WO2006106650A1 - マルテンサイト系ステンレス鋼の製造方法 - Google Patents
マルテンサイト系ステンレス鋼の製造方法 Download PDFInfo
- Publication number
- WO2006106650A1 WO2006106650A1 PCT/JP2006/306240 JP2006306240W WO2006106650A1 WO 2006106650 A1 WO2006106650 A1 WO 2006106650A1 JP 2006306240 W JP2006306240 W JP 2006306240W WO 2006106650 A1 WO2006106650 A1 WO 2006106650A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- softening
- stainless steel
- steel
- martensitic stainless
- heat treatment
- Prior art date
Links
Classifications
-
- 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
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
- C21D1/32—Soft annealing, e.g. spheroidising
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
- C21D9/085—Cooling or quenching
-
- 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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
-
- 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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Definitions
- the present invention relates to a method for preventing delayed fracture in martensitic stainless steel that undergoes martensitic transformation even when allowed to cool in the atmosphere, and the production of martensitic stainless steel having such delayed fracture preventing characteristics. Regarding the method.
- a common delay prevention measure is to limit the time from the end of pipe making to the start of heat treatment for quenching. To do so, heat treatment for imparting the necessary strength to the steel material by quenching must be performed immediately after pipe production. However, limiting the time until heat treatment for pipe making power also requires operation while frequently changing the heat treatment temperature, which reduces production efficiency.
- Japanese Patent Application Laid-Open No. 2004-43935 discloses a martensitic stainless steel seamless steel, which is based on limiting effective solid solution C and the amount of soot described below to 0.45 or less, and is suppressed in delay; Tubes are listed.
- the effective solute C and the amount of soot are determined by the steel composition. If an appropriate steel composition is selected in consideration of other properties such as strength and toughness, the amount of effective solute C and N may exceed 0.45. It cannot be said that it is perfect.
- An object of the present invention is to provide a method for preventing delayed fracture in a martensitic stainless steel that undergoes martensitic transformation during standing cooling in the air without limiting the time until the quenching heat treatment and the time until quenching heat treatment. Is to provide.
- Another object of the present invention is to provide a method for preventing delayed fracture effective in martensitic stainless steel having an effective solid solution C and a soot content exceeding 0.45.
- Still another object is to provide a method for producing martensitic stainless steel having excellent resistance to slowing down and cracking.
- the present invention is a method for preventing delayed fracture of a martensitic stainless steel that undergoes martensitic transformation during standing cooling in the atmosphere, and after hot heating the steel, Prior to heat treatment in which quenching is performed from a temperature of at least one Ac point of the steel, the softness parameter P defined below is 15,400 or more and the softening temperature T is less than the Ac point of the steel.
- the method is characterized in that pre-softening heat treatment is performed.
- the present invention the mass 0/0, C: 0.15 ⁇ 0.22% , Si: 0.05 ⁇ 1.0%, Mn: 0. 10 ⁇ 1.0%, Cr: 10.5 ⁇ 14.0%, P: 0.020% S: 0.010% or less, Al: 0.10% or less, Mo: 0 to 2.0%, V: 0.50% or less, Nb: 0 to 0.020%, Ca: 0 to 0.0050%, N: 0.1000% or less Martensitic stainless steel with the balance essentially Fe and impurity power
- delayed softening resistance is characterized in that pre-softening heat treatment is performed under the condition that the softening parameter P is 15,400 or more and the softening temperature T is lower than the Ac point of the steel.
- the present invention when a martensitic stainless steel pipe used as an oil well pipe or the like is manufactured, the occurrence of delayed fracture is effectively prevented by performing a pre-softening heat treatment immediately after the pipe manufacturing. Therefore, after that, heat treatment such as quenching can be performed at an arbitrary time to obtain a final product. This eliminates the need for quenching within a certain time after pipe making, and can prevent delayed fracture of the martensitic stainless steel pipe without impeding the operation.
- FIG. 1 is a graph collectively showing the results of Examples.
- the steel types targeted by the present invention include martensitic stainless steels that are misaligned as long as they undergo martensite transformation by standing cooling in the atmosphere.
- C carbon
- the lower limit of the C content is preferably 0.16%, more preferably 0.18%.
- Si is added as a steel deoxidizer. In order to obtain the effect, 0.05% or more of Si is added. To prevent toughness deterioration, the upper limit of Si content is 1.0%.
- the lower limit of the Si amount is preferably 0.16%, more preferably 0.20%.
- the upper limit is preferably 0.35%.
- Mn manganese
- the amount of Mn is preferably 0.30% or more, and is preferably 0.60% or less in order to ensure toughness after quenching.
- Cr chromium
- Cr is a basic component for obtaining the necessary corrosion resistance in martensitic stainless steel. Improves corrosion resistance against pitting corrosion and temporal corrosion, and CO
- Cr is a ferrite-forming element
- ⁇ -ferrite tends to be formed during high-temperature processing, and hot workability is impaired.
- the strength decreases.
- a preferable Cr content is 12.0% or more and 13.1% or less.
- the upper limit is set to 0.020%.
- the upper limit is set to 0.010%.
- A1 0.10% or less
- A1 (aluminum) is a force present in steel as an impurity. If its content exceeds 0.10%, the toughness deteriorates. Preferably it is 0.05% or less.
- Mo molybdenum
- Mo molybdenum
- V 0.50% or less
- V vanadium
- Yield ratio yield strength Z tensile strength
- Nb 0 to 0.020%
- Nb niobium
- Nb is an optional additive element. If Nb is added, there is an effect of increasing the strength. However, if the Nb content exceeds 0.020%, the toughness decreases, so the upper limit is made 0.020%. Since Nb is an expensive alloy element, it becomes economically inefficient when added in a large amount. Therefore, it is desirable that Nb be as little as possible.
- Ca is an optional additive element. Ca combines with S in the steel and has the effect of preventing deterioration of hot workability due to S grain boundary bias. However, if Ca exceeds 0.0050%, inclusions in the steel increase and the toughness decreases, so even when it is added, it should be 0.0050% or less.
- N nitrogen
- N is an austenite stabilizing element, and is an important element along with C in martensitic stainless steel, especially in improving hot workability. If the amount of N exceeds .1000%, the toughness will decrease and the amount of solute N will increase significantly and delayed fracture will occur more easily, so the upper limit of N will be 0.100%. . This upper limit is preferably 0.0500%. On the other hand, if the amount of N is too small, the efficiency of the de-N process in steelmaking deteriorates and the productivity is hindered, so the preferable lower limit of the amount of N is 0.0100%.
- the balance of the steel yarn other than the above elements is Fe and impurities (eg, Ti ⁇ titanium>, B ⁇ boron
- the susceptibility to delayed fracture in martensitic stainless steel is affected by the amount of solid solution of C and N in the steel. If the sum of 10 times the amount of solute N (C * + 10N *) exceeds 0.45, it will be slow; In other words, in the steel grade of (C * + 10N *) ⁇ 0.45, the occurrence of slow;
- N * (effective amount of N) N— [14 ⁇ (V / 51) + (Nb / 93) ⁇ / 10]-[ ⁇ (Ti / 48) + (B / 11) + (A1 / 27) ⁇ /
- each element symbol means the content in mass% of the element.
- a preliminary soft heat treatment is performed on the martensitic stainless steel having the above composition in order to prevent subsequent delayed fracture after hot working such as pipe making. I do.
- the cause of delayed fracture in martensitic stainless steel is nitrogen and hydrogen trapped in the strain introduced during the hot working stage, so it is possible to prevent delayed fracture by releasing these occluded gases.
- the pre-softening heat treatment is performed under the condition that the softness parameter P calculated by the following equation is 15,400 or more and the softening temperature T is less than the Ac point of the steel.
- the hardness of the material is reduced by softening heat treatment. If the softening parameter after the softening heat treatment is less than 15,400, the softness is insufficient, and there is a risk of delaying after the softening heat treatment. Even when heat treatment is performed so that the softening parameter is 15,400 or higher, the structure becomes weak again when the softening temperature, which is the temperature of the softening heat treatment, exceeds the Ac point of the steel.
- This pre-softening heat treatment is performed at the time of quenching from a temperature higher than the Ac point after hot working. Performed before final heat treatment. If delayed fracture has not occurred, pre-softening heat treatment can be performed at any point during this period, but it has passed 168 hours since the end of the final hot working (eg, rolling) (excluding neglected cooling time). Therefore, it is preferable to carry out preliminary soft heat treatment within 168 hours from the final hot working.
- the pre-softening heat treatment can be performed immediately after the end of the final hot working. For example, immediately after the end of the hot working, the steel is cooled to the M point or less immediately after the standing cooling is completed or during the standing cooling.
- pre-softening heat treatment After the martensitic transformation is completed after the lowering, pre-softening heat treatment can be performed.
- the pre-softening heat treatment is performed by heating to a softening temperature T of less than 1 Ac of the steel and holding at that temperature for a certain time. Since the holding time is the soft time t, it may be selected according to the soft temperature T so that the soft parameter P calculated by the above formula is 15,400 or more.
- the cooling after the softening heat treatment is preferably left cooling in the atmosphere.
- Hot working and final heat treatment (quenching) of martensitic stainless steel may be performed under normal conditions.
- hot working can be carried out by pipe making under the general production conditions of seamless steel pipe.
- the final heat treatment is generally performed by quenching at a temperature of 920 to 980 ° C, followed by tempering at 650 to 750 ° C.
- a martensitic stainless steel billet having the yarn composition shown in Table 1 (the balance being Fe and impurities) was hot-worked with Mannesmann tube to produce a seam with an outer diameter of 60.33 mm and a wall thickness of 4.83 mm. A steel-free tube was produced.
- a drop weight test piece having a length of 250 mm was collected from the obtained steel pipe, and the curvature of the tip of the test piece was measured.
- a 90 mm weight with a weight of 150 kg was dropped from a height of 0.2 m and an impact load (294 J) was applied.
- preliminary soft heat treatment was performed under two conditions (1) and (2) regarding the temperature of the heat treatment furnace (softening temperature) and the in-furnace time (softening treatment time). Table 2 also shows the softening parameter values under these conditions. The reason why the impact load is applied before the pre-softening heat treatment is to simulate the impact at the time of handling during steel pipe conveyance in the actual manufacturing process.
- the effective solute C and N content (Q) of each material is also calculated by the following formula force.
- N * N- [14 ⁇ (V / 51) + (Nb / 93) ⁇ / 10] [ ⁇ (Ti / 48) + (B / ll) + (Al / 27) ⁇ / 10] From Fig. 1, When Q ⁇ 0.45, delayed fracture does not occur even if the softening parameter by softening heat treatment is lower than 15,400, but when Q> 0.45, it can be understood that delayed fracture can be prevented when the softness parameter is 15,400. In other words, in Japanese Patent Application Laid-Open No. 2004-43935, it is slow;
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
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- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Description
Claims
Priority Applications (6)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP06730188A EP1867737B1 (en) | 2005-03-30 | 2006-03-28 | Method for producing martensitic stainless steel |
JP2007512531A JP4992711B2 (ja) | 2005-03-30 | 2006-03-28 | マルテンサイト系ステンレス鋼の製造方法 |
BRPI0608954-2A BRPI0608954B1 (pt) | 2005-03-30 | 2006-03-28 | Method for manufacturing a martensitic stainless steel tube |
CN2006800096614A CN101146917B (zh) | 2005-03-30 | 2006-03-28 | 马氏体类不锈钢的制造方法 |
US11/905,191 US7905967B2 (en) | 2005-03-30 | 2007-09-28 | Method of manufacturing martensitic stainless steel |
US12/952,471 US20110067785A1 (en) | 2005-03-30 | 2010-11-23 | Method of manufacturing martensitic stainless steel |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2005098221 | 2005-03-30 | ||
JP2005-098221 | 2005-03-30 |
Related Child Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US11/905,191 Continuation US7905967B2 (en) | 2005-03-30 | 2007-09-28 | Method of manufacturing martensitic stainless steel |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2006106650A1 true WO2006106650A1 (ja) | 2006-10-12 |
Family
ID=37073216
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/JP2006/306240 WO2006106650A1 (ja) | 2005-03-30 | 2006-03-28 | マルテンサイト系ステンレス鋼の製造方法 |
Country Status (8)
Country | Link |
---|---|
US (2) | US7905967B2 (ja) |
EP (1) | EP1867737B1 (ja) |
JP (1) | JP4992711B2 (ja) |
CN (1) | CN101146917B (ja) |
AR (1) | AR052732A1 (ja) |
BR (1) | BRPI0608954B1 (ja) |
RU (1) | RU2358020C1 (ja) |
WO (1) | WO2006106650A1 (ja) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN102251084A (zh) * | 2011-07-04 | 2011-11-23 | 南京迪威尔重型锻造股份有限公司 | 深海采油设备液压缸用钢锻件性能热处理工艺 |
Families Citing this family (7)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP5900922B2 (ja) * | 2012-03-14 | 2016-04-06 | 国立大学法人大阪大学 | 鉄鋼材の製造方法 |
CN102663498B (zh) * | 2012-04-28 | 2014-06-18 | 武汉大学 | 一种9%Cr马氏体耐热钢焊缝金属Ac1点的预测方法 |
CN104711482A (zh) * | 2015-03-26 | 2015-06-17 | 宝钢不锈钢有限公司 | 一种控氮马氏体不锈钢及其制造方法 |
RU2635205C2 (ru) * | 2016-01-11 | 2017-11-09 | Открытое акционерное общество "Российский научно-исследовательский институт трубной промышленности" (ОАО "РосНИТИ") | Способ термической обработки труб нефтяного сортамента из коррозионно-стойкой стали |
CN110643895B (zh) * | 2018-06-27 | 2021-05-14 | 宝山钢铁股份有限公司 | 一种马氏体不锈钢油套管及其制造方法 |
CN110643894B (zh) * | 2018-06-27 | 2021-05-14 | 宝山钢铁股份有限公司 | 具有良好的疲劳及扩孔性能的超高强热轧钢板和钢带及其制造方法 |
CN114137070B (zh) * | 2021-10-25 | 2023-10-10 | 湖南工学院 | 一种识别超声振动切削扬矿管螺纹中超声软化系数的方法 |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5825419A (ja) * | 1981-08-07 | 1983-02-15 | Sumitomo Metal Ind Ltd | マルテンサイト系ステンレス鋼の低温割れ防止法 |
JPH05171361A (ja) * | 1991-12-19 | 1993-07-09 | Sumitomo Metal Ind Ltd | マルテンサイト系ステンレス鋼と製造方法 |
Family Cites Families (5)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2707839B2 (ja) * | 1990-12-25 | 1998-02-04 | 住友金属工業株式会社 | マルテンサイト系継目無鋼管とその製造方法 |
AU739624B2 (en) * | 1999-05-18 | 2001-10-18 | Nippon Steel Corporation | Martensitic stainless steel for seamless steel pipe |
JP2003064416A (ja) * | 2001-08-21 | 2003-03-05 | Aichi Steel Works Ltd | 冷鍛性、温鍛性に優れた析出硬化型マルテンサイト系ステンレス鋼の製造方法 |
JP4126979B2 (ja) * | 2002-07-15 | 2008-07-30 | 住友金属工業株式会社 | マルテンサイト系ステンレス継目無鋼管とその製造方法 |
JP3895291B2 (ja) * | 2003-03-24 | 2007-03-22 | エヌケーケーシームレス鋼管株式会社 | 高強度9Cr鋼管の軟化熱処理方法 |
-
2006
- 2006-03-28 CN CN2006800096614A patent/CN101146917B/zh not_active Expired - Fee Related
- 2006-03-28 JP JP2007512531A patent/JP4992711B2/ja active Active
- 2006-03-28 RU RU2007139907/02A patent/RU2358020C1/ru not_active IP Right Cessation
- 2006-03-28 EP EP06730188A patent/EP1867737B1/en active Active
- 2006-03-28 WO PCT/JP2006/306240 patent/WO2006106650A1/ja active Application Filing
- 2006-03-28 BR BRPI0608954-2A patent/BRPI0608954B1/pt active IP Right Grant
- 2006-03-30 AR ARP060101250A patent/AR052732A1/es active IP Right Grant
-
2007
- 2007-09-28 US US11/905,191 patent/US7905967B2/en active Active
-
2010
- 2010-11-23 US US12/952,471 patent/US20110067785A1/en not_active Abandoned
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS5825419A (ja) * | 1981-08-07 | 1983-02-15 | Sumitomo Metal Ind Ltd | マルテンサイト系ステンレス鋼の低温割れ防止法 |
JPH05171361A (ja) * | 1991-12-19 | 1993-07-09 | Sumitomo Metal Ind Ltd | マルテンサイト系ステンレス鋼と製造方法 |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN102251084A (zh) * | 2011-07-04 | 2011-11-23 | 南京迪威尔重型锻造股份有限公司 | 深海采油设备液压缸用钢锻件性能热处理工艺 |
CN102251084B (zh) * | 2011-07-04 | 2013-04-17 | 南京迪威尔高端制造股份有限公司 | 深海采油设备液压缸用钢锻件性能热处理工艺 |
Also Published As
Publication number | Publication date |
---|---|
JPWO2006106650A1 (ja) | 2008-09-11 |
CN101146917A (zh) | 2008-03-19 |
EP1867737B1 (en) | 2012-03-21 |
RU2358020C1 (ru) | 2009-06-10 |
US20080078478A1 (en) | 2008-04-03 |
CN101146917B (zh) | 2010-11-17 |
BRPI0608954A2 (pt) | 2010-02-17 |
EP1867737A4 (en) | 2009-04-29 |
BRPI0608954B1 (pt) | 2017-06-20 |
AR052732A1 (es) | 2007-03-28 |
US20110067785A1 (en) | 2011-03-24 |
US7905967B2 (en) | 2011-03-15 |
EP1867737A1 (en) | 2007-12-19 |
JP4992711B2 (ja) | 2012-08-08 |
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