WO2017050227A1 - 一种高强韧性无缝钢管及其制造方法 - Google Patents
一种高强韧性无缝钢管及其制造方法 Download PDFInfo
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- WO2017050227A1 WO2017050227A1 PCT/CN2016/099561 CN2016099561W WO2017050227A1 WO 2017050227 A1 WO2017050227 A1 WO 2017050227A1 CN 2016099561 W CN2016099561 W CN 2016099561W WO 2017050227 A1 WO2017050227 A1 WO 2017050227A1
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- steel pipe
- seamless steel
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- quenching
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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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
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- 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
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- the invention relates to a pipe fitting and a manufacturing method thereof, in particular to a steel pipe and a manufacturing method thereof.
- the performance of seamless steel pipe can only be improved by adding alloying elements and controlling the offline heat treatment process after rolling.
- the 555 MPa (80 ksi) or higher level needs to obtain the corresponding seamless steel pipe by adding more alloying elements or off-line quenching and tempering treatment.
- this obviously increases the manufacturing cost of the seamless steel pipe.
- the conventional process steps of hot-rolled steel pipe is to first enter the pipe stock after rolling, and then heat treatment according to the need, which not only causes waste of waste heat after rolling of the steel pipe (usually the temperature of the steel pipe after rolling is above 900 ° C), It also brings about the complexity of the process and the increase in cost.
- offline heat treatment can not be used to strengthen the induced phase transformation effect after deformation of the material.
- the steel is directly subjected to in-line quenching after deformation, and its performance is significantly higher than that after cooling and then reheating and quenching.
- the object of the present invention is to provide a high-strength and toughness seamless steel pipe which has high strength and good toughness. Further, the seamless steel pipe according to the present invention does not add an expensive alloying element, and the alloy is economically expensive to add.
- the present invention proposes a high-strength and toughness seamless steel pipe whose chemical element mass percentage is:
- C is an important element to ensure the strength and hardenability of steel pipes.
- the C content is less than 0.1%, on the one hand, the strength of the steel is difficult to ensure, and on the other hand, it is difficult to avoid the precipitation of the pro-eutectoid ferrite, thereby affecting the sulfur resistance of the steel. Since the material is subjected to both deformation stress and tissue stress during on-line quenching, the material is more prone to cracking than off-line quenching. According to the technical solution of the present invention, controlling the C content between 0.1 and 0.25% can significantly reduce the formation of quench cracks in the seamless steel pipe.
- Si is an element brought into the steel by a deoxidizer. Once the content exceeds 0.5%, the tendency of cold and brittleness of the steel is remarkably increased, and for this reason, it is necessary to limit the Si content to 0.5% or less. At the same time, in order to ensure the deoxidation effect of the steel, it is necessary to keep the Si content in the steel at 0.1% or more.
- Al is also an element brought into the steel by a deoxidizing agent.
- a small amount of Al has a beneficial effect of refining the steel grains.
- the process steps such as tube casting and hot working may be adversely affected.
- Mn is also an element brought into the steel by a deoxidizer. Mn has a beneficial effect of expanding the austenite phase region, increasing the hardenability of the steel and refining the crystal grains. However, Mn is prone to segregation during solidification, resulting in a distinct banded structure in the seamless steel pipe. There is a significant difference between the hardness and the precipitation phase of the matrix of the banded structure and the seamless steel pipe, which in turn affects the toughness of the steel. Therefore, the high-strength toughness seamless steel pipe according to the present invention should be controlled to have a Mn content of 2.0% or less. At the same time, in order to ensure the hardenability of the steel, the Mn content in the steel should be made 0.6% or more.
- the reinforcing effect of the seamless steel pipe according to the present invention needs to be achieved by a combination of various effects such as solid solution strengthening and precipitation strengthening.
- various effects such as solid solution strengthening and precipitation strengthening.
- C In the case of no additional alloying elements, it must be guaranteed C, The Mn element has a certain content to obtain a sufficient strengthening effect. Therefore, when C and Mn satisfy the above relationship, the reinforcing effect of the steel can be effectively ensured, thereby ensuring high toughness of the steel.
- microstructure of the high-strength toughness seamless steel pipe according to the present invention is mainly martensite, and the ratio of martensite is not less than 75%.
- microstructure of the high-strength toughness seamless steel pipe according to the present invention further includes a small amount of ferrite and bainite.
- the main unavoidable impurities in the high-strength toughness seamless steel pipe according to the present invention are S, P and O.
- P and S are harmful elements in steel
- S will have adverse effects on the hot workability and toughness of steel
- P will adversely affect the hot workability and toughness of steel.
- ⁇ 0.005% P is controlled to ⁇ 0.02%.
- O is an element which lowers toughness and needs to be controlled to be 0.01% or less.
- the content of the O element is controlled to be 0.005% or less.
- the high-strength and toughness seamless steel pipe according to the present invention has a yield strength of ⁇ 555 MPa, and its full-scale impact energy of 0 ° C is >50 J.
- Another object of the present invention is to provide a method for producing a high-strength toughness seamless steel pipe.
- a seamless steel pipe having high strength and good toughness can be obtained by this manufacturing method.
- the manufacturing method of the high-strength toughness seamless steel pipe can fully utilize the residual heat after rolling, thereby effectively reducing the waste of energy consumption, thereby reducing the input cost of the process manufacturing, and the manufacturing method can also effectively avoid the cracking of the seamless steel pipe.
- a method for manufacturing a high-strength and toughness seamless steel pipe comprises the steps of:
- the cross-sectional area ratio of the tube blank to the waste pipe is greater than 4.5 (note that although only limited here)
- the lower limit of the cross-sectional area ratio of the tube blank and the waste pipe is 4.5
- the upper limit is not limited.
- the cross-sectional area ratio of the blank to the waste pipe is generally less than 10, that is, the The upper limit will be limited by the production capacity of the equipment);
- On-line quenching quenching and opening temperature is 850-1100 ° C, cooling rate is 20-60 ° C / s, and the Rockwell hardness of the steel tube after quenching is greater than 40 HRC;
- the tempering temperature is 500-700 °C.
- the core of the method for manufacturing the high-strength and toughness seamless steel pipe according to the present invention is the in-line quenching step.
- the in-line quenching is to directly quench the hot-rolled steel pipe, and the quenching in the prior art is generally off-line quenching. That is, the filled steel pipe will be first introduced into the pipe stock after rolling, and then heat treated according to the subsequent production needs, on the one hand not only causes waste of waste heat after rolling (usually the temperature of the steel pipe after rolling is above 900 ° C), on the other hand, the heat treatment process It also requires a large amount of heat energy, which greatly increases the heat energy consumption of the seamless steel pipe manufacturing method.
- the comprehensive mechanical properties of the steel after the rapid cold quenching of the hot-rolled steel pipe directly after deformation are significantly higher than the comprehensive mechanical properties of the steel which is reheated and quenched after cooling.
- the in-line quenching of the seamless steel pipe is very prone to cracking of the steel pipe. Therefore, the technical solution also strictly controls the specific process parameters of the in-line quenching, so that the manufacturing method of the present invention not only fully utilizes the post-rolling process as compared with the prior art.
- the residual heat also achieves the strengthening effect of the steel pipe through the deformation-induced phase transformation benefit of the steel pipe, preventing the cracking of the seamless steel pipe, thereby realizing the strength of the steel pipe and the steel pipe without additional expensive alloying elements. toughness.
- the quenching and cooling temperature is lower than 850 ° C, some pro-eutectoid ferrite will be formed in the steel pipe, and the required microstructure (for example, martensite structure) cannot be obtained after quenching, so Ensure that the temperature of the steel pipe is above 850 °C.
- the cooling rate is controlled between 20-60 ° C / s, because the cooling rate is slow, it is difficult to obtain the required microstructure (for example, martensite structure), and conversely, when the cooling rate is faster Since the internal stress is large after deformation of the steel pipe, it is easy to cause quenching cracking of the steel pipe.
- the tempering temperature when the tempering temperature is ⁇ 500 °C, the internal stress of the steel pipe cannot be effectively reduced, and the steel pipe has sufficient toughness, and when the tempering is stable >700 ° C, the microstructure in the steel pipe is The rate of decomposition and dislocation density (for example, martensite structure) is rapidly lowered, and for this reason, the high strength required for the steel pipe cannot be ensured, so the tempering temperature is controlled to 500 to 700 °C.
- the tube blank is heated to 1100-1250 ° C and held for 1-4 h.
- the tube blank before the tension reduction or the tension sizing step and the step of completing the tension reduction or the tension sizing step are performed.
- the cross-sectional area ratio of the subsequent blank is greater than 1.05. (It should be noted that although the lower limit of the ratio is limited to 1.05, the upper limit is not limited. However, according to the actual equipment, the upper limit of the ratio is generally about 1.3. That is to say, the upper limit value is limited by the production capacity of the equipment).
- the technical scheme of the invention fully utilizes the residual heat after rolling to realize the strengthening effect of the steel pipe by the deformation-induced phase change benefit, and saves the heat energy consumption of the production process and the steel pipe without adding expensive alloying elements.
- the comprehensive mechanical properties while also effectively avoiding cracking of steel pipes.
- the seamless steel pipe according to the present invention has high strength and a yield strength of ⁇ 555 MPa.
- the seamless steel pipe of the present invention also has high toughness, and its full-scale impact work of 0 ° C is >50 J.
- the seamless steel pipe according to the present invention is suitable for oil and gas production or pipes for mechanical structures.
- the method for manufacturing a high-strength and toughness seamless steel pipe according to the present invention can obtain a seamless steel pipe having high strength and good toughness by controlling the heat deformation amount, the quenching temperature, the cooling rate, and the tempering temperature of the steel pipe.
- the manufacturing method of the high-strength and toughness seamless steel pipe according to the present invention has simple process steps, low energy consumption, low cost and high efficiency.
- FIG. 1 is a microstructural view of a high strength and toughness seamless steel pipe according to an embodiment A7 of the present invention.
- On-line quenching uniformly spray water around the waste pipe or immerse the steel pipe in water for quenching, quenching and cooling temperature ⁇ 850 ° C, cooling rate is 20-60 ° C / s, and the Rockwell hardness of the steel pipe after quenching is greater than 40 HRC ;
- the tempering temperature is 500-700 ° C and the holding time is 1 hr.
- the key to the manufacturing method of the high-strength toughness seamless steel pipe is the steps (2) to (4), and does not mean that the manufacturing method of the high-strength toughness seamless steel pipe in the actual production process only includes the above steps, and other steps.
- the prior art in the art may be employed, and the other technical steps are not particularly limited.
- Table 1 lists the mass percentages of the respective chemical elements in the seamless steel pipes of Examples A1 to A8 and Comparative Examples B1 to B5.
- Table 2 lists specific process parameters of the manufacturing method of the seamless steel pipes of Examples A1 to A8 and Comparative Examples B1 to B5.
- the samples were subjected to mechanical properties tests, and the mechanical property parameters after the tests are shown in Table 3.
- the yield strength is obtained by processing the seamless steel pipe into an API arc sample and taking the average after the API standard test; the impact work is to process the seamless steel pipe into 10*10*55 size and V-shaped gap. Standard impact specimens, measured at 0 °C.
- Table 3 lists the relevant performance parameters of the seamless steel pipes of Examples A1 to A8 and Comparative Examples B1 to B5.
- the Mn element was too low and the value of C+Mn/6 was too low, so that the hardenability of the seamless steel pipe of Comparative Example B2 was affected, and the seamless steel pipe of Comparative Example B2 was used.
- the yield strength is only 520 MPa, indicating that the strength of the seamless steel pipe is not high and does not meet the strength requirements of the high strength and toughness seamless steel pipe of the present invention.
- the quenching temperature of the seamless steel pipe of Comparative Example B4 is too low, the pro-eutectoid ferrite is first generated in the microstructure in the steel pipe, thereby reducing the strength of the steel pipe, and the yield strength is 472 MPa.
- the cooling rate of the seamless steel tube of Comparative Example B5 is too slow, the martensite in the microstructure of the steel pipe is insufficient, and the seamless steel pipe cannot obtain sufficient strength. Therefore, the seamless steel pipe of Comparative Example B5 is obtained.
- the yield strength is only 422 MPa.
- Figure 1 shows the microstructure of the high strength toughness seamless steel pipe of Example A7.
- the microstructure of the high-strength toughness seamless steel pipe is mainly composed of martensite, and a small amount of ferrite and bainite are also present.
- the high-strength and toughness seamless steel pipe according to the present invention has low alloy addition cost and energy consumption in the manufacturing process step, and thus the production cost of the high-strength and toughness seamless steel pipe according to the present invention is more economical and has a wider application range, and can be extended to A steel pipe production line that has strict control requirements for production costs.
- the high strength and toughness seamless steel pipe according to the present invention can be used for oil and gas exploitation or mechanical structural pipes.
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Abstract
一种高强韧性无缝钢管,化学元素质量百分比为:C:0.1-0.25%,Si:0.1-0.5%,Al:0.01-0.1%,Mn:0.6-2%,余量为Fe和其他不可避免的杂质;此外还需满足:C+Mn/6≥0.35;以及一种无缝钢管的制备方法。
Description
本发明涉及一种管件及其制造方法,尤其涉及一种钢管及其制造方法。
由于无缝钢管的产品形态和制造方法的限制,长期以来仅能通过添加合金元素和控制轧后的离线热处理工艺来提升无缝钢管的产品性能。以油井管为例,555MPa(80ksi)以上级别需要通过添加较多的合金元素或离线调质处理才能获得相应的无缝钢管,然而,这样明显会增加无缝钢管的生产制造成本。
目前,热轧钢管的常规工艺步骤为轧制后先入管料库,随后再根据需要进行热处理,这种方式不仅造成了钢管轧后余热的浪费(通常轧后钢管温度在900℃以上),同时也带来了工序的复杂化和成本的增加。此外,采用离线热处理也无法利用材料形变后的诱导相变效应来进行强化,根据研究,钢材变形后直接进行在线淬火,其性能会明显高于冷却后再重新加热淬火工艺。
如上文所述的,既然本领域内技术人员已经知晓采用在线淬火可以使得无缝钢管获得更好的性能,为何现有技术仍然不采用在线淬火呢?这是因为,无缝钢管不用于一般的热轧钢管,由于其特殊的断面形状,无缝钢管相较于板材,其内应力状态更为复杂,因此若采用在线淬火工艺,一方面很难稳定控制其性能,另一方面容易造成钢管开裂。
发明内容
本发明的目的在于提供一种高强韧性无缝钢管,该无缝钢管兼具较高的强度和较好的韧性。此外,本发明所述的无缝钢管不添加昂贵的合金元素,其合金添加成本经济。
为了实现上述目的,本发明提出了一种高强韧性无缝钢管,其化学元素质量百分比为:
C:0.1-0.25%,
Si:0.1-0.5%,
Al:0.01-0.1%,
Mn:0.6-2%,
余量为Fe和其他不可避免的杂质;此外还需满足:C+Mn/6≥0.35。
本发明所述的高强韧性无缝钢管中的各化学元素的设计原理为:
碳:0.1-0.25%
C是保证钢管的强度及淬透性的重要元素。当C含量小于0.1%时,一方面钢的强度难以保证,另一方面难以避免先共析铁素体的析出,由此影响钢的抗硫性能。由于在线淬火时材料会受到变形应力及组织应力的双重影响,因此,较之于离线淬火,材料更容易出现裂纹。基于本发明的技术方案,将C含量控制在0.1-0.25%的范围之间可以明显地减少无缝钢管的淬火裂纹的形成。
硅:0.1-0.5%
Si是由脱氧剂而带入钢中的元素。一旦其含量超过0.5%时,会显著地增加钢的冷脆倾向,为此,需要将限制Si含量在0.5%以下。同时,为了保证钢的脱氧效果,需要令钢中的Si含量保持在0.1%以上。
铝:0.01-0.1%
同样地,Al也是由脱氧剂而带入钢中的元素。少量的Al具有细化钢晶粒的有益作用。可是,如果Al含量过高则会对管坯浇注、热加工等工艺步骤产生不利影响。鉴于此,需要将本发明所述的高强韧性无缝钢管中的Al含量设定为0.01-0.1%。
锰:0.6-2.0%
Mn也是由脱氧剂而带入钢中的元素。Mn具有扩大奥氏体相区,增加钢的淬透性并细化晶粒等有益作用。但是Mn在凝固时容易发生偏析,造成无缝钢管中会出现明显的带状组织。由于带状组织与无缝钢管的基体的硬度和析出相之间存在着明显的差异,继而会影响钢的韧性。因此,应当控制本发明所述的高强韧性无缝钢管中Mn含量在2.0%以下。与此同时,为了确保钢的淬透性,还应当使得钢中的Mn含量在0.6%以上。
C+Mn/6≥0.35
本发明所述的无缝钢管的强化效果需要通过固溶强化、析出强化等多种强化的综合效果来实现。在不额外添加其他合金元素的情况下,必须保证C、
Mn元素具有一定的含量,以获得足够的强化效果,因此,C和Mn满足上述关系式时能够有效地保证钢的强化效果,从而确保钢具有较高的强韧性。
进一步地,本发明所述的高强韧性无缝钢管的微观组织以马氏体为主,马氏体的相比例不低于75%。
更进一步地,本发明所述的高强韧性无缝钢管的微观组织还包括少量铁素体和贝氏体。
进一步地,在本发明所述的高强韧性无缝钢管中,其他不可避免的杂质中的S≤0.005%,P≤0.02%,O≤0.01%。
本发明所述的高强韧性无缝钢管中主要不可避免的杂质为S,P和O。其中,P和S均为钢中的有害元素,S对于钢的热加工性、韧性等都会产生不利影响,而P则会对钢的热加工性和韧性产生不利影响,为此需要将S控制得≤0.005%,将P控制得≤0.02%。O是降低韧性的元素,需要其含量控制在0.01%以下。优选地,将O元素的含量控制在0.005%以下。
进一步地,本发明所述的高强韧性无缝钢管的屈服强度≥555MPa,且其0℃全尺寸冲击功>50J。
本发明的另一目的在于提供一种高强韧性无缝钢管的制造方法。通过该制造方法能够获得强度高且韧性好的无缝钢管。该高强韧性无缝钢管的制造方法能够充分利用轧后余热,从而有效地减少了能耗的浪费,进而降低了工艺制造的投入成本,此外该制造方法还可以有效避免无缝钢管开裂。
为了达到上述发明目的,本发明所提供的一种高强韧性无缝钢管的制造方法,其依次包括步骤:
(1)冶炼并制得管坯;
(2)加热管坯,经穿孔、连轧、张力减径或张力定径制得荒管,其中管坯与荒管的横截面面积比大于4.5(需要说明的是,虽然此处仅限定了管坯与荒管的横截面面积比的下限为4.5,而没有限定其上限,然而根据实际设备情况,管坯与荒管的横截面面积比一般是达不到10以上的,也就是说该上限值会受到设备生产能力的限制);
(3)在线淬火:淬火开冷温度为850-1100℃,冷却速度20-60℃/s,淬火完成后的钢管洛氏硬度大于40HRC;
(4)回火:回火温度为500-700℃。
本发明所述的高强韧性无缝钢管的制造方法的核心在于在线淬火步骤,如前文所述的,在线淬火是将完成热轧的钢管直接进行淬火,而现有技术中的淬火一般为离线淬火,即充钢管在轧制后会先入管料库,再根据之后的生产需要进行热处理,一方面不仅造成了轧后余热的浪费(通常轧后钢管温度在900℃以上),另一方面热处理工艺又需要消耗大量的热能,这样会大幅度地提高无缝钢管的制造方法的热能消耗。而热轧钢管变形后直接进行快冷淬火后的钢材的综合力学性能要明显高于冷却后再重新进行加热淬火工艺的钢材的综合力学性能。然而无缝钢管采用在线淬火是非常容易出现钢管开裂的,因此本技术方案还严格控制了在线淬火的具体工艺参数,从而使得较之于现有技术,本发明的制造方法不仅充分利用了轧后余热,还通过钢管形变诱导相变效益实现了钢管的强化效果,防止了无缝钢管开裂,进而实现了在不额外添加昂贵合金元素的前提下,既提高了钢管的强度,又提升了钢管的韧性。
在在线淬火步骤中,如果淬火开冷温度低于850℃,钢管中将会有部分先共析铁素体生成,无法保证淬火后得到需要的微观组织(例如,马氏体组织),因此需要保证钢管温度在850℃以上。同时,将冷却速度控制在20-60℃/s范围之间,其原因在于:冷却速度较慢时,也难以得到需要的微观组织(例如,马氏体组织),反之,冷却速度较快时,由于钢管变形后内应力较大,则容易引起钢管的淬火开裂。
此外,在回火步骤中,当回火温度<500℃时,不能够有效地降低钢管的内应力,保证钢管具备足够的韧性,而当回火稳定>700℃时,由于钢管中的微观组织(例如,马氏体组织)的分解和位错密度的速度迅速降低,为此将无法保证钢管所需达到的高强度,故而,将回火温度控制为500-700℃。
进一步地,在本发明所述的高强韧性无缝钢管的制造方法中,在上述步骤(2)中,将管坯加热到1100-1250℃,并保持1-4h。
进一步地,在本发明所述的高强韧性无缝钢管的制造方法中,在上述步骤(2)中,进行张力减径或张力定径步骤之前的管坯和完成张力减径或张力定径步骤之后的管坯的横截面面积比大于1.05(需要说明的是,虽然此处仅限定了该比值的下限为1.05,而没有限定其上限,然而根据实际设备情况,该比值的上限一般在1.3左右,也就是说该上限值会受到设备生产能力的限制)。
进一步地,在本发明所述的高强韧性无缝钢管的制造方法中,在上述步骤
(3)中,向荒管周围均匀喷水或将钢管浸入水中以进行淬火。
本发明的技术方案充分利用了轧后余热,以通过形变诱导相变效益来实现钢管的强化效果,在无需添加昂贵合金元素的情况下,既节省了生产制造过程的热能消耗,又提升了钢管的综合力学性能,同时还能有效避免钢管开裂。
对于本技术方案来说,由于通过形变诱导相变效益来实现钢管的强化效果,因此,本发明所述的无缝钢管的强度高,其屈服强度≥555MPa。
另外,本发明所述的无缝钢管还具备较高的韧性,其0℃全尺寸冲击功>50J。
此外,本发明所述的无缝钢管适合于油气开采或机械结构用管。
本发明所述的高强韧性无缝钢管的制造方法通过控制钢管热变形量、淬火温度、冷却速度和回火温度,可以获得强度高且韧性好的无缝钢管。
此外,本发明所述的高强韧性无缝钢管的制造方法的工艺步骤简单、能耗省、成本低且效率高。
图1为本发明实施例A7的高强韧性无缝钢管的微观组织图。
下面将结合附图说明和具体的实施例对本发明所述的高强韧性无缝钢管及其制造方法做进一步的解释和说明,然而该解释和说明并不对本发明的技术方案构成不当限定。
实施例A1-A8和对比例B1-B5
按照下列步骤制造本发明实施例A1-A8和对比例B1-B5中的无缝钢管:
(1)冶炼并制得管坯:钢水冶炼,控制各化学元素的质量百分比如表1所示,将冶炼后的钢水直接浇注成圆管坯,或先浇注后再将铸坯锻造(或轧制)成管坯;
(2)加热管坯,经穿孔、连轧、张力减径或张力定径制得荒管:将管坯加热到1100-1250℃,并根据管坯尺寸保持1-4hr,为了保证强化效果,管坯与荒管的横截面面积比大于4.5,进行张力减径或张力定径之前的管坯和完成张力减径或张力定径之后的管坯的横截面面积比大于1.05;
(3)在线淬火:向荒管周围均匀喷水或将钢管浸入水中以进行淬火,淬火开冷温度≥850℃,冷却速度为20-60℃/s,淬火完成后的钢管洛氏硬度大于40HRC;
(4)回火:回火温度为500-700℃,保持时间1hr。
上述实施例和对比例中的无缝钢管的制造方法的具体工艺参数如表2所示,其中,在线淬火完成后的钢管的洛氏硬度采用洛氏硬度计测得。
需要说明的是,上述高强韧性无缝钢管的制造方法的关键在于步骤(2)至步骤(4),并不代表在实际生产过程中高强韧性无缝钢管的制造方法仅包括上述步骤,其他步骤采用本领域内的现有技术即可,本技术方案并不对其他步骤进行特别地限定。
表1列出了实施例A1-A8和对比例B1-B5的无缝钢管中的各化学元素的质量百分比。
表1.(wt.%,余量为Fe和除了S、P和O之外的其他不可避免的杂质元素)
表2列出了实施例A1-A8和对比例B1-B5的无缝钢管的制造方法的具体工艺参数。
表2.
对实施例A1-A8和对比例B1-B5的无缝钢管取样后,对样品进行力学性能测试,测试后的力学性能参数如表3所示。其中,屈服强度是将无缝钢管加工成API弧形试样后,按照API标准检验后取平均数后得出的;冲击功是将无缝钢管加工成10*10*55尺寸、V型缺口的标准冲击试样,在0℃下测得的。
表3列出了实施例A1-A8和对比例B1-B5的无缝钢管的相关性能参数。
表3.
序号 | 屈服强度Rp0.2(MPa) | 冲击功(全尺寸、0℃)(J) |
A1 | 590 | 118 |
A2 | 645 | 97 |
A3 | 790 | 89 |
A4 | 610 | 123 |
A5 | 708 | 130 |
A6 | 596 | 105 |
A7 | 698 | 121 |
A8 | 714 | 107 |
B1 | 705 | 35 |
B2 | 520 | 72 |
B3 | 496 | 68 |
B4 | 472 | 154 |
B5 | 422 | 165 |
结合表1和表3可以看出,由于实施例A1-A8的无缝钢管中的各化学元素质量百分比和工艺参数均在本发明的技术方案所限定的范围内,因此,实施例A1-A8的无缝钢管的屈服强度均≥590MPa且冲击功均≥89J。然而,由于对比例B1的无缝钢管中的P和S元素过高,故而,对比例B1的无缝钢管的冲击功仅为35J,说明该无缝钢管的韧性明显降低。另外,对比例B2的无缝钢管中的Mn元素过低且C+Mn/6的值也过低,因而,影响对比例B2的无缝钢管的淬透性,对比例B2的无缝钢管的屈服强度仅为520MPa,说明该无缝钢管的强度不高,并不符合本发明的高强韧性无缝钢管的强度要求。
结合表2和表3的内容可以获知,对比例B3-B5的无缝钢管中的Mn元素均超出了本发明的技术方案所限定的范围。又由于对比例B3的无缝钢管在步骤(2)中的管坯与荒管的横截面面积比和张力减径或张力定径步骤之前的管坯和完成张力减径或张力定径步骤之后的管坯的横截面面积比超出了本发明的技术方案所限定的范围,因此,影响了形变诱导相变的强化效果,从而导致钢管的强度不够,对比例B3的屈服强度仅仅为496MPa。另外,又由于对比例B4的无缝钢管的淬火温度过低致使钢管中的微观组织内先产生先共析铁素体,从而降低了钢管的强度,其屈服强度为472MPa。此外,又由于对比例B5的无缝钢管的冷却速度过慢,使得钢管的微观组织中的马氏体相比例不够,不能令无缝钢管获得足够的强度,因此,对比例B5的无缝钢管的屈服强度仅为422MPa。
综合表1,表2和表3可以知道,实施例A1-A8的无缝钢管的屈服强度均≥590MPa且冲击功均≥89J,由此表明实施例A1-A8的无缝钢管兼具较高的屈服强度和较好的韧性。
图1显示了实施例A7的高强韧性无缝钢管的微观组织。
从图1可以看出,该高强韧性无缝钢管的微观组织主要由马氏体组成,还存在少量的铁素体和贝氏体。
本发明所述的高强韧性无缝钢管的合金添加成本低且制造工艺步骤能耗省,由此本发明所述的高强韧性无缝钢管的生产成本更为经济,适用范围更广,可以推广至对于生产成本有着严格控制要求的钢管生产线。
本发明所述的高强韧性无缝钢管可以用于油气开采或机械结构用管。
需要注意的是,以上列举的仅为本发明的具体实施例,显然本发明不限于以上实施例,随之有着许多的类似变化。本领域的技术人员如果从本发明公开的内容直接导出或联想到的所有变形,均应属于本发明的保护范围。
Claims (9)
- 一种高强韧性无缝钢管,其特征在于,其化学元素质量百分比为:C:0.1-0.25%,Si:0.1-0.5%,Al:0.01-0.1%,Mn:0.6-2%,余量为Fe和其他不可避免的杂质;此外还需满足:C+Mn/6≥0.35。
- 如权利要求1所述的高强韧性无缝钢管,其特征在于,其微观组织以马氏体为主,马氏体的相比例不低于75%。
- 如权利要求2所述的高强韧性无缝钢管,其特征在于,其微观组织还包括少量铁素体和贝氏体。
- 如权利要求1所述的高强韧性无缝钢管,其特征在于,其他不可避免的杂质中的S≤0.005%,P≤0.02%,O≤0.01%。
- 如权利要求1所述的高强韧性无缝钢管,其特征在于,其屈服强度≥555MPa,且其0℃全尺寸冲击功>50J。
- 如权利要求1-5中任意一项所述的高强韧性无缝钢管的制造方法,其依次包括步骤:(1)冶炼并制得管坯;(2)加热管坯,经穿孔、连轧、张力减径或张力定径制得荒管,其中管坯与荒管的横截面面积比大于4.5;(3)在线淬火:淬火开冷温度850-1100℃,冷却速度20-60℃/s,淬火完成后的钢管洛氏硬度大于40HRC;(4)回火:回火温度为500-700℃。
- 如权利要求6所述的制造方法,其特征在于,在所述步骤(2)中,将管坯加热到1100-1250℃,并保持1-4h。
- 如权利要求6所述的制造方法,其特征在于,在所述步骤(2)中,进行张力减径或张力定径步骤之前的管坯和完成张力减径或张力定径步骤之后的管坯的横截面面积比大于1.05。
- 如权利要求6所述的制造方法,其特征在于,在所述步骤(3)中,向荒管周围均匀喷水或将钢管浸入水中以进行淬火。
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