CN105369151A - Piercing point for seamless pipe manufacturing - Google Patents
Piercing point for seamless pipe manufacturing Download PDFInfo
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- CN105369151A CN105369151A CN201510509250.2A CN201510509250A CN105369151A CN 105369151 A CN105369151 A CN 105369151A CN 201510509250 A CN201510509250 A CN 201510509250A CN 105369151 A CN105369151 A CN 105369151A
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Abstract
The invention provides a piercing point for seamless pipe manufacturing. The piercing point has the advantages of improved high temperature strength, properties of oxide scales, ductile property, toughness, and thermal cracking resistant property, and long service life. The surface of the piercing point is covered by oxide scale. The piercing point is characterized in that the piercing point other than the oxide scales is composed of the following components in percentage by weight: 0.10 to 0.25% of C, 0.05 to 0.80% of Si, 0.20 to 1.00% of Mn, 2.5 to 3.5% of Ni, 1.0 to 2.0% of Cr, 2.5 to 3.5% of Mo, 2.5 to 3.5% of W, 0.07 to 0.40% of Nb, 0.03 to 0.40% of Ti, and the balance being Fe and inevitable impurities. The texture of the piercing point other than the oxide scales comprises 1 to 10% of carbides and martensite.
Description
Technical field
The present invention relates to the seamless tube manufacture perforating head used in the manufacture of the seamless tube adopting mannesmann piercing method to carry out, particularly relate to the perforating head extending the life-span.
Background technology
Oil well pipe mainly adopts the manufacture of mannesmann piercing method.The perforating head that perforation uses, under being exposed to the harshest working conditions among instrument.In recent years, seamless tube employ hot under high stainless steel, the high alloy of resistance to deformation, the life-span of perforating head more and more reduces thus, and in extreme situations, 1 passage perforation becomes the limit.
About the life of perforating head, once there is following report: improve the life-span by the surface modification adopting PTA built-up welding, arc spraying carries out.
Patent documentation 1 discloses a kind of iron wire material taking Fe as principal constituent by arc spraying on the surface of mother metal and is formed by Fe
3o
4, the drilling/rolling top of tunicle that forms of the oxide compound such as FeO and Fe (metal).By this tunicle, excellent thermal insulation and anti-heat-blocking can be realized, obtain the perforating head of life-span length.
Patent documentation 2 relates generally to the improvement of the material of patent documentation 1, discloses after casting, carried out the material of the high rigidity of Dehydroepiandrosterone derivative.
Although these inventions achieve successfully in the life of perforating head, there is the problems such as cost is high, quality generation deviation.
As the method for the life of perforating head all the time, once reported the invention that effects on surface gives oxide skin.
Patent documentation 3 has disclosed at Surface Creation the tool for thermal processing of oxide skin.When oxide skin is rhombohedral iron ore, magnetite, wustite from skin, life when magnetite is 40 more than volume %.
Patent documentation 4 discloses the manufacture method of the hot tubulation instrument that can extend life tools.Patent documentation 4 discloses: compared with sand mo(u)ld, and the solidified structure of metal die casting is fine, its result, and become fine and close in the oxide skin of matrix (matrix) Surface Creation due to the miniaturization of matrix, peel resistance and resistance to heat-blocking improve.
Even if patent documentation 5 discloses the hot tubulation instrument also when material high for resistance to deformation being carried out tubulation with high work-ing life.In patent documentation 5, guarantee high temperature deformation resistance by a large amount of interpolations of Mo, W, improved peel resistance, the wearability of oxide skin by Ni, W.
Patent documentation 6 discloses the weldless steel tube drilling/rolling instrument stably with long life tools.In patent documentation 6, the oxide scale layer being formed at substrate side is made to be the netted oxide scale layer interweaved with steel matrix complexity, and make from the interface of oxide scale layer and base material to substrate side be in the depth direction 500 μm scope be organized as the tissue with the ferritic phase counting more than 50% by area occupation ratio, the stripping of inhibited oxidation cortex thus, wearing and tearing, improve the life-span of drilling/rolling instrument.
At first technical literature
Patent documentation 1: No. 2009/057471st, International Publication
Patent documentation 2: No. 2014/050975th, International Publication
Patent documentation 3: Japanese Unexamined Patent Publication 8-193241 publication
Patent documentation 4: Japanese Unexamined Patent Publication 8-300014 publication
Patent documentation 5: Japanese Unexamined Patent Publication 7-60314 publication
Patent documentation 6: Japanese Unexamined Patent Publication 2003-129184 publication
Summary of the invention
For the purpose of the life of perforating head, complete many inventions up to now, but be still not being met for stainless steel, heavy alloyed perforation life-span.
The damage of perforating head is by the wrinkle of (1) head melting loss and hot sticky and (2) body and gnaws meat and cause.For any one damage, hot strength and oxide skin proterties (adherence, thickness) all have an impact.And, as other damage, there is (3) longitudinal slit (crack and damage).In this damage, ductility, toughness and heat-resistant cracking have an impact.
If asynchronously solve this 3 problems, then can not realize the life of perforating head.Problem of the present invention is to provide by the raising of (1) hot strength, the improvement of (2) oxide skin proterties (adherence, thickness), (3) ductility, the raising of toughness, the improvement of heat-resistant cracking, thus extends the seamless tube manufacture perforating head in life-span.
The present inventor has concentrated on studies the method for perforating head long lifetime.It found that, be grouped into by selected suitable one-tenth, hardening capacity (hardenability) is improved, and make the tissue of top become carbide and the martensite of appropriate amount, hot strength is improved greatly.
In the final operation of the manufacture of perforating head, in order to give oilness, thermal insulation and implement oxide skin and give process, after generating oxide skin, cold in order to prevent the stripping of oxide skin from carrying out stove with the speed of cooling of 20 ~ 50 DEG C/h.The present inventor finds: by making Carbide Precipitation under being selected in this speed of cooling and the suitable one-tenth carrying out martensitic transformation is grouped into, hot strength can be made to improve.
In addition, the present inventor finds that the adherence of oxide skin depends on the fineness degree of the crystal grain of the tissue of top.
The cast steel product of metal die or sand casting can be used as perforating head.The crystal grain of casting state is thicker, is hundreds of μm ~ tens of mm.In the perforating head having carried out ferrite-pearlite phase transformation, thick crystal grain is made to become fine by the thermal treatment (austenite phase transformation) for giving oxide skin.But carried out the perforating head of martensitic transformation, even if carry out austenite phase transformation to give oxide skin, due to so-called " memory effect ", therefore crystal grain is still thick state, compared with perforating head in the past, the adherence of oxide skin reduces.
If only repeatedly annealed, then have the alloy that one-tenth of the present invention is grouped into and only repeatedly can carry out austenite → martensite → austenite → martensitic transformation, crystal grain remains the state of the thick particle of hundreds of μm ~ tens of mm of casting.
Crystal grain photo by giving the heating of oxide skin, stove deepfreeze and the perforating head that carried out ferrite-pearlite phase transformation and the perforating head that carried out martensitic transformation is shown in Fig. 1, Fig. 2.The crystal grain of the top of Ferrite-Perlite structure is fine, is 20 μm, but has carried out the coarse grains of the top of martensitic transformation, is about 500 μm.Its result, the scale interface area of martensitic stucture top, be significantly less than the scale interface area of ferrite+pearlitic structure top as shown in Figure 2, use each top to carry out the result of 13Cr stainless steel drifting test, head lifetime is also reduced to half i.e. 3 passages from 6 passages.That is, when only making the tissue of perforating head become martensite, although hot strength can be improved, can not get sufficient oxide skin adherence.
In imparting oxide skin, when the interfacial area of matrix and oxide skin is large, the adherence of oxide skin is excellent.About oxide skin, owing to being optionally oxidized crystal boundary compared in the crystal grain of matrix, when the crystal grain therefore come directly towards is fine, matrix and scale interface area increase, its result, and the adherence of oxide skin improves.
Therefore, the present inventor has concentrated on studies when the oxide skin of the top of carrying out martensitic transformation when oxide skin is given is given and has made the method for crystal grain miniaturization.It found that, before giving in oxide skin, makes the thick cohesion of carbide, the average crystal particle diameter of the tissue of top can be made to become fine.
In addition, about ductility, toughness, heat-resistant cracking, usually think in the perforating head carrying out martensitic transformation, with carrying out compared with the perforating head of ferrite-pearlite phase transformation, ductility, toughness, heat-resistant cracking reduce in the past.But the present inventor finds, by by C amount and carbide amount optimizing, compared with perforating head up to now, ductility, toughness, heat-resistant cracking can be improved.
Namely, the invention provides by (1) even if design, (2) that the very high one-tenth of the cold hardening capacity of also carrying out martensitic transformation of stove is grouped into make the optimizing of crystal grain miniaturization, (3) preferred carbon amounts in hardening capacity and carbide amount, thus the perforating head of long lifetime, its main idea is as follows.
(1) a kind of seamless tube manufacture perforating head, it is the seamless tube manufacture perforating head defining oxide skin on surface, it is characterized in that, the one-tenth of the top except above-mentioned oxide skin is grouped into by mass% containing C:0.10 ~ 0.25%, Si:0.05 ~ 0.80%, Mn:0.20 ~ 1.00%, Ni:2.5 ~ 3.5%, Cr:1.0 ~ 2.0%, Mo:2.5 ~ 3.5%, W:2.5 ~ 3.5%, Nb:0.07 ~ 0.40%, with Ti:0.03 ~ 0.40%, surplus is Fe and inevitable impurity, the organizational composition of the top except above-mentioned oxide skin comprises the carbide of 1 ~ 10%, and martensitic stucture.
(2) the seamless tube manufacture perforating head according to above-mentioned (1), is characterized in that, the average crystal particle diameter of described martensitic stucture is less than 50 μm.
(3) the seamless tube manufacture perforating head according to above-mentioned (1) or (2), it is characterized in that, it is one kind or two or more that the one-tenth of described perforating head is grouped into by mass% also containing in Mg:0.001 ~ 0.100%, REM:0.01 ~ 0.50%, Ca:0.0005 ~ 0.0500%, Al:0.005 ~ 0.200% and B:0.0001 ~ 0.0050%.
According to the present invention, can provide and hot strength is significantly improved with oxide skin proterties (adherence, thickness) compared with perforating head in the past and improves ductility, toughness, heat-resistant cracking, long-life seamless tube manufacture perforating head.
Accompanying drawing explanation
Fig. 1 is the figure of the tissue representing the perforating head having carried out ferrite+pearlitic transformation, and (a) is the tissue of perforating head inside, and (b) is the tissue of scale interface.
Fig. 2 is the figure of the tissue representing the perforating head having carried out martensitic transformation, and (a) is the tissue of perforating head inside, and (b) is the tissue of scale interface.
Fig. 3 (a) represents the figure utilizing scanning electron microscope (SEM) to observe the carbide tissue of the perforating head with oxide skin, and carbide has been carried out the figure of binarization of gray value by (b).
Fig. 4 (a) is after representing carbide agglomeration process, with the figure of the tissue of the perforating head of oxide skin, (b) represents not implement carbide agglomeration process and the figure of tissue with the perforating head of oxide skin.
Embodiment
Below, the present invention is described in detail.First, the one-tenth of perforating head of the present invention is grouped into is described.Below, the token about " % " that become to be grouped into means " quality % ".
C affects large element to hardening capacity.In addition, with Mo, W, Nb, Cr Formed compound.If the content of C is lower than 0.10%, then hardening capacity reduces, and can not get martensite in the cooling after oxide skin gives process.If the content of C is more than 0.25%, then carbide quantitative change is many, and toughness and heat-resistant cracking reduce.
Si is deoxidant element.If the content of Si is lower than 0.05%, then oxygen amount uprises, and ductility reduces.If the content of Si is more than 0.80%, then scale resistance improves, and the thickness of oxide skin is thinning.
Mn is deoxidant element, in the raising of hardening capacity, be all required element with C, Cr mono-.In order to obtain the effect as deoxidant element, the content of Mn needs to be more than 0.20%.If the content of Mn is more than 1.00%, then toughness reduces.
Ni generates the high necessary element of oxide skin of adherence.If the content of Ni is lower than 2.5%, then the concavo-convex minimizing of oxide skin and basal body interface.If the content of Ni is more than 3.5%, even if then carry out carbide agglomeration process, crystal grain does not become fine yet.
Cr and C, Mn are similarly the element improving hardening capacity.If the content of Cr is lower than 1.0%, then can not get sufficient hardening capacity.If the content of Cr is more than 2.0%, then the generation of oxide skin is suppressed, and scale thickness is not enough.
Mo to be solid-solution in matrix thus to improve hot strength.In addition, by generating double carbide M
6(M is metallic element to C; Identical below) also improve hot strength.And, be similarly with C, Cr, Mn the element improving hardening capacity.If the content of Mo is lower than 2.5%, then can not fully obtain hardening capacity and improve effect, hot strength also reduces.If the content of Mo is more than 3.5%, then grain boundary carbide increases, and ductility, toughness reduce.
W and Mo to be together solid-solution in matrix thus to improve hot strength.In addition, M is generated
6the carbide of C type thus improve hot strength.In addition, W generates low melting point oxide skin.If the content of W is lower than 2.5%, then fully can not obtain solution strengthening.If the content of W is more than 3.5%, then grain boundary carbide increases, and ductility, toughness reduce.
Nb to be solid-solution in matrix thus to improve hot strength while the carbide generating MC type.If the content of Nb is lower than 0.07%, then can not fully be strengthened, if the content of Nb is more than 0.40%, then crystallization goes out thick carbide, and toughness, ductility reduce.
Ti to be solid-solution in matrix thus to improve hot strength while generation TiN.If the content of Ti is lower than 0.03%, then can not fully be strengthened, if the content of Ti is more than 0.40%, then crystallization goes out thick nitride, and ductility, toughness reduce.
Mg, REM and Ca are arbitrary Addition ofelements, optional element, if but add within the limits prescribed, the further improvement of the adherence of oxide skin can be sought.REM is rare earth element.
If Mg content is lower than 0.001%, can't see oxide skin adherence and improve effect, if content is more than 0.100%, effect is saturated.
If REM content is lower than 0.01%, can't see oxide skin adherence and improve effect, if content is more than 0.50%, scale thickness is thinning.
If Ca content is lower than 0.0005%, can't see oxide skin adherence and improve effect, if content is more than 0.0500%, effect is saturated.
In addition, Al can be added in the scope of 0.005 ~ 0.200% as reductor.Addition is 0.005% ~ 0.200%.
In addition, in order to improve hardening capacity, B can be added in the scope of 0.0001 ~ 0.0050%.
The surplus becoming to be grouped into is Fe and inevitable impurity.So-called inevitably impurity, refers to owing to originally comprising in the feed or being mixed in the process manufactured etc. thus composition comprised in the present invention, is and the composition unintentionally added.
From the view point of ductility, toughness, heat-resistant cracking, among inevitable impurity, P and S is as well low, is preferably less than 0.02%.
Be grouped into by being defined as one-tenth as described above, hardening capacity significantly uprises, even the state of casting, also carries out martensitic transformation substantially.
Then, the tissue of matrix and oxide skin are described.
The organizational composition of top is the carbide of 1 ~ 10% and the martensitic stucture as matrix.Carbide and martensitic stucture improve hot strength, and also improve ductility, toughness, heat-resistant cracking.If be grouped into for one-tenth of the present invention, then after giving oxide skin at 950 ~ 1100 DEG C, cold by the stove of 20 ~ 50 DEG C/h, tissue carries out martensitic transformation.
When top of the present invention, due to carbide precipitate before martensitic transformation, be therefore difficult to identify martensite and lower bainite by opticmicroscope or measurement of hardness, also sometimes comprise lower bainite being called in martensitic tissue.
The amount of carbide, uses scanning electron microscope (SEM), observes 5 visual fields, obtain its area occupation ratio with 3000 times.When this alloy, there is crystalline carbon compound and the M of NbC and so on
6the carbide of separating out in cooling of C and so on.Crystalline carbon compound is helpless to hot strength, except therefore from the mensuration of area occupation ratio, obtains the area occupation ratio of carbide precipitate.Fig. 3 is illustrated in by one.A () represents the figure utilizing scanning electron microscope (SEM) to observe the carbide tissue of the perforating head with oxide skin, carbide has been carried out the figure of binarization of gray value by (b).
If carbide amount is lower than 1%, the improvement of hot strength is insufficient, if more than 10%, the reduction of toughness, ductility becomes remarkable.
The adherence of surface scale depends on the composition of oxide skin and concavo-convex.If the crystal grain of the tissue of top is fine, then can generate the high oxide skin of adherence.
In the present invention, process below implementing before oxide skin is given, make the thick cohesion of carbide, can make that the crystal grain of top is preferably fine turns to less than 50 μm.
Specifically, by carry out martensitic transformation top at AC
1700 ~ 750 DEG C of heating below transformation temperature, make M
6c, M
23c
6deng carbide cohesion, after making martensite become ferrite+carbide tissue, implement oxide skin and give process.Thus, martensite memory effect disappears, and can obtain trickle austenite crystal.More specifically, at AC
1point-30 ~ AC
1the temperature range heating of point-150 DEG C 3 ~ 20 hours.If Heating temperature is low, then carbide does not fully condense, if Heating temperature height, likely in actually operating more than AC
1transformation temperature.If heat-up time is short, carbide does not fully condense, if heat-up time is long, effect is saturated.
In the diagram, as the example of crystal grain of carrying out carbide agglomeration process, by after having processed 5 hours at 750 DEG C, carried out oxide skin and given the photo of the top of process and untreated product illustrate in the lump.Average crystal particle diameter in untreated situation is 87 μm, and by carbide agglomeration process, average crystal particle diameter becomes fine, is 12 μm.
This cohesion carbide oxide skin give process time, a part of solid solution, but a part remaining.Owing to being difficult to the carbide being observed precipitation when distinguishing remaining carbide and oxide skin imparting process cooling by SEM, therefore all measure its area as carbide precipitate.
After above-mentioned process, implement oxide skin process.Oxide skin is given process and is carried out in the following manner: the CO concentration in stove is in the combustion gases atmosphere of 1 ~ 8%, 950 ~ 1100 DEG C of heating 3 ~ 10 hours, then carries out stove with 20 ~ 50 DEG C/h cold.If CO concentration is low, Decarburized layer becomes the degree of depth and is greater than 2mm, if height, scale thickness is thinning.If treatment temp is low, scale thickness is thinning, if height, forms that comprise comparatively concrete dynamic modulus (pore), that adherence reduces oxide skin.If the treatment time is short, oxide skin is thin, if long, thickness is saturated.If be grouped into for one-tenth of the present invention, then pass through this heating, stove is cold, organizational composition becomes the carbide of 1 ~ 10% and the martensite of surplus.
If after oxide skin gives process, carry out the temper of 500 ~ 650 DEG C to martensite, then can improve ductility, toughness, heat-resistant cracking further.
Embodiment
[embodiment 1]
Cast out that to have the external diameter that the one-tenth shown in table 1 is grouped into be after the perforating head of 185mm, implement in electric furnace, in 700 ~ 750 DEG C of heating carbide agglomeration process of 5 hours.In the comparative example of a part, do not implement carbide agglomeration process.Then, the CO concentration in stove is in the combustion gases atmosphere of 1%, maintain 4 hours at 1000 DEG C after to carry out stove cold, thus carried out oxide skin and given process.
Use the perforating head defining oxide skin on surface obtained, tubulation is carried out to 13Cr stainless steel, have rated the life-span.Show the result in table 2.The damage of the perforating head of comparative example is the wrinkle of head melting loss, crack and damage, body, and the life-span is also short, but the damage of perforating head of the present invention is only head melting loss, and the life-span also substantially prolongs.
Table 1
Table 2
Claims (3)
1. a seamless tube manufacture perforating head, is the seamless tube manufacture perforating head defining oxide skin on surface, it is characterized in that,
The one-tenth of the top except described oxide skin is grouped into and contains by mass%
C：0.10～0.25％、
Si：0.05～0.80％、
Mn：0.20～1.00％、
Ni：2.5～3.5％、
Cr：1.0～2.0％、
Mo：2.5～3.5％、
W：2.5～3.5％、
Nb:0.07 ~ 0.40% and
Ti：0.03～0.40％，
Surplus is Fe and inevitable impurity,
The organizational composition of the top except described oxide skin comprises carbide and the martensite of 1 ~ 10%.
2. seamless tube manufacture perforating head according to claim 1, is characterized in that, the average crystal particle diameter of described martensitic stucture is less than 50 μm.
3. seamless tube manufacture perforating head according to claim 1 and 2, it is characterized in that, described one-tenth is grouped into and also contains by mass%
Mg：0.001～0.100％、
REM：0.01～0.50％、
Ca：0.0005～0.0500％、
Al:0.005 ~ 0.200% and
B：0.0001～0.0050％
In one kind or two or more.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2014166591A JP6385195B2 (en) | 2014-08-19 | 2014-08-19 | Piercer plug for seamless pipe manufacturing |
| JP2014-166591 | 2014-08-19 |
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| Publication Number | Publication Date |
|---|---|
| CN105369151A true CN105369151A (en) | 2016-03-02 |
| CN105369151B CN105369151B (en) | 2020-04-03 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201510509250.2A Active CN105369151B (en) | 2014-08-19 | 2015-08-18 | Piercing plug for manufacturing seamless pipe |
Country Status (4)
| Country | Link |
|---|---|
| JP (1) | JP6385195B2 (en) |
| KR (1) | KR102320752B1 (en) |
| CN (1) | CN105369151B (en) |
| TW (1) | TWI648108B (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106282782A (en) * | 2016-10-12 | 2017-01-04 | 天津钢管集团股份有限公司 | High alloy hot-puncturing process comes directly towards |
| CN111282996A (en) * | 2020-04-08 | 2020-06-16 | 冯永涛 | Piercing-rolling integrated four-section type composite top |
| CN112899564A (en) * | 2021-01-15 | 2021-06-04 | 常州宝菱重工机械有限公司 | Steel pipe piercing plug and preparation method thereof |
Citations (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH02179843A (en) * | 1988-12-29 | 1990-07-12 | Sumitomo Metal Ind Ltd | Tool material for hot tube making |
| CN1112165A (en) * | 1995-04-19 | 1995-11-22 | 宝山钢铁(集团)公司 | Steel pipe perforating heading material |
| JPH08206709A (en) * | 1994-12-09 | 1996-08-13 | Sumitomo Metal Ind Ltd | Tool for hot tube making and manufacture thereof |
| JPH11179407A (en) * | 1997-12-19 | 1999-07-06 | Nkk Corp | Tool for manufacturing seamless steel tube |
| US5939018A (en) * | 1984-10-10 | 1999-08-17 | Kawasaki Steel Corporation | Martensitic stainless steels for seamless steel pipe |
| JP2001330101A (en) * | 2000-05-19 | 2001-11-30 | Nissan Motor Co Ltd | Rolling element for continously variable transmission |
| JP2002047534A (en) * | 2000-07-28 | 2002-02-15 | Nippon Chuzo Kk | Tool for producing seamless tube and its production method |
| JP2005240135A (en) * | 2004-02-27 | 2005-09-08 | Jfe Steel Kk | Method for manufacturing wear-resistant steel having excellent bendability, and wear-resistant steel |
| US20070006946A1 (en) * | 2005-07-05 | 2007-01-11 | Takahiro Takano | Manufacturing method of martensite stainless seamless steel pipe |
| JP2007254775A (en) * | 2006-03-20 | 2007-10-04 | Nissan Motor Co Ltd | Self-piercing rivet and manufacturing method therefor |
| CN101070581A (en) * | 2006-05-12 | 2007-11-14 | 江苏南山冶金机械制造有限公司 | Stainless-steel seamless steel-pipe perforation push head |
| CN101070561A (en) * | 2006-05-12 | 2007-11-14 | 江苏南山冶金机械制造有限公司 | Through-hole top-end heat-treatment processing process |
| CN102586700A (en) * | 2012-03-05 | 2012-07-18 | 宜兴市景程模具有限公司 | High alloy tube piercing plug material and manufacturing method and surface processing method thereof |
| US20130264123A1 (en) * | 2012-04-10 | 2013-10-10 | Tenaris Connections Limited | Methods of manufacturing steel tubes for drilling rods with improved mechanical properties, and rods made by the same |
| WO2014050975A1 (en) * | 2012-09-28 | 2014-04-03 | 新報国製鉄株式会社 | Piercer plug material for producing seamless steel tube, and method for producing said material |
| CN103789685A (en) * | 2014-02-17 | 2014-05-14 | 上海海隆石油管材研究所 | High-strength high-toughness petroleum drill pipe and production method thereof |
Family Cites Families (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5920463A (en) * | 1982-07-22 | 1984-02-02 | Kawasaki Steel Corp | Manufacture of material for tool for manufacturing seamless steel pipe |
| JPS6024297A (en) * | 1983-07-18 | 1985-02-06 | Sumitomo Metal Ind Ltd | Guide shoe for manufacturing seamless steel pipe |
| JP2940188B2 (en) * | 1991-02-23 | 1999-08-25 | 住友金属工業株式会社 | Hot pipe making tool and method for producing the same |
| JP2683861B2 (en) | 1993-08-24 | 1997-12-03 | 住友金属工業株式会社 | Hot pipe making tool and method of manufacturing the same |
| JPH08193241A (en) | 1994-09-26 | 1996-07-30 | Kawasaki Steel Corp | Hot working tool and its production |
| JP2952382B2 (en) | 1995-04-27 | 1999-09-27 | 住友金属工業株式会社 | Manufacturing method of hot pipe making tool |
| JP4197364B2 (en) * | 1998-01-20 | 2008-12-17 | エヌケーケーシームレス鋼管株式会社 | Plug mill plug for seamless steel pipe manufacturing |
| JP3635531B2 (en) * | 2000-07-28 | 2005-04-06 | 日本鋳造株式会社 | Seamless pipe manufacturing tool and method for manufacturing the same |
| JP3797192B2 (en) | 2001-10-25 | 2006-07-12 | Ｊｆｅスチール株式会社 | Drilling and rolling tool |
| AU2005258507C1 (en) * | 2004-06-30 | 2008-10-30 | Nippon Steel Corporation | Ni base alloy material tube and method for production thereof |
| CA2572156C (en) * | 2004-06-30 | 2013-10-29 | Sumitomo Metal Industries, Ltd. | Fe-ni alloy pipe stock and method for manufacturing the same |
| CN100453685C (en) * | 2006-07-11 | 2009-01-21 | 无锡西姆莱斯石油专用管制造有限公司 | High Cr series stainless steel jointless oil well tube and its production method |
| DE102006045678B4 (en) | 2006-09-27 | 2012-08-09 | Continental Automotive Gmbh | Method for checking a tank ventilation device, control device and internal combustion engine |
| JP5321673B2 (en) * | 2011-11-30 | 2013-10-23 | Ｊｆｅスチール株式会社 | Drilling and rolling tool |
| KR102076584B1 (en) | 2012-10-22 | 2020-04-07 | 삼성전자주식회사 | Device and method of repairing memory cell and memory system including the same |
| CN103451551B (en) * | 2013-08-30 | 2015-07-01 | 北京工业大学 | Preparation method of cast steel perforator top tip with high-temperature resistance and corrosion resistance |
-
2014
- 2014-08-19 JP JP2014166591A patent/JP6385195B2/en active Active
-
2015
- 2015-08-11 KR KR1020150113305A patent/KR102320752B1/en active IP Right Grant
- 2015-08-14 TW TW104126574A patent/TWI648108B/en active
- 2015-08-18 CN CN201510509250.2A patent/CN105369151B/en active Active
Patent Citations (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5939018A (en) * | 1984-10-10 | 1999-08-17 | Kawasaki Steel Corporation | Martensitic stainless steels for seamless steel pipe |
| JPH02179843A (en) * | 1988-12-29 | 1990-07-12 | Sumitomo Metal Ind Ltd | Tool material for hot tube making |
| JPH08206709A (en) * | 1994-12-09 | 1996-08-13 | Sumitomo Metal Ind Ltd | Tool for hot tube making and manufacture thereof |
| CN1112165A (en) * | 1995-04-19 | 1995-11-22 | 宝山钢铁(集团)公司 | Steel pipe perforating heading material |
| JPH11179407A (en) * | 1997-12-19 | 1999-07-06 | Nkk Corp | Tool for manufacturing seamless steel tube |
| JP2001330101A (en) * | 2000-05-19 | 2001-11-30 | Nissan Motor Co Ltd | Rolling element for continously variable transmission |
| JP2002047534A (en) * | 2000-07-28 | 2002-02-15 | Nippon Chuzo Kk | Tool for producing seamless tube and its production method |
| JP2005240135A (en) * | 2004-02-27 | 2005-09-08 | Jfe Steel Kk | Method for manufacturing wear-resistant steel having excellent bendability, and wear-resistant steel |
| US20070006946A1 (en) * | 2005-07-05 | 2007-01-11 | Takahiro Takano | Manufacturing method of martensite stainless seamless steel pipe |
| JP2007254775A (en) * | 2006-03-20 | 2007-10-04 | Nissan Motor Co Ltd | Self-piercing rivet and manufacturing method therefor |
| CN101070581A (en) * | 2006-05-12 | 2007-11-14 | 江苏南山冶金机械制造有限公司 | Stainless-steel seamless steel-pipe perforation push head |
| CN101070561A (en) * | 2006-05-12 | 2007-11-14 | 江苏南山冶金机械制造有限公司 | Through-hole top-end heat-treatment processing process |
| CN102586700A (en) * | 2012-03-05 | 2012-07-18 | 宜兴市景程模具有限公司 | High alloy tube piercing plug material and manufacturing method and surface processing method thereof |
| US20130264123A1 (en) * | 2012-04-10 | 2013-10-10 | Tenaris Connections Limited | Methods of manufacturing steel tubes for drilling rods with improved mechanical properties, and rods made by the same |
| WO2014050975A1 (en) * | 2012-09-28 | 2014-04-03 | 新報国製鉄株式会社 | Piercer plug material for producing seamless steel tube, and method for producing said material |
| CN103789685A (en) * | 2014-02-17 | 2014-05-14 | 上海海隆石油管材研究所 | High-strength high-toughness petroleum drill pipe and production method thereof |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106282782A (en) * | 2016-10-12 | 2017-01-04 | 天津钢管集团股份有限公司 | High alloy hot-puncturing process comes directly towards |
| CN106282782B (en) * | 2016-10-12 | 2018-05-25 | 天津钢管集团股份有限公司 | High alloy hot-puncturing process comes directly towards |
| CN111282996A (en) * | 2020-04-08 | 2020-06-16 | 冯永涛 | Piercing-rolling integrated four-section type composite top |
| CN112899564A (en) * | 2021-01-15 | 2021-06-04 | 常州宝菱重工机械有限公司 | Steel pipe piercing plug and preparation method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JP6385195B2 (en) | 2018-09-05 |
| KR20160022258A (en) | 2016-02-29 |
| TW201615295A (en) | 2016-05-01 |
| JP2016041844A (en) | 2016-03-31 |
| CN105369151B (en) | 2020-04-03 |
| KR102320752B1 (en) | 2021-11-02 |
| TWI648108B (en) | 2019-01-21 |
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