CN103276315B - 900MPa-level ultrahigh-tenacity high-toughness pipeline steel plate and manufacturing method thereof - Google Patents
900MPa-level ultrahigh-tenacity high-toughness pipeline steel plate and manufacturing method thereof Download PDFInfo
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Abstract
The invention relates to a 900MPa-level ultrahigh-tenacity high-toughness pipeline steel plate. The 900MPa-level ultrahigh-tenacity high-toughness pipeline steel plate comprises the following chemical compositions in percentage by weight: 0.035%-0.065% of C, 0.15-%-0.40% of Si, 1.90%-2.50% of Mn, less than or equal to 0.012% of P, less than or equal to 0.0015% of S, 0.030%-0.055% of Nb, 0.010%-0.25% of Ti, 0-0.30% of Cu, 0.35%-0.60% of Cr, 0.10%-0.50% of Ni, 0-0.50% of Mo, 0.020%-0.050% of Al, 0.0010%-0.0030% of B, less than or equal to 0.0080% of N. The preparation method comprises the steps of: smelting and continuously casting into blanks; heating casting blanks; roughly rolling; finely rolling; fast cooling; straightening after stopping for 40-60S. By adding B and Cr elements and reducing the content of Nb, Mo and Ni, the production cost of the ultrahigh-tenacity X80 pipeline steel can be obviously lowered, and the efficiency can be improved; a metallographic structure is bainite plus less M-A structure, the main mechanical properties are as follows: more than or equal to 900MPa of RP0.2, more than or equal to 1050MPa of Rm, less than or equal to 0.90 of RP0.2/Rm, more than equal to 12% of elongation (A50mm), more than or equal to 200J of minus 20degree CKV2, and more than or equal to 5% of minus 15 degree CDWTT SA.
Description
Technical field
The present invention relates to microalloying steel making field, specifically for meeting domestic and international high pressure long distance pipeline trunk main to the demand of superstrength, high tenacity Pipeline Steel Plate, providing a kind of 900MPa grade high ductility Pipeline Steel Plate and manufacture method thereof.
Background technology
Along with the high speed development of world economy, grow with each passing day to the demand of oil, Sweet natural gas equal energy source resource, the construction of oil, Long-distance Transmission Pipeline obtains flourish.For improving the transport efficiency of long distance pipeline and the economy of operation, in recent years, transfer pressure and the caliber of pipeline constantly increase, for ensureing the security that high pressure long distance pipeline runs, also improve constantly the used intensity of pipe line steel material and the requirement of fracture toughness property, the large-scale engineering applications of ultrahigh-intensity high-toughness pipe line steel in following long distance pipeline has become inevitable.For this reason, the invention provides a kind of 900MPa grade super strength high tenacity Pipeline Steel Plate and manufacture method thereof.
Before patent of the present invention, number of patent application is the patent of invention " high-intensity high-tenacity X80 pipe line steel and hot rolled plate making process thereof " of 200410025584.41, number of patent application is the patent of invention " a kind of high-strength high-toughness X 80 hot rolling coiled sheet for spiral buried arc welding and production method thereof " of 200810227820.9, number of patent application be 200910237313.8 patent of invention " a kind of X 70 hot-rolled steel coil for pipeline steel and manufacture method thereof " etc. set forth the X70 that China's long distance pipeline trunk main mainly adopts at present, X80 level pipe line steel and manufacture method thereof, under the existing transfer pressure condition of long distance pipeline (10MPa or 12MPa), these series product can meet the safe operation of long distance pipeline, but what require along with long distance pipeline performance driving economy improves constantly, Cemented filling pressure improves further, X70 when the time comes, X80 level pipe line steel cannot meet the security requirement of conduit running.
Number of patent application is the Chinese invention patent " high-strength low-yield ratio X 90 hot-rolled steel plate and production method thereof " of 201210050624.5, number of patent application is the Chinese invention patent " a kind of high strength X 100 pipeline steel hot rolled slab and production method thereof " of 200810012150.9, the patent No. is the Japanese invention patent " X120 superstrength Welded Steel Pipe and manufacture method thereof " of JP2006233263, the patent No. is that the Japanese invention patent of JP2007023346 " has high strength welded steelpipe and the manufacture method thereof of excellent aging performance " etc. and set forth the various heterogeneity design of employing, in conjunction with the method for TMCP explained hereafter superstrength X90 ~ X120 level pipe line steel, this type of pipe line steel will have good applicability when Cemented filling pressure is at 12 ~ 18MPa, but as Cemented filling pressure improves further, the security requirement meeting pipeline operation will be difficult to equally.
Number of patent application be 201010276430.8 Chinese invention patent " manufacture method of low yield strength ratio superstrength X130 pipe line steel and hot rolled slab thereof " set forth the low C of a kind of employing, high Mn, high Nb, the appropriate Composition Design adding the alloying elements such as Cu, Cr, Ni, Mo, in conjunction with the method for conventional TMCP explained hereafter X130 level Pipeline Steel Plate.This production method can reach the high strength of 900MPa level pipe line steel, but does not add the good economy element of the strengthening effects such as B, V, and alloy designs cost is higher, is unfavorable for accomplishing scale production.
Number of patent application is that the U.S. patent Nos of US5900075 describes a kind of ultra high-strength pipeline steel being promoted Cu precipitation strength by thermal treatment; the method can reach the high strength of 900MPa level; but complex manufacturing, and process costs is higher, is unfavorable for realizing economical large-scale production.
Summary of the invention
The object of the invention is the deficiency in order to overcome about Hi-grade steel pipeline steel strength in prior art, the deficiency such as demand, the cost of alloy that can not meet following pressure piping are high, production process is complicated, a kind of the 900MPa grade super strength high tenacity Pipeline Steel Plate and the manufacture method thereof that are applicable to the construction of following ultra-high voltage long distance pipeline trunk main are provided, the method production process is simple, manufacturing cost is lower, and every Main Mechanical index reaches: R
p0.2>=900MPa, R
m>=1050MPa, R
p0.2/ R
m≤ 0.90, unit elongation (A
50mm)>=12% ,-20 DEG C of KV
2>=200J ,-15 DEG C of DWTT SA>=85%.
Realize the measure of above-mentioned purpose:
A kind of 900MPa grade super strength high tenacity Pipeline Steel Plate, the weight percent of its chemical composition is: C:0.035 ~ 0.065, Si:0.15 ~ 0.40, Mn:1.90 ~ 2.50, P :≤0.012, S :≤0.0015, Nb:0.030 ~ 0.055, Ti:0.010 ~ 0.025, Cu:0 ~ 0.30, Cr:0.35 ~ 0.60, Ni:0.10 ~ 0.50, Mo:0 ~ 0.50, Al:0.020% ~ 0.050, B:0.0010 ~ 0.0030, N :≤0.0080, Ni/Cu >=0.5, Cr+Cu+Ni≤1.1, all the other are Fe and inevitable impurity.
It is characterized in that: be also added with the Cu that weight percent content is≤0.30%.
Produce the method for above-mentioned steel plate, mainly comprise the following steps:
1) smelt also continuous casting and become base;
2) to strand heating, Heating temperature is controlled at 1050 ~ 1120 DEG C; Ensure the abundant solid solution of micro alloying element, prevent austenite crystal from too growing up simultaneously;
3) roughing is carried out: control roughing temperature at 980 ~ 1090 DEG C, every time draft is not less than 10%, makes the abundant refinement of austenite crystal, suppress Austenite Grain Growth simultaneously by dynamic and static recrystallize;
4) carry out finish rolling, control final rolling temperature at 750 ~ 920 DEG C, accumulative draft is not less than 70%, the grain size of dividing recrystallize to cause with preventing portion is uneven, make austenite crystal fully flatten simultaneously, form abundant deformation bands and be beneficial to forming core, organize after refinement phase transformation;
5) cool fast, controlled cooling model speed is at 30 ~ 60 DEG C/S, and final cooling temperature is no more than 200 DEG C;
6) before straightener, stop 40 ~ 60S after rapid cooling to align.
In the present invention, the mechanism of action of each element is as follows:
Carbon (C) content is 0.035 ~ 0.065%, adds a certain amount of carbon, significantly can improve the intensity of steel, but when carbon content exceedes to a certain degree, the low-temperature flexibility of steel significantly worsens, and thus carbon content is defined as 0.035 ~ 0.065%.
Silicon (Si) content is 0.15 ~ 0.40%, mainly plays solution strengthening effect, avoids excessively causing the moulding of steel because adding simultaneously, toughness significantly worsens.
Manganese (Mn) content is 1.90 ~ 2.50%, adds higher economic alloy element manganese, can significantly improve the intensity of steel, in addition, manganese can also crystal grain thinning to a certain extent, improves the impelling strength of steel, but excessive manganese easily forms segregation, cause composition and the tissue odds of steel.
Niobium (Nb) content is 0.030 ~ 0.055%, and niobium can significantly improve the austenite recrystallization temperature of steel, expands Unhydrated cement scope, be convenient to realize high temperature controlled rolling, reduce mill load, niobium can also suppress Austenite Grain Growth simultaneously, has significant refined crystalline strengthening and precipitation strength effect.But in high strength bainite steel, add the generation that excessive niobium can promote M-A island, reduce the toughness of welded heat affecting zone, and Nb belongs to noble metal, increase content and can significantly improve alloy designs cost, therefore, the content of niobium is controlled at lower level.
Titanium (Ti) content is 0.010 ~ 0.025%, the effect in steel of titanium and niobium is similar, there are stronger refined crystalline strengthening and precipitation strength effect, the titanium of trace can also at high temperature be combined with carbon, oxygen, form the precipitate of high temperature refractory, be conducive to the Austenite Grain Growth suppressing welded heat affecting zone, significantly improve the toughness of welded heat affecting zone.
Nickel (Ni) content is 0.10 ~ 0.50%, and nickel effectively can improve the hardening capacity of steel, has certain solution strengthening effect, significantly can also improve the low-temperature flexibility of steel.In addition, the check crack that nickel can also effectively stop the red brittleness of Cu to cause, and significantly improve the corrosion resistance nature of steel.But nickel and molybdenum similar, belong to noble metal, easily cause the manufacturing cost of steel significantly to improve, in addition, too high nickel content easily cause steel-plate iron oxide scale be difficult to remove, cause plate surface quality problem.
The content of chromium (Cr) is 0.35 ~ 0.60%, and chromium can significantly improve the hardening capacity of steel, and has certain solution strengthening effect, can substitute expensive alloying elements Mo, Ni to a great extent.In addition, add weather-proof, corrosion resistance nature that certain chromium can also improve steel, but add excessive, easily cause the ductile-brittle transition temperature of steel significantly to rise.
The content of molybdenum (Mo) is 0.001 ~ 0.50%, molybdenum is significantly postponed γ → α and is changed, suppress ferrite and pearlite forming core, promote to have the formation of the bainite/acicular ferrite of high density dislocation substructure, make steel obtain bainite/acicular ferrite structure within the scope of a wider cooling rate after rolling.For ensureing tissue, the performance uniformity in special think gauge Pipeline Steel Plate thickness of slab direction, Mo content is controlled in higher level.But molybdenum belongs to noble metal, add-on increase can improve the manufacturing cost of steel, and too high molybdenum also can cause the low-temperature flexibility of steel to worsen simultaneously.
The content of copper (Cu) is 0 ~ 0.30%, adds copper in right amount, improves intensity and the hardening capacity of steel, and can improve weather-proof, the corrosion resistance nature of steel.But copper is low melting point metal, easily causes hot-short, it is unfavorable to add the excessive low-temperature flexibility to steel.
The content of aluminium (Al) is 0.020 ~ 0.050%, and aluminium is deoxidant element main in steel, significantly can reduce the oxygen level in steel, and the simultaneously combination of aluminium and nitrogen forms AlN, can crystal grain thinning effectively.When but aluminium content is more than 0.05% in steel, easily cause the oxide inclusion of aluminium obviously to increase, reduce the cleanliness factor of steel, unfavorable to the low-temperature flexibility of steel.
The content of boron (B) is 0.0010 ~ 0.0030%, the forming core that the B adding trace can significantly suppress ferrite on austenite grain boundary, also make bainite transformation curve become flat simultaneously, even if thus within the scope of a larger cooling rate, also can obtain bainite structure when low-carbon (LC), make the intensity rank that pipe line steel reaches very high.But after add-on acquires a certain degree, the effect of B reaches capacity, and easily cause steel brittle, therefore the content of boron is controlled 0.0010 ~ 0.0030%.
Phosphorus (P), sulphur (S), nitrogen (N) content are respectively: [%P]≤0.012, [%S]≤0.0015, [%N]≤0.008.Phosphorus easily causes the cold short of steel, and sulphur easily causes hot-short, and nitrogen easily causes the quenching inefficacy of steel and deformation to lose efficacy, and causes the unstable properties of steel, therefore should reduce the content of the phosphorus in steel, sulphur, nitrogen as far as possible.
In addition, ensure Ni/Cu >=0.5, allow Cu and the Ni of low melting point form the higher complete solid solution of fusing point, what prevent low melting point Cu from causing is hot-short.
Ensure Cr+Cu+Ni≤1.1%, strictly control the alloy content total amounts such as chromium, copper, nickel, reduce cost of alloy, ensure that steel plate has good welding property.
In the present invention, main technique effect is as follows:
The present invention why by slab heating temperature at 1050 ~ 1120 DEG C, because by Theoretical Calculation and the experimental study of many experiments room, more than 1050 DEG C, microalloy carbon/the nitrogen compound of steel grade can be fully solid molten, and Heating temperature more than 1120 DEG C time, original austenite grain is sharply grown up, and therefore considered critical slab heating temperature is interval.
Why controlling in speed of cooling is 30 ~ 60 DEG C/s, final cooling temperature is controlled be no more than 200 DEG C, because calculated by Material Thermodynamics and the research of many experiments room, when speed of cooling is 30 ~ 60 DEG C/s, when final cooling temperature controls below 200 DEG C, effectively can improve the intensity of steel of the present invention, abundant refinement and malleableize cost tissue, obtain desirable strong, mould, toughness coupling.
The present invention compared with prior art, by adding the high-hardenability alloying elements such as B, Cr of less expensive, reducing the alloy dosage of the noble metals such as Nb, Mo, Ni, significantly can reduce production cost, enhance productivity.Indicate through test, metallographic structure of the present invention is the M-A tissue of desirable bainite+a small amount of Dispersed precipitate, and every Main Mechanical index reaches: yield strength (R
p0.2>=900MPa), tensile strength (R
m)>=1050MPa, yield tensile ratio (R
p0.2/ R
m)≤0.90, unit elongation (A
50mm)>=12% ,-20 DEG C of KV
2>=200J ,-15 DEG C of DWTT SA>=85%.
Embodiment
Below the present invention is described in detail:
Embodiment 1:
A kind of 900MPa grade super strength high tenacity Pipeline Steel Plate, its chemical composition and weight percent are: C:0.035%, Si:0.21%, Mn:2.41%, P:0.012%, S:0.0014%, Nb:0.055%, Ti:0.019%, Cu:0.14%, Cr:0.47%, Ni:0.37%, Mo:0.32%, Al:0.043%, B:0.0028%, N:0.0073%, and surplus is Fe and is inevitably mingled with.
Production craft step:
1) smelt also continuous casting and become base;
2) by heating steel billet extremely
1052 DEG C;
3) steel billet carries out roughing after coming out of the stove, and its start rolling temperature is
1031 DEG C, each percentage pass reduction>=10% of roughing, roughing end temp is
980 DEG C;
4) roughing treats after terminating that temperature starts to carry out finish rolling to 920 DEG C, and finish rolling end temp is 846 DEG C, and it is 80% that finish rolling adds up draft;
5) steel plate finish rolling carries out ultra-rapid cooling after terminating immediately, and final cooling temperature is 188 DEG C, and rate of cooling is: 36.4 DEG C/s;
6) steel plate is after ultra-rapid cooling, carries out brute force aligning before straightener after stopping 50s, obtained required steel plate.
Embodiment 2:
A kind of 900MPa grade super strength high tenacity Pipeline Steel Plate, its chemical composition and weight percent are: C:0.042%, Si:0.39%, Mn:2.50%, P:0.011%, S:0.0010%, Nb:0.051%, Ti:0.025%, Cu:0.30%, Cr:0.35%, Ni:0.42%, Mo:0.18%, Al:0.049%, B:0.0030%, N:0.0066%, and surplus is Fe and is inevitably mingled with.
Production craft step:
1), smelt also continuous casting and become base;
2), by heating steel billet to 1105 DEG C;
3), steel billet carries out roughing after coming out of the stove, and its start rolling temperature is 1084 DEG C, and each percentage pass reduction of roughing is not less than 10%, and roughing end temp is 1066 DEG C;
4), roughing treat after terminating temperature start to carry out finish rolling to 900 DEG C, finish rolling end temp is 826 DEG C, and it is 79.1% that finish rolling adds up draft;
5), steel plate finish rolling carries out ultra-rapid cooling after terminating immediately, and final cooling temperature is 188 DEG C, and rate of cooling is: 30.5 DEG C/s;
6), steel plate after ultra-rapid cooling, carry out brute force aligning stop 45s before straightener after, obtained required steel plate.
Embodiment 3:
A kind of 900MPa grade super strength high tenacity Pipeline Steel Plate, its chemical composition and weight percent are: C:0.048%, Si:0.34%, Mn:2.32%, P:0.010%, S:0.0011%, Nb:0.047%, Ti:0.015%, Cu:0%, Cr:0.60%, Ni:0.32%, Mo:0.36%, Al:0.032%, B:0.0026%, N:0.0060%, and surplus is Fe and is inevitably mingled with.
Production craft step:
1) smelt also continuous casting and become base;
2) by heating steel billet to 1120 DEG C;
3) steel billet carries out roughing after coming out of the stove, and its start rolling temperature is 1090 DEG C, and each percentage pass reduction of roughing is not less than 10%, and roughing end temp is 1078 DEG C;
4) roughing treats after terminating that temperature starts to carry out finish rolling to 890 DEG C, and finish rolling end temp is 804 DEG C, and it is 80% that finish rolling adds up draft;
5) steel plate finish rolling carries out ultra-rapid cooling after terminating immediately, and final cooling temperature is 195 DEG C, and rate of cooling is: 59.8 DEG C/s;
6) steel plate is after ultra-rapid cooling, carries out brute force aligning before straightener after stopping 60s, obtained required steel plate.
Embodiment 4:
A kind of 900MPa grade super strength high tenacity Pipeline Steel Plate, its chemical composition and weight percent are: C:0.054%, Si:0.27%, Mn:2.15%, P:0.008%, S:0.0008%, Nb:0.042%, Ti:0.012%, Cu:0.19%, Cr:0.52%, Ni:0.28%, Mo:0.24%, Al:0.021%, B:0.0013%, N:0.0054%, and surplus is Fe and is inevitably mingled with.
Production craft step:
1) smelt also continuous casting and become base;
2) by heating steel billet to 1083 DEG C;
3) steel billet carries out roughing after coming out of the stove, and its start rolling temperature is 1062 DEG C, and each percentage pass reduction of roughing is not less than 10%, and roughing end temp is 1036 DEG C;
4) roughing treats after terminating that temperature starts to carry out finish rolling to 880 DEG C, and finish rolling end temp is 794 DEG C, and it is 77.8% that finish rolling adds up draft;
5) steel plate finish rolling carries out ultra-rapid cooling after terminating immediately, and final cooling temperature is 166 DEG C, and rate of cooling is: 43.2 DEG C/s;
6) steel plate is after ultra-rapid cooling, carries out brute force aligning before straightener after stopping 40s, obtained required steel plate.
Embodiment 5:
A kind of 900MPa grade super strength high tenacity Pipeline Steel Plate, its chemical composition and weight percent are: C:0.059%, Si:0.15%, Mn:1.91%, P:0.007%, S:0.0005%, Nb:0.032%, Ti:0.010%, Cu:0.23%, Cr:0.43%, Ni:0.12%, Mo:0.50%, Al:0.028%, B:0.0010%, N:0.0046%, and surplus is Fe and is inevitably mingled with.
Production craft step:
1) smelt also continuous casting and become base;
2) by heating steel billet to 1053 DEG C;
3) steel billet carries out roughing after coming out of the stove, and its start rolling temperature is 1030 DEG C, and each percentage pass reduction of roughing is not less than 10%, and roughing end temp is 983 DEG C;
4) roughing treats after terminating that temperature starts to carry out finish rolling to 850 DEG C, and finish rolling end temp is 752 DEG C, and it is 77.8% that finish rolling adds up draft;
5) steel plate finish rolling carries out ultra-rapid cooling after terminating immediately, and final cooling temperature is 182 DEG C, and rate of cooling is: 46.9 DEG C/s;
6) steel plate is after ultra-rapid cooling, carries out brute force aligning before straightener after stopping 50s, obtained required steel plate.
Embodiment 6:
A kind of 900MPa grade super strength high tenacity Pipeline Steel Plate, its chemical composition and weight percent are: C:0.065%, Si:0.24%, Mn:2.03%, P:0.006%, S:0.0007%, Nb:0.039%, Ti:0.017%, Cu:0.28%, Cr:0.48%, Ni:0.50%, Mo:0.0013%, Al:0.043%, B:0.0015%, N:0.0073%, and surplus is Fe and is inevitably mingled with.
Production craft step:
1) smelt also continuous casting and become base;
2) by heating steel billet to 1078 DEG C;
3) steel billet carries out roughing after coming out of the stove, and its start rolling temperature is 1060 DEG C, and each percentage pass reduction of roughing is not less than 10%, and roughing end temp is 1034 DEG C;
4) roughing treats after terminating that temperature starts to carry out finish rolling to 865 DEG C, and finish rolling end temp is 777 DEG C, and it is 80% that finish rolling adds up draft;
5) steel plate finish rolling carries out ultra-rapid cooling after terminating immediately, and final cooling temperature is 100 DEG C, and rate of cooling is: 52.5 DEG C/s;
6) steel plate carries out brute force aligning stop 60s before straightener after ultra-rapid cooling after, obtained required steel plate.
The horizontal salient features detection statistics table of each embodiment of table 1
Above-described embodiment is only the best and exemplifies, and is not the restriction to embodiments of the present invention.
Claims (2)
1. a 900MPa grade super strength high tenacity Pipeline Steel Plate, its chemical composition and weight percent are: C:0.042%, Si:0.39%, Mn:2.50%, P:0.011%, S:0.0010%, Nb:0.051%, Ti:0.025%, Cu:0.30%, Cr:0.35%, Ni:0.42%, Mo:0.18%, Al:0.049%, B:0.0030%, N:0.0066%, and surplus is Fe and is inevitably mingled with;
Production craft step:
1), smelt also continuous casting and become base;
2), by heating steel billet to 1105 DEG C;
3), steel billet carries out roughing after coming out of the stove, and its start rolling temperature is 1084 DEG C, and each percentage pass reduction of roughing is not less than 10%, and roughing end temp is 1066 DEG C;
4), roughing treat after terminating temperature start to carry out finish rolling to 900 DEG C, finish rolling end temp is 826 DEG C, and it is 79.1% that finish rolling adds up draft;
5), steel plate finish rolling carries out ultra-rapid cooling after terminating immediately, and final cooling temperature is 188 DEG C, and rate of cooling is: 30.5 DEG C/s;
6), steel plate after ultra-rapid cooling, carry out brute force aligning stop 45s before straightener after, obtained required steel plate.
2. a 900MPa grade super strength high tenacity Pipeline Steel Plate, its chemical composition and weight percent are: C:0.059%, Si:0.15%, Mn:1.91%, P:0.007%, S:0.0005%, Nb:0.032%, Ti:0.010%, Cu:0.23%, Cr:0.43%, Ni:0.12%, Mo:0.50%, Al:0.028%, B:0.0010%, N:0.0046%, and surplus is Fe and is inevitably mingled with;
Production craft step:
1) smelt also continuous casting and become base;
2) by heating steel billet to 1053 DEG C;
3) steel billet carries out roughing after coming out of the stove, and its start rolling temperature is 1030 DEG C, and each percentage pass reduction of roughing is not less than 10%, and roughing end temp is 983 DEG C;
4) roughing treats after terminating that temperature starts to carry out finish rolling to 850 DEG C, and finish rolling end temp is 752 DEG C, and it is 77.8% that finish rolling adds up draft;
5) steel plate finish rolling carries out ultra-rapid cooling after terminating immediately, and final cooling temperature is 182 DEG C, and rate of cooling is: 46.9 DEG C/s;
6) steel plate is after ultra-rapid cooling, carries out brute force aligning before straightener after stopping 50s, obtained required steel plate.
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| CN104141099B (en) * | 2014-08-12 | 2016-05-18 | 北京首钢股份有限公司 | A kind of manufacture method of super thick specification X70 hot-rolled sheet coil |
| DE102016108633A1 (en) * | 2016-05-10 | 2017-11-30 | Benteler Steel/Tube Gmbh | Fuel injection line and tubular duct |
| CN106048181B (en) * | 2016-07-27 | 2018-11-20 | 武汉钢铁有限公司 | A kind of low temperature think gauge pipe line steel preparation method suitable for hot continuous rolling producing line |
| CN106498263A (en) * | 2016-10-13 | 2017-03-15 | 南京创贝高速传动机械有限公司 | A kind of high-speed gear box is vented the production technology of Taper Pipe |
| CN114962815A (en) * | 2022-06-24 | 2022-08-30 | 中国重型机械研究院股份公司 | Pipeline system for ultrahigh pressure fluid transmission |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006265577A (en) * | 2005-03-22 | 2006-10-05 | Jfe Steel Kk | Method for producing high strength, high toughness steel sheet |
| CN101649425A (en) * | 2009-09-08 | 2010-02-17 | 武汉钢铁(集团)公司 | X120 pipeline steel with low crack sensitivity and high toughness and manufacturing method thereof |
| KR20110130983A (en) * | 2010-05-28 | 2011-12-06 | 현대제철 주식회사 | High strength steel plate with excellent low-temperature toughness, 560mpa tensile strength for line pipe and the method of manufacturing thereof |
| CN102373387A (en) * | 2011-11-02 | 2012-03-14 | 武汉钢铁(集团)公司 | Steel plate for large-strain cold-bent tube and manufacturing method thereof |
| CN102400062A (en) * | 2010-09-07 | 2012-04-04 | 鞍钢股份有限公司 | X130 pipe line steel with low yield ratio and ultrahigh strength and manufacturing method of hot rolled flat plate of X130 pipe line steel |
-
2013
- 2013-05-17 CN CN201310183606.9A patent/CN103276315B/en not_active Expired - Fee Related
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006265577A (en) * | 2005-03-22 | 2006-10-05 | Jfe Steel Kk | Method for producing high strength, high toughness steel sheet |
| CN101649425A (en) * | 2009-09-08 | 2010-02-17 | 武汉钢铁(集团)公司 | X120 pipeline steel with low crack sensitivity and high toughness and manufacturing method thereof |
| KR20110130983A (en) * | 2010-05-28 | 2011-12-06 | 현대제철 주식회사 | High strength steel plate with excellent low-temperature toughness, 560mpa tensile strength for line pipe and the method of manufacturing thereof |
| CN102400062A (en) * | 2010-09-07 | 2012-04-04 | 鞍钢股份有限公司 | X130 pipe line steel with low yield ratio and ultrahigh strength and manufacturing method of hot rolled flat plate of X130 pipe line steel |
| CN102373387A (en) * | 2011-11-02 | 2012-03-14 | 武汉钢铁(集团)公司 | Steel plate for large-strain cold-bent tube and manufacturing method thereof |
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