 0.0150%; and
[00111] the rest: Fe and impurities,
[00112] (c) where a solder joint weld metal includes as the chemical composition, in terms of% by mass:
[00113] C: 0.120% to 0.250%;
[00114] Si: 0.05% to 0.80%;
[00115] Mn: 0.20% to 2.50%;
[00116] Al: 0.0050% to 0.1000%;
[00117] P: 0.050% or less;
[00118] S: 0.020% or less;
[00119] N: 0.015% or less;
[00120] Cu: 0% to 0.50%;
[00121] Ni: 0% less than 0.70%;
[00122] Cr: 0% to 2.50%;
[00123] Mo: 0% to 1.00%;
[00124] Ti: 0% to 0.100%;
[00125] Nb: 0% to 0.100%;
[00126] V: 0% to 0.30%;
[00127] B: 0% to 0.0100%;
[00128] O: 0% to 0.100%;
[00129] Mg: 0% to 0.100%;
[00130] Ca: 0% to 0.100%;
[00131] REM: 0% to 0.0100%;
[00132] the rest: Fe and impurities,
[00133] the CEN of the weld metal calculated by Expression 1 below ranges from 0.20% by mass to 0.58% by mass,
[00134] the average Vickers HV hardness of the weld metal calculated at 1 mm from outside to inside from a weld metal surface ranges from 380 to 533, and
[00135] all items (a) to (c) are satisfied. CEN = [C] + (0.75 + 0.25xtanh (20x ([C] - 0.12))) x ([Si] / 24 + [Mn] / 6 + [Cu] / 15 + [Ni] / 20 + ([ Cr] + [Mo] + [Nb] + [V]) / 5 + 5x [B]) ... (Expression 1)
[00136] where the elements with [] represent the quantities (% by mass) of the corresponding elements.
[00137] (3) In accordance with a third aspect of the invention, a method is offered for the production of a solder joint by performing an arc welding with gaseous protection, using a flux-cored metallic wire filled with flux in a steel sheath, over any of a steel sheet having a Vickers HV hardness of more than 565 and 693 or less, a sheet thickness of 12 mm to 20 mm, a C content of 0.350% by weight at 0.450% by weight mass, and a CEN calculated by Expression 2 below from 0.20% by mass to 0.85% by mass, and a steel sheet having a Vickers HV hardness of more than 565 and 693 or less, a greater sheet thickness than 20 mm to 50 mm or less, a C content of 0.350 wt% to 0.450 wt%, and a CEN calculated by Expression 2 below 0.20 wt% to 0.85 wt%, the method including:
[00138] (a) during electric arc welding with gas protection, perform a preheating operation so that the temperature of the steel plate is 100 ° C or more in the case where the plate thickness of the plate steel is 20 mm or less, and in the case where the sheet thickness of the steel sheet is greater than 20 mm, perform the preheating operation so that the temperature of the steel sheet is 150 ° C or more,
[00139] (b) where the melting core metal wire contains one or more of CaF2, BaF2, SrF2, and MgF2, and when the sum of the amounts of these is β or β relative to the total mass of the melting core metal wire ranges from 3.3% to 8.0% in terms of% by weight, [00140] the metal fluxing core wire contains one or more of Ti oxides, Si oxides, Mg oxides, and Al oxides, and when the sum of their quantities is β or β in relation to the total mass of the melting core metal wire, it varies from 0.10% to 1.50% in terms of% by mass,
[00140] the metal fluxing core wire contains one or more of Ti oxides, Si oxides, Mg oxides, and Al oxides, and when the sum of the amounts of these is β o β in relation to the total mass of the wire melting core metal ranges from 0.10% to 1.50% in terms of% by mass,
[00141] a sum of the amounts of CaCO3, BaCO3, SrCO3, and MgCO3 in relation to the total mass of the melting core wire is less than 0.60% in terms of% by mass,
[00142] an amount of iron powder in the flux in relation to the total mass of the metallic flux wire is less than 10.0% in terms of% by mass,
[00143] a ratio of the amount of CaF2 to β is 0.90 or more,
[00144] a ratio of β to β is 3.0 or more and 80.0 or less,
[00145] an amount of CaO in relation to the total mass of the molten core metal wire is less than 0.20% in terms of% by mass,
[00146] the metal melting core wire includes chemical components excluding metal fluorides, metal oxides, and metal carbonates, in relation to the total mass of the metal melting core wire, in terms of% by mass:
[00147] C: 0.060% to 0.350%;
[00148] Si: 0.05% to 1.80%;
[00149] Mn: 0.50% to 4.00%;
[00150] P: 0.050% or less;
[00151] S: 0.020% or less;
[00152] Al: 0.005% to 0.150%;
[00153] Cu: 0% to 0.75%;
[00154] Ni: 0% less than 1.00%;
[00155] Cr: 0% to 3.50%;
[00156] Mo: 0% to 1.50%;
[00157] Ti: 0% to 0.150%;
[00158] Nb: 0% to 0.15%;
[00159] V: 0% to 0.45%;
[00160] B: 0% to 0.0500%;
[00161] Mg: 0% to 2.0%;
[00162] Ca: 0% to 2.0%;
[00163] REM: 0% to 0.0150%;
[00164] the rest: Fe and impurities,
[00165] (c) where a weld metal of the weld joint includes as the chemical composition, in terms of% by mass:
[00166] C: 0.120% to 0.250%;
[00167] Si: 0.05% to 0.80%;
[00168] Mn: 0.20% to 2.50%;
[00169] Al: 0.0050% to 0.1000%;
[00170] P: 0.050% or less;
[00171] S: 0.020% or less;
[00172] N: 0.015% or less;
[00173] Cu: 0% to 0.50%;
[00174] Ni: 0% less than 0.70%;
[00175] Cr: 0% to 2.50%;
[00176] Mo: 0% to 1.00%;
[00177] Ti: 0% to 0.100%;
[00178] Nb: 0% to 0.100%;
[00179] V: 0% to 0.30%;
[00180] B: 0% to 0.0100%;
[00181] O: 0% to 0.100%;
[00182] Mg: 0% to 0.100%;
[00183] Ca: 0% to 0.100%;
[00184] REM: 0% to 0.0100%; and
[00185] the rest: Fe and impurities,
[00186] the CEN of the weld metal calculated by Expression 2 below varies from 0.20% by mass to 0.58% by mass,
[00187] the average Vickers HV hardness of the weld metal calculated at 1 mm from outside to inside from a weld metal surface ranges from 380 to 533, and
[00188] all items (a) to (c) are satisfied. CEN = [C] + (0.75 + 0.25xtanh (20x ([C] - 0.12))) x ([Si] / 24 + [Mn] / 6 + [Cu] / 15 + [Ni] / 20 + ([ Cr] + [Mo] + [Nb] + [V]) / 5 + 5x [B]) ... (Expression 2)
[00189] where the elements with [] represent the quantities (% by mass) of the corresponding elements.
[00190] (4) In the method for producing a solder joint described in items (1) to (3), the amount of CaO in the metal fluxing core wire can be 0.15% or less in terms of % by mass in relation to the total mass of the melting core metal wire.
[00191] (5) In the method for producing a solder joint described in any of items (1) to (4), the metal fluxing core wire may include chemical components excluding metal fluorides, metal oxides, and metallic carbonates, in relation to the total mass of the molten core metal wire, in terms of% by mass:
[00192] Ni: 0% to 0.1%.
[00193] (6) In the method for producing a solder joint described in any of items (1) to (5), the metal fluxing core wire may include chemical components excluding metal fluorides, metal oxides, and metallic carbonates, in relation to the total mass of the molten core metal wire, in terms of% by mass:
[00194] Cu: 0% to 0.50%;
[00195] Cr: 0% to 1.00%;
[00196] Mo: 0% to 0.50%;
[00197] Ti: 0% to 0.050%; and
[00198] Nb: 0% to 0.05%.
[00199] (7) In the method for producing a solder joint described in any of items (1) to (6), the steel sheath of the melting core metal wire may have a groove similar to the groove.
[00200] (8) In the method for producing a solder joint described in any of items (1) to (6), the steel sheath of the melting core metal wire may not have a slot similar to the groove.
[00201] (9) In the method for producing a solder joint described in any of items (1) to (8), a perfluoropolyether oil can be applied to a surface of the melting core metal wire. [EFFECTS OF THE INVENTION]
[00202] According to the aspects of the present invention, it is possible to obtain a weld joint using a high hardness steel plate having a high C content and a surface hardness of HV380 or more and HV693 or less with a metal of base, and has a weld metal that has a surface hardness of HV320 or more and HV533 or less and excellent abrasion resistance and does not cause cold cracking easily, or a probe metal that has a surface hardness of HV380 or more and HV533 or less and excellent abrasion resistance and does not easily cause cold cracking. [BRIEF DESCRIPTION OF THE DRAWINGS]
[00203] FIG. 1 is a diagram showing the relationship between the hardness of a base metal, the amount of diffusible hydrogen in the weld metal, and a preheating temperature limit for crack prevention.
[00204] FIG. 2 is a diagram showing the relationship between a CEN and a preheating temperature limit for preventing cracking in the weld metal having an amount of diffusible hydrogen less than 1.0 ml / 100 g between weld metals having a hardness of HV337 or more and HV533 or less.
[00205] FIG. 3A is a view showing a cut section of a metallic wire.
[00206] FIG. 3B is a view showing a cut section of a metallic wire.
[00207] FIG. 3C is a view showing a cut section of a metallic wire. [MODALITIES OF THE INVENTION]
[00208] With respect to a weld joint that uses a high hardness steel plate as a base metal, the inventors found that when the amount of diffusible hydrogen in the weld metal immediately after welding is lower than 1 , 0 ml / 100 g as described above, a preheating temperature limit for low temperature cracking does not depend significantly on the weld metal and the sensitivity of the weld metal having a hardness of HV337 or more and HV533 or less and the weld metal having a hardness of HV380 or more and HV533 or less when cold cracking can be significantly reduced.
[00209] In addition, to enable the amount of diffusible hydrogen in the weld metal immediately after welding to be lower than 1.0 ml / 100 g, the inventors repeated the analysis varying the combination of the flux components of a metal wire melting core and mixing ratios.
[00210] As a result, it has been found that fluorides including CaF2 are particularly effective in reducing the amount of hydrogen, and the amount of diffusible hydrogen in the weld metal can be significantly reduced by allowing a certain amount of fluoride to be contained in the components of the flux, and the amount of diffusible hydrogen can be stably suppressed to be lower than 1.0 ml / 100 g by adjusting the amount of oxides and allowing the mixing ratios of fluorides and oxides to be within ranges predetermined.
[00211] The present invention was made based on the analyzes. In the following, an aspect of a method for producing a weld joint according to an embodiment will be described.
[00212] The present invention relates to a weld joint that is formed using a thick, high hardness steel sheet that is widely used as an abrasion resistant steel sheet, has a C content of 0.12 % to 0.45% in terms of% by mass, and a hardness of HV380 or more and HV693 or less as a base metal, and gas-shielded electric arc welding using steel plate.
[00213] In the present invention, the weld metal has a chemical composition like that of item (1) or (2) described above.
[00214] Below, the reasons why the chemical composition of the weld metal is limited are described. In the description that follows, "%" means "mass%" where not particularly specified. (C: 0.100% to 0.250%)
[00215] C is the element that most affects the hardness of the weld metal. When the hardness of the base metal is HV380 or more, it is preferable that the surface hardness of the weld metal is at least HV337 or more to ensure a degree of abrasion resistance for the weld metal. Therefore, the C content of the weld metal must be 0.100% or more. In addition, when the hardness of the base metal is HV380 or more, it is preferable that the surface hardness of the weld metal is also HV380 or more to ensure a degree of abrasion resistance similar to that of the base metal. In the case that the surface hardness of the weld metal needs to be HV380 or more, the C content of the weld metal needs to be 0.120% or more. However, when the C content is higher than 0.250%, the hardness of the weld metal is greater than HV533 and therefore the toughness of the weld metal can be reduced. Therefore, the upper limit of the C content is 0.250%. In addition, typically, the C content of the weld metal of a weld joint made using a metal fluxing core wire having a C content of 0.010% to less than 0.060%, which will be described below, is 0.100% 0.170%. To enable the base metal to stably acquire a hardness of HV380 or more, the lower limit of the C content should be 0.130% or 0.140%. In addition, to allow the weld metal to stably acquire toughness, the upper limit of the C content must be 0.230% or 0.210%. (Si: 0.05% to 0.80%)
[00216] Si is an antioxidant element and reduces the O content of the weld metal, and therefore a certain amount of Si is added to the flux to improve sharpness. Therefore, the Si content in the weld metal is also 0.05% or more. As needed, the lower Si content limit should be 0.10%, 0.15%, or 0.20%. When Si is contained in a proportion that is greater than 0.80%, the toughness of the weld metal can be deteriorated, and thus 0.80% is the upper limit of the Si content. To increase the hardness of the weld metal , the upper limit of the Si content should be 0.70%, 0.65%, 0.60%, or 0.50%. (Mn: 0.20% to 2.50%)
[00217] Mn forms MnS and therefore has an effect of suppressing the boundary heating of grains due to S, and therefore at least 0.20% or more of Mn is contained in the weld metal. In addition, Mn is an element that guarantees the temperability of the weld metal and is therefore effective in increasing strength. Therefore, in order to obtain hardness in a stable manner, 0.50% or more of Mn is preferably contained. To increase the hardness of the weld metal, the lower limit of the Mn content must be 0.60%, 0.70%, 0.80%, or 0.90%. On the other hand, when Mn is contained in a proportion of more than 2.50%, the sensitivity to bordering pebbles of the grains is increased, and thus the toughness of the weld metal is deteriorated. Therefore, 2.50% is the upper limit of the Mn content. To increase the hardness of the weld metal, the upper limit of the Mn content should be limited to 2.30%, 2.10%, 1.90%, 1.70%, or 1.50%. (Al: 0.0050% to 0.1000%)
[00218] Al is an antioxidant element and, like Si, reduces the O content of the weld metal, and therefore has an effect of improving the sharpness of the weld metal. Therefore, a certain amount of Al needs to be added to the flux. Typically, 0.0050% or more Al is contained in the weld metal of the weld joint made using the flux-cored metal wire in accordance with this embodiment. When the Al content is lower than 0.0050%, there is a concern that the low temperature toughness of the weld metal may be degraded. On the other hand, when Al is contained in a proportion of more than 0.1000%, Al forms nitrides or oxides and thus deteriorates the toughness of the weld metal. Therefore, 0.1000% is the upper limit of the Al content. To increase the hardness of the weld metal, the upper limit of the Al content must be limited to 0.0900%, 0.0800%, 0.0700% , or 0.0600%. (P: 0.050% or less)
[00219] P is an element of impurity and deteriorates toughness. Therefore, the P content needs to be reduced as much as possible. However, as a range in which an adverse effect of P on toughness is acceptable, the P content of the weld metal is limited to 0.050% or less. As necessary, the upper limit of the P content should be limited to 0.030%, 0.0250%, 0.0200%, or 0.0150%. The lower limit of the P content need not be limited. The lower limit of the P content is 0%. (S: 0.020% or less)
[00220] S is an impurity element, and when an excessive amount of S is present in the weld metal, both toughness and ductility are deteriorated, and so it is preferable that the S content is excessively reduced. As a range in which an adverse effect of S on toughness and ductility is acceptable, the S content of the weld metal is limited to 0.020% or less. As necessary, the upper limit of the S content should be limited to 0.015%, 0.010%, 0.008%, or 0.006%. The lower limit of the S content need not be limited. The lower limit of the S content is 0%. (N: 0.015% or less)
[00221] N is inevitably contained in the weld metal. However, when the N content is higher than 0.015%, AlN or coarse BN is formed and in this way the toughness is reduced. As the upper limit at which the effect of N on the weld metal is acceptable, the N content is limited to 0.015% or less. As necessary, the upper limit of the N content should be limited to 0.010%, 0.008%, or 0.006%. The lower limit of the N content does not need to be limited. The lower limit of the N content is 0%. (O: 0% to 0.100%)
[00222] O is inevitably contained in the weld metal. However, as a range in which an adverse effect of O on toughness and ductility is acceptable, the O content of the weld metal is limited to 0.100% or less. As needed, the upper limit of the O content should be 0.080%, 0.060%, 0.050%, or 0.040%. The lower limit of the O content need not be limited. The lower limit of the O content is 0%. (Cu: 0% to 0.50%)
[00223] Cu can improve the resistance and toughness of the weld metal and therefore can be contained as a selective element. However, when the Cu content is higher than 0.50%, the toughness can be reduced. Therefore, the Cu content of the weld metal is 0.50% or less. As necessary, the upper limit for the Cu content should be 0.40% or 0.30%. The lower limit of the Cu content should not be limited. Therefore, the lower limit of the Cu content is 0%. On the other hand, to obtain a sufficient strengthening effect, 0.10% or more of Cu must be contained in the weld metal. As a method of including Cu in the weld metal, there is a method of adding Cu to the surface coating of the sheath of the wire or to the flux as a single element or an alloying element, among others. (Ni: 0% to less than 0.70%)
[00224] Ni is considered to be an effective element in improving toughness and can be contained as a selective element. However, in the case where the C content is high, the Ni effect is limited, and since Ni is an expensive element, the Ni content in the weld metal is lower than 0.70%. As necessary, the upper limit of the Ni content should be 0.60%, 0.40%, or 0.20%. The lower limit of Ni content should not be limited. Therefore, the lower limit of the Ni content is 0%. On the other hand, in order to sufficiently obtain a tenacity-improving effect, 0.05% or more of Ni must be contained in the weld metal. (Cr: 0% to 2.50%)
[00225] Cr is an element that increases the hardenability and is effective in increasing the hardness of the weld metal, and therefore can be contained as a selective element. However, when Cr is contained in excess in a proportion of more than 2.50%, the toughness can be reduced. Therefore, 2.50% is the upper limit of the Cr content. As needed, the upper Cr content limit should be 1.50%, 1.00%, 0.70%, or 0.40%. The lower limit of Cr content should not be limited. Therefore, the lower limit of the Cr content is 0%. On the other hand, in the case of adding Cr in order to increase the hardness of the weld metal, in order to obtain the effect, 0.10% or more of Cr must be contained. (Mo: 0% to 1.00%)
[00226] Mo is an element that increases the hardenability and is effective in increasing the hardness of the weld metal, and therefore can be contained as a selective element. However, when Mo is contained in excess in a proportion of more than 1.00%, the toughness can be reduced. Therefore, 1.00% is the upper limit of the Mo content. As needed, the upper limit for Mo content should be 0.70%, 0.60%, 0.40%, or 0.20%. The lower limit of Mo content should not be limited. Therefore, the lower limit of the Mo content is 0%. On the other hand, in the case of adding Mo in order to increase the hardness, in order to obtain the effect, 0.05% or more of Mo must be contained. (Ti: 0% to 0.100%)
[00227] Ti is, like Al, effective as an antioxidant element, has an effect of reducing the O content of the weld metal, and therefore can be contained as a selective element. In addition, Ti is also effective in fixing N dissolved in solid ("solid-soluted N") and mitigating an adverse effect on toughness. However, when the Ti content in the weld metal is greater than 0.100% and is therefore excessive, the possibility of deterioration of toughness due to the formation of coarse oxides and deterioration of toughness due to strengthening by excessive precipitation is increased. Therefore, the upper limit of the Ti content is 0.100%. As needed, the upper limit of the Ti content should be 0.080%, 0.050%, 0.030%, or 0.020%. The lower limit of the Ti content should not be limited. Therefore, the lower limit of the Ti content is 0%. In order to improve toughness, 0.010% or more of Ti must be contained. (Nb: 0% to 0.100%)
[00228] Nb is soluble in solid ("solid-soluted") in the weld metal and has an effect of improving the hardness of the weld metal, and therefore can be contained as a selective element. However, when Nb is contained in a proportion of more than 0.100%, Nb is excessively contained in the weld metal, forms coarse precipitates, and therefore deteriorates toughness, which is not preferable. Therefore, the upper limit of the Nb content is 0.100%. As needed, the upper limit of the Nb content should be 0.080%, 0.050%, 0.030%, or 0.020%. The lower limit of the Nb content should not be limited. Therefore, the lower limit of the Nb content is 0%. In order to increase the hardness of the weld metal, 0.010% or more of Nb must be contained. (V: 0% to 0.30%)
[00229] V is an element that increases the hardenability and is effective in increasing the hardness of the weld metal, and therefore can be contained as a selective element. However, when V is in excess in a proportion of more than 0.30%, the toughness can be reduced. Therefore, the upper limit of the V content is 0.30%. As needed, the upper limit for the V content should be 0.25%, 0.20%, or 0.15%. The lower limit of the V content should not be limited. Therefore, the lower limit of the V content is 0%. In order to increase the hardness of the weld metal, 0.01% or more of V must be contained. (B: 0% to 0.0100%)
[00230] When an appropriate amount of B is contained in the weld metal, B is bonded to the N dissolved in solid and forms BN, and therefore has an effect of reducing the adverse effect of soluble N on the toughness. In addition, B increases temperability and contributes to improving strength, and therefore can be contained as a selective element. To achieve this effect, 0.0003% or more of B must be contained. On the other hand, when the B content is higher than 0.0100%, B is excessively contained in the weld metal, forms coarse BN or B compounds such as Fe23 (C, B) 6, and therefore deteriorates the toughness, which is not preferable. Therefore, the upper limit of the B content in the case of including B is 0.0100%. As needed, the upper limit of the B content should be 0.0080%, 0.0060%, 0.0040%, or 0.0020%. The lower limit of the B content need not be limited, and the lower limit of the B content is 0%. (Mg: 0% to 0.100%)
[00231] The lower limit of the Mg content does not need to be limited, and the lower limit of the Mg content is 0%. However, Mg is a strong antioxidant element and therefore reduces the O content in the weld metal, and 0.001% or more of Mg must be contained to improve the weld metal's ductility and toughness. However, when the Mg content in the weld metal is higher than 0.100%, a reduction in toughness due to the formation of coarse oxides in the weld metal cannot be overlooked. Therefore, even if Mg is included, the Mg content is 0.100% or less. As needed, the upper limit for the Mg content should be 0.0080%, 0.0060%, 0.0040%, or 0.0020%. (Ca: 0% to 0.100%) (REM: 0% to 0.0100%)
[00232] The lower limits of the amounts of Ca and REM need not be limited, and the lower limits of the amounts of Ca and REM are 0%. However, both Ca and REM change the structure of sulfides in the weld metal to refine the sizes of sulfides and oxides and are therefore effective in improving ductility and toughness, and therefore 0.002% or more of Ca and 0.0002 % or more of REM must be contained. On the other hand, when Ca and REM are contained in excess, the sulfides and oxides become thicker and cause deterioration in ductility and toughness. Therefore, in the case of including Ca and REM, the upper limits of the content of Ca and REM are 0.100% and 0.0100%, respectively.
[00233] In the weld metal having the chemical composition above, the rest containing iron (Fe) as its main component may also contain impurities that are incorporated during the production process, among others, in a range in which the characteristics of the gasket welding according to this modality are not harmed. (CEN: 0.20% by mass to 0.58% by mass)
[00234] As illustrated in FIG. 2, with respect to the weld metal having a hardness of HV380 or more and HV533 or less, when the amount of diffusible hydrogen in the weld metal is lower than 1.0 ml / 100 g, allowing the CEN calculated by Expression 1 is equal to 0.58% by mass or less, the preheat temperature limit for crack prevention can be 25 ° C or less in a y-groove weld crack test according to the standard JIS Z 3158, and therefore welding can be carried out substantially without preheating.
[00235] Here, in order to reliably prevent cracking of the weld, the upper limit of the CEN must be 0.55% by mass, 0.53% by mass, 0.50% by mass, 0.47% by mass , or 0.45% by weight. To enable the hardness of the weld metal to be HV380 or more, the lower limit of the CEN is 0.20% by mass. When the hardness of the weld metal is high, the abrasion resistance is improved. Therefore, the lower limit of the CEN should be 0.24% by mass, 0.28% by mass, 0.30% by mass, or 0.32% by mass.
[00236] (a) A base metal in which the Vickers HV hardness of the base metal is HV380 or more and HV514 or less (corresponding to HB360 or more and HB475 or less), the plate thickness of the base metal is 20 mm to 100 mm, the C content of the base metal is 0.120% to 0.300%, and the CEN calculated by Expression 1 is from 0.20% by mass to 0.75% by mass.
[00237] (b) A base metal in which the Vickers HV hardness of the base metal is higher than HV514 and equal to or lower than HV565 (corresponding to more than HB475 and equal to or lower than HB530), the thickness of The base metal plate is 12 mm to 100 mm, the C content of the base metal is 0.120% to 0.300%, and the CEN calculated by Expression 1 is 0.20% by mass to 0.75% by mass.
[00238] (c) A base metal in which the Vickers HV hardness of the base metal is higher than HV565 and equal to or lower than HV693 (corresponding to more than HB530 and equal to or lower than HB650), the thickness of The base metal plate is 6 mm to 12 mm, the C content of the base metal is 0.350% to 0.450%, and the CEN calculated by Expression 1 is 0.20% by mass to 0.85% by mass.
[00239] With respect to the base metal that satisfies any of the items (a) to (c) described above, in the case where the temperature of the base metal is 10 ° C or more during electric arc welding with gaseous protection, it is not necessary to perform a preheating operation during welding. However, in the case where the temperature of the base metal is lower than 10 ° C, a preheating operation needs to be carried out so that the temperature of the base metal reaches 10 ° C or more. That is, only in the case where the temperature of the base metal (steel plate) is lower than 10 ° C, the preheating operation needs to be carried out for the temperature of the base metal (steel plate) to reach at 10 ° C or more. The upper temperature limit (preheating temperature) of the base metal does not need to be particularly determined and can be less than 75 ° C or less than 50 ° C.
[00240] (d) A base metal in which the Vickers HV hardness of the base metal is higher than HV565 and equal to or lower than HV693 (corresponding to more than HB530 and equal to or lower than HB650), the thickness of The base metal plate is 12 mm to 20 mm, the C content of the base metal is 0.350% to 0.450%, and the CEN calculated by Expression 1 is 0.20% by mass to 0.85% by mass.
[00241] (e) A base metal in which the Vickers HV hardness of the base metal is higher than HV565 and equal to or lower than HV693 (corresponding to more than HB530 and equal to or lower than HB650), the thickness of The base metal plate is 20 mm to 50 mm, the C content of the base metal is 0.350% to 0.450%, and the CEN calculated by Expression 1 is 0.20% by mass to 0.85% by mass.
[00242] With respect to the base metal that satisfies item (d) or (e) described above, in the case where the base metal plate thickness is 20 mm or less during arc welding with gas protection , preheating is performed to heat the base metal to 100 ° C or more. In the case where the base metal plate thickness is greater than 20 mm, preheating is performed to heat the base metal to 150 ° C or more. The upper temperature limit (preheating temperature) of the base metal does not need to be particularly determined and can be less than 175 ° C or less than 150 ° C. To obtain a Vickers hardness of HV380 or more, the CEN is allowed to be 0.20% by mass. CEN = [C] + (0.75 + 0.25xtanh (20x ([C] - 0.12))) x ([Si] / 24 + [Mn] / 6 + [Cu] / 15 + [Ni] / 20 + ([ Cr] + [Mo] + [Nb] + [V]) / 5 + 5x [B]) ... (Expression 1)
[00243] Here, elements with [] represent the quantities (% by mass) of the corresponding elements.
[00244] In Expression 1, with respect to the elements that are not contained, [] corresponding to the elements is replaced by zero. This calculation method is common for the base metal (steel plate) and the weld metal.
[00245] In the present invention, an average Vickers hardness of the weld metal measured at 1 mm from outside inward from the surface thereof is HV337 or more and HV533 or less, or HV380 or more and HV533 or less. In the present invention, the amount of diffusible hydrogen in the weld metal immediately after welding is lower than 1.0 ml / 100 g.
[00246] When the hardness measured at a position 1 mm from outside to inside the surface is HV337 or more and HV533 or less, an abrasion resistance requirement that is necessary for the weld metal is satisfied. When the hardness is lower than HV337, the abrasion resistance is insufficient. When the hardness is higher than HV533, cold cracking is likely to occur.
[00247] To measure the hardness, the weld metal section is cut in a direction perpendicular to the welding direction and polished to obtain a sample, the 10-point Vickers hardness of the sample in a position 1 mm from outside to inside The weld metal surface is measured, and its average value is calculated to obtain the hardness.
[00248] With respect to the amount of diffusible hydrogen in the weld metal immediately after welding, as described above with reference to FIG. 1, when the amount of diffusible hydrogen is lower than 1.0 ml / 100 g, the preheating temperature limit to prevent cracking at low temperature does not depend significantly on the hardness of the weld metal, and the sen -sensitivity of the weld metal having a hardness of HV337 or more and HV533 or less and of the weld metal having a hardness of HV380 or more and HV533 or less when cold cracking can be significantly reduced.
[00249] The amount of diffusible hydrogen is measured by a gas chromatography method based on the JIS Z 3118 standard (method for measuring the amount of hydrogen released from steel welds in 2007).
[00250] In addition, the hydrogen diffusion speed is relatively fast at room temperature, and therefore the amount of diffusible hydrogen in the weld metal needs to be measured immediately after welding. Therefore, the amount of diffusible hydrogen cannot be measured accurately unless it is measured immediately after welding.
[00251] To produce a weld joint having the weld metal described above, thick steel sheets of high hardness to be welded are used as the base metal, and two plates of the base metal are placed in the welding position to form a groove between them, electric arc welding with gaseous protection is carried out on them using a flux-cored metal welding wire to generate weld metal between the base metal plates, so that a weld joint formed of the weld metal and from the steel plates to the base metal on both sides of the weld metal is formed.
[00252] Next, the steel plate, the flux-cored metal weld wire, and the welding conditions used to form the weld metal will be described.
[00253] As the steel sheet is the base metal, a high hardness thick steel sheet having a C content of 0.120% or more and 0.450% or less in terms of mass% and a hardness of HV380 is used or more and HV693 or less.
[00254] Regarding the plate thickness of the steel plate to be used, a steel plate having a thickness of 6 mm or more and 100 mm or less, generally called thick plate, is employed.
[00255] Steel sheet that satisfies such conditions is widely used where abrasion resistance is required, such as a machine for civil engineering and construction works, and its chemical composition is not particularly limited except for the C content. However, as an example, steel includes as a chemical composition:
[00256] C: 0.120% to 3.000%, Si: 0.10% to 0.55%, Mn: 0.20% to 2.00%, Al: 0.01% to 0.10%, P: 0.020 % or less, S: 0.015% or less, Cu: 0.50% or less, Ni: 1.00% or less, Cr: 1.20% or less, Mo: 0.60% or less, Nb: 0 , 05% or less, V: 0.10% or less, and B: 0.0050% or less. In addition, steel in which the CEN calculated by Expression 1 is 0.20% by mass to 0.85% by mass is used.
[00257] The upper limit of the CEN is 0.85% by mass, so as not to cause cracking of the weld in the area affected by the heat (HAZ) of the base metal. To more reliably prevent weld cracking at HAZ, the upper limit of the CEN should be 0.80% by mass, 0.75% by mass, 0.73% by mass, 0.70% by mass, 0 , 68% by mass, 0.65% by mass, 0.63% by mass, or 0.60% by mass. To enable the hardness of the base metal to be HV380 or more, the lower limit of the CEN is 0.20% by mass. To increase the hardness of the base metal, the lower limit of the CEN should be 0.24% by mass, 0.28% by mass, 0.30% by mass, 0.32% by mass, 0.35% by weight. mass, or 0.38% by mass. The CEN of a steel plate in which the base metal hardness is HV565 or less generally does not exceed 0.75% by weight. Therefore, the upper limit of the CEN of a steel plate in which the hardness of the base metal is HV565 or less is 0.75% by weight.
[00258] As a method for measuring the hardness of the base metal, a method for measuring the Vickers hardness of five or more points in a position 1 mm from the outside inward from the surface of the base metal section towards sheet thickness and obtain the average value of the same is used.
[00259] Subsequently, with regard to the flux-cored metal welding wire to be used, the flux components and the alloy components thereof will be described separately. The component quantities in the description of the flux-cored solder wire represent the% by mass relative to the total mass of the flux-cored solder wire.
[00260] Initially, the components of the flux inserted in a steel sheath of the metallic wire will be described.
[00261] Including a predetermined amount of one type or two or more types of metal fluorides including CaF2, BaF2, SrF2, and MgF2 and one type or two or more types of metal oxides including Ti oxides (for example, TiO2 ), Si oxides (for example, SiO2), Mg oxides (for example, MgO), and Al oxides (for example, Al2O3) in the weld wire and allowing the fluoride and oxide ratios to be within a predetermined range, the amount of hydrogen diffusible in the weld metal is stably less than 1.0 ml / 100 g.
[00262] The requirements for obtaining this effect are, when the total amount of CaF2, BaF2, SrF2, and MgF2 that is contained is β allow the total amount DD in relation to the total mass of the melting core wire in terms of% in mass is 3.3% or more and 8.0% or less, when the total amount of Ti oxides, Si oxides, Mg oxides, and Al oxides contained is β allow the total amount β in relation to total mass of the molten core metal wire in terms of% by mass is 0.10% or more and 1.50% or less, allowing the ratio of CaF2 to β content to be 0.90 or more, and allow ratio ([total amount α] / [total amount β]) of the total amount β to the total amount β is 3.0 or more and 80.0 or less.
[00263] When the total amount β of the metal fluorides contained is lower than 3.3%, the amount of diffusible hydrogen in the weld metal cannot be stably less than 1.0 ml / 100 g. To further reduce the amount of diffusible hydrogen in the weld metal, the lower limit of the total amount β must be 3.5%, 3.7%, or 3.9%. When the total amount β is higher than 8.0%, exhalation or welding slag is formed in excess, and therefore the welding workability is significantly degraded, which is not preferable. In order to avoid excessive generation of exhalations or welding slag, the upper limit of the total amount β must be 7.5%, 7.0%, 6.5%, 6.0%, or 5.7%. When the total amount β of the metal oxides contained is less than 0.10%, the shape of the welding beads can be deteriorated. When the total amount β is higher than 1.50%, the toughness can be degraded. To improve the shape of the welding beads, the lower limit of the total amount β must be 0.20%, 0.30%, 0.40%, or 0.50%. To improve toughness, the upper limit of the total amount β must be 1.30%, 1.20%, 1.10%, 1.00%, 0.90%, or 0.80%.
[00264] In addition, when the ratio of the total amount α to the total amount β is lower than 3.0, the amount of diffusible hydrogen in the weld metal must not be stably less than 1.0 ml / 100 g. When their ratio is higher than 80.0, exhales or welding slag are generated in excess, and therefore the welding workability is significantly degraded, which is not preferable. To further reduce the amount of diffusible hydrogen in the weld metal, the lower limit of the ratio ([total amount α] / [total amount β]) should be 3.2, 3.5, 3.7, or 4.0. To avoid excessive generation of exhalations or welding slag, the upper limit of the ratio ([total amount α] / [total amount β]) should be 40.0, 30.0, 20.0, 15.0, or 13.0. In the case where the ratio of CaF2 to β content is lower than 0.90, the amount of diffusible hydrogen in the weld metal must not be less than 1.0 ml / 100 g. This is because CaF2 has the greatest effect in reducing the amount of diffusible hydrogen between metal fluorides. A situation in which the ratio of CaF2 to β is maximized means a case in which no metal fluoride other than CaF2 is contained in the flux. Therefore, the upper limit of the ratio of CaF2 to α is 1.0.
[00265] Therefore, the total amount β of the metal fluorides contained, the total amount β of the metal oxides, and the ratio of the total amount β of the metal fluorides to the total amount β of the metal oxides are limited as described above.
[00266] In addition, the total amount β is the content in the metal fluxing core wire, and the content is also obtained by adding metal fluorides contained in a binder (sodium silicate containing mainly SiO2) used to granulate the flux, among others .
[00267] To the melting core welding wire according to this modality, one or two or more types of metallic carbonates including CaCO3, BaCO3, SrCO3, and MgCO3 can be added in order to improve an arc stabilizing effect and the arc concentration. However, when one type or two or more types of metal carbonates are added in a proportion of 0.60% or more, the arc concentration becomes too strong, and therefore the amount of burr generated is increased. In addition, the amount of oxygen in the weld metal is increased. Therefore, in the case of including metal carbonates, the sum of the amounts of metal carbonates is less than 0.60%. The lower limit of the sum of the quantities of metal carbonates is 0%. To suppress the amount of burr generated, the upper limit must be 0.50%, 0.40%, 0.20%, or 0.10%.
[00268] The reason why metal fluorides reduce the amount of diffusible hydrogen is not necessarily clear. However, it is believed that metal fluorides are decomposed by the welding arc and the generated fluorine is bound to hydrogen and spreads in the air as HF gas, or hydrogen is attached to the weld metal as HF in the state it is in. finds.
[00269] In the present invention, it is preferable that CaO is not added to the flux. Therefore, the lower limit of the CaO content is 0%. However, there may be cases where CaO is contained in the flux raw material. In this case, the CaO content is limited to less than 0.20%. The CaO content is preferably 0.15% or less or 0.10% or less. When the CaO content is limited to less than 0.20%, the effects according to the method for producing a weld joint according to this modality are obtained. CaO comes into contact with air and becomes CaOH. Therefore, there is a possibility that CaO may increase the amount of diffusible hydrogen in the weld metal.
[00270] The quantities of alloying elements in the metal fluxing core wire excluding metal fluorides, metal oxides, and metal carbonates are limited as follows.
[00271] (C: 0.010% to 0.350% in the case where the average Vickers HV hardness of the weld metal measured at 1 mm from outside to inside from the surface varies from 337 to 440, and 0.060% to 0.350% in the case where the average Vickers HV hardness of the weld metal measured at 1 mm from outside to inside from the surface ranges from 380 to 533)
[00272] When the C content in the metal fluxing core wire is lower than 0.010%, the C content of the weld metal is lower than 0.100%, and therefore the hardness of the weld metal is lower than HV337 . Therefore, the C content in the melting core wire is 0.010% or more. When the C content in the molten core wire is lower than 0.060%, the C content of the weld metal is lower than 0.120%, and therefore the hardness of the weld metal is lower than HV380. Therefore, to allow the hardness of the weld metal to be HV380, the C content in the metal fluxing core wire is 0.060% or more. To increase the hardness of the weld metal, the lower limit of the C content must be 0.020% or 0.030%. To further increase the hardness of the weld metal, the lower limit of the C content may be 0.070%, 0.080%, 0.090%, 0.100%, or 0.110%. When the C content in the metal fluxing core wire is greater than 0.350%, the C content of the weld metal is greater than 0.250%. Therefore, the C content in the melting core wire is 0.350% or less. To increase the resistance to cold cracking of the weld metal, the upper limit of the C content should be 0.300%, 0.250%, 0.180%, 0.170%, or 0.160%.
[00273] (Si: 0.05% to 1.80%)
[00274] When the Si content in the metal fluxing core wire is lower than 0.05%, the Si content of the weld metal is lower than 0.05%. Therefore, the Si content in the metal fluxing core wire is 0.05% or more. To reduce the content of the weld metal, the lower limit of the Si content should be 0.10%, 0.20%, 0.30%, or 0.40%. When the Si content in the molten core metal wire is greater than 1.80%, the Si content of the weld metal is greater than 0.80% even when oxidative consumption is considered. Therefore, the Si content in the melting core wire is 1.80% or less. To increase the hardness of the weld metal, the upper limit of the Si content must be 1.50%, 1.20%, 1.00%, 0.80%, or 0.60%.
[00275] (Mn: 0.50% to 4.00%)
[00276] When the Mn content in the metal fluxing core wire is lower than 0.50%, the Mn content of the weld metal is lower than 0.20%. Therefore, the Mn content in the metal fluxing core wire is 0.50% or more. To increase the hardness of the weld metal, the lower limit of the Mn content must be 0.70%, 0.80%, 0.90%, 1.00%, or 1.10%. When the Mn content in the metal fluxing core wire is greater than 4.00%, the Mn content of the weld metal is greater than 2.50% even when oxidative consumption is considered. Therefore, the Mn content in the metal fluxing core wire is 4.00% or less. To increase the hardness of the weld metal, the upper limit of the Mn content must be 3.00%, 2.50%, 2.20%, 2.00%, or 1.80%.
[00277] (P: 0.050% or less)
[00278] When the P content in the metal fluxing core wire is higher than 0.050%, the P content of the weld metal can be higher than 0.050%. Therefore, the P content in the melting core wire is 0.050% or less. As needed, the upper limit of the P content can be limited to 0.030%, 0.025%, 0.020%, or 0.015%. The lower limit of the P content need not be limited. The lower limit of the P content is 0%.
[00279] (S: 0.020% or less)
[00280] When the S content in the metal fluxing core wire is higher than 0.020%, the S content of the weld metal can be higher than 0.020%. Therefore, the content of S in the melting core wire is 0.020% or less. As needed, the upper limit of the S content can be limited to 0.015%, 0, 010%, 0.008%, or 0.006%. The lower limit of the S content need not be limited. The lower limit of the S content is 0%.
[00281] (Al: 0.005% to 0.150%)
[00282] When the Al content in the metal fluxing core wire is lower than 0.005%, the Al content of the weld metal is lower than 0.005%. Therefore, the content of Al in the metal fluxing core wire is 0.005% or more. To further reduce the content of the weld metal, the lower limit of the Al content should be 0.007%, 0.010%, or 0.012%. When the Al content in the flux-coring wire is higher than 0.150%, the Al content of the weld metal may be higher than 0.100%. Therefore, the content of Al in the metal fluxing core wire is 0.150% or less. To increase the hardness of the weld metal, the upper limit of the Al content can be limited to 0.090%, 0.070%, 0.050%, or 0.040%.
[00283] (Cu: 0% less than or equal to 0.75%)
[00284] When the Cu content in the metal fluxing core wire is higher than 0.75%, the Cu content of the weld metal is higher than 0.50%. Therefore, the Cu content in the melting core wire is 0.75% or less. To further reduce the Cu content of the weld metal, the Cu content should be 0.50% or less. As necessary, the upper limit for the Cu content should be 0.40% or 0.30%. The lower limit of the Cu content may not be limited. Therefore, the lower limit of the Cu content is 0%. On the other hand, to increase the hardness of the weld metal, 0.10% or more of Cu may be contained in the weld metal.
[00285] (Ni: 0% less than 1.00%)
[00286] When the Ni content in the molten core metallic wire is 1.00% or more, the Ni content of the weld metal is equal to 0.70% or more, and the cost of the alloy of the metallic wire is increased. Therefore, the Ni content in the metal fluxing core wire is lower than 1.00%. To prevent cracking by solidification of the weld metal, the upper limit of the Ni content should be 0.50%, 0.40%, 0.30%, 0.20%, or 0.10%. The lower limit of Ni content may not be limited. Therefore, the lower limit of the Ni content is 0%.
[00287] (Cr: 0% to 3.50%)
[00288] When the Cr content in the molten core metal wire is higher than 3.50%, the Cr content of the weld metal is higher than 2.50%. Therefore, the Cr content in the melting core wire is 3.50% or less. As needed, the upper Cr content limit should be 1.50%, 1.00%, 0.50%, or 0.10%. The lower limit of Cr content may not be limited. Therefore, the lower limit of the Cr content is 0%. On the other hand, in the case of adding Cr in order to increase the hardness of the weld metal, in order to obtain the effect, 0.05% or more of Cr may be contained.
[00289] (Mo: 0% to 1.50%)
[00290] When the Mo content in the molten core metal wire is higher than 1.50%, the Mo content of the weld metal is higher than 1.00%. Therefore, the Mo content in the melting core wire is 1.50% or less. To increase hardness, the upper limit for Mo content should be 0.70%, 0.50%, 0.30%, or 0.20%. The lower limit of Mo content may not be limited. Therefore, the lower limit of the Mo content is 0%. On the other hand, in the case of adding Mo in order to increase the hardness of the weld metal, in order to obtain the effect, 0.05% or more of Mo may be contained.
[00291] (Ti: 0% to 0.150%)
[00292] When the Ti content in the metal fluxing core wire is higher than 0.150%, the Ti content of the weld metal is higher than 0.100%. Therefore, the Ti content in the metal fluxing core wire is 0.150% or less. To increase hardness, the upper limit of the Ti content should be 0.100%, 0.080%, or 0.050%. The lower limit of Ti content may not be limited. Therefore, the lower limit of the Ti content is 0%. In order to increase toughness, 0.010% or more of Ti may be contained.
[00293] (Nb: 0% to 0.15%)
[00294] When the Nb content in the metal fluxing core wire is higher than 0.15%, the Nb content of the weld metal is higher than 0.10%. Therefore, the Nb content in the metal fluxing core wire is 0.15% or less. To increase hardness, the upper limit of the Nb content must be 0.10%, 0.08%, or 0.05%. The lower limit of the Nb content may not be limited. Therefore, the lower limit of the Nb content is 0%. In order to increase the hardness of the weld metal, 0.01% or more of Nb may be contained.
[00295] (V: 0% to 0.45%)
[00296] When the V content in the molten core metal wire is higher than 0.45%, the V content in the weld metal is higher than 0.30%. Therefore, the V content in the melting core wire is 0.45% or less. To increase hardness, the upper limit of the V content must be 0.25%, 0.20%, or 0.15%. The lower limit of the V content may not be limited. Therefore, the lower limit of the V content is 0%. In order to increase the hardness of the weld metal, 0.01% or more of V may be contained.
[00297] (B: 0% to 0.0500%)
[00298] When the B content in the metal fluxing core wire is higher than 0.0500%, the B content of the weld metal is higher than 0.0100%. Therefore, the B content in the deep core metal wire is 0.0500% or less. To increase the hardness, the upper limit of the B content must be 0.0400%, 0.0200%, 0.0100%, or 0.0050%. The lower limit of the B content need not be limited, and the lower limit of the B content is 0%.
[00299] (Mg: 0% to 2.0%)
[00300] When the Mg content of the flux-cored wire is higher than 2.0%, the Mg content of the weld metal is higher than 0.10%. Therefore, the Mg content in the metal fluxing core wire is 2.0% or less. To increase the toughness and ductility of the weld metal, the upper limit of the Mg content should be 1.5%, 1.0%, 0.4%, or 0.2%. The lower limit of the Mg content does not need to be limited, and the lower limit of the Mg content is 0%.
[00301] (Ca: 0% to 2.0%)
[00302] When the Ca content in the molten core metal wire is higher than 2.0%, the Ca content of the weld metal is higher than 0.10%. Therefore, the Ca content in the metal fluxing core wire is 2.0% or less. To increase the toughness and ductility of the weld metal, the upper limit of the Ca content must be 1.5%, 1.0%, 0.5%, or 0.3%. The lower limit of Ca content does not need to be limited, and the lower limit of Ca content is 0%.
[00303] (REM: 0% to 0.0150%)
[00304] When the REM content in the metal fluxing core wire is higher than 0.0150%, the REM content of the weld metal is higher than 0.0100%. Therefore, the REM content in the melting core wire is 0.0150% or less. To increase the toughness and ductility of the weld metal, the upper limit of the REM content should be 0.0100%, 0.0050%, or 0.0030%. The lower limit of the REM content need not be limited, and the lower limit of the REM content is 0%.
[00305] The reason why the chemical composition of the metal fluxing core wire according to this modality is limited outside described above. With regard to the other chemical composition of the remaining alloys, the remainder containing mainly Fe may also contain impurities that are incorporated during the production process, among others, in a range in which the characteristics of the weld joint according to this modality are not affected. The Fe component contains Fe in the steel sheath, and Fe in the form of iron powder and alloy components added to the flux. The iron powder content in the flux is lower than 10.0% in terms of% by weight relative to the total mass of the flux-coring wire. When the iron powder content is increased, there may be some case where the amount of oxygen is also increased. As needed, the iron powder content can be lower than 5.0% or less than 1.0%. Since the iron powder does not need to be contained, the lower limit of the iron powder content is 0%.
[00306] Next, the morphology of the melting core metal wire will be described.
[00307] The metal flux-cored wire is mainly divided into a seamless metal wire (that is, a wire in which the seams of the steel sheath are welded together) in which groove-like seams are not formed in the sheath steel, and a metallic thread with seams in which the seams of the steel sheath have a slot similar to the groove. The present invention can employ any sectional structure. However, to suppress the cold cracking of the weld metal, a seamless groove-like metallic wire (seamless wire) is preferable.
[00308] Hydrogen infiltrating the weld zone during welding is dispersed in the weld metal and the steel side is accumulated in a stress concentration zone, and acts as a cause of the occurrence of cold cracking. As the source of hydrogen, mention is made of the humidity maintained in the welding material, the moisture incorporated from the air, rust or crusts adhered to the steel surface, among others. However, during welding in which the cleaning of the welding zone and the conditions of the protective gas are sufficiently controlled, the hydrogen contained in the metallic wire, mainly in the form of moisture, becomes the main cause of diffusible hydrogen that is present in the gasket. weld.
[00309] Therefore, it is preferable that a seamless (seamless) pipe similar to the groove is used as the steel sheath to suppress hydrogen infiltration in the air from the steel sheath to the flux until the metal wire is used afterwards to be produced. In the case where a (seamed) tube with groove-like seams is used as the steel sheath, moisture in the air easily seeps into the flux from the groove-like seams (sewn portion) of the sheath. Therefore, when such a tube is used as is, infiltration of the hydrogen source such as moisture cannot be avoided. Therefore, in the event that a period of time from production to use is long, it is preferable that the inner wire is vacuum-packed, that is, stored in a container that can be kept in a dry state.
[00310] In addition, to improve the transport performance of the wire, there may be a case in which lubricating oil is applied to the surface of the wire. From the point of view of reducing the amount of dispersible hydrogen, such as lubricating oil applied to the surface of the metallic wire, oil that does not contain hydrogen such as perfluorolether oil (PFPE) is preferable.
[00311] The metal melting core wire used in the present invention can be produced by the same production process as that of a typical method of producing a metal melting core wire.
[00312] That is, first, a steel strip that will transform into the sheath, and a flux in which metal fluorides, alloy components, metal oxides, metal carbonates, and an arc stabilizer are mixed to have predetermined levels prepared. . While the steel strip is transported in its longitudinal direction, the steel strip is transformed into an open tube (U shape) by a forming cylinder to be used as the steel sheath, the flux is supplied from the opening of the tube opened during forming, and the faces of the opening edges opposite each other are subjected to dotted seam welding. A seamless tube obtained by welding is stretched, and is quenched during drawing or after the drawing process is completed, thereby obtaining a (seamless) tube having a desired wire diameter without groove-like seams. In addition, a metallic wire (with seam) having groove-like seams is obtained by supplying a flux from the open tube opening to be shaped like a seamed tube that is not subjected to seam welding, and tube stretching . A cutting section of the metal wire without groove-like cracks, which is done by dotted seam welding, is illustrated in FIG. 3A. When the section is polished and etched, traces of welding are observed. However, when the section is not etched, traces of welding are not observed. Therefore, the section can be said to be "seamless". On p.111 of "New Edition of Introduction to Welding and Joining Techniques" (2008) edited by "the Japan Welding Society" and published by Sanpo Publications Incorporated, a seamless type is described. As illustrated in FIG. 3B, when brazing is performed after butt joining, or as illustrated in FIG. 3C, when brazing is performed after caulking, metallic wires without grooves similar to the groove can also be obtained. In FIGS. 3B and 3C, the metallic wires that are not subjected to brazing and are used as they are become metallic wires having grooves similar to the groove.
[00313] In the present invention, electric arc welding with gaseous protection as multilayer welding is carried out on the steel sheet using the metal flux-coring wire that meets the conditions described above to form weld metal that satisfies the conditions described above, way reaching the goal. The gas arc welding method with gas protection is not particularly limited, and a method typically used can be employed. For example, as the protective gas, as well as 100% CO2 gas, a mixed gas of 3% by volume to 20% by volume of CO2 gas and Ar gas, or similar can be used. The flow rate of the protective gas can be in typical conditions, that is, about 15 L / min to 30 L / min.
[00314] In addition, with regard to welding conditions such as current, voltage, among others, for example, a current of 200 A to 350 A, a voltage of 25 V to 35 V, among others can be used. The welding rate can be controlled in order to allow welding heat input ranging from 10 kJ / cm to 50 kJ / cm.
[00315] The shape of the solder joint produced is determined depending on the application or similar and is not particularly limited. Weld joints in which a groove is formed, such as a typical butt joint, a corner joint, and a T joint can be applied. Therefore, the shape of the steel plate to be welded can be shaped so that at least a portion of it in which the weld joint is formed is shaped like a plate, and the shape may not be entirely the shape of a plate . For example, cast steel can also be included. In addition, the steel sheet is not limited to several steel sheets, and a single steel sheet can be transformed into a predetermined shape such as the shape of a tube. However, a butt weld joint can also be used. [EXAMPLES]
[00316] In the following, the applicability and effects of the weld joint according to this modality will be described with reference to the Examples.
[00317] Steel sheets having the components shown in Table 1 were used as base metals. In addition, as reinforcement metals for welding, the same steel plates as the base metals were used.
[00318] While a steel strip was transported in its longitudinal direction, the steel strip was transformed into an open tube by a forming cylinder, a flux was supplied from the opening of the open tube during forming, and the edge faces from the opening opposite each other they were subjected to dotted seam welding, thus forming a seamless tube similar to the groove. During the work of drawing a metallic wire from the formed tube, a hardening was carried out, thus producing a melting core metal wire with a final wire diameter of Φ 1.2 mm. In addition, some of the steel sheets were turned into tubes having seams similar to the groove that were not subjected to seam welding, and the tubes were stretched, thereby producing metal wires with a melting core having a wire diameter of Φ 1, 2 mm. In the case of the metallic wire having grooves similar to the groove, the entire metallic wire was vacuum packed and stored in a container so that it could be kept in a dry state until the welding was carried out.
[00319] The chemical components of the produced melting core metal wire were analyzed as follows. First, the filler flux was extracted from the metal flux-cored wire, and the metal flux-cored wire was separated into the steel sheath and the flux. The chemical components of the steel sheath were obtained by measuring the content of each of the metallic components by means of chemical analysis. The chemical components of the flux were analyzed in the following order. First, the constituent materials and components of the flux were subjected to quantitative evaluation by X-ray diffraction and fluorescent X-ray spectroscopy. Then, the flux was separated into a slag and an alloy content using a separation method such as flotation or magnetic separation, and their chemical components were analyzed by performing chemical analysis, gas analysis, gas, or similar. The chemical compositions of the molten core metallic wire produced are shown in Tables 2-1-1 to 2-2, and in Tables 3-1-1 to 3-2.
[00320] The base metals were allowed to join buttocks together with a 16 mm root opening and a 20 ° groove angle using the flux-cored metal wire, and were welded using the reinforcement metal under the conditions of welding patterns shown in Tables 4-1-1 to 4-2-3. On the grooved surface surfaces of the base metal and the reinforcement metal, greasing of two or more layers and an excessive height of weld metal of 3 mm or more was carried out using the tested melting core wire.
[00321] Here, as Ti oxides, Si oxides, Mg oxides, and Al oxides, TiO2, SiO2, MgO, and Al2O3 were respectively used. In Tables 2-2 to 2-4, metal carbonates include CaCO3, Ba-CO3, SrCO3, and MgCO3.
[00322] The results of the analysis of the chemical compositions of the solder metals obtained are shown in Tables 5-1-1, 5-1-2, 52-1, 5-2-2, 5-2-4, and 5- 2-5. A sample of a polished section of the weld metal, which is perpendicular to the welding direction, was obtained, and the Vickers hardness of 10 points of the sample in a position 1 mm from outside to inside the weld metal surface was measured, and was converted to Brinell hardness using the SAE J417 hardness conversion table (1983). In addition, a Charpy test piece No. 4 (V notch of 2 mm) based on JIS Z3111 (2005) was obtained, and the energy absorbed Charpy from the weld metal at -40 ° C was measured. An energy absorbed at -40 ° C of 27 J or more has been assessed as approved.
[00323] The results obtained from the hardness and the Charpy test are shown in Tables 5-1-3, 5-2-3, and 5-2-6.
[00324] In addition, a cold crack test and a test to measure the amount of dispersible hydrogen were performed on each of the solder joints obtained under the same welding conditions. Like the cold crack test, a test based on the JIS Z 3158 standard (y-groove cold crack test method in 1993) was performed at room temperature (25 ° C), and the absence of cracks in surfaces and sections was assessed as approved. The test to measure the amount of dispersible hydrogen was carried out according to a gas chromatography method based on the JIS Z 3118 standard (method for measuring the amount of hydrogen released from steel welds in 2007). An amount of dispersible hydrogen of less than 1.0 ml / 100 g was assessed as approved.
[00325] The results are shown in Tables 5-1-3, 5-2-3, and 5-2-6.
[00326] During welding, a significant level of generation of exhalations or slag was assessed as poor welding workability. A low level of generation of exhales or slag was evaluated as good welding workability. The results are shown in Tables 5-1-3, 5-2-3, and 5-2-6.
[00327] As shown in the test results of Table 5-1-3, the weld metals of Examples 1 to 54 which are examples of the present invention were excellent in all items ranging from hardness, toughness, resistance to cold cracking, and welding workability and therefore passed the tests.
[00328] On the other hand, as shown in the test results of Tables 5-2-3 to 5-2-6, the weld metals of Comparative Examples 101 to 165 did not meet the requirements specified in the present invention and at least one of the items of hardness, toughness, resistance to cold cracking, and welding workability did not pass the tests. The numbers underlined in the Comparative Examples of Tables 5-2-1 to 5-2-6 represent values outside the ranges of the present invention. TABLE 1
TABLE 2-1-1


TABLE 2-1-2


PFPE; perfluorpolyether oil ** with seam: the steel sheath having the shape of a gap similar to the groove TABLE 2-2



TABLE 3-1-1


TABLE 3-1-2

TABLE 3-2


TABLE 4-1-1



TABLE 4-1-2



TABLE 4-2-1


TABLE 4-2-2


TABLE 4-2-3



TABLE 5-1-1



TABLE 5-1-2



Note 1: Fe and impurities TABLE 5-1-3



TABLE 5-2-1

Note 1: Fe and impurities TABLE 5-2-2

Note 1: Fe and impurities TABLE 5-2-3

TABLE 5-2-4


Note 1: Fe and impurities TABLE 5-2-5


TABLE 5-2-6

[INDUSTRIAL APPLICABILITY]
[00140] According to the present invention, in a weld joint using a high hardness steel sheet having a C content and a surface hardness of HV380 or more and HV693 or less as a base metal, it is possible to obtain a weld metal that has a surface hardness of HV337 or more and HV533 or less and excellent abrasion resistance or a weld metal that has a surface hardness of HV380 or more and HV533 or less and excellent abrasion resistance without the occurrence of cracking cold even when no preheating is carried out. Consequently, the welding efficiency can be significantly increased, and therefore such a weld joint is extremely valuable in the industrial field.

权利要求:
Claims (9)
[0001]
1. Method for the production of a solder joint by performing an arc welding with gaseous protection, using a metal wire with a fluxing core filled with flux in a steel sheath, over any of a steel sheet having a Vickers HV hardness 380 or more and 514 or less, a sheet thickness from 20 mm to 100 mm, a C content of 0.120% by weight to 0.300% by weight, and a CEN calculated by Expression 1 below 0.20% in mass at 0.75% by mass, a steel sheet having a Vickers HV hardness of more than 514 and 565 or less, a sheet thickness from 12 mm to 100 mm, a C content of 0.120% by mass at 0.300% by mass, and a CEN calculated by Expression 1 below from 0.20% by mass to 0.75% by mass, and a steel plate having a Vickers HV hardness of more than 565 and 693 or less, a plate thickness from 6 mm to 12 mm, a C content of 0.350 wt% to 0.450 wt%, and a CEN calculated by Expression 1 after 0.20 wt% to 0.85 wt%, comprising:(a) during electric arc welding with gas protection, do not perform a preheating operation in the case where the steel plate temperature is 10 ° C or more, and in the case where the steel plate temperature is lower than 10 ° C, perform the preheating operation so that the temperature of the steel sheet is 10 ° C or more, (b) where the metal melting core wire contains one or more of CaF2, BaF2, SrF2, and MgF2, and when the sum of their quantities is α o α in relation to the total mass of the melting core metal wire varies from 3.3% to 8.0% in terms of% by mass, the metallic wire of Fusing core contains one or more of Ti oxides, Si oxides, Mg oxides, and Al oxides, and when the sum of their amounts is β or β relative to the total mass of the fluxing metal wire, it varies from 0 , 10% to 1.50% in terms of% by weight, a sum of the amounts of CaCO3, BaCO3, SrCO3, and MgCO3 in relation to the total mass of the melting core wire is less than 0.60% in term those of% by mass, an amount of iron powder in the flux in relation to the total mass of the metallic wire of the flux core is less than 10.0% in terms of% by mass, a ratio of the amount of CaF2 to α is 0.90 or more, a ratio of β to β is 3.0 or more and 80.0 or less, an amount of CaO in relation to the total mass of the melting core wire is less than 0.20% in terms of % by mass, the metal core flux includes as a chemical composition excluding metal fluorides, metal oxides, and metal carbonates, in relation to the total mass of the metal core flux, in terms of% by mass: C: 0.010% a less than 0.060%; Si: 0.05% to 1.80%; Mn: 0.50% to 4.00%; P: 0.050% or less; S: 0.020% or less; Al: 0.005% to 0.150%; Cu: 0% to 0.75%; Ni: 0% to less than 1.00%; Cr: 0% to 3.50%; Mo: 0% to 1.50%; Ti: 0% to 0.150%; Nb: 0% to 0.15%; V: 0% to 0.45%; B: 0% to 0.0500%; Mg: 0% to 2.0%; Ca: 0% to 2.0%; REM: 0% to 0.0150%; and the rest: Fe and impurities, (c) where a weld metal from the weld joint includes as the chemical composition, in terms of% by mass: C: 0.100% to 0.170%; Si: 0.05% to 0.80%; Mn: 0.20% to 2.50%; Al: 0.0050% to 0.1000%; P: 0.050% or less; S: 0.020% or less; N: 0.015% or less; Cu: 0% to 0.50%; Ni: 0% to less than 0.70%; Cr: 0% to 2.50%; Mo: 0% to 1.00%; Ti: 0% to 0.100%; Nb: 0% to 0.100%; V: 0% to 0.30%; B: 0% to 0.0100%; O: 0% to 0.100%; Mg: 0% to 0.100%; Ca: 0% to 0.100%; REM: 0% to 0.0100%; and the rest: Fe and impurities, the CEN of the weld metal calculated by Expression 1 below varies from 0.20% by mass to 0.58% by mass, the average Vickers HV hardness of the weld metal calculated at 1 mm outside to inside from a weld metal surface ranges from 337 to 440, and all items (a) to (c) are satisfied. CEN = [C] + (0.75 + 0.25xtanh (20x ([C] - 0.12))) x ([Si] / 24 + [Mn] / 6 + [Cu] / 15 + [Ni] / 20 + ([ Cr] + [Mo] + [Nb] + [V]) / 5 + 5x [B]) ... (Expression 1) where the elements with [] represent the quantities (% by mass) of the corresponding elements.
[0002]
2. Method for the production of a solder joint by performing an arc welding with gaseous protection, using a metallic wire of flux core filled with flux in a steel sheath, over any one of a steel sheet having a Vickers HV hardness 380 or more and 514 or less, a sheet thickness from 20 mm to 100 mm, a C content of 0.120% by weight to 0.300% by weight, and a CEN calculated by Expression 1 below 0.20% in mass at 0.75% by mass, a steel sheet having a Vickers HV hardness of more than 514 and 565 or less, a sheet thickness from 12 mm to 100 mm, a C content of 0.120% by mass at 0.300% by mass, and a CEN calculated by Expression 1 below from 0.20% by mass to 0.75% by mass, and a steel plate having a Vickers HV hardness of more than 565 and 693 or less, a plate thickness from 6 mm to 12 mm, a C content of 0.350 wt% to 0.450 wt%, and a CEN calculated by Expression 1 after 0.20 wt% to 0.85 wt%, comprising:(a) during electric arc welding with gas protection, do not perform a preheating operation in the case where the steel plate temperature is 10 ° C or more, and in the case where the steel plate temperature is lower than 10 ° C, perform the preheating operation so that the temperature of the steel sheet is 10 ° C or more, (b) where the metal melting core wire contains one or more of CaF2, BaF2, SrF2, and MgF2, and when the sum of their quantities is α o α in relation to the total mass of the melting core metal wire varies from 3.3% to 8.0% in terms of% by mass, the metallic wire of Fusing core contains one or more of Ti oxides, Si oxides, Mg oxides, and Al oxides, and when the sum of their amounts is β or β relative to the total mass of the fluxing metal wire, it varies from 0 , 10% to 1.50% in terms of% by weight, a sum of the amounts of CaCO3, BaCO3, SrCO3, and MgCO3 in relation to the total mass of the melting core wire is less than 0.60% in term those of% by mass, an amount of iron powder in the flux in relation to the total mass of the metallic flux wire is less than 10.0% in terms of% by mass, a ratio of the amount of CaF2 to β is 0 , 90 or more, a ratio of α to α is 3.0 or more and 80.0 or less, an amount of CaO in relation to the total mass of the melting core wire is less than 0.20% in terms of% in bulk, the metal fluxing core wire includes chemical components excluding metal fluorides, metal oxides, and metal carbonates, relative to the total mass of the metal fluxing core wire, in terms of% by weight: C: 0.060% to 0.350%; Si: 0.05% to 1.80%; Mn: 0.50% to 4.00%; P: 0.050% or less; S: 0.020% or less; Al: 0.005% to 0.150%; Cu: 0% to 0.75%; Ni: 0% to less than 1.00%; Cr: 0% to 3.50%; Mo: 0% to 1.50%; Ti: 0% to 0.150%; Nb: 0% to 0.15%; V: 0% to 0.45%; B: 0% to 0.0500%; Mg: 0% to 2.0%; Ca: 0% to 2.0%; REM: 0% to 0.0150%; and the rest: Fe and impurities, (c) where a weld metal from the weld joint includes as the chemical composition, in terms of% by mass: C: 0.120% to 0.250%; Si: 0.05% to 0.80%; Mn: 0.20% to 2.50%; Al: 0.0050% to 0.1000%; P: 0.050% or less; S: 0.020% or less; N: 0.015% or less; Cu: 0% to 0.50%; Ni: 0% to less than 0.70%; Cr: 0% to 2.50%; Mo: 0% to 1.00%; Ti: 0% to 0.100%; Nb: 0% to 0.100%; V: 0% to 0.30%; B: 0% to 0.0100%; O: 0% to 0.100%; Mg: 0% to 0.100%; Ca: 0% to 0.100%; REM: 0% to 0.0100%; the rest: Fe and impurities, the CEN of the weld metal calculated by Expression 1 below ranges from 0.20% by weight to 0.58% by weight, the average Vickers HV hardness of the weld metal calculated at 1 mm from the outside inward from a weld metal surface ranges from 380 to 533, and all items (a) to (c) are satisfied. CEN = [C] + (0.75 + 0.25xtanh (20x ([C] - 0.12))) x ([Si] / 24 + [Mn] / 6 + [Cu] / 15 + [Ni] / 20 + ([ Cr] + [Mo] + [Nb] + [V]) / 5 + 5x [B]) (Expression 1) where the elements with [] represent the quantities (% by mass) of the corresponding elements.
[0003]
3. Method for the production of a solder joint by performing an arc welding with gaseous protection, using a metal wire with a flux core filled with flux in a steel sheath, over any of a steel sheet having a Vickers HV hardness of more than 565 and 693 or less, a plate thickness from 12 mm to 20 mm, a C content of 0.350% by weight to 0.450% by weight, and a CEN calculated by Expression 2 below 0.20% in mass at 0.85% by mass, and a steel sheet having a Vickers HV hardness of more than 565 and 693 or less, a sheet thickness greater than 20 mm to 50 mm or less, a C content of 0.350% by mass at 0.450% by mass, and a CEN calculated by Expression 2 after 0.20% by mass at 0.85% by mass, characterized by comprising: (a) during electric arc welding with gas protection, perform a preheating operation so that the temperature of the steel sheet is 100 ° C or more in the case where the sheet thickness of the steel sheet is 20 mm or less os, and in the case where the plate thickness of the steel plate is higher than 20 mm, perform the preheating operation so that the temperature of the steel plate is 150 ° C or more, (b) where the wire melting core metal contains one or more of CaF2, BaF2, SrF2, and MgF2, and when the sum of their amounts is α o α in relation to the total mass of the melting core metal wire ranges from 3.3% to 8, 0% in terms of% by mass, the metal fluxing core wire contains one or more of Ti oxides, Si oxides, Mg oxides, and Al oxides, and when the sum of the quantities of these is β or β in The total mass of the molten core wire varies from 0.10% to 1.50% in terms of% by weight, a sum of the amounts of CaCO3, BaCO3, SrCO3, and MgCO3 in relation to the total mass of the metal wire melting core is less than 0.60% in terms of mass%, an amount of iron powder in the melting relative to the total mass of the melting core metal wire is less than 10.0% in terms of mass% a, a ratio of the amount of CaF2 to β is 0.90 or more, a ratio of α to β is 3.0 or more and 80.0 or less, an amount of CaO relative to the total mass of the metal wire melting core is less than 0.20% in terms of weight%, (c) melting core metal wire includes chemical components excluding metallic fluorides, metal oxides, and metallic carbonates, relative to the total mass of the core metal wire flux, in terms of mass%: C: 0.060% to 0.350%; Si: 0.05% to 1.80%; Mn: 0.50% to 4.00%; P: 0.050% or less; S: 0.020% or less; Al: 0.005% to 0.150%; Cu: 0% to 0.75%; Ni: 0% to less than 1.00%; Cr: 0% to 3.50%; Mo: 0% to 1.50%; Ti: 0% to 0.150%; Nb: 0% to 0.15%; V: 0% to 0.45%; B: 0% to 0.0500%; Mg: 0% to 2.0%; Ca: 0% to 2.0%; REM: 0% to 0.0150%; the rest: Fe and impurities, (c) where a weld metal of the weld joint includes as the chemical composition, in terms of% by mass: C: 0.120% to 0.250%; Si: 0.05% to 0.80%; Mn: 0.20% to 2.50%; Al: 0.0050% to 0.1000%; P: 0.050% or less; S: 0.020% or less; 1. 0.015% or less; Cu: 0% to 0.50%; Ni: 0% to less than 0.70%; Cr: 0% to 2.50%; Mo: 0% to 1.00%; Ti: 0% to 0.100%; Nb: 0% to 0.100%; V: 0% to 0.30%; B: 0% to 0.0100%; 2. 0% to 0.100%; Mg: 0% to 0.100%; Ca: 0% to 0.100%; REM: 0% to 0.0100%; and the rest: Fe and impurities, 3. CEN of the weld metal calculated by Expression 2 below ranges from 0.20% by weight to 0.58% by weight, the average Vickers HV hardness of the weld metal calculated at 1 mm from outside to inside from a weld metal surface ranges from 380 to 533, and all items (a) to (c) are satisfied. CEN = [C] + (0.75 + 0.25xtanh (20x ([C] - 0.12))) x ([Si] / 24 + [Mn] / 6 + [Cu] / 15 + [Ni] / 20 + ([ Cr] + [Mo] + [Nb] + [V]) / 5 + 5x [B]) (Expression 2) where the elements with [] represent the quantities (% by mass) of the corresponding elements.
[0004]
Method for the production of a weld joint according to any one of claims 1 to 3, characterized in that the amount of CaO in the metal fluxing core wire is 0.15% or less in terms of% in mass in relation to the total mass of the melting core metal wire.
[0005]
Method for the production of a weld joint according to any one of claims 1 to 4, characterized in that the metal flux-cored wire includes chemical components excluding metal fluorides, metal oxides, and metal carbonates, in in relation to the total mass of the molten core metal wire, in terms of% by mass: Ni: 0% to 0.1%.
[0006]
6. Method for the production of a solder joint according to any one of claims 1 to 5, characterized in that the metal flux-cored wire includes chemical components excluding metallic fluorides, metal oxides, and metal carbonates, in in relation to the total mass of the molten core metal wire, in terms of% by mass: Cu: 0% to 0.50%; Cr: 0% to 1.00%; Mo: 0% to 0.50%; Ti: 0% to 0.050%; and Nb: 0% to 0.05%.
[0007]
Method for the production of a solder joint according to any one of claims 1 to 6, characterized in that the steel sheath of the melting core metal wire does not have a groove-like gap.
[0008]
Method for the production of a weld joint according to any one of claims 1 to 6, characterized in that the steel sheath of the melting core metal wire has a groove-like gap.
[0009]
Method for the production of a solder joint according to any one of claims 1 to 8, characterized in that a perfluorpolyether oil is applied to a surface of the melting core metal wire.

类似技术:

---

公开号 | 公开日 | 专利标题

---

BR112015029349B1|2020-12-08|method for the production of weld joints

---

JP5644984B1|2014-12-24|Flux-cored wire, welding method using flux-cored wire, manufacturing method of welded joint using flux-cored wire, and welded joint

---

JP5565518B2|2014-08-06|Welding method, welded joint manufacturing method and welded joint

---

EP3427890B1|2021-06-02|Flux-cored wire, manufacturing method of welded joint, and welded joint

---

CA3011332C|2020-10-27|Flux-cored wire, manufacturing method of welded joint, and welded joint

---

JP6390204B2|2018-09-19|Flux-cored wire for gas shielded arc welding

---

JP5696824B1|2015-04-08|Manufacturing method of welded joint

---

JP6829111B2|2021-02-10|Filling material for TIG welding

---

JP2008168312A|2008-07-24|HIGH Ni FLUX-CORED WIRE HAVING EXCELLENT HIGH-TEMPERATURE CRACK RESISTANT CHARACTERISTIC, AND FILLET WELDING METHOD USING THE SAME

---

JP2017164768A|2017-09-21|HIGH Ni FLUX-CORED WIRE FOR GAS SHIELDED ARC WELDING AND METHOD OF MANUFACTURING WELDED JOINT

---

JP2001294992A|2001-10-26|Welded steel pipe excellent in gaseous co2 corrosion resistance and hydrogen sulfide cracking resistance

同族专利:

---

公开号 | 公开日

---

CA2915026A1|2015-05-14|

---

AU2014345139B2|2016-03-31|

---

KR101655057B1|2016-09-06|

---

CA2915026C|2016-10-04|

---

MX2015017087A|2016-04-11|

---

PH12015502625A1|2016-03-07|

---

MY158148A|2016-09-15|

---

WO2015068443A1|2015-05-14|

---

CN105339132A|2016-02-17|

---

CN105339132B|2017-04-12|

---

MX352525B|2017-11-29|

---

BR112015029349A2|2017-07-25|

---

PH12015502625B1|2016-03-07|

---

CA2926569C|2017-04-18|

---

WO2015068261A1|2015-05-14|

---

CA2926569A1|2015-05-14|

---

AU2014345139A1|2015-12-17|

---

KR20150136551A|2015-12-07|

引用文献:

---

公开号 | 申请日 | 公开日 | 申请人 | 专利标题

---

---

JP2687006B2|1989-02-18|1997-12-08|新日本製鐵株式会社|Flux-cored wire for gas shielded arc welding for refractory steel|

---

JPH08257785A|1995-01-23|1996-10-08|Nippon Steel Corp|Flux cored wire for arc welding to improve low temp. crack resistance of steel weld zone|

---

JPH08197283A|1995-01-23|1996-08-06|Nippon Steel Corp|Flux cored wire for mig welding by which high-toughness weld zone having lessened welding deformation is obtainable|

---

JP3354460B2|1997-11-11|2002-12-09|川崎製鉄株式会社|Covered arc welding method for high strength steel|

---

JP2001205483A|2000-01-19|2001-07-31|Nippon Steel Weld Prod & Eng Co Ltd|Flux-containing wire for gas shield arc welding|

---

JP4564245B2|2003-07-25|2010-10-20|新日本製鐵株式会社|Super high strength welded joint with excellent low temperature cracking property of weld metal and method for producing high strength welded steel pipe|

---

JP5136466B2|2008-03-28|2013-02-06|新日鐵住金株式会社|Flux-cored wire for welding high-strength steel and method for producing the same|

---

US8878099B2|2008-05-27|2014-11-04|Nippon Steel & Sumikin Stainless Steel Corporation|Flux cored wire for welding duplex stainless steel which refines solidified crystal grains|

---

EP2489461B1|2009-12-16|2016-04-13|Nippon Steel & Sumitomo Metal Corporation|Wire containing flux for gas-sealed arc welding, allowing all-position welding|

---

CN102753300B|2010-06-07|2014-04-30|新日铁住金株式会社|Ultra high-strength welded joint and method for producing same|

---

JP5607002B2|2011-02-02|2014-10-15|株式会社神戸製鋼所|Weld metal with excellent resistance to hydrogen embrittlement|

---

MX355893B|2011-02-14|2018-05-04|Nippon Steel & Sumitomo Metal Corp|Welded duplex stainless joint.|

---

JP5606985B2|2011-04-08|2014-10-15|株式会社神戸製鋼所|Weld metal with excellent resistance to hydrogen embrittlement|

---

EP2848355B1|2012-05-08|2018-01-03|Nippon Steel & Sumitomo Metal Corporation|Flux-containing wire for welding ultrahigh-tensile steel|

---

KR101616237B1|2013-01-31|2016-04-27|신닛테츠스미킨 카부시키카이샤|Flux cored wire, welding method using flux cored wire, method for producing welded joint using flux cored wire, and welded joint|MX2018010526A|2016-03-08|2018-11-09|Nippon Steel & Sumitomo Metal Corp|Flux-cored wire, weld joint manufacturing method and weld joint.|

---

EP3427890B1|2016-03-08|2021-06-02|Nippon Steel Corporation|Flux-cored wire, manufacturing method of welded joint, and welded joint|

---

GB2548175B|2016-03-09|2018-10-03|Goodwin Plc|A steel, a welding consumable and a cast steel product|

---

CN106346166A|2016-08-31|2017-01-25|晋城市金菲机电有限公司|Low-temperature preheating high-strength flux-cored wire and production process thereof|

---

JP6874425B2|2017-03-06|2021-05-19|日本製鉄株式会社|Manufacturing method of flux-cored wire and welded joint for gas shielded arc welding|

---

KR102134310B1|2017-12-26|2020-07-15|주식회사 포스코|Cold-rolled steel sheet for flux cored wire and manufacturing the same|

---

EP3753670A4|2018-03-28|2021-09-08|Nippon Steel Corporation|Method for manufacturing flux-cored wire, flux-cored wire and method for manufacturing welded joint|

---

AU2018416187A1|2018-03-28|2020-08-06|Nippon Steel Corporation|Method for manufacturing flux-cored wire, flux-cored wire and method for manufacturing welded joint|

---

CN108588572A|2018-07-27|2018-09-28|安徽卓煌机械设备有限公司|A kind of high strength easy welding grinding roller basis material|

---

CN109440011A|2018-12-27|2019-03-08|攀钢集团江油长城特殊钢有限公司|A kind of nitrogenous welding wire steel of vacuum induction furnace smelting low-alloy and its smelting process|

---

KR102233335B1|2019-02-26|2021-03-29|고려용접봉 주식회사|Smaw welded metal having excellent strength|

---

JPWO2020196875A1|2019-03-27|2020-10-01|

---

CN110819770B|2019-10-28|2021-08-20|鞍钢股份有限公司|Steel plate for large-thickness hydrogenation reactor shell and manufacturing method thereof|

---

WO2021125280A1|2019-12-20|2021-06-24|Ｊｆｅスチール株式会社|Steel wire for gas-shielded arc welding, gas-shielded arc welding method, and method for manufacturing gas-shielded arc welded joint|

---

US20210229204A1|2020-01-29|2021-07-29|Lincoln Global, Inc.|Systems and methods for multi-wire submerged arc welding using a flux-cored wire electrode|

法律状态:
2018-11-06| B06F| Objections, documents and/or translations needed after an examination request according art. 34 industrial property law|

---

2019-07-30| B06U| Preliminary requirement: requests with searches performed by other patent offices: suspension of the patent application procedure|

---

2019-09-10| B25D| Requested change of name of applicant approved|Owner name: NIPPON STEEL CORPORATION (JP) |

---

2020-08-18| B09A| Decision: intention to grant|

---

2020-12-08| B16A| Patent or certificate of addition of invention granted|Free format text: PRAZO DE VALIDADE: 20 (VINTE) ANOS CONTADOS A PARTIR DE 07/08/2014, OBSERVADAS AS CONDICOES LEGAIS. |

优先权:

---

申请号 | 申请日 | 专利标题

---

PCT/JP2013/080242|WO2015068261A1|2013-11-08|2013-11-08|Method for producing weld joint|

---

JPPCT/JP2013/080242|2013-11-08|

---

PCT/JP2014/070878|WO2015068443A1|2013-11-08|2014-08-07|Method for producing weld joint|

---