CN1932063A - High-strength low-welding crack sensitivity steel thick plate and production method thereof - Google Patents
High-strength low-welding crack sensitivity steel thick plate and production method thereof Download PDFInfo
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- CN1932063A CN1932063A CN 200510047196 CN200510047196A CN1932063A CN 1932063 A CN1932063 A CN 1932063A CN 200510047196 CN200510047196 CN 200510047196 CN 200510047196 A CN200510047196 A CN 200510047196A CN 1932063 A CN1932063 A CN 1932063A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 104
- 239000010959 steel Substances 0.000 title claims abstract description 104
- 238000003466 welding Methods 0.000 title claims abstract description 79
- 230000035945 sensitivity Effects 0.000 title claims abstract description 22
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 19
- 238000005096 rolling process Methods 0.000 claims abstract description 27
- 238000005516 engineering process Methods 0.000 claims abstract description 25
- 238000001816 cooling Methods 0.000 claims abstract description 22
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 17
- 238000001953 recrystallisation Methods 0.000 claims abstract description 16
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 14
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 13
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 13
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 11
- 239000000126 substance Substances 0.000 claims abstract description 11
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 11
- 238000005496 tempering Methods 0.000 claims abstract description 9
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 15
- 229910052720 vanadium Inorganic materials 0.000 claims description 13
- 229910052759 nickel Inorganic materials 0.000 claims description 12
- 238000010438 heat treatment Methods 0.000 claims description 10
- 229910052802 copper Inorganic materials 0.000 claims description 8
- 229910052750 molybdenum Inorganic materials 0.000 claims description 8
- 230000001186 cumulative effect Effects 0.000 claims description 6
- 230000000694 effects Effects 0.000 claims description 6
- 238000005098 hot rolling Methods 0.000 claims description 6
- 239000004615 ingredient Substances 0.000 claims description 6
- 238000010791 quenching Methods 0.000 claims description 6
- 230000000171 quenching effect Effects 0.000 claims description 6
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 6
- 239000010953 base metal Substances 0.000 claims description 5
- 238000002791 soaking Methods 0.000 claims description 4
- 238000003723 Smelting Methods 0.000 claims description 3
- 238000009749 continuous casting Methods 0.000 claims description 3
- 239000013078 crystal Substances 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 238000007670 refining Methods 0.000 claims description 3
- 238000010079 rubber tapping Methods 0.000 claims description 3
- 239000012535 impurity Substances 0.000 abstract description 2
- 238000012360 testing method Methods 0.000 description 29
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- 229910052751 metal Inorganic materials 0.000 description 15
- 230000032683 aging Effects 0.000 description 14
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- 238000000034 method Methods 0.000 description 12
- 239000000203 mixture Substances 0.000 description 4
- 238000010998 test method Methods 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
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- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical group CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 1
- 229910001563 bainite Inorganic materials 0.000 description 1
- 235000011089 carbon dioxide Nutrition 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 239000000498 cooling water Substances 0.000 description 1
- 229960000935 dehydrated alcohol Drugs 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 238000009434 installation Methods 0.000 description 1
- 239000011229 interlayer Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000003607 modifier Substances 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 238000004881 precipitation hardening Methods 0.000 description 1
- RMLPZKRPSQVRAB-UHFFFAOYSA-N tris(3-methylphenyl) phosphate Chemical compound CC1=CC=CC(OP(=O)(OC=2C=C(C)C=CC=2)OC=2C=C(C)C=CC=2)=C1 RMLPZKRPSQVRAB-UHFFFAOYSA-N 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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Abstract
The invention discloses a high-strength low-welding crack sensitivity steel thick plate and a production method thereof, which adopts the following chemical components (in percentage by weight): c: 0.06% -0.09%, Si: 0.15% -0.55%, Mn: 1.00% -1.60%, P: less than or equal to 0.015%, S: less than or equal to 0.006 percent, Ni: 0.15-0.40%, Cr: less than or equal to 0.30 percent, Mo: less than or equal to 0.30 percent, Cu: less than or equal to 0.30 percent, V: 0.02 to 0.06%, Nb: 0.005% -0.05%, Als: 0.010% -0.04%, the balance of Fe and inevitable impurities, and the chemical components of the steel must meet the following requirements: pcm is less than or equal to 0.20 percent; ceq is less than or equal to 0.42 percent, the maximum thickness of the produced steel plate can reach 75mm by adopting the technologies of austenite complete recrystallization region and austenite non-recrystallization region for controlling rolling, online laminar cooling, offline tempering and the like, and the tensile strength of the steel plate is more than or equal to 610 MPa.
Description
Technical field
The invention belongs to low alloy steel and make the field, it relates to a kind of steel for welded structures, specifically is that a kind of tensile strength is 610MPa level low welding crack sensibility high-strength steel and production method thereof.
Background technology
Before the present invention, the spy opens in clear 49-37814 communique and the special fair 4-13406 communique and has been disclosed as the reduction welding crack sensibility, the technology of falling C and adding Ti-B.So far, tensile strength 600MPa level low welding crack sensibility high-strength steel plate adopts the quenching and tempering type production technology basically, nearly all is by adding the hardening capacity that B guarantees steel.Guarantee the intensity of steel with B, increase the hardening capacity of steel, chemical ingredients and create conditions and will change may cause the hardness of mother metal unstable properties, particularly welded heat affecting zone to significantly improve.The raising of welded heat affecting zone hardness degenerates the toughness of welding welded bonds.
Open clear 60-9086 the spy, the spy opens flat 2-254119, and the spy opens clear 59-113120, and the spy opens the technology that has proposed not add B in the clear 61-12970 communique.
Wherein the spy opens clear 60-9086, Te Kaiping 2-254119, the technology that the spy opens in the clear 59-113120 communique all is the technology of the non-modified shaped steel of 600MPa level, but finds out that from embodiment the thickness of slab upper limit that these technology are suitable for all is about 20mm, and thicker steel plate is record not.
Te Kaiping 10-68045 communique is the production method with good welds crack sensitivity and large-line energy welding back HI high impact value steel of 570MPa high intensity levels.This armor plate strength is on the low side.And to Nb in the steel, V content (effectively Nb)+250V+210Ceq 〉=t+40 (t is steel plate thickness mm) is limited, so the thickness of steel plate also will be restricted with formula 625.
Just also not record of the production of domestic relevant thick steel plate with high strength and low welding crack sensitivity (the thickest reaching more than the 75mm) at present.
Summary of the invention
The purpose of this invention is to provide a kind of low-welding crack-sensitive Wide and Heavy Plates and production method thereof, steel plate tensile strength 〉=610MPa, the steel plate maximum width reaches 3900mm, and the steel plate maximum ga(u)ge reaches 75mm.Steel plate has the low-welding crack-sensitive excellent properties.
To achieve the above object, the present invention adopts following chemical ingredients (by weight percentage): C:0.06%～0.09%, Si:0.15%～0.55%, Mn:1.00%～1.60%, P: S≤0.015% :≤0.006%, Ni:0.15～0.40%, Cr: Mo≤0.30%: Cu≤0.30% :≤0.30%, V:0.02～0.06%, Nb:0.005%～0.05%, Als:0.010%～0.04%, surplus are Fe and inevitably are mingled with.
In addition, steel chemical composition of the present invention also must satisfy:
Pcm＝C+Si/30+Ni/60+(Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.20％；
Ceq＝C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14≤0.42％；
When concrete scheme of the present invention has the 40mm of production with lower steel plate, C:0.06% in the steel～0.07%, Si:0.15%～0.30%, Mn:1.20%～1.50%, P≤0.015%, S≤0.006%, Ni:0.15～0.25%, Mo:0.15%～0.25%, Cu:0.05%～0.15%, V:0.02%～0.04%, Nb:0.005%～0.02%, Als:0.010%～0.040%, surplus are Fe and inevitably are mingled with.Pcm maximum 0.187%, Ceq maximum 0.404%.
When concrete scheme of the present invention has the 40～75mm of production steel plate, C:0.07% in the steel～0.09%, Si:0.15%～0.30%, Mn:1.30%～1.50%, P≤0.015%, S≤0.006%, Ni:0.15～0.25%, Mo:0.20%～0.30%, Cu:0.10%～0.20%, V:0.03%～0.06%, Nb:0.010%～0.04%, Als:0.010%～0.04%, surplus are Fe and inevitably are mingled with.Pcm maximum 0.195%, Ceq maximum 0.418%.
Details are as follows to the reason of C, Si, Mn, P, S, Als, Ni, Cr, Mo, V, Cu, Nb limited amount among the present invention:
C:C≤0.06 o'clock need be added other and be improved the hardening capacity element, and cost is raise, and toughness and weldability degenerate.Welding joint toughness for after guaranteeing welding crack sensibility and adding Nb is limited to 0.09% on the C.
Si: play a role in guaranteeing strength of parent and strength of welded joint for making Si, Si should be greater than 0.15%.
Mn: guaranteeing that for making Mn strength of parent and strength of welded joint play a role, its content answers 〉=1.20%.But Mn＞1.60% o'clock degenerates welding crack sensibility, and owing to brings excessive hardening capacity that base metal tenacity and joint toughness are degenerated.
P, S:P, S are impurity elements.Be limited in P≤0.015%; S≤0.006%.
Als:Als can reduce the amount and the size thereof of M-A constituent element, has reduced solid solution N amount.The content of Al is 〉=0.010% generally speaking, is limited to 0.040% on the adding Als.
Ni, Cr:Ni, Cr help improving the intensity of mother metal and welding joint.Ni can further improve toughness.But surpass required amount Ceq is increased, cause the toughness reduction and the processibility of welding joint to degenerate, so the content of Ni be: 0.15%～0.40% as addition.Be limited to 0.30% on the Cr.
Mo: effective to improving strength of parent and strength of welded joint, on be limited to 0.30%.For guaranteeing required hardening capacity, the following of interpolation is limited to 0.15%.
Cu：
Cu helps improving the intensity of mother metal and welding joint.Be limited to 0.30% on the Cu.
Nb：
Be to guarantee strength of parent and strength of welded joint, the dosage of Nb should 〉=0.005%, but Nb 〉=0.05% o'clock welding joint toughness degenerates, so will be defined as 0.05% on the Nb, is limited to 0.03% on preferably.The raising hardening capacity effect of solid solution Nb when utilizing rolling the heating.Can reduce the add-on that other improves the hardening capacity element with the direct quenching method.The precipitation-hardening effect of Nb carbonitride when utilizing temper after the direct quenching.This method can guarantee the intensity of speed of cooling less than the steel plate center on surface.That is to say that this method has guaranteed that not only necessary hardening capacity has also guaranteed the intensity of steel plate.
V：
V adds for guaranteeing strength of parent and strength of welded joint, and addition is 0.02～0.06%.But,, will make the welding crack sensibility variation, and diminish base metal tenacity as surpassing 0.1%.
B: to the chemical ingredients of steel and the variation of creating conditions, cause the hardness of mother metal unstable properties, particularly welded heat affecting zone to significantly improve for fear of B, and the toughness of welding welded bonds is degenerated, do not add B in the steel of the present invention.
Pcm：
Pcm represents the welding cold crack sensitivity coefficient, under common environment, does not need preheating during welding procedure, so be defined in≤0.20%.
Ceq：
Ceq is the carbon equivalent value.The 610N/mm of thicker specification
2The grade high-strength steel guarantees strength of parent and strength of welded joint by adding Nb, and the Ceq value can be no more than 0.42%.
Thickness range of the present invention, the i.e. scope of 23～75mm.
The production method of high-strength steel of the present invention adopts molten iron to give treatment technology, converter smelting, and LF stove+Clean Steel technologies such as VD stove vacuum-treat are smelted and continuous casting.
A) Heating temperature before the hot rolling:
Heating temperature is if surpass 1200 ℃, may cause steel original austenite grains thickization and can not guarantee the toughness of mother metal, so on be limited to 1200 ℃.The steel billet tapping temperature is 1150～1180 ℃.But consider the suitable dissolving of microalloy element, Heating temperature must guarantee to be lower than 1000 ℃.
B) rolling condition:
Rolling technology adopts austenite perfect recrystallization district+two the stage controlled rollings in austenite non-recrystallization district technology after the steel soaking of the present invention.
The austenite recrystallization district is rolling: the fs of controlled rolling, temperature range is between 1100～970 ℃.For guaranteeing base metal tenacity and avoid producing the thick crystal grain of local anomaly that should make every time draft greater than 8%, preferably greater than 10%, maximum single pass draft is 20%.
Austenite non-recrystallization district is rolling: the subordinate phase of controlled rolling, temperature range be controlled at≤and 930 ℃.For thereby the effect that guarantees grain refining reaches yield strength and the flexible purpose that improves steel, should guarantee cumulative deformation 〉=55% in this stage, the cumulative maximum deflection is 65%.
C) online laminar flow cooling (direct quenching):
After hot rolling finishes, with temperature at Ar
3Above steel plate is forced cooling (controlled chilling carries out) in the ACC device.When forcing cooling water is applied on the steel plate equably, the water temp of going into of steel plate is 745～780 ℃, and the final cooling temperature of steel plate is controlled at 420～500 ℃ of intervals.The speed of cooling of steel plate is controlled at 5～13 ℃/S interval.The speed of cooling that should make thickness of slab 1/2t place at least 1 ℃/more than the S.
D) temper:
The purpose of temper is implemented for eliminating stress.Also have in the present invention and make Nb and V carbide separate out the special role that improves and guarantee strength of parent.Can achieve the above object carrying out tempering more than 600 ℃.But tempering when the temperature that surpasses 650 ℃, intensity significantly reduces.
So advantage of the present invention and effect exist: chemical composition design is simple, by element addition and kind few principle of trying one's best, reasonably adjust the proportional quantity of each element, control welding cold crack sensitivity coefficient value Pcm≤0.20%, control carbon equivalent value Ceq≤0.42%, as long as the weld heat input input is satisfied≤the 40KJ/cm condition, can guarantee the performance of postwelding steel plate, reduce production cost; Adopt technologies such as austenite perfect recrystallization district+two stage controlled rollings in austenite non-recrystallization district, the cooling of online laminar flow and off-line tempering, the steel plate interior tissue is ferrite+bainite heterogeneous structure, is handling less than 600 ℃ of following stress-removals the welding back, organize and do not change, the thickness of this steel plate reaches 75mm, steel plate tensile strength 〉=610MPa, and steel plate need not to carry out modifier treatment, possesses the low-welding crack-sensitive excellent properties.Production technique of the present invention is easy, is fit to produce in batches operation, and steel plate welding back is functional.
Description of drawings
Accompanying drawing 1 is 30mm steel plate full thickness hardness test result of the present invention,
Accompanying drawing 2 is 55mm steel plate full thickness hardness test result of the present invention,
Accompanying drawing 3 is 75mm steel plate full thickness hardness test result of the present invention,
The oblique Y groove welding crack test of accompanying drawing 4 the present invention schematic diagram.
Embodiment
The chemical ingredients of steel of the present invention is (by weight percentage), C:0.06%～0.09%, Si:0.15%～0.55%, Mn:1.00%～1.60%, P≤0.015%, S≤0.006%, Ni:0.15～0.40%, Cr≤0.30%, Mo≤0.30%, Cu≤0.30%, V:0.02～0.06%, Nb:0.005%～0.05%, Als:0.010%～0.04%, surplus are Fe and inevitably are mingled with.
In addition, steel chemical composition of the present invention also must satisfy:
Pcm＝C+Si/30+Ni/60+(Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.20％；
Ceq＝C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14≤0.40％。
When concrete scheme of the present invention has the 40mm of production with lower steel plate, C:0.06% in the steel～0.07%, Si:0.15%～0.30%, Mn:1.20%～1.50%, P≤0.015%, S≤0.006%, Ni:0.15～0.25%, Mo:0.15%～0.25%, Cu:0.05%～0.15%, V:0.02%～0.04%, Nb:0.005%～0.02%, Als:0.010%～0.040%, surplus are Fe and inevitably are mingled with.Pcm maximum 0.187%, Ceq maximum 0.404%.
When concrete scheme of the present invention has the 40～75mm of production steel plate, C:0.07% in the steel～0.09%, Si:0.15%～0.30%, Mn:1.30%～1.50%, P≤0.015%, S≤0.006%, Ni:0.15～0.25%, Mo:0.20%～0.30%, Cu:0.10%～0.20%, V:0.03%～0.06%, Nb:0.010%～0.04%, Als:0.010%～0.04%, surplus are Fe and inevitably are mingled with.Pcm maximum 0.195%, Ceq maximum 0.418%.
Adopt molten iron to give treatment technology by above-mentioned composition, converter smelting, LF stove+Clean Steel technologies such as VD stove vacuum-treat are smelted the molten steel of producing, make continuously cast bloom through slab caster, the temperature control heating was carried out in shove charge after continuous casting steel billet arrived Thick Plate Plant, and the slab laggard horizontal high voltage water surface de-scaling of coming out of the stove is handled.Its rolling technology step is as follows:
A) Heating temperature before the hot rolling:
Billet heating temperature must guarantee to be lower than 1000 ℃, does not the highlyest surpass 1200 ℃, and best tapping temperature is 1150～1180 ℃.
B) rolling condition:
Rolling technology adopts austenite perfect recrystallization district+two the stage controlled rollings in austenite non-recrystallization district technology after the steel soaking of the present invention;
The austenite recrystallization district is rolling: the fs of controlled rolling, temperature range for guaranteeing base metal tenacity and avoiding producing the thick crystal grain of local anomaly, should make every time draft greater than 8% between 1100～970 ℃, maximum single pass draft is 20%, and optimum value is 12%～15%.
Austenite non-recrystallization district is rolling: the subordinate phase of controlled rolling, temperature range be controlled at≤and 930 ℃.For thereby the effect that guarantees grain refining reaches yield strength and the flexible purpose that improves steel, should guarantee cumulative deformation 〉=55% in this stage, the cumulative maximum deflection is 65%;
C) online laminar flow cooling (direct quenching):
After hot rolling finishes, with temperature at Ar
3Above steel plate is forced cooling (controlled chilling carries out) in the ACC device, should make water be applied on the steel plate equably when forcing cooling, the water temp of going into of steel plate is 745～780 ℃, laminar flow cooling roller bed speed 0.5～0.9m/s, and the final cooling temperature of steel plate is controlled at 420～500 ℃ of intervals; The speed of cooling of steel plate is controlled at 5～13 ℃/S interval, the speed of cooling at thickness of slab 1/2t place at least 1 ℃/more than the S;
D) temper:
The purpose of temper is implemented for eliminating stress, also have in the present invention and make Nb and V carbide separate out the special role that improves and guarantee strength of parent, can achieve the above object carrying out tempering more than 600 ℃, the highlyest be no more than 650 ℃, optimum tempering temperature is 610～630 ℃.
Table 1 is several embodiments of the present invention and testing performance index result.
The present invention has done corresponding test to other indexs of welding steel.
1. strain aging sensitivity test:
Sample is taken from TMCP+ Annealed Strip finished product steel plate, tests according to GB4160 " the strain aging sensitivity test method (summer is than ballistic method) of steel ", and the strain aged test result is as follows for steel plate (laterally sample):
30.0mm steel plate:
| Test temperature | No strain ballistic work (J) | 5% strain aging ballistic work (J) | 5% strain aging sensitivity coefficient Cv (%) | 10% strain aging ballistic work (J) | 10% strain aging sensitivity coefficient Cv (%) |
| Normal temperature | 268 308 288 288 | 278 268 278 275 | 4.5 | 220 236 238 231 | 19.8 |
| 0℃ | 310 286 286 294 | 254 239 228 240 | 18.4 | 253 220 255 243 | 17.3 |
| -20℃ | 280 245 290 272 | 238 246 256 247 | 9.2 | 246 228 228 234 | 14.0 |
55.0mm steel plate:
| Test temperature | No strain ballistic work (J) | 5% strain aging ballistic work (J) | 5% strain aging sensitivity coefficient Cv (%) | 10% strain aging ballistic work (J) | 10% strain aging sensitivity coefficient Cv (%) |
| Normal temperature | 220 260 260 247 | 212 258 230 233 | 5.7 | 242 224 220 229 | 7,3 |
| 0℃ | 185 220 250 218 | 211 202 225 213 | 2.3 | 174 204 196 191 | 12.4 |
| -20℃ | 185 187 190 188 | 220 140 168 176 | 6.4 | 145 130 122 133 | 23.3 |
75.0mm steel plate:
| Test temperature | No strain ballistic work (J) | 5% strain aging ballistic work (J) | 5% strain aging sensitivity coefficient Cv (%) | 10% strain aging ballistic work (J) | 10% strain aging sensitivity coefficient Cv (%) |
| Normal temperature | 254 277 275 269 | ＞293 268 287 283 | -5.2 | 272 286 289 282 | -4.8 |
| 0℃ | 275 272 266 271 | 234 235＞293 254 | 6.3 | 254 250 270 258 | 4.8 |
| -20℃ | 244 221 210 225 | ＞293 263 254 270 | -20 | 213 255＞293 256 | -13.8 |
2. steel plate full thickness hardness test:
Test-results is shown in Fig. 1～3.
3.NDT test:
Carry out according to GB6803 " the nil-ductility temperature drop weight test method of ferritic steel " standard.Sample type is the P3 type, is of a size of 16mm * 50mm * 130mm.Heat-eliminating medium is dehydrated alcohol, dry ice and liquid nitrogen, and soaking time is 30 minutes, and blow energy is 400J (the thick test plate (panel) blow energy of 30.0mm is 450J).
Test-results is as follows:
| Specification | -40℃ | -45℃ | -55℃ | -60℃ | -78℃ | -90 ℃ (reference) | NDT(℃) |
| 30mm | -- | -- | ○○ | ○○ | ○○ | ○× | -78～-90 |
| 40mm | -- | -- | ○○ | ○× | -60 | ||
| 45mm | -- | -- | ○○ | ○○ | ○○ | ○× | -78～-90 |
| 50mm | -- | -- | ○○ | ○○ | ○○ | ○× | -78～-90 |
| 55mm | -- | -- | ○○ | ○○ | ○○ | ○× | -78～-90 |
| 67mm | -- | ○○ | ○× | -55 | |||
| 75mm | ○○ | ○○ | ○× | ○× | -55 |
Annotate: because the testing installation condition is limit ,≤-78 ℃ temperature can't accurately be controlled (only for reference).
4. steel plate welding test of the present invention
1) maximum hardness test: 30mm, 45mm, 55mm, 67mm, 75mm steel plate are tested by GB4675.5-84 " welded heat affecting zone maximum hardness test method ".
Welded heat affecting zone maximum hardness test result
| Welding process | Covered arc welding | |||||||
| Welding conditions | Wlding | J607RH (φ 4.0mm) Golden Bridge's wlding | ||||||
| Oven dry | 400℃×2h | |||||||
| Room temperature ℃ | 24 | |||||||
| Humidity % | 61 | |||||||
| Electric current A | 170 | |||||||
| | 25 | |||||||
| Speed mm/ | 150 | |||||||
| Heat input KJ/mm | 1.7 | |||||||
| | 30 | 45 | 55 | 67 | 75 | |||
| Initial temperature ℃ | 24 | Maximum hardness HV5 | 286 | 299 | 283 | 254 | 257 | |
| 75 | 282 | 283 | 262 | 246 | 246 | |||
2) oblique Y groove welding crack test
By GB4675.1-84 " tiltedly Y type groove welding crack test method " 30mm, 45mm, 55mm, 67mm, 75mm steel plate are tested.Test principle figure as shown in Figure 6.
Oblique Y groove welding crack test result
| Welding process | Covered arc welding | ||||||
| Welding conditions | Welding material | J607RH(φ4.0mm) | |||||
| Oven dry | 400℃× | ||||||
| Temperature ℃ | |||||||
| 25 | |||||||
| Humidity % | 64 | ||||||
| Electric current A | 170 | ||||||
| | 25 | ||||||
| Speed mm/ | 150 | ||||||
| Heat input KJ/mm | 1.7 | ||||||
| | 30 | 45 | 55 | 67 | 75 | ||
| | 25℃ | Flawless is arranged | ○○○ | ○○○ | ○○○ | ○○○ | ○○○ |
| 50℃ | ○○○ | ○○○ | ○○○ | ○○○ | ○○○ | ||
Zero flawless produces
3) welding joint test
Utilize covered arc welding and shielded welding to carry out the jam welding of 30mm, 45mm, 55mm and 67mm steel plate, and take a sample and check by JB4708-2000 " steel pressure vessel welding technology evaluation ".
3.1 weldprocedure
Jam welding technology
| Welding process | Covered arc welding | Shielded welding |
| Form | The X type, 60 ° | The X type, 60 ° |
| Welding material | J607RH(φ5.0mm) | TM-60(φ1.2mm) |
| Shielding gas | ---- | Ar80％+ |
| Oven dry | 400℃×2h | ---- |
| | 25 | |
| Humidity % | 64 | |
| Electric current A | 210 | 250 |
| | 25 | 28 |
| Speed mm/min | 140 | 280 |
| Heat input KJ/mm | 2.2 | 1.5 |
| Preheating ℃ | Do not have | |
| Interlayer temperature ℃ | Below 150 ℃ | |
The covered arc welding backing welding adopts φ 4.0mm welding rod, electric current 170A, voltage 25V, speed 110mm/min, heat input 2..2KJ/min.
3.2 the stretching of welding joint and cold bending test
The stretching of welding joint and cold bending test result
| Thickness mm | Welding process | Stretch | Clod wash D=4a, α=180 ° | |
| R
m， | Fracture position | |||
| 30 | Manual welding | 690 | Weld seam | ○○○○ |
| 730 | Weld seam | |||
| Gas is protected weldering | 665 | Weld seam | ○○○○ | |
| 670 | Weld seam | |||
| 45 | Manual welding | 625 | Mother metal | ○○○○ |
| 630 | Mother metal | |||
| Gas is protected weldering | 630 | Mother metal | ○○○○ | |
| 635 | Mother metal | |||
| 55 | Manual welding | 615 | Mother metal | ○○○○ |
| 615 | Mother metal | |||
| Gas is protected weldering | 680 | Weld seam | ○○○○ | |
| 670 | Weld seam | |||
| 67 | Manual welding | 630 | Mother metal | ○○○○ |
| 630 | Mother metal | |||
| Gas is protected weldering | 665 | Mother metal | ○○○○ | |
| 660 | Mother metal | |||
Zero is that clod wash is qualified.
3.3 the impact ductility test of welding joint
The impact ductility test result of welding joint
| Thickness mm | Welding process | -20℃A kV，J | ||
| Weld seam | Welded bonds | The heat affected | ||
| 30 | Manual welding | 133 | 160 | 238 |
| Gas is protected weldering | 108 | 112 | 135 | |
| 45 | Manual welding | 122 | 126 | 192 |
| Gas is protected weldering | 107 | 196 | 162 | |
| 55 | Manual welding | 139 | 152 | 178 |
| Gas is protected weldering | 140 | 200 | 178 | |
| 67 | Manual welding | 153 | 194 | 202 |
| | 122 | 214 | 215 | |
| Gas is protected weldering | 109 | 165 | 157 | |
| Gas is protected | 91 | 185 | 168 | |
3.4 the serial impelling strength of weld seam and heat affected zone
The serial impact ductility test result of weld seam and heat affected zone
| Thickness mm | Welding process | Weld seam A KV，J | Heat affected zone A
KV， |
||||||||||
| 20 |
0℃ | -20℃ | -30℃ | -40℃ | -60 |
20 |
0℃ | -20℃ | -30℃ | -40℃ | -60 |
||
| 30 | Manual welding | 175 | 156 | 133 | 99 | 70 | 45 | 257 | 266 | 238 | -- | 188 | 178 |
| Gas is protected weldering | 127 | 101 | 108 | 82 | 75 | 45 | 251 | 220 | 135 | -- | 203 | 96 | |
| 45 | Manual welding | 166 | 151 | 122 | 122 | 93 | 57 | 232 | 233 | 192 | 217 | 121 | 149 |
| Gas is protected weldering | 105 | 117 | 107 | 113 | 69 | 35 | 212 | 218 | 162 | 121 | 200 | 39 | |
| 55 | Manual welding | 166 | 166 | 139 | 125 | 108 | 57 | 203 | 203 | 178 | 187 | 125 | 81 |
| Gas is protected weldering | 143 | 141 | 140 | 82 | 65 | 53 | 214 | 200 | 178 | 175 | 142 | 49 | |
| 67 | Manual welding | -- | 157 | 153 | -- | 124 | 53 | -- | 232 | 202 | -- | 164 | 107 |
| Gas is protected weldering | 156 | 127 | 109 | 86 | 64 | 39 | -- | 194 | 157 | 197 | 190 | 54 | |
Table 1
| C | Si | Mn | P | S | Als | Ni | Cr | Cu | Mo | V | Nb | Pcm | Ceq | Thickness mm | The thick mm of intermediate blank | Two-stage start rolling temperature ℃ | Two-stage finishing temperature ℃ | Open cold temperature ℃ | Return red temperature ℃ | Roller table speed m/s | Rel (MPa) | Rm (MPa) | A (％) | Akv-20 ℃ horizontal (J) | |
| 1 | 0.065 | 0.24 | 1.53 | 0.0089 | 0.0017 | 0.03 | 0.23 | 0.05 | 0.14 | 0.25 | 0.04 | 0.024 | 0.185 | 0.411 | 75 | 130 | 850 | 830 | 769 | 505 | 0.5 | 550 | 650 | 23.0 | 270 260 250 |
| 2 | 0.079 | 0.26 | 1.48 | 0.0089 | 0.0027 | 0.027 | 0.25 | 0.05 | 0.15 | 0.25 | 0.04 | 0.022 | 0.198 | 0.418 | 67 | 130 | 834 | 798 | 770 | 503 | 0.5 | 580 | 665 | 19.5 | 240 252 295 |
| 3 | 0.06 | 0.26 | 1.57 | 0.0089 | 0.0017 | 0.024 | 0.24 | 0.04 | 0.16 | 0.25 | 0.04 | 0.022 | 0.181 | 0.410 | 60 | 130 | 849 | 837 | 761 | 429 | 0.5 | 610 | 675 | 19.5 | 290 293 295 |
| 4 | 0.06 | 0.24 | 1.55 | 0.0099 | 0.0017 | 0.022 | 0.26 | 0.06 | 0.17 | 0.26 | 0.04 | 0.024 | 0.184 | 0.415 | 55 | 130 | 880 | 870 | 777 | 464 | 0.5 | 590 | 670 | 22.0 | 231 220 204 |
| 5 | 0.06 | 0.26 | 1.53 | 0.0079 | 0.0017 | 0.028 | 0.24 | 0.04 | 0.16 | 0.25 | 0.04 | 0.022 | 0.181 | 0.405 | 50 | 120 | 870 | 816 | 750 | 420 | 0.5 | 530 | 630 | 20.5 | 235 290 290 |
| 6 | 0.07 | 0.25 | 1.51 | 0.0079 | 0.0017 | 0.033 | 0.22 | 0.04 | 0.15 | 0.25 | 0.04 | 0.02 | 0.175 | 0.397 | 45 | 110 | 880 | 854 | 777 | 439 | 0.6 | 590 | 670 | 20.0 | 330 310 280 |
| 7 | 0.06 | 0.27 | 1.56 | 0.0079 | 0.0017 | 0.027 | 0.24 | 0.04 | 0.15 | 0.25 | 0.04 | 0.022 | 0.180 | 0.408 | 40 | 100 | 890 | 827 | 752 | 430 | 0.6 | 615 | 695 | 20.5 | 295 290 295 |
| 8 | 0.06 | 0.26 | 1.50 | 0.0079 | 0.0027 | 0.028 | 0.22 | 0.04 | 0.15 | 0.25 | 0.04 | 0.020 | 0.176 | 0.398 | 35 | 80 | 870 | 824 | 769 | 442 | 0.65 | 600 | 660 | 21.0 | 300 305 310 |
| 9 | 0.06 | 0.27 | 1.48 | 0.0079 | 0.0017 | 0.034 | 0.23 | 0.04 | 0.14 | 0.25 | 0.04 | 0.020 | 0.175 | 0.396 | 30 | 70 | 860 | 791 | 755 | 430 | 0.8 | 555 | 655 | 21.5 | 290 290 290 |
| 10 | 0.06 | 0.26 | 1.45 | 0.0109 | 0.0017 | 0.028 | 0.22 | 0.04 | 0.15 | 0.25 | 0.04 | 0.02 | 0.173 | 0.390 | 23 | 70 | 855 | 788 | 754 | 450 | 0.9 | 575 | 660 | 24.5 | 365 385 410 |
Claims (7)
1, a kind of thick steel plate with high strength and low welding crack sensitivity, it is characterized in that adopting following chemical ingredients (by weight percentage): C:0.06%～0.09%, Si:0.15%～0.55%, Mn:1.00%～1.60%, P: S≤0.015% :≤0.006%, Ni:0.15～0.40%, Cr: Mo≤0.30%: Cu≤0.30% :≤0.30%, V:0.02～0.06%, Nb:0.005%～0.05%, Als:0.010%～0.04%, surplus is Fe and inevitably is mingled with that the chemical ingredients of steel also must satisfy:
Pcm＝C+Si/30+Ni/60+(Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.20％；
Ceq＝C+Mn/6+Si/24+Ni/40+Cr/5+Mo/4+V/14≤0.42％。
2, a kind of thick steel plate with high strength and low welding crack sensitivity according to claim 1, when producing 40mm with lower steel plate, C:0.06% in the steel～0.07%, Si:0.15%～0.30%, Mn:1.20%～1.50%, P≤0.015%, S≤0.006%, Ni:0.15～0.25%, Mo:0.15%～0.25%, Cu:0.05%～0.15%, V:0.02%～0.04%, Nb:0.005%～0.02%, Als:0.010%～0.040%, surplus is Fe and inevitably is mingled with, the Pcm maximum value is 0.187%, and the Ceq maximum value is 0.404%.
3, a kind of thick steel plate with high strength and low welding crack sensitivity according to claim 1, when producing 40～75mm steel plate, C:0.07% in the steel～0.09%, Si:0.15%～0.30%, Mn:1.30%～1.50%, P≤0.015%, S≤0.006%, Ni:0.15～0.25%, Mo:0.20%～0.30%, Cu:0.10%～0.20%, V:0.03%～0.06%, Nb:0.010%～0.04%, Als:0.010%～0.04%, surplus is Fe and inevitably is mingled with, the Pcm maximum value is 0.195%, and the Ceq maximum value is 0.418%.
4, according to the production method of each described a kind of thick steel plate with high strength and low welding crack sensitivity among the claim 1-3, it is characterized in that, adopt molten iron to give treatment technology, converter smelting, LF stove+Clean Steel technologies such as VD stove vacuum-treat are smelted and continuous casting, and its rolling technology step is as follows:
A) Heating temperature before the hot rolling:
Billet heating temperature must guarantee to be lower than 1000 ℃, does not the highlyest surpass 1200 ℃
B) rolling condition:
Rolling technology adopts austenite perfect recrystallization district+two the stage controlled rollings in austenite non-recrystallization district technology after the steel soaking of the present invention;
The austenite recrystallization district is rolling: the fs of controlled rolling, temperature range for guaranteeing base metal tenacity and avoiding producing the thick crystal grain of local anomaly, should make every time draft greater than 8% between 1100～970 ℃, maximum single pass draft is 20%, and optimum value is 12%～15%.
Austenite non-recrystallization district is rolling: the subordinate phase of controlled rolling, temperature range be controlled at≤and 930 ℃.For thereby the effect that guarantees grain refining reaches yield strength and the flexible purpose that improves steel, should guarantee cumulative deformation 〉=55% in this stage, the cumulative maximum deflection is 65%;
C) online laminar flow cooling (direct quenching):
After hot rolling finishes, with temperature at Ar
3Above steel plate is forced cooling (controlled chilling carries out) in the ACC device, should make water be applied on the steel plate equably when forcing cooling, the water temp of going into of steel plate is 745～780 ℃, laminar flow cooling roller bed speed 0.5～0.9m/s, and the final cooling temperature of steel plate is controlled at 420～500 ℃ of intervals; The speed of cooling of steel plate is controlled at 5～13 ℃/S interval, the speed of cooling at thickness of slab 1/2t place at least 1 ℃/more than the S;
D) temper:
The purpose of temper is implemented for eliminating stress, and also has the special role that Nb and V carbide is separated out improve and guarantee strength of parent in the present invention, can achieve the above object carrying out tempering more than 600 ℃, the highlyest is no more than 650 ℃.
5, the production method of a kind of thick steel plate with high strength and low welding crack sensitivity according to claim 4, heating steel billet tapping temperature is 1150～1180 ℃.
6, the production method of a kind of thick steel plate with high strength and low welding crack sensitivity according to claim 4 is characterized in that the single pass draft greater than 10%, and optimum value is 12%～15%.
7, the production method of a kind of thick steel plate with high strength and low welding crack sensitivity according to claim 4 is characterized in that tempering temperature is 610～630 ℃.
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