CN1332058A - Welding rod resulting in high fatigue strength of welded joint - Google Patents
Welding rod resulting in high fatigue strength of welded joint Download PDFInfo
- Publication number
- CN1332058A CN1332058A CN 01130810 CN01130810A CN1332058A CN 1332058 A CN1332058 A CN 1332058A CN 01130810 CN01130810 CN 01130810 CN 01130810 A CN01130810 A CN 01130810A CN 1332058 A CN1332058 A CN 1332058A
- Authority
- CN
- China
- Prior art keywords
- welding rod
- fatigue strength
- welding
- titanium
- ferromanganese
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Images
Landscapes
- Nonmetallic Welding Materials (AREA)
Abstract
The present invention aims at raising fatigue strength of welded joint and omitting post-welding machining. The coating of the welding rod consists of marble 20-35 wt%, fluorite 8-15 wt%, titanium white powder 2-5 wt%, ferromanganese 3-8 wt%, RE duriron 1-6 wt%, ferrotitanium 4-8 wt%, iron powder 2-6 wt%, quartz 2-6 wt%, metal Cr 13-28 wt%, metal Ni 10-25 wt%, argil 0.2-2 wt%, alkali powder 0.2-1 wt%, carboxymenthyl cellulose 0.2-1 wt%, and synthetic mica 0.2-2 wt%; and the core wire is made of H08A steel. The roast temperature and time of the welding rod is 350 deg.c and 2 hr. The welding rod can be used widely in welded structure to bear fatigue load, especially that with enormous number of weld seams.
Description
Technical field
The present invention relates to a kind of welding rod.
Technical background
Show that according to present statistics fatigue is welded main failure mode, its reason is that the stress of surface cracks at welding toe of joint is concentrated and the effect of residual-tensile stress, makes the fatigue strength of welding point be lower than the fatigue strength of base metal significantly.Therefore, in order to guarantee reliability of structure, when the Welding Structure of alternate load was born in design, regulation and stipulation was with the fatigue strength of the welding point fatigue strength of structure as a whole, and do not adopt the fatigue strength of base metal, and obviously this causes significant wastage.Even so, under the stress raisers effect of joint, integrally-built premature fatigue still can take place lost efficacy, bring about great losses, even human casualty accident.Therefore improving welded joint fatigue strength has great economic benefit and social benefit.At present, both at home and abroad about the main method that improves welded joint fatigue strength have that TIG moltenly amends the law, grinder buffing method, local machined method, ballistic method, hammering method, shot-peening method, transship method, local rolling process, explosion method, laser cladding method and Gunnert method or the like in advance.As above one common shortcoming is arranged is to belong to postwelding processing to method, and promptly postwelding increases by a procedure, especially for large welded structures spare, can greatly increase the amount of labour and labour cost.
Summary of the invention
The objective of the invention is to overcome shortcoming and defect of the prior art, providing a kind of need not process by postwelding, can reduce the welding rod of effective raising welded joint fatigue strength of the amount of labour and labour cost significantly.
The present invention is used to improve the welding rod of welded joint fatigue strength, is made up of core wire and coating, it is characterized in that, each component of described coating and weight percent content (%) are: marble 20-35, fluorite 8-15, titanium dioxide 2-5, ferromanganese 3-8, rare earth ferrosilicon 1-6, ferro-titanium 4-8, iron powder 2-6, quartzy 2-6, crome metal 13-28, metallic nickel 10-25, chalk 0.2-2, alkali face 0.2-1, carboxymethyl cellulose 0.2-1, synthetic mica 0.2-2.
The present invention is used to improve each component preferred content of welded joint fatigue strength covering of an electrode: marble 25-30, fluorite 9-12, titanium dioxide 2-4, ferromanganese 3-6, rare earth ferrosilicon 1-4, ferro-titanium 4-8, iron powder 2-6, quartzy 2-4, crome metal 19-25, metallic nickel 16-22, chalk 0.2-2, alkali face 0.2-1, carboxymethyl cellulose 0.2-1, synthetic mica 0.2-2.
The comparatively economic coating component content that the present invention is used to improve the welded joint fatigue strength welding rod is: marble 28-35, fluorite 11-15, titanium dioxide 3-5, ferromanganese 5-8, rare earth ferrosilicon 2-6, ferro-titanium 4-8, iron powder 2-6, quartzy 3-6, crome metal 13-20, metallic nickel 10-16, chalk 0.2-2, alkali face 0.2-1, carboxymethyl cellulose 0.2-1, synthetic mica 0.2-2.
The present invention is used to improve each component optimum content of welded joint fatigue strength covering of an electrode: marble 30, fluorite 12, titanium dioxide 2, ferromanganese 5, rare earth ferrosilicon 1, ferro-titanium 5, iron powder 2, quartz 3, crome metal 20, metallic nickel 17, chalk 1, alkali face 0.5, carboxymethyl cellulose 0.5, synthetic mica 1.
The general welding rod of welding rod of the present invention has great raising at fatigue strength with on fatigue life, and can remove the postwelding manufacturing procedure from, greatly reduces the amount of labour and labour cost.The present invention can be widely used in the Welding Structure of bearing fatigue load, especially the large welded structures of weld seam enormous amount, as bridge, steamer, oil platform, vehicles or the like, also can be used for the reparation of product fatigue fracture, have great economic and social benefit.Test result shows that the fatigue strength of the general welding rod of the welding rod of high-fatigue strength can improve 10%-40%, and can improve 2-25 times fatigue life.
Description of drawings
Fig. 1 is used to improve the welding rod of welded joint fatigue strength and the cooling expansion curve figure of common welding rod deposited metal.
The phase transition temperature of Fig. 2 weld metal is to the figure that influences of residual stress.
Fig. 3 fatigue strength is tested used test specimen figure.
Fig. 4 fatigue strength is tested used test specimen vertical view.
The specific embodiment
The invention will be further described below in conjunction with drawings and Examples.
Ferrous materials can produce structural transformation and follow volumetric expansion in cooling procedure, for most ferrous materials, Structural transformation (greater than plasticity temperature of material) under higher temperature finishes, and this moment, material was in mecystasis, thereby body Long-pending expansion can not affect welding residual stress. But for the ferrous materials of certain alloying component, its phase transformation starting point and end Point all appears at lower temperature, and this moment, material was in elastoplasticity or elastic stage, and the phase transformation volumetric expansion will reduce welding The residual-tensile stress that thermal field causes, the volumetric expansion amount is more big, residual-tensile stress is more little, in addition occur residual compression should Power, this will reduce the detrimental effect of residual-tensile stress Welded Joints fatigue strength, thereby improve the fatigue of welding point Intensity. The present invention will develop the welding rod that a kind of weld metal produces big phase change expansion amount at low temperatures, makes the weld seam gold The residual-tensile stress that belongs to reduces or produces compressive residual stress, is used for improving the fatigue strength of welding point.
The actual measurement cooling expansion curve of the present invention and common welding rod deposited metal as shown in Figure 1.
The cooling procedure of common E5015 welding rod changes along curve 1, and the structural transformation of its weld metal is 787 ℃ of beginnings, 630 ℃ of end, the phase change expansion strain only has 0.11%, and whole phase transition process does not have phase transformation all in mecystasis The generation of stress. After phase transformation finished, the weld metal volume continued to shrink, and along with reduction and the flexible recovery of temperature, draws Stretch that stress occurs and the yield strength (varying with temperature) that constantly increases to material is maintained to room temperature. Welding rod of the present invention is cold But process changes along curve 2 and 3, and before phase transformation, weld metal draws along with reduction and the flexible recovery of temperature Material yield intensity when stretching the stress appearance and constantly increasing to starting temperature of transformation. In starting temperature of transformation Ms point, Austria Family name's body begins to martensite transfor mation, but because martensite quantity is also less, the phase change expansion strain is not enough to offset Ovshinsky body temperature Degree contraction strain, curve continue to descend, until phase strain starting point Ts, curve begins to rise the i.e. phase transformation of weld metal Expansion strain just really begins, until phase strain end point Tf, T in theoryfRoom temperature should be equaled, the residual of maximum can be obtained The overbottom pressure stress under compression. MfBe martensite phase transformation end point. Phase change expansion dependent variable ε p is more big, and the remnants in the weld metal draw It is more little to stretch stress, and weld metal just may obtain compressive residual stress, thereby improves the fatigue strength of welding point. This The key that bright welding rod can make weld metal produce compression stress has 2 points: one, weld metal phase strain end point TfAt near room temperature, because at TfThe time phase expansion strain peak, at this moment can obtain maximum phase change expansion dependent variable. Its two: maximal phase variable expansion strain stress p should be greater than the tensile elasticity strain stress s of material.
The phase transition temperature of weld metal to the impact of residual stress as shown in Figure 2.
Welding rod weld structure of the present invention low-carbon martensite, obtaining martensitic purpose is to make weld seam at martensite Volumetric expansion during phase transformation produces compressive residual stress, and low-carbon martensite has the good comprehensive mechanical properties such as toughness. One As the deposited metal of austenite stainless steel-made welding rod (18-8,25-10,25-23 type), the scope of ni content is 8%-29%, The scope that contains the Cr amount is 16%-25%, and weld metal is always austenite in cooling procedure, do not have the martensite phase transformation.
According to above principle and analysis foundation, developed the raising that is used for that is suitable for mild steel and low-alloy high-strength steel use and welded The welding rod of joint fatigue strength. Core wire adopts H08A, adopts the multiple element alloying, by the coating transition alloy elements, With the base alloy system of Mn-Ni-Cr system as the development welding rod, coating is low hydorgew sodium type, and core wire and coating all should be controlled Phosphorus content is to guarantee the formation of weld metal low-carbon martensite.
As seen from Figure 1, when phase transition temperature is 191 ℃, the compressive residual stress value maximum of weld metal, weldering this moment The fatigue strength of joint is also the highest. Therefore be preferable range of the present invention at phase transition temperature 100-250 ℃. Among the embodiment L3-L6 is this type of welding rod, wherein the L5 best results.
Yet phase transition temperature is more low, requires the alloy content in the weld metal more high, and cost is more high comparatively speaking. By During 250-350 ℃ of martensitic phase height temperature range, the compressive residual stress of weld metal is with respect to 191 ℃ as can be known for Fig. 2 The time compressive residual stress be low, but but its alloy content decrease, then the welding rod cost also can decrease. For this reason, We are from economic angle and improve effect and consider, and design quality and satisfy as above requirement, the welding rod that cost is relatively low. L7-L10 welding rod among the embodiment is this type of welding rod.
Technology is mixed each component in above-described embodiment in proportion routinely, and utilizing modulus is that 3.0 potassium-sodium water glass stirs, Make welding rod at hydraulic press, core wire is the H08A steel, and diameter is 4.0mm, and the welding rod external diameter after the coating is 7.0mm, weldering Bar sintering temperature and time are 350 ℃ * 2 hours.
Electrode size also can adopt the specification of 3.2mm, and the welding rod external diameter after the coating is 5.4-5.8mm; If core wire adopts Diameter is 4.0mm, and the welding rod external diameter after the coating can be 6.8-7.2mm. Among the embodiment L1-L10, each component and weight percent content (%) see the following form.
| Embodiment | Marble | Fluorite | Titanium dioxide | Ferromanganese | Rare earth ferrosilicon | Ferro-titanium | Iron powder | Quartzy | Chalk | The alkali face | Carboxymethyl cellulose | Synthetic mica | Hafnium metal powfer | Metal nickel powder |
| L1 | 20 | 9 | 2 | 3 | 1 | 5 | 2 | 3 | 1 | 0.5 | 0.5 | 1 | 28 | 24 |
| L2 | 25 | 10 | 2 | 3 | 1 | 5 | 2 | 3 | 1 | 0.5 | 0.5 | 1 | 25 | 21 |
| L3 | 27 | 9 | 2 | 5 | 1 | 5 | 2 | 3 | 1 | 0.7 | 0.3 | 1 | 23 | 20 |
| L4 | 29 | 11 | 2 | 5 | 1 | 5 | 2 | 3 | 1 | 0.5 | 0.5 | 1 | 21 | 18 |
| L5 | 30 | 12 | 2 | 5 | 1 | 5 | 2 | 3 | 1 | 0.5 | 0.5 | 1 | 20 | 17 |
| L6 | 30 | 12 | 3 | 6 | 1 | 5 | 2 | 3 | 1 | 0.5 | 0.5 | 1 | 19 | 16 |
| L7 | 29 | 13 | 4 | 6 | 3 | 5 | 3 | 3 | 1 | 0.5 | 0.5 | 1 | 17 | 14 |
| L8 | 35 | 11 | 3 | 6 | 2 | 5 | 3 | 3 | 1 | 0.7 | 0.3 | 1 | 16 | 13 |
| L9 | 32 | 12 | 3 | 6 | 3 | 6 | 4 | 4 | 1 | 0.5 | 0.5 | 1 | 15 | 12 |
| L10 | 33 | 13 | 4 | 7 | 3 | 6 | 4 | 4 | 1 | 0.7 | 0.3 | 1 | 13 | 10 |
Deposited metal main component scope (%) and martensitic transformation temperature see the following form among above-mentioned each corresponding embodiment.
| Welding rod | C | Mn | Si | P | S | Cr | Ni | Mo | Nb | Fe | Ms/℃ |
| L1 | 0.05 | 1.10 | 0.33 | 0.007 | 0.007 | 11.40 | 10.37 | 0.04 | 0.01 | Surplus | 35 |
| L2 | 0.04 | 0.28 | 0.18 | 0.006 | 0.008 | 10.54 | 10.09 | 0.03 | 0.03 | Surplus | 80 |
| L3 | 0.05 | 1.12 | 0.21 | 0.009 | 0.008 | 10.50 | 10.03 | 0.04 | 0.03 | Surplus | 113 |
| L4 | 0.04 | 0.30 | 0.18 | 0.006 | 0.007 | 10.57 | 9.85 | 0.04 | 0.02 | Surplus | 144 |
| L5 | 0.07 | 1.25 | 0.23 | 0.012 | 0.015 | 9.10 | 8.46 | 0.05 | 0.01 | Surplus | 191 |
| L6 | 0.08 | 1.35 | 0.17 | 0.012 | 0.015 | 7.78 | 6.88 | 0.06 | 0.02 | Surplus | 231 |
| L7 | 0.07 | 1.30 | 0.23 | 0.012 | 0.017 | 6.30 | 5.29 | 0.04 | 0.01 | Surplus | 298 |
| L8 | 0.08 | 1.23 | 0.42 | 0.014 | 0.013 | 5.72 | 4.92 | 0.03 | 0.02 | Surplus | 312 |
| L9 | 0.09 | 1.51 | 0.47 | 0.017 | 0.015 | 5.07 | 4.43 | 0.05 | 0.01 | Surplus | 325 |
| L10 | 0.09 | 1.63 | 0.48 | 0.016 | 0.014 | 4.87 | 4.34 | 0.04 | 0.03 | Surplus | 345 |
The used test specimen of fatigue experiment as shown in Figure 3, Figure 4. Mainboard [1] is the Q235B steel plate of 190 * 60 * 8mm, Its gauge length section width is 40mm; Gusset joint plate [2] is the Q235B steel plate of 50 * 15 * 8mm. Employing has big remaining The longitudinal seam gusset joint plate welding point pattern that stress and big stress are concentrated is with welding rod of the present invention and E5015 welding rod difference Weld, angle welding [3] is welded together around gusset joint plate [2], about leg height 8mm, and arcing point and welding arc Put at the middle part of gusset joint plate [2] weld seam electric current I=160A. Carry out fatigue experiment 10 tons of high-cycle fatigue experimental machine, Frequency f=139Hz, Cyclic Stress compares r=0.1.
The fatigue experiment comparing result of the various embodiments described above and common E5015 welding rod is as follows.
| Embodiment | Fatigue strength improves (%) | Improve fatigue life (doubly) |
| L1 | 23 | 11 |
| L2 | 27 | 15 |
| L3 | 30 | 18 |
| L4 | 38 | 22 |
| L5 | 41 | 25 |
| L6 | 37 | 20 |
| L7 | 28 | 15 |
| L8 | 21 | 9 |
| L9 | 15 | 5 |
| L10 | 11 | 2 |
Claims (4)
1. a welding rod that is used to improve welded joint fatigue strength is made up of core wire and coating, it is characterized in that, each component of described coating and weight percent content (%) are: marble 20-35, fluorite 8-15, titanium dioxide 2-5, ferromanganese 3-8, rare earth ferrosilicon 1-6, ferro-titanium 4-8, iron powder 2-6, quartzy 2-6, crome metal 13-28, metallic nickel 10-25, chalk 0.2-2, alkali face 0.2-1, carboxymethyl cellulose 0.2-1, synthetic mica 0.2-2.
2. welding rod according to claim 1 is characterized in that, each constituent content of described coating is: marble 25-30, fluorite 9-12, titanium dioxide 2-4, ferromanganese 3-6, rare earth ferrosilicon 1-4, ferro-titanium 4-8, iron powder 2-6, quartzy 2-4, crome metal 19-25, metallic nickel 16-22, chalk 0.2-2, alkali face 0.2-1, carboxymethyl cellulose 0.2-1, synthetic mica 0.2-2.
3. welding rod according to claim 1 is characterized in that, each constituent content of described coating is: marble 28-35, fluorite 11-15, titanium dioxide 3-5, ferromanganese 5-8, rare earth ferrosilicon 2-6, ferro-titanium 4-8, iron powder 2-6, quartzy 3-6, crome metal 13-20, metallic nickel 10-16, chalk 0.2-2, alkali face 0.2-1, carboxymethyl cellulose 0.2-1, synthetic mica 0.2-2.
4. welding rod according to claim 1 is characterized in that, each constituent content of described coating is: marble 30, fluorite 12, titanium dioxide 2, ferromanganese 5, rare earth ferrosilicon 1, ferro-titanium 5, iron powder 2, quartz 3, crome metal 20, metallic nickel 17, chalk 1, alkali face 0.5, carboxymethyl cellulose 0.5, synthetic mica 1.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 01130810 CN1116957C (en) | 2001-08-24 | 2001-08-24 | Welding rod resulting in high fatigue strength of welded joint |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 01130810 CN1116957C (en) | 2001-08-24 | 2001-08-24 | Welding rod resulting in high fatigue strength of welded joint |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1332058A true CN1332058A (en) | 2002-01-23 |
| CN1116957C CN1116957C (en) | 2003-08-06 |
Family
ID=4670163
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN 01130810 Expired - Fee Related CN1116957C (en) | 2001-08-24 | 2001-08-24 | Welding rod resulting in high fatigue strength of welded joint |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN1116957C (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102248327A (en) * | 2011-06-27 | 2011-11-23 | 天津市金桥焊材集团有限公司 | High-corrosion-resistance, high-strength, high-toughness and high-weather-resistance welding rod |
| CN102581448A (en) * | 2012-02-01 | 2012-07-18 | 天津大学 | Welding process method for improving stress corrosion resistance of stainless steel pipe inner wall welding joint |
| CN106216884A (en) * | 2016-07-29 | 2016-12-14 | 安徽飞弧焊业股份有限公司 | A kind of Stability Analysis of Structures is without copper facing coating welding wire |
| CN111185691A (en) * | 2018-11-15 | 2020-05-22 | 天津大学 | High-toughness low-phase-change-point metal powder-cored welding wire |
| CN111195786A (en) * | 2018-11-19 | 2020-05-26 | 天津大学 | Low-phase-change-point welding material design method based on dilution rate |
-
2001
- 2001-08-24 CN CN 01130810 patent/CN1116957C/en not_active Expired - Fee Related
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102248327A (en) * | 2011-06-27 | 2011-11-23 | 天津市金桥焊材集团有限公司 | High-corrosion-resistance, high-strength, high-toughness and high-weather-resistance welding rod |
| CN102248327B (en) * | 2011-06-27 | 2012-12-26 | 天津市金桥焊材集团有限公司 | High-corrosion-resistance, high-strength, high-toughness and high-weather-resistance welding rod |
| CN102581448A (en) * | 2012-02-01 | 2012-07-18 | 天津大学 | Welding process method for improving stress corrosion resistance of stainless steel pipe inner wall welding joint |
| CN106216884A (en) * | 2016-07-29 | 2016-12-14 | 安徽飞弧焊业股份有限公司 | A kind of Stability Analysis of Structures is without copper facing coating welding wire |
| CN111185691A (en) * | 2018-11-15 | 2020-05-22 | 天津大学 | High-toughness low-phase-change-point metal powder-cored welding wire |
| CN111195786A (en) * | 2018-11-19 | 2020-05-26 | 天津大学 | Low-phase-change-point welding material design method based on dilution rate |
Also Published As
| Publication number | Publication date |
|---|---|
| CN1116957C (en) | 2003-08-06 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN1257789C (en) | Cored welding wire for lifting welding joint fatigue performance | |
| CN1257790C (en) | Solid welding wire for lifting welding joint fatigne performance | |
| CN107964626B (en) | A kind of yield strength 500MPa grade low-temp high tenacity is hot rolled H-shaped and preparation method thereof | |
| Eckerlid et al. | Fatigue properties of longitudinal attachments welded using low transformation temperature filler | |
| KR20220127335A (en) | Resistance spot welding method and manufacturing method of resistance spot welding seam | |
| US20140087320A1 (en) | Method of reheating rail weld zone | |
| CN100595016C (en) | Welding method of bainitic steel fork and carbon steel rail | |
| CN1116957C (en) | Welding rod resulting in high fatigue strength of welded joint | |
| CN103480976B (en) | A kind of high-intensity high-tenacity gas shield welding wire | |
| CN109530444A (en) | A kind of stainless steel roll of high-tensile 304 and processing technology | |
| CN1408504A (en) | Build-up welding chemical core wire for repairing cold rolling middle roller transition layer | |
| CN116145023A (en) | High-strength high-toughness high-extrusion-resistance sleeve and processing method thereof | |
| CN109365536A (en) | A kind of stainless steel roll of high stability 304 and preparation method | |
| Klimpel | The problem of welding cast irons is examined taking the example of a spheroidal cast iron | |
| CN115780979A (en) | Steel rail flash welding and joint heat treatment process of pearlite steel rail containing Cr, nb and RE | |
| CN112792127B (en) | Production process of CB890QL hot-rolled round steel for crawler crane boom | |
| JPH09279304A (en) | High strength steel wire with weld zone and its production | |
| CN116833539A (en) | Mobile gas pressure welding and joint heat treatment process for Nb and RE containing pearlitic steel rail | |
| CN117961224A (en) | Welding method of high manganese steel and maraging steel | |
| CN116770048A (en) | Fixed flash welding and joint heat treatment method for rare earth high-strength heat-treated steel rail | |
| CN117660736A (en) | Heat treatment method for 350HB grade steel rail welded joint | |
| DE19828048C2 (en) | Use of a nickel-martensitic steel alloy for chains and chain components | |
| JP2005262281A (en) | Welded joint excellent in fatigue life | |
| CN117020374A (en) | High-hardness 75N390 HB-level steel rail fixing flash welding and joint heat treatment method | |
| Kußmaul et al. | Characterization of the Cyclic Material Properties of Shape Welded Tempered and Quenched Steels 10 MnMoNi 5 5 and 20 NiCrMoV 14 5 |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| C19 | Lapse of patent right due to non-payment of the annual fee | ||
| CF01 | Termination of patent right due to non-payment of annual fee |