WO2017171070A1 - Fil machine à haute résistance laminé à chaud présentant une excellente résistance à la corrosion fissurante provoquée par l'hydrogène sulfuré - Google Patents

Fil machine à haute résistance laminé à chaud présentant une excellente résistance à la corrosion fissurante provoquée par l'hydrogène sulfuré Download PDF

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Publication number
WO2017171070A1
WO2017171070A1 PCT/JP2017/013784 JP2017013784W WO2017171070A1 WO 2017171070 A1 WO2017171070 A1 WO 2017171070A1 JP 2017013784 W JP2017013784 W JP 2017013784W WO 2017171070 A1 WO2017171070 A1 WO 2017171070A1
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Prior art keywords
less
hot
amount
rolled wire
ssc resistance
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PCT/JP2017/013784
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English (en)
Japanese (ja)
Inventor
将 高山
智一 増田
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株式会社神戸製鋼所
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Priority claimed from JP2017034928A external-priority patent/JP2017186654A/ja
Application filed by 株式会社神戸製鋼所 filed Critical 株式会社神戸製鋼所
Publication of WO2017171070A1 publication Critical patent/WO2017171070A1/fr

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires

Definitions

  • the present disclosure relates to a hot rolled wire used for manufacturing a steel wire. More specifically, the present invention relates to a hot-rolled wire used for producing a steel wire useful as a reinforcing material for a part used in a sour environment containing hydrogen sulfide or a flexible riser.
  • a flexible riser is used to pump up crude oil.
  • the flexible riser is manufactured using a resin pipe and a steel wire, and the steel wire is used as a reinforcing material for the resin pipe. Therefore, the steel wire is particularly required to have a high yield strength of 900 MPa or more.
  • the steel wire since the oil field is in a sour environment containing hydrogen sulfide, the steel wire has characteristics that suppress sulfide stress cracking (SSC) (hereinafter sometimes referred to as SSC resistance). Is required.
  • SSC resistance is known to improve as the strength decreases in a sour environment containing hydrogen sulfide, but the hot rolled wire used as the material for the steel wire has high strength and excellent SSC resistance. Is required.
  • Patent Document 1 proposes a martensitic steel for a line pipe that exhibits excellent sulfide stress corrosion cracking resistance even in an environment containing a small amount of hydrogen sulfide and is excellent in tensile properties at high temperatures.
  • This martensitic steel for line pipes is a so-called 13% Cr steel containing Cr in the range of 10 to 14%, reducing the C content to 0.02% or less and the N content to 0.07% or less, Ni, Mo, and further carbide forming elements such as Ti, Zr, and Ta are appropriately added, and Nb and / or V are added in appropriate amounts.
  • Patent Document 2 proposes a hot-rolled wire having a high yield strength of 900 MPa or more and excellent SSC resistance.
  • the segregation degree (S max / S ave ) calculated based on the average value S ave (mass%) of the S amount and the maximum value S max (mass%) of the S amount is appropriately controlled. There is a feature.
  • Patent Document 1 Although the martensitic steel for line pipes described in Patent Document 1 is excellent in SSC resistance, it is thought that the yield strength at room temperature is low because the C content is suppressed to 0.02% or less. .
  • Patent Document 2 in order to control the segregation degree of S, it is necessary to strictly control the rolling conditions during hot rolling.
  • the embodiment of the present invention has been made paying attention to the above-described circumstances, and an object thereof is to provide a hot-rolled wire rod having high strength and excellent SSC resistance.
  • the high-strength hot-rolled wire rod excellent in sulfide stress corrosion cracking resistance according to the embodiment of the present invention that has solved the above problems is % By mass C: 0.10 to 0.7%, Si: more than 0%, 2.0% or less, Mn: 0.3 to 2.0%, Cr: 0.05 to 2.0%, V: 0.05-0.5% P: more than 0%, 0.02% or less, S: more than 0%, 0.008% or less, and Al: more than 0%, 0.05% or less, The balance consists of iron and inevitable impurities, The K value represented by the following formula (1) is 1.7 to 10, The gist is that the amount of hydrogen is more than 0 ppm and 1.0 ppm or less.
  • the high-strength hot-rolled wire preferably further contains at least one element selected from the group consisting of the following (a) to (d) as other elements in mass%.
  • a hot-rolled wire having high strength and excellent SSC resistance is provided by appropriately controlling the component composition of the hot-rolled wire and the amount of hydrogen contained in the hot-rolled wire. it can.
  • the inventors of the present invention have made extensive studies in order to increase the SSC resistance after securing the strength of the hot-rolled wire material used as the steel wire material.
  • the amount of C, Si, Mn, Cr, V, and Al is controlled so that the K value satisfies a predetermined relationship, after ensuring the strength of the wire by strictly controlling the component composition, And it discovered that if the amount of hydrogen contained in the wire was reduced to a predetermined value or less, the SSC resistance of the wire could be improved, and the embodiment of the present invention was completed.
  • the hot-rolled wire according to the embodiment of the present invention has C: 0.10 to 0.7%, Si: more than 0%, 2.0% or less, Mn: 0.3 to 2.0%, Cr: 0 0.05 to 2.0%, V: 0.05 to 0.5%, P: more than 0%, 0.02% or less, S: more than 0%, 0.008% or less, and Al: more than 0%, It contains 0.05% or less.
  • C is an element necessary for ensuring the strength of the hot-rolled wire, and is contained by 0.10% or more.
  • the amount of C is preferably 0.2% or more, more preferably 0.25% or more.
  • the C amount is 0.7% or less, preferably 0.65% or less, more preferably 0.6% or less.
  • the Si amount is preferably 0.05% or more.
  • the amount of Si is more preferably 0.06% or more, still more preferably 0.07% or more.
  • the Si amount is 2.0% or less.
  • the amount of Si is preferably 1.95% or less, more preferably 1.90% or less, and still more preferably 1.85% or less.
  • Mn is an element that improves the hardenability, increases the strength of the hot rolled wire rod, and improves the corrosion resistance.
  • the amount of Mn decreases, the corrosion resistance is inferior, so the SSC resistance cannot be improved. Therefore, in the embodiment of the present invention, the amount of Mn is set to 0.3% or more.
  • the amount of Mn is preferably 0.40% or more, more preferably 0.5% or more.
  • the amount of Mn is set to 2.0% or less.
  • the amount of Mn is preferably 1.80% or less, more preferably 1.6% or less.
  • the Cr amount needs to be 0.05% or more.
  • the amount of Cr is preferably 0.1% or more, more preferably 0.3% or more.
  • the Cr amount is 2.0% or less.
  • the amount of Cr is preferably 1.95% or less, more preferably 1.9% or less, and still more preferably 1.6% or less.
  • V is an element that combines with C in steel to form fine VCs that serve as hydrogen trap sites and improves SSC resistance. If the amount of V is too small, the amount of VC deposited decreases, so that the hydrogen trap capability is insufficient and the SSC resistance cannot be improved. Therefore, in the embodiment of the present invention, the V amount needs to be 0.05% or more.
  • the V amount is preferably 0.08% or more, more preferably 0.10% or more.
  • the V amount is 0.5% or less.
  • V amount is preferably 0.48% or less, more preferably 0.45% or less.
  • the P amount is an element that segregates at the grain boundaries, lowers the grain boundary strength, and easily causes grain boundary breakage due to hydrogen. If the amount of P is excessive, the SSC resistance deteriorates. Therefore, in the embodiment of the present invention, the P amount is 0.02% or less.
  • the amount of P is preferably 0.019% or less, more preferably 0.018% or less.
  • the amount of P is preferably reduced as much as possible. However, since it is expensive to make the amount of P less than 0.0001%, it is preferably 0.0001% or more.
  • S is an element that segregates at the grain boundaries, lowers the grain boundary strength, and easily causes grain boundary breakage due to hydrogen.
  • S is an element that lowers the SSC resistance because it generates MnS and serves as a starting point for fracture.
  • the S amount is set to 0.008% or less.
  • the amount of S is preferably 0.007% or less, more preferably 0.006% or less.
  • the amount of S is preferably reduced as much as possible. However, since it is expensive to make the amount of S less than 0.0001%, it is preferably 0.0001% or more.
  • Al like Si, is an element that acts as a deoxidizer and contributes to reducing the amount of dissolved oxygen in the hot-rolled wire rod.
  • the Al content is preferably 0.001% or more.
  • the amount of Al is more preferably 0.002% or more, and further preferably 0.003% or more.
  • the Al amount is 0.05% or less.
  • the amount of Al is preferably 0.04% or less, more preferably 0.03% or less.
  • the component composition of the hot rolled wire according to the embodiment of the present invention is as described above, and the balance is iron and inevitable impurities.
  • the hot-rolled wire further includes, as other elements, (a) Cu: more than 0%, 0.5% or less, (b) B: more than 0%, 0.01% or less, (c) Ti: 0% At least one selected from more than 0.01% and Nb: more than 0% and 0.2% or less, (d) Mo: more than 0%, 1% or less, Etc. may be contained.
  • (A) Cu is an element that forms a film on the surface of the hot-rolled wire, prevents entry of hydrogen, and improves SSC resistance.
  • the amount of Cu is preferably 0.05% or more.
  • the amount of Cu is more preferably 0.10% or more, and still more preferably 0.12% or more. However, even if Cu is contained excessively, the effect of addition is saturated, so the Cu content is preferably 0.5% or less.
  • the amount of Cu is more preferably 0.47% or less, and still more preferably 0.45% or less.
  • (B) B is an element that contributes to improving hardenability and increasing strength.
  • the B content is preferably 0.001% or more.
  • the amount of B is more preferably 0.0015% or more, and further preferably 0.002% or more.
  • the amount of B is preferably 0.01% or less.
  • the amount of B is more preferably 0.0080% or less, still more preferably 0.0070% or less.
  • Ti and Nb are elements that refine crystal grains, suppress crack growth, and improve SSC resistance.
  • the Ti content is preferably 0.010% or more, more preferably 0.015% or more, and still more preferably 0.020% or more.
  • the Ti content is preferably 0.01% or less.
  • the amount of Ti is more preferably 0.095% or less, still more preferably 0.090% or less.
  • Nb like Ti, contributes to improving the SSC resistance because it refines the crystal grains and suppresses crack growth.
  • the Nb content is preferably 0.05% or more, more preferably 0.08% or more, and still more preferably 0.10% or more.
  • the Nb amount is preferably 0.2% or less, more preferably 0.19% or less, and still more preferably 0.18% or less.
  • Mo is an element that acts to improve the hardenability and increase the strength of the hot-rolled wire rod.
  • the Mo amount is preferably 0.03% or more, more preferably 0.05% or more, and further preferably 0.1% or more.
  • the Mo amount is preferably 1% or less.
  • K value 1.2 ⁇ 4.0 ⁇ [C] ⁇ 0.9 ⁇ [Si] + 3.5 ⁇ [Mn] + 0.9 ⁇ [Cr] + 15.3 ⁇ [V] ⁇ 27.3 ⁇ [Al ] (1)
  • the K value is a value set in consideration of the relationship between the amount of alloying elements contained in the hot-rolled wire and the SSC resistance, and the coefficient of each alloying element means the degree of contribution to improving the SSC resistance. is doing. That is, in order to improve the SSC resistance, it is important to improve the corrosion resistance and hydrogen embrittlement resistance in a sour environment containing hydrogen sulfide. And when the present inventors examined, among the alloy elements contained in a hot-rolled wire, Mn, Cr, and V all contribute to improving SSC resistance, and C, Si, and Al Were found to act to degrade the SSC resistance.
  • Mn and Cr have an action of improving the corrosion resistance of the hot-rolled wire, and V captures hydrogen by the hydrogen trap effect to make it harmless, and both contribute to the improvement of SSC resistance.
  • C reduces corrosion resistance
  • Si promotes the grain boundary segregation of impurity elements and promotes the progress of cracks
  • Al is an element that generates inclusions such as AlN that cause fracture. It acts to degrade the SSC resistance.
  • the K value is set to 1.7 or more.
  • the K value is preferably 2.5 or more, more preferably 3.3 or more, and still more preferably 4.1 or more.
  • the K value is set to 10 or less.
  • the K value is preferably 9.7 or less, and more preferably 9.5 or less.
  • the hot-rolled wire according to the embodiment of the present invention has a hydrogen content of more than 0 ppm and 1.0 ppm or less. That is, one of the causes of sulfide stress corrosion cracking (SSC) is hydrogen, and when a large amount of hydrogen enters the hot rolled wire rod, it becomes brittle and breaks. By the way, the hot-rolled wire is subjected to quenching and tempering heat treatment to make the metal structure martensite as necessary. Therefore, hydrogen escapes from the hot-rolled wire to some extent during this heat treatment.
  • SSC sulfide stress corrosion cracking
  • the hot-rolled wire contains a lot of hydrogen, it is obtained by drawing the hot-rolled wire after heat treatment and the hot-rolled wire after heat treatment. Since a lot of hydrogen remains in the steel wire to be produced, it breaks early in a sour environment containing hydrogen sulfide. Therefore, the smaller the amount of hydrogen contained in the hot-rolled wire, the smaller the amount of hydrogen remaining in the hot-rolled wire after heat treatment and the steel wire obtained by drawing the hot-rolled wire after heat treatment. SSC property can be improved. From such a viewpoint, in the embodiment of the present invention, the amount of hydrogen contained in the hot-rolled wire is set to 1.0 ppm or less. The amount of hydrogen is preferably 0.9 ppm or less, more preferably 0.8 ppm or less. The smaller the amount of hydrogen, the better. However, since it takes a cost to approach 0 ppm, 0.01 ppm or more is preferable.
  • the hot-rolled wire according to the embodiment of the present invention can be produced by melting steel that satisfies the above component composition by a conventional method, heating a steel slab obtained by split rolling, and hot rolling. .
  • the above hot rolling is performed so that the mounting temperature after hot rolling is 850 to 1000 ° C. If the mounting temperature is lower than 850 ° C., the amount of hydrogen contained in the hot-rolled wire tends to increase, and the SSC resistance cannot be improved. Therefore, the above-mentioned installation temperature is 850 ° C. or more.
  • the setting temperature is preferably 870 ° C. or higher, more preferably 880 ° C. or higher.
  • the higher the mounting temperature the easier it is for hydrogen to escape from the hot-rolled wire, but if the mounting temperature is too high, decarburization tends to occur. Therefore, the above-mentioned set temperature is 1000 ° C. or less.
  • the above-mentioned set temperature is preferably 990 ° C. or lower, more preferably 980 ° C. or lower.
  • the wire diameter ⁇ of the hot rolled wire is, for example, about 10 to 16 mm.
  • the hot-rolled wire obtained by hot rolling is preferably subjected to heat treatment such as quenching and tempering to make the metal structure martensite as necessary.
  • Quenching may be performed, for example, by heating to 850 to 1000 ° C., holding for 5 to 15 minutes, and then cooling to room temperature.
  • the average speed during cooling is preferably 30 to 100 ° C./second, for example.
  • Tempering may be performed by heating and holding at 400 to 650 ° C. for 15 to 45 minutes, for example.
  • the hot-rolled wire obtained by heat treatment is a material for producing steel wires that require SSC resistance, such as parts used in sour environments containing hydrogen sulfide or reinforcing materials such as flexible risers. Can be used.
  • the hot-rolled wire which concerns on this invention will be obtained by trial and error by the manufacturing method different from the manufacturing method mentioned above. could be possible.
  • the composition shown in Table 1 below was satisfied, and the balance was made of steel consisting of iron and inevitable impurities, and the resulting molten steel was cast to produce a steel slab.
  • the K value is calculated based on the component composition shown in the following Table 1 and the above formula (1), and the calculation result is shown in the following Table 1.
  • the line (-) indicates that the component composition was not detected.
  • the component amount (for example, Cr amount of steel type S) of the alloy element described as “0.00” in Table 1 indicates that the alloy element is contained in less than 0.01%.
  • Table 1 and Table 2 described later the underlined numerical values indicate that they are out of the scope of the embodiment of the present invention. However, it should be noted that “-” is not underlined even if it falls outside the scope of the embodiment of the present invention.
  • the obtained steel slab was subjected to ingot rolling, and the obtained billet was hot-rolled so that the mounting temperature after hot rolling became the temperature shown in Table 2 below to produce a hot-rolled wire.
  • the obtained hot-rolled wire has a diameter of 12 mm.
  • the amount of hydrogen contained in the obtained hot rolled wire was measured according to the following procedure.
  • the obtained hot rolled wire was subjected to heat treatment such as quenching and tempering to obtain a test material.
  • Quenching was performed by heating to 850 to 1000 ° C. and holding for 5 to 15 minutes, and then cooling to room temperature at an average cooling rate of 30 ° C./second or more.
  • Tempering was performed by heating to 400 to 650 ° C. and holding for 15 to 45 minutes.
  • the strength and SSC resistance of the test material obtained by heat treatment were evaluated by the following procedure.
  • a yield strength of 900 MPa or more was determined as high strength, and the result was accepted.
  • SSC resistance A test piece for the Method A method defined by NACE Standard TM0177-2005 was taken from the above test material, and the SSC resistance of the test material was evaluated by the Method A method. That is, the collected test piece was immersed in Solution A containing 5.0% by mass of NaCl and 0.5% by mass of CH 3 COOH, saturated with H 2 S gas in the Solution A, and the yield strength measured above. 80% stress (YS) was applied, the time until fracture was measured, and the SSC resistance was evaluated based on the measured time. The measurement results are shown in Table 2 below.
  • a break time of 720 hours or more was determined to be excellent in SSC resistance, and was determined as acceptable.
  • Examples 2 to 17 are examples that satisfy the requirements stipulated in the embodiment of the present invention. Since the component composition and the amount of hydrogen are appropriately controlled, the yield strength is a high strength of 900 MPa or more and includes hydrogen sulfide. Under a condition where 80% stress of yield strength is applied in a corrosive environment, the time to fracture is 720 hours or more, and the SSC resistance is excellent.
  • No. 1 and 18 to 30 are examples that do not satisfy the requirements defined in the embodiment of the present invention, and either the strength or the SSC resistance is inferior. Details will be described below.
  • No. No. 1 was an example in which the amount of hydrogen contained in the hot-rolled wire increased because the mounting temperature after hot rolling was low, and the SSC resistance could not be improved.
  • No. No. 19 had a lot of C and increased cracking susceptibility, so SSC resistance could not be improved.
  • No. No. 20 is an example in which there was too much Si, and since segregation deteriorated, the SSC resistance could not be improved.
  • No. No. 21 was an example in which Mn was small and the K value was too small, and because the corrosion resistance was inferior, the SSC resistance could not be improved.
  • No. No. 22 is an example in which there was a lot of Mn and the K value was too large, and SSC resistance could not be improved because the toughness decreased.
  • No. No. 25 was not able to improve SSC resistance because there was little Cr and corrosion resistance fell.
  • No. No. 26 is an example in which there was too much Cr, and the tough ductility was lowered, and cracks progressed starting from excessively generated Cr-based carbonitrides, so SSC resistance could not be improved.
  • No. No. 28 is an example in which there was a large amount of Al and the K value was too small. Since a large amount of AlN or the like that caused corrosion was generated, the corrosion resistance deteriorated and the SSC resistance could not be improved.
  • No. No. 29 was an example in which the K value was too small, the corrosion resistance was deteriorated, and the hydrogen trap effect could not be obtained, so the SSC resistance could not be improved.
  • No. No. 30 is an example in which the K value was large and the amount of hydrogen contained in the hot-rolled wire increased, and because the toughness decreased, the SSC resistance could not be improved.
  • No. Nos. 1 to 6 and 11 are examples in which the steel type E is used, and the mounting temperature after hot rolling is changed. As is clear from these results, it can be seen that the higher the mounting temperature after hot rolling, the smaller the amount of hydrogen contained in the hot rolled wire.
  • the disclosure of the present specification includes the following aspects.
  • (Aspect 1) % By mass C: 0.10 to 0.7%, Si: more than 0%, 2.0% or less, Mn: 0.3 to 2.0%, Cr: 0.05 to 2.0%, V: 0.05 to 0.5% P: more than 0%, 0.02% or less, S: more than 0%, 0.008% or less, and Al: more than 0%, 0.05% or less,
  • the balance consists of iron and inevitable impurities
  • the K value represented by the following formula (1) is 1.7 to 10
  • a high-strength hot-rolled wire rod having excellent resistance to sulfide stress corrosion cracking, wherein the hydrogen content is more than 0 ppm and 1.0 ppm or less.
  • the present application includes a Japanese patent application filed on March 31, 2016, Japanese Patent Application No. 2016-070164, and a Japanese patent application filed on February 27, 2017, Japanese Patent Application No. 2017. Accompanied by priority claim based on -034928.
  • Japanese Patent Application No. 2016-070164 and Japanese Patent Application No. 2017-034928 are incorporated herein by reference.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

Cette invention concerne un fil machine à haute résistance laminé à chaud, satisfaisant une composition de constituants prédéterminée, dont valeur K représentée par la formule (1) va de 1,7 à 10, et dont la teneur en hydrogène est supérieure à 0 ppm et inférieure ou égale à 1,0 ppm. Dans la formule (1), les crochets se réfèrent à la teneur en % en masse de l'élément entre crochets. (1): valeur K = 1,2 – 4,0 × [C] - 0,9 × [Si] + 3,5 × [Mn] + 0,9 × [Cr] + 15,3 × [V] - 27,3 × [Al]
PCT/JP2017/013784 2016-03-31 2017-03-31 Fil machine à haute résistance laminé à chaud présentant une excellente résistance à la corrosion fissurante provoquée par l'hydrogène sulfuré WO2017171070A1 (fr)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP2016-070164 2016-03-31
JP2016070164 2016-03-31
JP2017034928A JP2017186654A (ja) 2016-03-31 2017-02-27 耐硫化物応力腐食割れ性に優れた高強度熱間圧延線材
JP2017-034928 2017-02-27

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107747059A (zh) * 2017-11-30 2018-03-02 攀钢集团攀枝花钢铁研究院有限公司 含V、Ti、Cr微合金建筑钢盘条及其生产方法
CN114672737A (zh) * 2021-12-22 2022-06-28 邢台钢铁有限责任公司 一种线材及其生产方法

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2000517381A (ja) * 1996-09-09 2000-12-26 アンスティテュ フランセ デュ ペトロール 自硬鋼線材の製造方法、補強用線材及び可撓性導管への利用方法
WO2015159650A1 (fr) * 2014-04-18 2015-10-22 株式会社神戸製鋼所 Fil laminé à chaud

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2000517381A (ja) * 1996-09-09 2000-12-26 アンスティテュ フランセ デュ ペトロール 自硬鋼線材の製造方法、補強用線材及び可撓性導管への利用方法
WO2015159650A1 (fr) * 2014-04-18 2015-10-22 株式会社神戸製鋼所 Fil laminé à chaud

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN107747059A (zh) * 2017-11-30 2018-03-02 攀钢集团攀枝花钢铁研究院有限公司 含V、Ti、Cr微合金建筑钢盘条及其生产方法
CN114672737A (zh) * 2021-12-22 2022-06-28 邢台钢铁有限责任公司 一种线材及其生产方法

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