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CN101300365A - Methods for heat treating thick-walled forgings - Google Patents

Methods for heat treating thick-walled forgings Download PDF

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Publication number
CN101300365A
CN101300365A CNA200680040529XA CN200680040529A CN101300365A CN 101300365 A CN101300365 A CN 101300365A CN A200680040529X A CNA200680040529X A CN A200680040529XA CN 200680040529 A CN200680040529 A CN 200680040529A CN 101300365 A CN101300365 A CN 101300365A
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alloy steel
low alloy
forging
quenchant
temperature
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菲利蒲·A·胡夫
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Hydril Co LP
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    • 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
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • 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
    • 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
    • C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
    • 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
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • 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
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Articles (AREA)
  • Forging (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Strip Materials And Filament Materials (AREA)

Abstract

A method for heat treating thick-walled forgings including heating a low alloy steel to an austenitizing temperature, wherein the low alloy steel comprises carbon of about 0.05-0.2 wt. %, manganese of about 0.3-0.8 wt. %, and nickel of about 0.25-1.0 wt. %. The method further includes quenching the low alloy steel in a quench media, and then tempering the low alloy steel for less than about thirty minutes per inch of critical section thickness plus about two hours.

Description

The heat treating method of thick-walled forgings
Technical field
Present invention relates in general to thermal treatment thick-walled forgings field.More specifically, the present invention relates to utilize the low alloy steel of special component and control tempering and quenching technology to come the thermal treatment thick-walled forgings.
Background technology
Well control system is the importance of oil-gas exploration.When probing well in oil-gas exploration is for example used, security device must place in position to prevent since with the moving phase related unscheduled event of probing to personnel's injury and to the damage of equipment.
Drilling well in the oil-gas exploration relates to and penetrates multiple subsurface geologic structures or " layer ".Sometimes, well can penetrate the layer with the reservoir pressure that is much higher than the pressure that keeps in the well.When this took place, this well was called as " running into well kick (overflow) (kick) ".Due to the pressure increase that is associated with well kick flows in the well by resident fluid (it can be a liquid, gas or its combination) basically.The well kick of elevated pressures will be propagated to aboveground (from the high pressure area to the area of low pressure) by the inlet point from well.If allow well kick to arrive ground, drilling fluid, well logger and other wellbore structures may spray well so.These " ejectas " can cause the catastrophic destruction of drilling rigs (comprise, for example, rig) and rig personnel's heavy casualties.
Because the danger of blowout, usually in the deep water drilling rig on ground or the seabed preventer (BOP) be installed measured to control well kick until carrying out active to seal well effectively.BOP can be activated like this so that well kick can suitably be controlled also " recycling " system.
Fig. 1 represents annular BOP 101 of the prior art.Annular BOP 101 comprises shell 102, have and extend through shell and be arranged on hole 102 around the longitudinal center line 103.Packing unit 105 is arranged in the annular BOP 101, and also around longitudinal center line 103.Packing unit 105 comprises resilient ring body 107 and a plurality of metal insert 109.BOP 101 is by the fluid-actuated in the opening 113 that pumps into piston chamber 112 for annular.This fluid applies pressure to piston 117, and its driven plunger 117 that makes progress is with compression seal glue core 105 around longitudinal center line 103.Under the situation that drilling rod exists along longitudinal center line 103, packing unit 105 is with around the sealing drilling rod.When fluid was pumped in the opening 115 of piston chamber, annular BOP 101 carried out similar reversing motion.The fluid transfer downward force is to piston 117 then, makes the packing unit radial expansion.Removable head 119 also can enter packing unit 105, thereby if necessary can keep in repair or change packing unit 105.
Therefore because BOP must bear high pressure, importantly the wall of BOP is thicker and have a homogeneous mechanical performance: tensile strength and hardness.Forging is such as the forging that uses among the BOP, generally by being made with the low alloy steel that improves intensity and reach specific minimum mechanical performance by thermal treatment.The low-alloy Heat Treatment Of Steel is finished by steel is carried out normalizing, austenitizing, quenching and tempering usually.Normalizing relates to the heating steel to reaching the ferrite granularity of competent time with refining steel more than the critical temperature, reduces residual unequal stress and produces more homogeneous mechanical performance.Forging is allowed to cool off still air from normalizing temperature then.In order to obtain highest hardness, metal carries out liquid hardening behind austenitizing handles.Austenitizing comprises that the heating steel is to reaching time enough more than the critical temperature grain pattern is changed into austenite in order to quenching.In quenching process, the metal of austenitizing is dipped into quenchant and is the brinish quenching tank such as water, oil or polymkeric substance and under few situation, can stir this quenchant tempestuously and be mainly bainite or martensite microstructure so that realization is transformed into, thereby improve the hardness and the physical strength of metal to reach critical speed of cooling.At last, the low alloy steel that is used for this purposes always extremely comes tempering below the lower critical temperature, ductility and toughness that this has reduced the high strength and the hardness of quenching metal and has improved metal by the reheat forging.Tempering is also referred to as " steel tempering " or is called for short " tempering ".
When using heavy forging to produce pressurized vessel, importantly the increased intensity of steel is all even on the whole section thickness at forging as far as possible after thermal treatment.When having many inches thick, steel is difficult to obtain uniform hardness of steel.When quenching forging big, can the having necessary high speed of cooling with the contacted outside surface of quenchant and change to greatest extent and incidental mechanical characteristics obtaining of forging.Yet, towards the rate of cooling of the interior metal piece at forging center along with metal block is more and more far and gradually slack-off from surface and quenchant.Therefore, in having the steel of several inches section thicknesses, mechanical property and hardness at the most difficult increase metal of the inner innermost metal block of forging are used to produce the minimum critical cooling velocity that changes mutually because this metal block can not quench apace and can not satisfy in many cases.
When using heavy forging to make pressurized vessel, importantly even as far as possible on the whole thickness of increased intensity at forging of steel after thermal treatment.When the thickness of steel is that many inches are difficult to obtain uniform hardness of steel when thick.When the quenching heavy forging, forging may have necessary high speed of cooling to realize maximum hardness with the contacted outside surface of quenchant.But, in forging inside along with metal block more and more away from quenchant, its speed of cooling is slack-off gradually.Therefore, in having the steel of several inch thickness, in the hardness of the inner innermost metal block of forging, because mass can not quench as soon as possible with the most difficult raising metal.
Depth of hardenability be metal in relatively large section thickness equably in response to heat treated ability.Known in the industry that low alloy steel has good depth of hardenability.Low alloy steel AISI4130 has the yield strength from 75 to 80Ksi scope, and its depth of hardenability is generally limited to about two inches, means by heat treatment step, can estimate that given yield strength remains in two inches the scope.AISI 4140, and another kind of low alloy steel has similar from 75 to 80Ksi yield strength scope be limited to six inches depth of hardenability basically.
For big BOP and pressurized vessel, the cross section of steel may be thick above 20 inches.Therefore, need have the composition of steel of big depth of hardenability so that obtain the high strength grade.
Summary of the invention
In one aspect, the present invention relates to a kind of method that is used for the thermal treatment thick-walled forgings.This method comprises: heating low alloy steel is to austenitizing temperature, and wherein this low alloy steel comprises the carbon of about 0.05-0.2wt.%, the approximately manganese of 0.3-0.8wt.%, and the nickel of about 0.25-1.0wt.%.This method also is included in this low alloy steel that quenches in the quenchant, and this low alloy steel of tempering reaches less than per inch throat section thickness and added about two hours in about 30 minutes then.
In yet another aspect, the present invention relates to a kind of forging.This forging comprises the carbon of about 0.05-0.2wt.%, the approximately manganese of 0.3-0.8wt.% and the approximately nickel of 0.25-1.0wt.%.This forging also comprises about at least 8 inches tranverse sectional thickness, greater than the inside yield strength of about 85Ksi and about at the most 237 Bu Shi (Brinell) hardness value.
By following explanation and claim, other aspects of the present invention and advantage will be apparent.
Description of drawings
Fig. 1 represents the cut away view of the annular preventer of prior art.
Fig. 2 represents schema, and graphic extension is according to the method for a kind of thermal treatment forging of the embodiment of the invention.
Fig. 3 represents the graph of relation of the temperature of the cooling power of water and water.
Fig. 4 represents that steel is in water and the hardness result figure that quenches in salt solution.
Embodiment
An aspect the invention provides the method that is used for the thermal treatment thick-walled forgings.More specifically, disclosed method can be used for being created on the BOP that all needs the high rigidity grade on the whole width of wall.
As mentioned above, for thick-walled forgings bears hyperbaric environment, the low alloy steel with certain preferred component must be by thermal treatment to improve hardness and intensity.
A kind of according to an embodiment of the invention method is used the carbon that comprises about 0.05-0.2wt.%, the approximately manganese of 0.3-0.8wt.% and the approximately low alloy steel of the nickel of 0.25-1.0wt.%.By this chemical constitution, when according to one embodiment of the invention during by thermal treatment, this low alloy steel can have the depth of hardenability greater than eight inches.In another embodiment, the ratio of nickel can be defined as about 0.5-1.0wt.%.Except carbon, manganese and nickel, the chemical ingredients of the low alloy steel among embodiment can also comprise greater than 0 phosphorus up to about 0.04wt.%, greater than 0 up to about 0.04% sulphur, greater than 0 silicon up to about 0.5wt.%, the about chromium of 2.0-2.5wt.%, and the about molybdenum of 0.45-1.15wt.%.In one embodiment, molybdenum can be 0.90-1.10wt.%.
Except big hardening capacity thickness, low alloy steel should present very high fracture toughness.Fracture toughness is measured during high strain fracture (strain fracture) by the amount of the energy of absorbed.More tough material absorbs more energy than hard brittle material.Low alloy steel of the present invention can be provided at big high pressure vessel such as using required fracture toughness among the BOP.
The generalized case of the steel smelting technology in present technique field can obtain such low alloy steel, and preferred p and s content more much lower than the above maximum value that provides is provided for it.The p and s of use reduced amounts helps to obtain the high fracture toughness of steel.In addition, when steel alloy is melted in a time-out by original composition at first, can handle (calcium treated) oxide morphology control to be provided and to improve fracture toughness through calcium at the melting process middle-low alloy steel.In addition, low alloy steel can comprise that aluminium and/or vanadium are so that deoxidation and reduction and grain refining.
In one embodiment of the invention, the low-alloy Heat Treatment Of Steel is carried out according to the standing procedure that is used for heat-treated metal: normalizing, austenitizing, quenching and tempering.Thereby usually carry out optional normalizing treatment control this low alloy steel reach selection normalizing temperature approximately ± 25 °F (± 14 ℃) in.Normalizing temperature is chosen as the above 25-50 of austenitizing temperature °F (14-28 ℃) usually.Forging is reheated forming austenite at austenitizing temperature such as at least 1725 °F (940 ℃) then, and the temperature of selection is controlled in approximately ± 25 in °F (± 14 ℃).After the austenitizing, forging is quenched in the submergence quenching tank that is fiercely stirred then, and wherein the initial temperature of quenchant is no more than about 75 °F (24 ℃).When quenching beginning, keep the temperature of initial quench media can provide more effective quenching by the speed of cooling that increases low alloy steel less than about 75 °F.For the forging that has greater than the section thickness of about 8 inches (approximately 20cm), the temperature of quenchant should not allow to surpass about 95 °F (35 ℃) when quenching end.For thick forging to about 20 inches (51cm), the temperature of quenchant should not allow to surpass about 75 °F (24 ℃) when quenching end.In order to realize this point, the selection temperature of quenchant raises and will determine effectively and the appropriate necessary quenchant minimum of quenching.The selection temperature of quenchant raises more little, can require the amount of quenchant many more to receive the heat from the equivalent of forging.Alternatively, quenching tank will need by 75 (24 ℃) or colder quenchant is full of or quenchant will need by cooling system circulation to maintain the temperature at below 75 °F (24 ℃).
Control initial quench media temperature less than about 55 °F and will cause than penetration of hardness bigger when quenching in the quenchant of forging at warmer, higher temperature greater than about 32 °F.Fig. 3 comes from Metals Handbook, and the 9th edition, roll up 4, the 35 pages, the relation curve of the cooling power of expression quenchant and initial quench media temperature, wherein water is as quenchant.As shown in Figure 3, the cooling power of water increases along with initial temperature and reduces rapidly, is illustrated in the lower water of initial temperature can quench more quickly forging and can obtain bigger penetration of hardness of water.But, along with initial quench media temperature reduces, forging easier generations that become is broken and rupture, and is also referred to as " hardening crack ".Therefore, should make great efforts not make initial quench media temperature too low to avoid hardening crack and fracture.
For low alloy steel, with respect to water, salt solution is preferred quenchant, because can provide higher hardness result than water for low alloy steel salt solution.Salt solution is than water generates bubble still less, surface that therefore can moistening low alloy steel.This makes salt solution to make low alloy steel have higher hardness result with the speed cooling low alloy steel of almost twice in water.Fig. 4 comes from Metals Handbook, and the 9th edition, roll up 4, the 37 pages, the expression steel is in water and the result who quenches in salt solution.As shown in Figure 4, when quenching under the uniform temp of 180 (80 ℃), corresponding brinish hardness result is higher than the water hardness result.Although salt solution can quench quickly to increase the penetration of hardness of low alloy steel, salt solution has more corrodibility and aggressiveness than water.Therefore, need take measures to protect quenched materials and quenching apparatus not damaged by salt solution.
After the quenching, forging tempering under the tempering temperature of selecting reaches the extra soaking time (soak time) that the per inch section thickness added one or two hour at least in 30 minutes.The tempering temperature of selecting should remain on approximately ± 15 °F (± 8 ℃) in.
In the prior art, low alloy steel per inch section thickness tempering 45 minutes to hour adds under tempering temperature to keep one to two hours.But, the so long tempering hold-time may cause the overtempering of alloy, causes the unnecessary loss of the mechanical property of low alloy steel.As a result, low alloy steel may not satisfy the requirement of tensile strength and hardness.
Normalizing, austenitizing and tempered temperature are decided according to the composition of alloy and steel.Can be with reference to the material specification of special component so that determine suitable normalizing, austenitizing and tempering temperature, and suitable quenchant.
Fig. 2 represents schema, and graphic extension is according to the method for the thermal treatment forging of the embodiment of the invention.In the method the low alloy steel forging of Shi Yonging make by chemical ingredients of the present invention and tranverse sectional thickness usually greater than 8 inches.This method is with 210 beginnings of optional normalizing operation, wherein forging at approximately ± 25 °F (± 14 ℃) with the interior normalizing temperature that is heated to.After optional normalizing operation 210, then in austenitizing operation 220, approximately ± 25 (± 14 ℃) being reheated to the austenitic temperature scope of the austenitic temperature of selecting with interior forging.Then, in quenching process 230, utilize the submergence quenching tank that is fiercely stirred, forging is immersed in the quenchant.The quenchant that uses in quenching process 230 should have the initial temperature less than 75 (24 ℃).But, if the initial temperature of quenchant is controlled between about 55 °F (13 ℃) and 32 °F (0 ℃), can obtain bigger forging penetration of hardness so.Less than about 12 inches forging, quenching tank should be enough big so that quenchant is no more than 95 °F (35 ℃) when quenching end for thickness.Less than about 20 inches forging, quenching tank should be enough big so that quenchant is no more than 75 °F (24 ℃) when quenching end for thickness.In addition, in quenching process 230, for the quenching heavy forging, salt solution is than the preferred quenchant of water.The tempering process 240 of forging is followed after quenching process 230.Forging be heated to selection tempering temperature approximately ± 15 °F (± 8 ℃) in.Especially, forging was added the soaking time of one or two extra hour in 30 minutes by tempering per inch thickness.For example, ten inches thick forging being made up of chemical ingredients of the present invention should tempering about six to seven hours.The forging that produces by method 200 will have the depth of hardenability greater than eight inches, and can satisfy safely as the necessary specific mechanical characteristic of BOP.Especially, forging can satisfy the standard of API (American Petroleum Institute) (" API ") for the pressurized vessel member, shown in API Specification 16A/ISO 13533 the 6.3rd part.
The combination of the control of disclosed chemical ingredients, thermal treatment temp, quenchant control and tempering time control can produce inside yield strength with at least about 85Ksi, at least approximately 100Ksi ultimate strength, at least 20% unit elongation, at least 70% relative reduction in area and from the forging of the surface hardness scope of about 217 to 237 Brinell hardness numbers.Yield strength is meant the imposed stress that low alloy steel can stand before viscous deformation.Ultimate strength is meant the imposed stress that low alloy steel can stand before damage or fracture.Unit elongation is meant the low alloy steel length variations that relative original length can stand before fail in tension.Relative reduction in area is meant that the maximum of the cross-sectional area that low alloy steel can stand with respect to original cross-sectional area changes before fail in tension.At least about 217 Brinell hardness number has guaranteed that low alloy steel satisfies the minimum mechanical properties about yield strength and ultimate strength.About at the most 237 Brinell hardness number has guaranteed that low alloy steel satisfies the regulation of NACE MR0175/ISO 15156 for the low alloy steel that will be used for acid work.BOP is exposed to the exclusive requirement that is therefore satisfied the regulation of NACE MR0175/ISO 15156 in the acid work (sour service) by API 16A requirement sometimes.Acid work is meant that metal alloy is comprising hydrogen sulfide, i.e. H 2Use in the drilling fluid environment of S (its concentration enough causes being exposed to the SSCC of the sensitive metal alloy of these environment, i.e. sulfide-stress cracking (Sulfide StressCorrosion Cracking)).
The chief component of the annular BOP101 of the prior art that can be made by low alloy steel of the present invention comprises shell 102, piston 117 and removable head 119.It will be appreciated by those skilled in the art that low alloy steel of the present invention is not limited to pressurized vessel.Other embodiment that have been used in combination thick-walled forgings can be made by low alloy steel of the present invention.
Although the embodiment about limited quantity has illustrated the present invention, those skilled in the art have benefited from the disclosure, will be understood that can imagine other embodiment and can not break away from the present invention's scope as disclosed herein.Therefore, scope of the present invention should only be limited by claim.

Claims (20)

1. the method for a thermal treatment thick-walled forgings, this method comprises:
Heating low alloy steel is to austenitizing temperature, and wherein this low alloy steel comprises the manganese of the carbon of about 0.05-0.2wt.%, about 0.3-0.8wt.% and the nickel of about 0.25-1.0wt.%;
This low alloy steel quenches in quenchant; And
This low alloy steel of tempering reaches less than per inch throat section thickness and added about two hours in about 30 minutes.
2. the method for claim 1, its middle-low alloy steel also comprises greater than 0 phosphorus up to about 0.04wt.%, greater than 0 up to about 0.04% sulphur, greater than 0 silicon up to about 0.5wt.%, the about chromium of 2.0-2.5wt.%, and the about molybdenum of 0.45-1.15wt.%.
3. the process of claim 1 wherein that low alloy steel comprises the nickel of about 0.5-1.0wt.%.
4. the process of claim 1 wherein that low alloy steel also comprises aluminium.
5. the process of claim 1 wherein that low alloy steel also comprises vanadium.
6. the process of claim 1 wherein that low alloy steel is handled through calcium during melting process.
7. the method for claim 1 also is included in heating low alloy steel this low alloy steel of normalizing to the austenitizing temperature.
8. the process of claim 1 wherein that quenchant is a salt solution.
9. the process of claim 1 wherein that the finishing temperature of quenchant is less than about 95 Fahrenheit temperature (35 centigradetemperature).
10. utilize the preventer of the method manufacturing of claim 1.
11. a forging comprises:
The carbon of about 0.05-0.2wt.%;
The manganese of about 0.3-0.8wt.%;
The nickel of about 0.25-1.0wt.%;
At least about 8 inches tranverse sectional thickness;
Inside yield strength greater than about 85Ksi; With
About at the most 237 Brinell hardness.
12. the forging of claim 11 also comprises greater than 0 phosphorus up to about 0.04wt.%.
13. the forging of claim 11 also comprises greater than 0 up to about 0.04% sulphur.
14. the forging of claim 11 also comprises greater than 0 silicon up to about 0.5wt.%.
15. the forging of claim 11 also comprises the chromium of about 2.0-2.5wt.%.
16. the forging of claim 11 also comprises the molybdenum of about 0.45-1.15wt.%.
17. the forging of claim 11 also comprises at least approximately ultimate strength of 100Ksi.
18. the forging of claim 11 also comprises about at least 20% unit elongation.
19. the forging of claim 11 also comprises about at least 70% reduction of area.
20. the forging of claim 11 also comprises about at least 217 Brinell hardness number.
CNA200680040529XA 2005-09-29 2006-09-29 Methods for heat treating thick-walled forgings Pending CN101300365A (en)

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CN107002155B (en) * 2014-11-18 2019-06-11 安赛乐米塔尔公司 For manufacture high strength steel product method and thus obtained steel product
US11371109B2 (en) 2014-11-18 2022-06-28 Arcelormittal Method for manufacturing a high strength steel product and steel product thereby obtained
CN107805756A (en) * 2016-09-09 2018-03-16 中国石化工程建设有限公司 A kind of cryogenic steel, low-temperature pressure container and steel for pipe pipe and preparation method thereof

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NO20081850L (en) 2008-06-17
CA2623995A1 (en) 2007-04-05
WO2007038789A1 (en) 2007-04-05
EA200800969A1 (en) 2008-08-29
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US20070068607A1 (en) 2007-03-29
EP1929054A4 (en) 2010-03-31

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