CN104862613A - High-strength steel, high-strength steel pipe and manufacturing method of high-strength steel pipe - Google Patents
High-strength steel, high-strength steel pipe and manufacturing method of high-strength steel pipe Download PDFInfo
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Abstract
The invention discloses high-strength steel which comprises the following chemical elements by mass percent: 0.11-0.18% of C, 0.1-0.4% of Si, 1.0-1.6% of Mn, 0.25-0.9% of Cr, 0.10-0.50% of Mo, 0.10-0.55% of W, 0.01-0.08% of Nb, 0.01-0.12% of V, 0.10-0.40% of Ni, greater than 0 and less than 0.0020% of V, greater than 0 and less than or equal to 0.004% of N, greater than 0 and less than or equal to 0.010% of Ti, less than 0.0030% of O, less than 0.005% of S, 0.001-0.005% of Ca+Mg and the balance of Fe and other inevitable impurities. In addition, (B+Ti)/N is greater than 1. The invention further provides a high-strength steel pipe manufactured by the high-strength steel and a manufacturing method of the high-strength steel pipe. The high-strength steel and the steel pipe meet 980MPa strength and have excellent low-temperature toughness.
Description
Technical field
The present invention relates to a kind of steel grade and manufacture method thereof, particularly relate to a kind of high-strength steel and manufacture method thereof.
Background technology
At present, engineering machinery and steel construction piece are gradually towards large load-bearing, lightweight future development.Particularly for the steel construction piece bearing high-load, the deadweight reducing structure not only can reduce material cost, also helps the supporting capacity improving steel construction piece.But, when alleviating dead load, also to ensure that the security of structural part is an awkward problem simultaneously.This is because the welding difficulty of high-strength steel is the toughness of the heat affected zone that must ensure welding assembly, and in addition on the one hand, for steel construction piece, because processing assembling process mainly relies on technique for welding, workload needed for welding processing is larger, therefore, in order to increase work efficiency, weldprocedure compared with large-line energy must be adopted to enhance productivity.Therefore, the intensity of welding joint and toughness are also technical problems urgently to be resolved hurrily how to make the structural part mother metal of high-strength and high ductility can also ensure under the condition compared with high heat-input amount.
Publication number is CN1146784A, and publication date is on April 2nd, 1997, and the Chinese patent literature that name is called " weldable high-tensile steel of excellent in low temperature toughness " discloses a kind of ultrahigh-strength steel.Ultrahigh-strength steel disclosed in this patent documentation with the addition of the elements such as Cu, B, Cr, Ca and V further in low-carbon (LC)-Gao Mn-Ni-Mo-trace Ti system steel, non-recrystallization austenitic transformation microstructure be specified in steel containing being less than 10 μm by average austenite particle diameter (dr) forms tempered martensite+Martensite-Bainite Mixed Microstructure (this tissue has the tempered martensite of more than 60%), or be specified to the microtexture being formed the tempered martensite with more than 90% by non-recrystallization austenitic transformation, and P value is defined in the scope of 1.9 ~ 4.0.The above-mentioned thermal weld stress amount that patent document discloses this high-strength steel is 5kJ/cm, but in actual production, the thermal weld stress amount of steelwork component, considerably beyond this numerical value, will reach more than 15kJ/cm usually.For this reason, when being in relatively large thermal weld stress amount, the heat affected zone crystal grain of this high-strength steel can obviously be grown up, thus causes the intensity of this steel sharply to decline.
Publication number is CN101397640A, and publication date is on April 1st, 2009, and the Chinese patent literature that name is called " yield strength 960MPa level Welded Structural Steel " describes a kind of superstrength Welded Structural Steel.Welded Structural Steel disclosed in this patent documentation comprises chemical element (in wt.%): C:0.14 ~ 0.19wt.%, Si:0.15 ~ 0.40wt.%, Mn:1.40 ~ 1.7wt.%, Mo:0.41 ~ 0.60wt.%, B:0.0005 ~ 0.002wt.%, CR:0 ~ 0.50wt.%, Ni:0 ~ 0.40wt.%, Nb:0 ~ 0.03wt.%, Ti:0.010 ~ 0.050wt.%, Als:0.01 ~ 0.06wt.%, P≤0.020, S≤0.010, all the other are Fe and inevitable impurity, go back demand fulfillment: carbon equivalent ce V (%) <0.65 or PCM (%) <0.35 simultaneously.-20 DEG C of ballistic works of this Welded Structural Steel are 52J, and therefore its toughness is lower than the technical program.
Summary of the invention
The object of the present invention is to provide a kind of high-strength steel, it has sufficiently high tensile strength, good low-temperature flexibility and excellent welding property.
To achieve these goals, the present invention proposes a kind of high-strength steel, its chemical element mass percentage content is:
C：0.11-0.18％，
Si：0.1-0.4％，
Mn：1.0-1.6％，
Cr：0.25-0.9％，
Mo：0.10-0.50％，
W：0.10-0.55％，
Nb：0.01-0.08％，
V：0.01-0.12％，
Ni：0.10-0.40％，
B：0<B<0.0020％，
N：0＜N≤0.004％，
Ti：0<Ti≤0.010％，
O：O<0.0030％，
S：S<0.005％，
Ca and Mg:Ca+Mg:0.001-0.005%,
Surplus is Fe and other inevitable impurity;
Meet relational expression in addition: (B+Ti)/N>1.
The principle of design of each chemical element in high-strength steel of the present invention is:
Carbon: C is the necessary chemical element guaranteeing matrix strength.In the technical program, if C content lower than 0.11% time, its intensity that steel can not be made to reach required.But, if C content higher than 0.18% time, will the weldability of steel be affected, and the toughness of the heat affected zone of steel is reduced.For this reason, the C content in high-strength steel of the present invention needs to control as 0.11-0.18%.
Silicon: Si in steel as reductor.In order to reach deoxidation effect, at least need the Si adding 0.1%.But, if add weldability and the toughness that too many Si will reduce steel.For high-strength steel of the present invention, Si content should be set as 0.1-0.4%.
Manganese: Mn is also a kind of reductor.Meanwhile, Mn guarantees that steel has the indispensable element of higher intensity and better low-temperature flexibility concurrently.Therefore in the technical program, the content of Mn must more than 1.0%, but, the Mn of too much content then can increase the hardening capacity of steel, not only can reduce toughness and the weldability of HAZ (welded heat affecting zone), but also steel can be caused in continuous casting process to produce center segregation.Meanwhile, the low-temperature flexibility of the mother metal after welding also can worsen.Given this, the Mn content in high-strength steel of the present invention needs to control as 1.0-1.6%.
Chromium: Cr can improve the intensity of mother metal and weld, to promote the hardening capacity of steel.But, when Cr content is too high, not only makes the weld cracking susceptibility of steel increase, and the toughness of welded heat affecting zone can be reduced.Therefore, the Cr content in high-strength steel of the present invention needs to control as 0.25-0.9%.
Molybdenum: Mo can improve the hardenability of steel.The hardenability that Mo better can improve steel is added in containing the steel of B element.Meanwhile, Mo is also strengthening element, and it can improve the intensity of material effectively.In the technical program, in order to make steel obtain higher intensity, the content of Mo at least will reach 0.10%.But, add Mo too much and the HAZ toughness of steel also can be made to reduce.For this reason, the Mo content in high-strength steel of the present invention needs to be set between 0.10-0.50% scope.
Tungsten: W can improve the hardenability of steel, and improves the intensity of material.More crucially, compare to other alloying elements such as Mo, W is while raising intensity, and its degree reducing the welding property of steel is relatively low.In order to reach strengthening effect, the lower limit set of W content is 0.10%, but, add W too much and the HAZ toughness of steel can be made to reduce, for this reason, need the upper limit of the W content in steel to be set as 0.55%.
Niobium: Nb is the important element obtaining fine-grained steel, and it can postpone austenite recrystallization to play the effect of crystal grain thinning when hot rolling.In cooling afterwards and course of hot rolling, NbC particle dispersion is separated out, and can play again the effect of precipitation strength, subsequently reheat in process, Nb can play again and hinder the effect of Austenite Grain Growth.Consider the toughness of heat affected zone and on-the-spot weldability, the content of Nb can not be too high.For this reason, the Nb content in high-strength steel of the present invention is controlled as 0.01-0.08%.
Vanadium: in general, the effect that V plays is roughly the same with Nb.But in high-strength steel, the precipitating reinforcing effect that interpolation V produces is better, and the compound of Nb and V adds the comprehensive mechanical property that more can improve high-strength steel of the present invention further.Similarly, consider the toughness of heat affected zone and on-the-spot weldability, the content of V can not be too high.Given this, the V content in high-strength steel of the present invention controls between the scope of 0.01-0.12%.
Nickel: Ni can improve the low-temperature flexibility of material and on-the-spot weldability.Compare to alloying elements such as adding Mn, Cr or Mo, the interpolation of Ni not only can not form the sclerotic tissue being unfavorable for low-temperature flexibility in steel, adds the toughness that the Ni of content more than 0.1% is conducive to the HAZ improving steel on the contrary.But, during Ni too high levels, the toughness of the HAZ of steel and on-the-spot weldability can be worsened again.For high-strength steel of the present invention, control Ni content is needed to be 0.10-0.40%.
Boron, titanium and nitrogen: B, Ti, N are the comparatively crucial alloying elements of the present invention.By adding appropriate B, Ti element, the welding property of material can be improved.The B element of trace can also improve the hardening capacity of material.Free nitrogen in steel is harmful to toughness of material, and B, Ti that compound is added secure the free N in material.In welding process of cooling, the BN that separates out can the tissue of refinement heat affected zone, improves the toughness of material.The solid solubility temperature of TiN can reach more than 1400 DEG C, at high temperature still can small and dispersed.In addition, the pinning effect of the TiN in welding process can stop austenite crystal growing up at high temperature effectively.But, excessive B, Ti of being solid-solution in matrix can induce Intragranular Acicular Ferrite forming core, thus reduce the intensity of heat affected zone.Based on this, B content in high-strength steel is set as by technical scheme of the present invention: 0<B<0.0020%, Ti content is set as: 0<Ti≤0.010%, and N content is set as 0 < N≤0.004%.Meanwhile, these three kinds of elements also demand fulfillment relational expression: (B+Ti)/N>1, reason is: if (B+Ti)/N≤1, then can reduce the welding fusion area of steel under high heat-input state and the toughness of heat affected zone significantly.
Calcium, magnesium, sulphur and oxygen: Ca, Mg, S and O are also the key elements in high-strength steel of the present invention.O and S easily forms inclusion in steel, isolate the continuity of matrix in steel, this can have a negative impact to the intensity of material and toughness, for this reason, the content of necessary strict control O and S, O content is controlled as <0.0030%, and S content is controlled as <0.0050%.Because Ca, Mg and O and S have very strong bonding force, make the liquid inclusions nodularization in steel, the inclusion simultaneously generated is difficult to polymerization in the liquid phase and has higher fusing point, therefore, while at high temperature obtaining the inclusion of stable, small and dispersed, also can not produce the thick inclusion that may cause steel other defect.The tiny inclusion of this disperse can play and stop the effect that in steelmaking process, austenite crystal is at high temperature grown up, to realize crystal grain thinning, to improve the beneficial effect of toughness.But excessive MgO, MgS, CaO and CaS will induce the ferrite forming core of intracrystalline in welding process of cooling, thus reduce the intensity of welding joint.Therefore, while reduction O, S content, the scope limiting Mg, Ca total amount is also needed.The total amount of the Ca+Mg in high-strength steel of the present invention needs to control between 0.001-0.005% scope.
High-strength steel of the present invention adds the alloying elements such as appropriate Cr, Mo, W, V, Nb by compound, and by the Optimization Technology step of postorder to obtain high-strength steel of the present invention.Technical scheme of the present invention improves the intensity of steel by the solution strengthening of alloying element and precipitation strength, makes steel also have good low-temperature flexibility while maintenance high strength.On this basis, control O, S content, the interpolation total amount of control Ca and Mg is to reduce the quantity of steel inclusion and to control the shape of inclusion.Meanwhile, compound adds Ti, B element, and controls N element content, enough high to obtain intensity, the enough high and high-strength steel that welding property is excellent of low-temperature flexibility.
It should be noted that, based on technical scheme of the present invention, " intensity is enough high " or " sufficiently high intensity " refers to that tensile strength reaches more than 980Mpa, and the low-temperature impact toughness at " low-temperature flexibility is enough high " or " sufficiently high low-temperature flexibility " refers to-40 DEG C is greater than 52J." welding property is excellent " then refers in larger thermal weld stress situation, and such as, when thermal weld stress amount reaches more than 15kJ/cm, the heat affected zone of the steel after welding still has above-mentioned sufficiently high intensity and sufficiently high low-temperature flexibility.
Further, high-strength steel of the present invention also meets Ceq=C+Mn/6+ (Cr+Mo+V)/5+Ni/15<0.62.
The object of control Ceq=C+Mn/6+ (Cr+Mo+V)/5+Ni/15<0.62 is the welding property improving material, reduces the preheating temperature of welding, reduces the welding flaw of material.If Ceq >=0.62, so the welding pre-heating temperature of material more than 150 DEG C, will be unfavorable for field size production operation like this.
Further, the microtexture of high-strength steel of the present invention is tempered sorbite.
Further, in high-strength steel of the present invention, above-mentioned tempered sorbite has BN and the TiN precipitate of disperse.
On the matrix of the tempered sorbite in high-strength steel of the present invention, can form the precipitate of BN, TiN of a large amount of disperse, the solid solubility temperature of these precipitates is higher, effectively can stop the fast growth of heat affected zone crystal grain in welding process.
Further, in high-strength steel of the present invention, above-mentioned tempered sorbite also have NbC precipitate and/or the VC precipitate of disperse.
The NbC precipitate of the disperse on tempered sorbite and/or VC precipitate can not only play the effect of precipitation strength, can also play the effect hindering Austenite Grain Growth reheating in process subsequently.
Further, there is the nodule of small and dispersed in high-strength steel of the present invention.
Further, above-mentioned inclusion be MgO, MgS, CaO and CaS at least one of them.
There is between Mg, Ca and O and S very strong bonding force, the liquid inclusions nodularization in steel can be made, and the inclusion generated is difficult to polymerization in liquid phase and has higher fusing point, thus at high temperature stablized, the inclusion of small and dispersed.These inclusiones be MgO, MgS, CaO and CaS at least one of them.The inclusion of these small and disperseds can play and stop the effect that in steelmaking process, austenite crystal is at high temperature grown up, thus reaches the Advantageous Effects of crystal grain thinning, raising toughness.
Preferably, in high-strength steel of the present invention, by the content of B, Ti and N element be further: B:0.0011-0.0016%, Ti:0.003-0.008%, N:0.003-0.004%.
Preferably, in high-strength steel of the present invention, by the content of O, S, Mg and Ca element be further: O<0.0024%; S<0.004%; Ca+Mg:0.001-0.004%.
Another object of the present invention is to provide a kind of High Tensile Steel Tube, it has higher intensity.In addition, this High Tensile Steel Tube has good low-temperature flexibility and excellent welding property.
In order to realize above object, the present invention proposes a kind of High Tensile Steel Tube, it is weldless steel tube, and it is obtained by any one high-strength steel referred to above.
Further, the tensile strength of High Tensile Steel Tube of the present invention is greater than 980MPa, and the low-temperature impact work at-40 DEG C is greater than 52J; When more than 15kJ/cm thermal weld stress amount after welding, the tensile strength of welding joint and heat affected zone is greater than 980MPa, and the low-temperature impact work at-40 DEG C is greater than 52J.
Another object of the present invention is the manufacture method providing a kind of High Tensile Steel Tube, and it comprises step: steel-making; Be cast as round base; Tube rolling; Thermal treatment.
Further, in the manufacture method of High Tensile Steel Tube of the present invention, in above-mentioned heat treatment step, carry out modifier treatment to steel pipe, wherein quenching temperature is 880-930 DEG C, and soaking time is 30-60min, then shrend; Then 580-650 DEG C is carried out high tempering, and soaking time is 30-80min; Then steel pipe is carried out hot straightening, hot straightening temperature 500-600 DEG C.
Further, in the manufacture method of High Tensile Steel Tube of the present invention, in above-mentioned tube rolling step, bore a hole after the soaking of circle base, wherein soaking temperature is 1220-1260 DEG C, and piercing temperature is 1200-1240 DEG C; Then carry out tube rolling, temperature is 980 DEG C-1200 DEG C.
Further, in the manufacture method of High Tensile Steel Tube of the present invention, after above-mentioned heat treatment step, also there is welding step.This welding step refers to carries out docking welding by two High Tensile Steel Tubes of the present invention.
High Tensile Steel Tube of the present invention is after employing large thermal weld stress amount (being greater than 15kJ/cm) docking welding, and be still greater than 980MPa in the tensile strength of its welding joint and heat affected zone, the low-temperature impact toughness at-40 DEG C is still greater than 52J.
High Tensile Steel Tube of the present invention, when tensile strength > 980MPa, can also have excellent low-temperature flexibility concurrently, the low-temperature impact work > 52J at-40 DEG C.In addition, High Tensile Steel Tube of the present invention is when the large thermal weld stress amount of more than 15kJ/cm, welding joint after welding and the tensile strength of heat affected zone still can be greater than 980MPa, and the low-temperature impact work at low-temperature flexibility still can ensure-40 DEG C is simultaneously greater than 52J.
Embodiment
Below specific embodiment is made further explanation high-strength steel of the present invention, High Tensile Steel Tube and manufacture method thereof, but this explanation and explanation do not form improper restriction to technical scheme of the present invention.
The High Tensile Steel Tube in embodiment A 1-A7 and comparative example B1-B5 is manufactured according to following step:
1) make steel: external refining and vacuum outgas, and the mass percent proportioning controlling each chemical element is as shown in table 1;
2) round base is cast as: adopt continuous casting mode to be cast as round base;
3) tube rolling: bore a hole after the soaking of circle base, wherein soaking temperature is 1220-1260 DEG C, and piercing temperature is 1200-1240 DEG C; Then carry out tube rolling, rolling temperature is 980-1200 DEG C, rolls rear air cooling and carries out sawing;
4) thermal treatment: modifier treatment is carried out to steel pipe, wherein, quenching temperature is 880-930 DEG C, and soaking time is 30-60min, then shrend; Then 580-650 DEG C is carried out high tempering, and soaking time is 30-80min; Then steel pipe is carried out hot straightening, hot straightening temperature 500-600 DEG C;
5) weld: adopt gasshielded arc welding two High Tensile Steel Tubes to be carried out docking welding; the heat input of welding is 16kJ/cm; preheating temperature when simultaneously welding adopts the minimum preheating temperature that can prevent steel pipe from producing HAZ cold crack, this preheating temperature < 150 DEG C.
It should be noted that, in above-mentioned steps (5), the tensile strength >=980MPa of the deposited metal of the welding wire adopted.
Concrete technology parameter in each step involved by above-mentioned manufacture method is in detail see table 2.
Table 1 lists the mass percentage content of each chemical element in the high-strength steel of embodiment A 1-A7 and comparative example B1-B5.
Table 1. (wt.%, surplus is Fe and other inevitable impurity)
| Sequence number | A1 | A2 | A3 | A4 | A5 | A6 | A7 | B1 | B2 | B3 | B4 | B5 |
| C | 0.14 | 0.12 | 0.16 | 0.11 | 0.18 | 0.15 | 0.14 | 0.093 | 0.2 | 0.16 | 0.14 | 0.15 |
| Si | 0.25 | 0.37 | 0.28 | 0.4 | 0.1 | 0.24 | 0.29 | 0.32 | 0.31 | 0.38 | 0.25 | 0.26 |
| Mn | 1.5 | 1.25 | 1.36 | 1.0 | 1.4 | 1.38 | 1.6 | 1.89 | 1.59 | 1.33 | 1.43 | 1.44 |
| Cr | 0.48 | 0.72 | 0.25 | 0.90 | 0.41 | 0.65 | 0.47 | / | 0.72 | 0.73 | 0.56 | 0.71 |
| Mo | 0.50 | 0.35 | 0.25 | 0.45 | 0.32 | 0.10 | 0.36 | 0.57 | 0.56 | 0.33 | 0.33 | 0.39 |
| W | 0.27 | 0.42 | 0.55 | 0.10 | 0.29 | 0.50 | 0.13 | / | 0.38 | 0.43 | 0.42 | 0.45 |
| Nb | 0.06 | 0.04 | 0.08 | 0.03 | 0.01 | 0.04 | 0.05 | 0.024 | 0.03 | 0.036 | 0.03 | / |
| V | 0.01 | 0.04 | 0.09 | 0.05 | 0.12 | 0.10 | 0.09 | / | 0.13 | 0.03 | 0.12 | 0.05 |
| Ni | 0.15 | 0.10 | 0.40 | 0.25 | 0.22 | 0.27 | 0.32 | 0.48 | 0.24 | 0.17 | 0.25 | 0.28 |
| B | 0.0012 | 0.0015 | 0.0011 | 0.0016 | 0.0014 | 0.0014 | 0.0015 | / | / | / | / | / |
| N | 0.004 | 0.004 | 0.004 | 0.003 | 0.004 | 0.003 | 0.003 | 0.005 | 0.003 | 0.008 | 0.003 | 0.004 |
| Ti | 0.008 | 0.004 | 0.007 | 0.003 | 0.003 | 0.004 | 0.008 | 0.012 | 0.002 | 0.002 | 0.001 | 0.001 |
| O | 0.0022 | 0.0016 | 0.0022 | 0.0017 | 0.0018 | 0.0024 | 0.002 | 0.004 | 0.0025 | 0.001 | 0.0045 | 0.0025 |
| S | 0.002 | 0.002 | 0.002 | 0.001 | 0.002 | 0.003 | 0.004 | 0.002 | 0.002 | 0.003 | 0.006 | 0.002 |
| Ca+Mg | 0.002 | 0.0018 | 0.005 | 0.0035 | 0.0024 | 0.001 | 0.0023 | / | / | 0.0015 | / | / |
| (B+Ti)/N | 2.3 | 1.38 | 2.03 | 1.53 | 1.1 | 1.8 | 3.17 | 2.4 | 0.67 | 0.25 | 0.33 | 0.25 |
| Ceq* | 0.6 | 0.56 | 0.53 | 0.57 | 0.6 | 0.57 | 0.61 | 0.55 | 0.76 | 0.61 | 0.6 | 0.63 |
* note: Ceq=C+Mn/6+ (Cr+ Mo+V)/5+Ni/15
Table 2 lists the processing parameter of the manufacture method of the High Tensile Steel Tube of embodiment A 1-A7 and comparative example B1-B5.
Table 2.
The tensile strength of the High Tensile Steel Tube respectively in testing example A1-A7 and comparative example B1-B5, and-40 DEG C of pendulum impact tests are carried out for the heat affected zone of the High Tensile Steel Tube in embodiment A 1-A7 and comparative example B1-B5.Test result is listed in table 3.
Table 3 lists the mechanical property parameters of the High Tensile Steel Tube in embodiment A 1-A7 and comparative example B1-B5.
Table 3.
By
Associative list 1 and table 3 can be found out, compared to embodiment A 1-A7, multinomial chemical element in the steel pipe of comparative example B1 exceeds technical scheme limited range of the present invention, so the tensile strength of body after welding of the steel pipe of comparative example B1 and welding joint does not all reach 980MPa.In addition, because (the B+Ti)/N in the steel pipe of comparative example B2-B5 is all beyond technical scheme limited range of the present invention, therefore, the HAZ toughness of the steel pipe of comparative example B2-B5 is poor.
As can be seen from Table 3, the tensile strength >=995MPa of the body of High Tensile Steel Tube after welding of embodiment A 1-A7, low-temperature impact toughness (-40 DEG C) AKv >=87J; After adopting large thermal weld stress amount to weld, tensile strength >=985MPa, HAZ low-temperature impact toughness (-40 DEG C) AKv >=53J of welding joint.Meanwhile, the yield strength of the High Tensile Steel Tube in embodiment A 1-A7 also reaches more than 945MPa.Illustrate thus, the High Tensile Steel Tube described in the technical program has higher intensity, with excellent low-temperature flexibility and excellent welding property.
It should be noted that above enumerate be only specific embodiments of the invention, obviously the invention is not restricted to above embodiment, have many similar changes thereupon.If all distortion that those skilled in the art directly derives from content disclosed by the invention or associates, protection scope of the present invention all should be belonged to.
Claims (16)
1. a high-strength steel, is characterized in that, its chemical element mass percentage content is:
C:0.11-0.18%, Si:0.1-0.4%, Mn:1.0-1.6%, Cr:0.25-0.9%, Mo:0.10-0.50%, W:0.10-0.55%, Nb:0.01-0.08%, V:0.01-0.12%, Ni:0.10-0.40%, 0<B<0.0020%, 0 < N≤0.004%, 0<Ti≤0.010%, O<0.0030%, S<0.005%, Ca+Mg:0.001-0.005%, surplus is Fe and other inevitable impurity; Meet relational expression in addition: (B+Ti)/N>1.
2. high-strength steel as claimed in claim 1, is characterized in that, also meet Ceq=C+Mn/6+ (Cr+Mo+V)/5+Ni/15<0.62.
3. high-strength steel as claimed in claim 1, it is characterized in that, its microtexture is tempered sorbite.
4. high-strength steel as claimed in claim 3, is characterized in that described tempered sorbite having BN and the TiN precipitate of disperse.
5. high-strength steel as claimed in claim 3, is characterized in that described tempered sorbite also having NbC precipitate and/or the VC precipitate of disperse.
6. high-strength steel as claimed in claim 1, it is characterized in that, it has the nodule of small and dispersed.
7. high-strength steel as claimed in claim 6, is characterized in that, described inclusion be MgO, MgS, CaO and CaS at least one of them.
8. high-strength steel as claimed in claim 1, it is characterized in that, the content of B, Ti and N element is further: B 0.0011-0.0016%, Ti 0.003-0.008%, N 0.003-0.004%.
9. high-strength steel as claimed in claim 1, it is characterized in that, the content of O, S, Mg and Ca element is further: O<0.0024%; S<0.004%; Ca+Mg:0.001-0.004%.
10. high-strength steel as claimed in claim 1, is characterized in that, also meet Ceq=C+Mn/6+ (Cr+Mo+V)/5+Ni/15<0.62; And the microtexture of described high-strength steel is tempered sorbite, described tempered sorbite have BN and the TiN precipitate of disperse and the NbC precipitate of disperse and/or VC precipitate; Described high-strength steel has the nodule of small and dispersed, described inclusion be MgO, MgS, CaO and CaS at least one of them.
11. 1 kinds of High Tensile Steel Tubes, it is weldless steel tube, it is characterized in that, it adopts as the high-strength steel in claim 1-10 as described in any one obtains.
12. High Tensile Steel Tube as claimed in claim 11, it is characterized in that, its tensile strength is greater than 980MPa, and the low-temperature impact work at-40 DEG C is greater than 52J; When more than 15kJ/cm thermal weld stress amount after welding, the tensile strength of welding joint and heat affected zone is greater than 980MPa, and the low-temperature impact work at-40 DEG C is greater than 52J.
The manufacture method of 13. High Tensile Steel Tubes as described in claim 11 or 12, it comprises step: steel-making; Be cast as round base; Tube rolling; Thermal treatment.
14. the manufacture method of High Tensile Steel Tube as claimed in claim 13, it is characterized in that, in described heat treatment step, carry out modifier treatment to steel pipe, wherein quenching temperature is 880-930 DEG C, and soaking time is 30-60min, then shrend; Then 580-650 DEG C is carried out high tempering, and soaking time is 30-80min; Then steel pipe is carried out hot straightening, hot straightening temperature 500-600 DEG C.
The manufacture method of 15. High Tensile Steel Tubes as claimed in claim 13, is characterized in that, in described tube rolling step, bore a hole after the soaking of circle base, wherein soaking temperature is 1220-1260 DEG C, and piercing temperature is 1200-1240 DEG C; Then carry out tube rolling, temperature is 980-1200 DEG C.
16. the manufacture method of High Tensile Steel Tube as claimed in claim 13, is characterized in that also having welding step after described heat treatment step.
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105586529A (en) * | 2016-02-25 | 2016-05-18 | 宝山钢铁股份有限公司 | 890MPa-level high-strength steel, steel pipe and manufacturing method of steel pipe |
| CN106048414A (en) * | 2016-07-07 | 2016-10-26 | 无锡戴尔普机电设备有限公司 | A novel material for connecting rod of air volume adjusting valve |
| CN106195434A (en) * | 2016-07-07 | 2016-12-07 | 无锡戴尔普机电设备有限公司 | A kind of Novel air adjustable valve sharf material |
| CN107841681A (en) * | 2017-10-24 | 2018-03-27 | 上海大学 | Perforation casing material and preparation method thereof |
| CN111748727A (en) * | 2019-03-27 | 2020-10-09 | 宝山钢铁股份有限公司 | Ultrahigh-strength seamless steel pipe with excellent weldability and manufacturing method thereof |
| CN112553526A (en) * | 2020-11-20 | 2021-03-26 | 林州凤宝管业有限公司 | 960 MPa-level ultrahigh-strength structural steel, steel pipe and manufacturing method and application thereof |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102796966A (en) * | 2011-05-25 | 2012-11-28 | 宝山钢铁股份有限公司 | High-intensity steel and steel pipes and preparation method thereof |
| WO2013100106A1 (en) * | 2011-12-28 | 2013-07-04 | 新日鐵住金株式会社 | High strength steel pipe having excellent ductility and low temperature toughness, high strength steel sheet, and method for producing steel sheet |
| CN104046910A (en) * | 2014-06-30 | 2014-09-17 | 宝山钢铁股份有限公司 | Ultrahigh-strength ultrahigh-toughness oil casing and manufacturing method thereof |
-
2015
- 2015-05-26 CN CN201510274901.4A patent/CN104862613A/en active Pending
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102796966A (en) * | 2011-05-25 | 2012-11-28 | 宝山钢铁股份有限公司 | High-intensity steel and steel pipes and preparation method thereof |
| WO2013100106A1 (en) * | 2011-12-28 | 2013-07-04 | 新日鐵住金株式会社 | High strength steel pipe having excellent ductility and low temperature toughness, high strength steel sheet, and method for producing steel sheet |
| CN104046910A (en) * | 2014-06-30 | 2014-09-17 | 宝山钢铁股份有限公司 | Ultrahigh-strength ultrahigh-toughness oil casing and manufacturing method thereof |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105586529A (en) * | 2016-02-25 | 2016-05-18 | 宝山钢铁股份有限公司 | 890MPa-level high-strength steel, steel pipe and manufacturing method of steel pipe |
| CN106048414A (en) * | 2016-07-07 | 2016-10-26 | 无锡戴尔普机电设备有限公司 | A novel material for connecting rod of air volume adjusting valve |
| CN106195434A (en) * | 2016-07-07 | 2016-12-07 | 无锡戴尔普机电设备有限公司 | A kind of Novel air adjustable valve sharf material |
| CN107841681A (en) * | 2017-10-24 | 2018-03-27 | 上海大学 | Perforation casing material and preparation method thereof |
| CN111748727A (en) * | 2019-03-27 | 2020-10-09 | 宝山钢铁股份有限公司 | Ultrahigh-strength seamless steel pipe with excellent weldability and manufacturing method thereof |
| CN111748727B (en) * | 2019-03-27 | 2022-01-14 | 宝山钢铁股份有限公司 | Ultrahigh-strength seamless steel pipe with excellent weldability and manufacturing method thereof |
| CN112553526A (en) * | 2020-11-20 | 2021-03-26 | 林州凤宝管业有限公司 | 960 MPa-level ultrahigh-strength structural steel, steel pipe and manufacturing method and application thereof |
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