CN105369151B - Piercing plug for manufacturing seamless pipe - Google Patents
Piercing plug for manufacturing seamless pipe Download PDFInfo
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- CN105369151B CN105369151B CN201510509250.2A CN201510509250A CN105369151B CN 105369151 B CN105369151 B CN 105369151B CN 201510509250 A CN201510509250 A CN 201510509250A CN 105369151 B CN105369151 B CN 105369151B
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- 238000004519 manufacturing process Methods 0.000 title claims abstract description 16
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 31
- 239000000203 mixture Substances 0.000 claims abstract description 19
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 239000013078 crystal Substances 0.000 claims description 17
- 239000011159 matrix material Substances 0.000 claims description 9
- 150000001247 metal acetylides Chemical class 0.000 claims description 9
- 239000000654 additive Substances 0.000 claims description 2
- 230000000996 additive effect Effects 0.000 claims description 2
- 238000004227 thermal cracking Methods 0.000 abstract description 9
- 229910052799 carbon Inorganic materials 0.000 abstract description 6
- 229910052804 chromium Inorganic materials 0.000 abstract description 5
- 229910052721 tungsten Inorganic materials 0.000 abstract description 5
- 229910052748 manganese Inorganic materials 0.000 abstract description 4
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 4
- 229910052759 nickel Inorganic materials 0.000 abstract description 3
- 229910052758 niobium Inorganic materials 0.000 abstract description 3
- 238000011282 treatment Methods 0.000 description 25
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- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- 239000000463 material Substances 0.000 description 6
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- 230000015271 coagulation Effects 0.000 description 5
- 238000005345 coagulation Methods 0.000 description 5
- 230000006872 improvement Effects 0.000 description 5
- 229910045601 alloy Inorganic materials 0.000 description 4
- 239000000956 alloy Substances 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 229910052761 rare earth metal Inorganic materials 0.000 description 4
- 229920006395 saturated elastomer Polymers 0.000 description 4
- 239000010935 stainless steel Substances 0.000 description 4
- 229910001220 stainless steel Inorganic materials 0.000 description 4
- 229910000859 α-Fe Inorganic materials 0.000 description 4
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N Iron oxide Chemical compound [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 2
- 238000005054 agglomeration Methods 0.000 description 2
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- SZVJSHCCFOBDDC-UHFFFAOYSA-N iron(II,III) oxide Inorganic materials O=[Fe]O[Fe]O[Fe]=O SZVJSHCCFOBDDC-UHFFFAOYSA-N 0.000 description 2
- 230000003446 memory effect Effects 0.000 description 2
- 239000011148 porous material Substances 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
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- 239000010959 steel Substances 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 229910001208 Crucible steel Inorganic materials 0.000 description 1
- -1 NbC Chemical class 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
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- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000003763 carbonization Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
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- 238000007796 conventional method Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000006356 dehydrogenation reaction Methods 0.000 description 1
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- 229910052595 hematite Inorganic materials 0.000 description 1
- 239000011019 hematite Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- LIKBJVNGSGBSGK-UHFFFAOYSA-N iron(3+);oxygen(2-) Chemical group [O-2].[O-2].[O-2].[Fe+3].[Fe+3] LIKBJVNGSGBSGK-UHFFFAOYSA-N 0.000 description 1
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Articles (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention provides a piercing plug for manufacturing seamless pipes, which improves high-temperature strength and scale properties, improves ductility, toughness and thermal cracking resistance, and has a long service life. A piercing plug for seamless pipe production having an oxide scale formed on the surface thereof, characterized in that the composition of the plug other than the oxide scale contains, in mass%, C: 0.10 to 0.25%, Si: 0.05-0.80%, Mn: 0.20 to 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 to 0.40%, and Ti: 0.03 to 0.40%, and the balance Fe and unavoidable impurities, wherein the structure of the plug other than the oxide skin includes 1 to 10% of carbide and martensite.
Description
Technical Field
The present invention relates to a piercing plug for seamless pipe production used for seamless pipe production by a mannesmann piercing method, and more particularly to a piercing plug having an extended life.
Background
Oil well pipes are mainly manufactured by the mannesmann perforation method. The piercing plug used for piercing is exposed to the most severe conditions of use among the tools. In recent years, stainless steel or high alloy having high deformation resistance in a hot state has been used for seamless pipes, and the life of the piercing plug has been reduced more and more, and in an extreme case, 1-pass piercing has become the limit.
With respect to the life extension of piercing plugs, the following reports have been made: the life is improved by surface modification by PTA overlaying and arc spraying.
Patent document 1 discloses a method of forming a base material composed of Fe by arc spraying an iron wire material containing Fe as a main component on a surface of the base material3O4And a film composed of an oxide such as FeO and Fe (metal). The film can realize excellent heat insulation and heat adhesion prevention, and can provide a long-life piercing plug.
Patent document 2 relates mainly to the improvement of the material of patent document 1, and discloses a high-hardness material subjected to dehydrogenation treatment after casting.
These inventions have succeeded in extending the life of the piercing plug, but have problems such as high cost and variation in quality.
As a conventional method for prolonging the life of a piercing plug, an invention for applying scale to a surface has been reported.
Patent document 3 discloses a hot working tool having an oxide scale formed on the surface thereof. When the oxide scale is hematite, magnetite and wustite from the outer layer, the magnetite is more than 40 volume percent, the service life is prolonged.
Patent document 4 discloses a method for manufacturing a hot pipe tool capable of extending the tool life. Patent document 4 discloses: as a result, scale formed on the surface of the matrix (matrix) becomes dense due to the miniaturization of the matrix structure, and the peeling resistance and the hot adhesion resistance are improved.
Patent document 5 discloses a tool for hot pipe forming having a long service life even when a material having high deformation resistance is formed into a pipe. In patent document 5, high temperature deformability is ensured by adding a large amount of Mo and W, and peeling resistance and wear resistance of the scale are improved by Ni and W.
Patent document 6 discloses a tool for piercing and rolling a seamless steel pipe, which has a long tool life stably. In patent document 6, the scale layer formed on the substrate side is a mesh scale layer which is intricately interlaced with the steel substrate, and the structure in the range of 500 μm in the depth direction from the interface between the scale layer and the substrate side to the substrate side is a structure having a ferrite phase at an area ratio of 50% or more, whereby the peeling and abrasion of the scale layer are suppressed, and the life of the piercing-rolling tool is improved.
Prior art documents
Patent document 1: international publication No. 2009/057471
Patent document 2: international publication No. 2014/050975
Patent document 3: japanese laid-open patent publication No. 8-193241
Patent document 4: japanese laid-open patent publication No. 8-300014
Patent document 5: japanese laid-open patent publication No. 7-60314
Patent document 6: japanese patent laid-open publication No. 2003-129184
Disclosure of Invention
Many inventions have been made to extend the life of piercing plugs, but the life of piercing for stainless steel and high alloy is still unsatisfactory.
Damage to the piercing point is caused by (1) head meltdown and hot tack, and (2) body creasing and biting. In any damage, the high-temperature strength and the properties (adhesion and thickness) of the scale are affected. Further, as another damage, (3) a longitudinal crack (cracking damage) is given. In connection with this damage, ductility, toughness and thermal cracking resistance are affected.
If these 3 problems are not solved simultaneously, the life of the piercing plug cannot be extended. The present invention addresses the problem of providing a piercing plug for manufacturing seamless pipes, the piercing plug having an extended life by (1) an increase in high-temperature strength, (2) an improvement in scale properties (adhesion and thickness), (3) an improvement in ductility and toughness, and an improvement in thermal cracking resistance.
The present inventors have intensively studied a method for extending the life of a piercing plug. As a result, it has been found that selection of an appropriate composition improves hardenability (hardenability), and the structure of the plug is formed of carbides and martensite in appropriate amounts, thereby greatly improving high-temperature strength.
In the final step of manufacturing the piercing plug, a scale application treatment is performed to impart lubricity and heat insulation, and after the scale is formed, furnace cooling is performed at a cooling rate of 20 to 50 ℃/hr to prevent the scale from peeling off. The inventor finds that: by selecting an appropriate composition for precipitating carbide and causing martensitic transformation at this cooling rate, the high-temperature strength can be improved.
Further, the present inventors found that the adherence of the scale depends on the fineness of the crystal grains of the structure of the plug.
As the piercing plug, a cast steel product cast by a metal mold or a sand mold may be used. The as-cast crystal grains are relatively coarse and several hundred μm to several tens mm. In the piercing plug subjected to ferrite-pearlite transformation, coarse crystal grains are made fine by heat treatment (austenite transformation) for providing scale. However, even if the piercing plug subjected to the martensitic transformation undergoes the austenitic transformation for providing the scale, the crystal grains are still coarse due to the so-called "memory effect", and the adhesion of the scale is lowered as compared with the conventional piercing plug.
When annealing is repeated, the alloy having the composition of the present invention repeats austenite → martensite → austenite → martensite, and the crystal grains are still in the form of coarse grains of several hundred μm to several tens mm in diameter.
Fig. 1 and 2 show photographs of the grains of the piercing plug subjected to ferrite-pearlite transformation by heating and furnace cooling treatment for applying scale, and the piercing plug subjected to martensite transformation. The grain size of the ferrite-pearlite structure plug was 20 μm in size, but the grain size of the plug subjected to martensite transformation was about 500 μm in size. As a result, the scale interface area of the martensite structure plug was significantly smaller than that of the ferrite + pearlite structure plug as shown in fig. 2, and the 13Cr stainless steel piercing test using each plug also reduced the plug life from 6 passes to half, that is, 3 passes. That is, when the structure of the piercing plug is merely made martensite, the high-temperature strength can be improved, but sufficient scale adherence cannot be obtained.
In addition, when the interface area between the substrate and the scale is large in order to provide the scale, the scale has excellent adhesion. In the scale, the grain boundary is selectively oxidized in the grains of the base, and therefore, when the grains of the plug are fine, the interface area between the base and the scale increases, and as a result, the adherence of the scale is improved.
Therefore, the present inventors have intensively studied a method for refining crystal grains at the time of scale application of a plug which undergoes martensite transformation at the time of scale application. As a result, they have found that the average crystal grain size of the structure of the plug can be made fine by coarsening and agglomerating carbide before the scale is applied.
In addition, regarding ductility, toughness, and thermal cracking resistance, it is generally considered that in a piercing plug subjected to martensite transformation, ductility, toughness, and thermal cracking resistance are reduced as compared with a conventional piercing plug subjected to ferrite-pearlite transformation. However, the present inventors have found that by optimizing the amount of C and the amount of carbide, the ductility, toughness, and thermal cracking resistance can be improved as compared with conventional piercing plugs.
That is, the present invention provides a piercing plug having a long life by (1) designing a composition having a very high hardenability that undergoes martensite transformation even in furnace cooling, (2) refining crystal grains, and (3) optimizing the amount of carbon that is preferable in terms of hardenability and the amount of carbide, and the gist thereof is as follows.
(1) A piercing plug for seamless pipe production having an oxide scale formed on the surface thereof, characterized in that the composition of the plug other than the oxide scale contains, in mass%, C: 0.10 to 0.25%, Si: 0.05-0.80%, Mn: 0.20 to 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 to 0.40%, and Ti: 0.03 to 0.40%, and the balance Fe and inevitable impurities, wherein the structure of the plug other than the scale includes 1 to 10% of carbide and martensite.
(2) The piercing plug for manufacturing a seamless pipe according to the above (1), wherein the martensite structure has an average crystal grain size of 50 μm or less.
(3) The piercing plug for manufacturing a seamless pipe according to the above (1) or (2), characterized in that the piercing plug further contains, in terms of mass%, Mg: 0.001-0.100%, REM: 0.01 to 0.50%, Ca: 0.0005 to 0.0500%, Al: 0.005-0.200%, and B: 0.0001-0.0050% of 1 or more.
According to the present invention, it is possible to provide a piercing plug for manufacturing seamless pipes, which has improved ductility, toughness, and thermal cracking resistance, and has a long life, while remarkably improving high-temperature strength and scale properties (adhesion and thickness) as compared with conventional piercing plugs.
Drawings
Fig. 1 is a view showing the structure of a piercing plug in which ferrite + pearlite transformation has been performed, where (a) is the structure inside the piercing plug, and (b) is the structure at the scale interface.
Fig. 2 is a view showing the structure of the piercing plug subjected to the martensitic transformation, where (a) is the structure inside the piercing plug, and (b) is the structure at the scale interface.
Fig. 3(a) is a view showing the carbide structure of the oxidized piercing plug observed by a Scanning Electron Microscope (SEM), and (b) is a view obtained by binarizing the carbide in gray scale.
Fig. 4(a) is a view showing the structure of the scaled piercing plug after the carbide coagulation treatment, and (b) is a view showing the structure of the scaled piercing plug without the carbide coagulation treatment.
Detailed Description
The present invention will be described in detail below. First, the composition of the piercing plug of the present invention will be described. Hereinafter, the expression "%" of the component composition means "% by mass".
C is an element having a large influence on hardenability. Further, carbide is formed with Mo, W, Nb, and Cr. If the content of C is less than 0.10%, hardenability is lowered, and martensite is not obtained in cooling after the scale application treatment. If the content of C exceeds 0.25%, the amount of carbide becomes large, and the toughness and thermal crack resistance are lowered.
Si is a deoxidizing element. If the Si content is less than 0.05%, the oxygen content becomes high and the ductility is lowered. If the Si content exceeds 0.80%, the oxidation resistance is improved and the oxide scale film thickness becomes thin.
Mn is a deoxidizing element, and is an element necessary for improving hardenability together with C, Cr. In order to obtain the effect as a deoxidizing element, the content of Mn needs to be 0.20% or more. If the Mn content exceeds 1.00%, the toughness is lowered.
Ni is an element necessary for forming scale having high adhesion. If the Ni content is less than 2.5%, the irregularities at the interface between the scale and the matrix are reduced. If the Ni content exceeds 3.5%, the crystal grains are not made fine even if carbide coagulation treatment is performed.
Cr is an element for improving hardenability, similarly to C, Mn. If the Cr content is less than 1.0%, sufficient hardenability cannot be obtained. If the Cr content exceeds 2.0%, the formation of scale is suppressed and the scale thickness is insufficient.
Mo is dissolved in a matrix in a solid state to improve high-temperature strength. In addition, by forming a composite carbide M6C (M is a metal element; the same applies hereinafter) also improves the high-temperature strength. Further, the element is an element for improving hardenability, similarly to C, Cr, and Mn. If the Mo content is less than 2.5%, the hardenability-improving effect cannot be sufficiently obtained, and the high-temperature strength is also lowered. If the Mo content exceeds 3.5%, grain boundary carbides increase, and ductility and toughness deteriorate.
W is dissolved in the matrix together with Mo to improve the high-temperature strength. In addition, M is generated6Type C carbides thus improve high temperature strength. In addition, W forms a low melting point scale. If the W content is less than 2.5%, the solid solution strengthening cannot be sufficiently obtained. If the W content exceeds 3.5%, grain boundary carbides increase, and ductility and toughness deteriorate.
Nb forms MC type carbide and is solid-dissolved in the matrix to improve high temperature strength. If the content of Nb is less than 0.07%, the strengthening cannot be sufficiently obtained, and if the content of Nb exceeds 0.40%, coarse carbides are crystallized, and the toughness and ductility are lowered.
Ti is dissolved in the matrix while generating TiN, thereby improving the high-temperature strength. If the content of Ti is less than 0.03%, the strengthening cannot be sufficiently obtained, and if the content of Ti exceeds 0.40%, coarse nitrides are crystallized, and the ductility and toughness are lowered.
Mg, REM and Ca are optional additive elements, and are not essential elements, but if they are added within a predetermined range, the adhesion of the scale can be further improved. REM is a rare earth element.
If the content of Mg is less than 0.001%, the effect of improving the scale adhesion is not observed, and if the content exceeds 0.100%, the effect is saturated.
When the content of REM is less than 0.01%, the effect of improving the scale adhesion is not observed, and when the content exceeds 0.50%, the scale thickness becomes thin.
If the content of Ca is less than 0.0005%, the effect of improving the scale adhesion is not observed, and if the content exceeds 0.0500%, the effect is saturated.
Further, Al may be added in the range of 0.005 to 0.200% as a deoxidizer. The addition amount is 0.005-0.200%.
In addition, B may be added in the range of 0.0001 to 0.0050% in order to improve hardenability.
The balance of the composition is Fe and inevitable impurities. The inevitable impurities are components contained in the present invention, for example, by being originally contained in the raw materials or being mixed in during the production process, and are not intentionally added.
Among the inevitable impurities, P and S are preferably low, and preferably 0.02% or less, from the viewpoint of ductility, toughness, and thermal cracking resistance.
By defining the above-described composition, hardenability is remarkably increased, and almost martensite transformation proceeds even in a cast state.
Next, the structure and scale of the substrate will be described.
The structure of the plug is composed of 1 to 10% of carbide and a martensite structure as a base. Carbides and martensite structures increase high temperature strength and also improve ductility, toughness, and hot crack resistance. In the composition of the present invention, after an oxide skin is formed at 950 to 1100 ℃, the structure undergoes martensitic transformation by furnace cooling at 20 to 50 ℃/hr.
In the plug of the present invention, since carbide precipitates before martensite transformation, it is difficult to distinguish martensite and lower bainite by an optical microscope or hardness measurement, and lower bainite may be included in a structure called martensite.
The amount of carbide was determined by observing 5 fields at 3000 times using a Scanning Electron Microscope (SEM) to determine the area ratio. In the case of the present alloy, there are crystal carbides such as NbC, and M6C, and the like, which are precipitated during cooling. Since the crystalline carbide does not contribute to the high-temperature strength, the area ratio of the precipitated carbide was determined except for the measurement of the area ratio. An example is shown in FIG. 3. (a) Shows carbonization of the oxidized piercing plug observed by a Scanning Electron Microscope (SEM)The structure of the carbide is shown, and (b) is a graph obtained by binarizing the carbide in gray scale.
If the amount of carbide is less than 1%, the improvement of the high-temperature strength is insufficient, and if it exceeds 10%, the reduction of the toughness and ductility becomes significant.
The adhesion of the surface scale depends on the composition of the scale and its irregularities. If the crystal grains of the structure of the plug are fine, scale having high adhesion can be generated.
In the present invention, the following treatment is performed before the scale is applied to coarsen and agglomerate the carbide, so that the crystal grains of the plug can be preferably made fine to 50 μm or less.
Specifically, the plug subjected to the martensitic transformation is set at AC1Heating to 700-750 ℃ below the phase transformation point to enable M to be in contact with the metal6C、M23C6The carbide is coagulated to change martensite into a ferrite + carbide structure, and then the scale-providing treatment is performed. This eliminates the martensite memory effect, and fine austenite grains can be obtained. More specifically, at AC1Point-30 to AC1Heating at the temperature of-150 ℃ for 3-20 hours. If the heating temperature is low, the carbide is not sufficiently agglomerated, and if the heating temperature is high, it may exceed AC in actual operation1A point of phase change. If the heating time is short, the carbide is not sufficiently agglomerated, and if the heating time is long, the effect is saturated.
In FIG. 4, a photograph of a plug subjected to scale-forming treatment after treatment at 750 ℃ for 5 hours is shown together with an untreated article as an example of crystal grains subjected to carbide agglomeration treatment. The average crystal grain size in the untreated state was 87 μm, while the average crystal grain size was made fine to 12 μm by carbide agglomeration treatment.
The agglomerated carbides partially form a solid solution during the scale forming treatment, but partially remain. Since it is difficult to distinguish the remaining carbide from the carbide precipitated when the scale addition treatment is cooled by SEM observation, the area of all the carbide is measured as precipitated carbide.
Following the above treatment, a scale treatment is performed. The scale-giving treatment is performed by: heating the mixture at 950-1100 ℃ for 3-10 hours in a combustion gas atmosphere with a CO concentration of 1-8% in a furnace, and then cooling the mixture at 20-50 ℃/hour. If the CO concentration is low, the depth of the decarburized layer becomes more than 2mm, and if it is high, the thickness of the scale becomes thin. When the treatment temperature is low, the thickness of the scale becomes small, and when the treatment temperature is high, the scale containing many pores (pores) and having reduced adhesion is formed. If the treatment time is short, the oxide scale is thin, and if the treatment time is long, the thickness is saturated. When the composition is the composition of the present invention, the heating and furnace cooling result in 1 to 10% carbide and the balance martensite.
After the scale-imparting treatment, the martensite is tempered at 500 to 650 ℃, whereby the ductility, toughness and thermal cracking resistance can be further improved.
Examples
[ example 1]
A piercing plug having an outer diameter of 185mm and having a composition shown in Table 1 was cast, and then subjected to carbide coagulation treatment by heating at 700 to 750 ℃ for 5 hours in an electric furnace. In some of the comparative examples, the carbide coagulation treatment was not performed. Then, the furnace was kept at 1000 ℃ for 4 hours in a combustion gas atmosphere having a CO concentration of 1% in the furnace, and then cooled, thereby performing a scale-adding treatment.
Using the obtained piercing plug having the oxide scale formed on the surface, 13Cr stainless steel was formed into a pipe, and the life was evaluated. The results are shown in Table 2. The damage of the piercing plug of the comparative example was head fusion damage, crack damage, and wrinkles of the body, and the life was also short, but the damage of the piercing plug of the present invention was only head fusion damage, and the life was also greatly extended.
TABLE 1
TABLE 2
Claims (2)
1. A piercing plug for seamless pipe production having an oxide scale formed on the surface thereof, characterized in that,
the composition of the plug other than the oxide scale is contained in 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 to 0.40%, and
Ti：0.03~0.40%，
the balance being Fe and unavoidable impurities,
the structure of the plug other than the scale includes 1 to 10% by area of precipitated carbides and martensite as a matrix,
the martensite structure has an average crystal grain diameter of 50 [ mu ] m or less.
2. The piercing plug for manufacturing a seamless pipe according to claim 1, characterized in that the composition further contains, in mass% >, an additive
Mg：0.001~0.100%、
REM：0.01~0.50%、
Ca：0.0005~0.0500%、
Al: 0.005 to 0.200%, and
B：0.0001~0.0050%
1 or 2 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 CN105369151A (en) | 2016-03-02 |
| CN105369151B true CN105369151B (en) | 2020-04-03 |
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| JP (1) | JP6385195B2 (en) |
| KR (1) | KR102320752B1 (en) |
| CN (1) | CN105369151B (en) |
| TW (1) | TWI648108B (en) |
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| 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 |
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2014
- 2014-08-19 JP JP2014166591A patent/JP6385195B2/en active Active
-
2015
- 2015-08-11 KR KR1020150113305A patent/KR102320752B1/en active Active
- 2015-08-14 TW TW104126574A patent/TWI648108B/en active
- 2015-08-18 CN CN201510509250.2A patent/CN105369151B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| KR20160022258A (en) | 2016-02-29 |
| JP2016041844A (en) | 2016-03-31 |
| CN105369151A (en) | 2016-03-02 |
| TW201615295A (en) | 2016-05-01 |
| KR102320752B1 (en) | 2021-11-02 |
| TWI648108B (en) | 2019-01-21 |
| JP6385195B2 (en) | 2018-09-05 |
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