CN102162071A - Limit mandrel steel material for rolled tubes and preparation method thereof - Google Patents
Limit mandrel steel material for rolled tubes and preparation method thereof Download PDFInfo
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- CN102162071A CN102162071A CN2010101124179A CN201010112417A CN102162071A CN 102162071 A CN102162071 A CN 102162071A CN 2010101124179 A CN2010101124179 A CN 2010101124179A CN 201010112417 A CN201010112417 A CN 201010112417A CN 102162071 A CN102162071 A CN 102162071A
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Abstract
The invention relates to high-performance limit mandrel steel material for rolled tubes and a preparation method thereof. The steel material comprises the following components in percentage by mass: 0.40-0.48% of C, 0.40-0.80% of Si, 0.30-0.60% of Mn, at most 0.010% of P, at most 0.008% of S, 2.30-3.00% of Cr, 2.0-2.5% of Mo, 1.0-1.5% of V, 0.50-0.80% of Ni, 0.04-0.10% of Nb, 0.015-0.035% of Al, and the balance of Fe and inevitable impurity. The limit mandrel steel material for rolled tubes has favorable high-temperature properties, and greatly prolongs the service life of the mandrel. The mandrel prepared from the steel material provided by the invention can be used for rolling 3500-4200 tubes by one charging, but H13 steel can only be used for rolling 2000-3000 rubes under the same conditions. The invention prolongs the service life by about 50%, lowers the production cost of the steel tubes and enhances the production efficiency.
Description
Technical field
The invention belongs to field of alloy steel, relate generally to a kind of manufacturing tube rolling high-performance retained mandrel steel and manufacture method thereof.
Background technology
At present, tube rolling mainly is to make with USS hot-work die steel H13 with retained mandrel.This steel has characteristics such as obdurability has both, technology stability is good, production cost is relatively low and is widely adopted.But H13 only is suitable for using at the working condition below 600 ℃.Because during plug will penetrate greater than 1000 ℃ high temperature hollow billet in the work engineering, the plug body externally forces still to need under the cooling conditions to bear the high temperature up to 700 ℃, when thermal cycling stresses surpasses the high-temperature yield strength of plug itself, mandrel surface will produce heat fatigue cracking, quickens the early failure of plug.Existing H13 retained mandrel after 2000～3000 cold and hot fatigue and cyclic, owing to the thermal fatigue well damage causes scrapping, causes production cost to increase with steel, and production efficiency reduces.Therefore, in order to improve the life-span of tube rolling, must improve the fatigue lifetime of steel with retained mandrel.
Adopt the investigator of constant stress control thermal fatigue test to generally believe that the strength of materials is higher, fatigue lifetime is longer, because high yield strength can be resisted the stress that thermal cycling produces.As long as the stress that thermal cycling produces is no more than YIELD STRENGTH, material just can not ftracture.Therefore, improving the high-temperature yield strength and the anti-temper softening ability of mandrel steel material, is the key point that improves its work-ing life.
For obtaining this high-performance retained mandrel steel, consider that from the composition design angle composition of reply H13 steel is suitably adjusted, and adds the strong alloying element of some anti-temper softening abilities, to improve the mechanical behavior under high temperature of steel.As the disclosed steel of patent application CN200510085632.3, though with H13 mutually specific tenacity have some improvement, but because Mo, V content are lower in the steel, and do not contain the Nb element, therefore its mechanical behavior under high temperature is close with the H13 performance with anti-temper softening ability, does not reach tangible improvement.And for example the disclosed steel of patent application CN200410075066.3 is improved performance though added one or more alloying elements such as RE, W, B, Zr, Mg, Ti, also makes the manufacturing process complexity simultaneously, and production cost increases.In addition, its C, Mo, V content are lower, and Si, Cr content are higher, and the intensity of improving steel is also had certain restriction.
Therefore, need a kind of steel of excellent property at high temperature badly, as the material of tube rolling with retained mandrel.
Summary of the invention
The object of the present invention is to provide a kind of high-performance tube rolling retained mandrel steel.
For achieving the above object, steel provided by the present invention, its composition quality degree is: C:0.40～0.48%, Si:0.40～0.80%, Mn:0.30～0.60%, P: S≤0.010% :≤0.008%, Cr:2.30～3.00%, Mo:2.00～2.50%, V:1.00～1.50%, Ni:0.50～0.80%, Nb:0.04～0.10%, Al:0.015～0.035%, surplus is Fe and unavoidable impurities.
In addition, the present invention also provides a kind of manufacture method of above-mentioned steel, comprises electric arc furnace and ladle furnace vacuum refinement, esr, forging, annealing, modifier treatment successively, and wherein modifier treatment comprises oil quenching and two steps of high tempering.
Preferably, the temperature of described oil quenching is 1050-1100 ℃.
Preferably, the temperature of described high tempering is 620-700 ℃.Further preferably, described high tempering temperature is 650-700 ℃.
To further specify the present invention below.
The present invention reduces Cr content in the composition design, increase Mo, V content, to promote high-temperature stable phase Mo
2C and V
4C
3Formation, and reduce high temperature unstable phase Cr
7C
3And Cr
23C
6Formation, thereby improve its use temperature.In addition, make V
4C
3Dissolve in the austenite, need to adopt the austenitizing temperature more than 1050 ℃, will cause the alligatoring of austenite crystal.Therefore after in steel, adding the Nb micro alloying element, can form the better tiny NbC particle of stability,, make the obvious refinement of austenite crystal, thereby improve the plasticity and toughness of steel to stop growing up of austenite crystal.Simultaneously, the present invention utilizes this rule to make invention steel grade tempering temperature when producing obviously to improve just, thereby has obviously improved the anti-temper softening ability of steel.In addition, because tempering temperature more near its use temperature, makes the invention steel in use have better structure stability.Moreover, because of after adding an amount of Ni, its ductility and toughness at room temperature is further improved in the steel.
Below the design of composition of steel of the present invention is described:
The increase of C:C content can make the hot strength of steel, hot hardness and wearability improve, and therefore the C content of H13 steel suitably can be improved.But C content is too high, can cause its toughness to reduce, and therefore, the C content of steel of the present invention adopts 0.40～0.48%.
Played deoxidation and improved corrosion proof effect in the Si:Si adding steel.But Si can reduce the thermal conductivity of steel, increases the heat accumulation effect of plug, thereby reduces the work-ing life of plug.And Si content increases, and can reduce the impelling strength of material.Therefore, the Si mass percentage content in the steel remains on 0.40～0.80% scope, helps to obtain best tough cooperation.
Mn:Mn is the essential element of obdurability that improves steel, and limiting its mass percentage content scope at this is 0.30～0.60%.
Cr: the Cr part in the steel is dissolved in and is played the solution strengthening effect in the steel, and another part combines with C and forms Cr
7C
3And Cr
23C
6, but these two kinds of carbide at high temperature are unsettled, at high temperature can not play good strengthening effect.In addition, when Cr mass percentage content＞3%, can stop V
4C
3Generation and postpone Mo
2The coherence of C is separated out, and influences the strengthening effect of Mo and V.Therefore, must reduce Cr content.The mass percentage content of Cr is 2.30～3.00% in steel of the present invention.
The adding of Mo:Mo is in order to improve the secondary hardening effect.Generally in order to produce the secondary hardening effect, the add-on of Mo is not less than 1.0%, adds 3.0% and just reaches the extreme value effect, adds 2.00～2.50% and can obtain best effect.Therefore, the mass percentage content of Mo is 2.00～2.50% in steel of the present invention.
The effect of V:V mainly is crystal grain thinning and tissue, increases temper resistance and secondary hardening effect.When V content hangs down, the not enough V that forms
4C
3, can not produce the secondary hardening effect; Surpass at 1.5% o'clock owing to the precipitate alligatoring makes mis-behave.Therefore, controlling its mass percentage content is 1.00～1.50%.
Ni:Ni is in order to improve temperature-room type plasticity and toughness.Add-on is lower than 0.30%, DeGrain, and still, in hot-work die steel, Ni can promote in the quench cooled process to have reduced carbide forming element in the matrix, thereby to have reduced its thermostability along the austenite grain boundary carbide precipitate.Therefore, do not add too much Ni in high performance hot-work die steel, controlling its quality percentage composition in the present invention is 0.50～0.80%.
The adding of Nb:Nb is for crystal grain thinning, the intensity that has improved material and plasticity.But add-on is lower than at 0.04% o'clock, and DeGrain surpasses at 0.10% o'clock owing to the precipitate alligatoring makes mis-behave.
Al:Al has played the effect of desoxydatoin and crystal grain thinning in steel.When add-on is lower than 0.015%, DeGrain, add-on surpasses 0.035%, the mechanical property variation.
The present invention is conceived to improve the high-temperature behavior and the anti-temper softening ability of material in the material design, suitably improve the content of Mo, V alloy element, reduce the Cr constituent content, and add an amount of Nb, Ni element, foreign matter contents such as control P, S, after final modified thermal treatment, can obtain high performance retained mandrel steel.
Compare with steel with existing retained mandrel, the present invention has following beneficial effect:
1, high-temperature behavior is good, improved the plug life-span greatly, but the plug of invention steel manufacturing rolls off the production line through once installing to and repairs 3500～4200 of wroughtsteel pipes, and H13 steel 2000～3000 of wroughtsteel pipes under similarity condition improve about 50% its work-ing life;
2, reduce steel pipe's production cost and enhancing productivity.
Embodiment
According to the chemical ingredients requirement of steel grade of the present invention, steel billet is through electric arc furnace and ladle furnace vacuum refinement, esr, forging and annealing.In the modifier treatment, at 1060 ℃ of following oil quenchings, afterwards respectively at 620 ℃ and 700 ℃ of following high temperings, to make the steel sample of different size.In order to contrast, in production steel of the present invention, the Comparative Examples that adopts same process to produce the H13 steel.Embodiment/Comparative Examples is taken a sample, carry out room temperature and high temperature tension test, room temperature shock test and last machine certification test respectively.Its result is as follows.
The chemical ingredients of table 1 embodiment and Comparative Examples (wt%)
The mechanical property of table 2 embodiment steel and Comparative Examples steel and work-ing life are relatively
Tube rolling of the present invention is good with retained mandrel steel mechanical behavior under high temperature, and anti-temper softening ability is strong, and improve work-ing life greatly, can replace common H13 retained mandrel steel.Its successful design and exploitation will bring huge economic benefit, and its market outlook will be very huge.
Claims (5)
1. tube rolling retained mandrel steel, its composition quality degree is:
C 0.40～0.48
Si 0.40～0.80
Mn 0.30～0.60
P ≤0.010
S ≤0.008
Cr 2.30～3.00
Mo 2.00～2.50
V 1.00～1.50
Ni 0.50～0.80
Nb 0.04～0.10
Al 0.015～0.035
Surplus is Fe and unavoidable impurities.
2. make the method for steel as claimed in claim 1, it is characterized in that, described method comprises electric arc furnace and ladle furnace vacuum refinement, esr, forging, annealing, modifier treatment successively, and wherein, modifier treatment comprises oil quenching and two steps of high tempering.
3. method as claimed in claim 2 is characterized in that, the temperature of described oil quenching is 1050-1100 ℃.
4. method as claimed in claim 2 is characterized in that, the temperature of described high tempering is 620-700 ℃.
5. method as claimed in claim 4 is characterized in that, the temperature of described high tempering is 650-700 ℃.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 201010112417 CN102162071B (en) | 2010-02-23 | 2010-02-23 | Limit mandrel steel material for rolled tubes and preparation method thereof |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN 201010112417 CN102162071B (en) | 2010-02-23 | 2010-02-23 | Limit mandrel steel material for rolled tubes and preparation method thereof |
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|---|---|
| CN102162071A true CN102162071A (en) | 2011-08-24 |
| CN102162071B CN102162071B (en) | 2013-06-19 |
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103033463A (en) * | 2012-12-26 | 2013-04-10 | 江南大学 | Method for simultaneously detecting two pathogenic bacteria by employing quantum dot marked aptamer recognition and flow cytometry |
| CN104227350A (en) * | 2014-09-02 | 2014-12-24 | 中原特钢股份有限公司 | Preparing method of retained mandrel |
| CN104451028A (en) * | 2014-11-25 | 2015-03-25 | 南通新正大特钢有限公司 | Smelting process for mandrel steel |
| CN105568173A (en) * | 2014-10-15 | 2016-05-11 | 宝钢特钢有限公司 | High-strength high-toughness low-alloy heat-resistant steel and preparation method thereof |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0657380A (en) * | 1992-08-13 | 1994-03-01 | Nippon Steel Corp | Mandrel-rolling core bar having long service life |
| CN1251786A (en) * | 1999-10-19 | 2000-05-03 | 赵士英 | Technology for manufacturing mandrel used to roll seamless steel tube |
| JP2000226635A (en) * | 1999-02-05 | 2000-08-15 | Sumitomo Metal Ind Ltd | Hot tool steel excellent in high temperature strength and toughness |
| JP2001293504A (en) * | 2000-04-13 | 2001-10-23 | Sumitomo Metal Ind Ltd | Mandrel bar and its producing method |
| CN1616700A (en) * | 2003-08-28 | 2005-05-18 | 河南中原特殊钢厂 | Steel for processing movement limiting core stick of continuous tube grimper and its producing process |
-
2010
- 2010-02-23 CN CN 201010112417 patent/CN102162071B/en active Active
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0657380A (en) * | 1992-08-13 | 1994-03-01 | Nippon Steel Corp | Mandrel-rolling core bar having long service life |
| JP2000226635A (en) * | 1999-02-05 | 2000-08-15 | Sumitomo Metal Ind Ltd | Hot tool steel excellent in high temperature strength and toughness |
| CN1251786A (en) * | 1999-10-19 | 2000-05-03 | 赵士英 | Technology for manufacturing mandrel used to roll seamless steel tube |
| JP2001293504A (en) * | 2000-04-13 | 2001-10-23 | Sumitomo Metal Ind Ltd | Mandrel bar and its producing method |
| CN1616700A (en) * | 2003-08-28 | 2005-05-18 | 河南中原特殊钢厂 | Steel for processing movement limiting core stick of continuous tube grimper and its producing process |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103033463A (en) * | 2012-12-26 | 2013-04-10 | 江南大学 | Method for simultaneously detecting two pathogenic bacteria by employing quantum dot marked aptamer recognition and flow cytometry |
| CN104227350A (en) * | 2014-09-02 | 2014-12-24 | 中原特钢股份有限公司 | Preparing method of retained mandrel |
| CN105568173A (en) * | 2014-10-15 | 2016-05-11 | 宝钢特钢有限公司 | High-strength high-toughness low-alloy heat-resistant steel and preparation method thereof |
| CN105568173B (en) * | 2014-10-15 | 2017-07-28 | 宝钢特钢有限公司 | A kind of high-obdurability low-alloy heat resisting steel and its manufacture method |
| CN104451028A (en) * | 2014-11-25 | 2015-03-25 | 南通新正大特钢有限公司 | Smelting process for mandrel steel |
Also Published As
| Publication number | Publication date |
|---|---|
| CN102162071B (en) | 2013-06-19 |
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