CN102094153A - High-strength high-toughness alloy steel for bolts and preparation method thereof - Google Patents
High-strength high-toughness alloy steel for bolts and preparation method thereof Download PDFInfo
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Abstract
The invention relates to high-strength high-toughness alloy steel for bolts, which comprises the following alloy elements in percentage by mass: 0.15 to 0.23 percent of C, 0.10 to 0.35 percent of Si, 0.20 to 0.45 percent of Mn, less than or equal to 0.03 percent of P, less than or equal to 0.025 percent of S, 1.10 to 1.45 percent of Cr, 3.30 to 3.90 percent of Ni, 0.20 to 0.45 percent of Mo, less than or equal to 0.05 percent of Cu, less than or equal to 0.03 percent of Al, and the balance of Fe and impurity elements. The invention also provides a preparation method. Various mechanical property indexes of the steel are superior or equal to those of Germany 1.6772 steel; and the steel can completely meet the requirements of mechanical properties of CHTC main stud bolts and HG through bolts, and can equally or equivalently replace the Germany 1.6772 steel to be used for producing the CHTC main stud bolts and HG through bolts.
Description
Technical field
The present invention relates to a kind of high-intensity high-tenacity bolt steel alloy, relate in particular to a kind of steel alloy that is used for the high-intensity high-tenacity bolt on the high pressure water feeding pump for boiler.
Background technology
(its operating pressure is respectively 420bar and 280bar for the CHT of the German KSB company that Shanghai KSB Pumps Co., Ltd. introduce to produce and the key equipment that HG series high voltage boiler feedpump is the supercritical generating unit, working temperature reaches 230 ℃), CHTC master's threaded stud and HG rod bolt then are the vital parts of water pump packing and pressure-bearing, and its quality, Performance And Reliability play crucial effects to the safe and reliable operation of unit.CHTC master's threaded stud and HG rod bolt material are original design to be German 1.6772 trade mark steel, and its mechanical property requirements is listed in table 1 (as follows).
German 1.6772 trade mark steel mechanics performance indexs of table 1
This material relies on German import always fully, and not only cost height (a HG rod bolt cost is 10,000 yuan), and supply of material progress can not guarantee often, and the demonstration of existing data there are indications that German supplier may stop the supply of this material at any time.This not only has a strong impact on water pump production and schedule of deliveries, and may have influence on the energy security of China.
Therefore, press for that research and development are a kind of to be equal to or the production domesticization material of equivalent substitution Germany 1.6772 trade mark steel, break external blockade on new techniques, technical monopoly, step up a big step so that this type equipment of China is produced, and significantly reduce cost, be the energy security of China condition that provides safeguard.
Summary of the invention
Purpose of the present invention, provide a kind of high-intensity high-tenacity bolt steel alloy at the problems referred to above exactly, this steel alloy interalloy constituent content requires lower, the content of particularly more rare important strategic material Ni, Mo is also all lower, but this steel alloy can satisfy CHTC master's threaded stud and HG rod bolt mechanical property requirements fully.
Another object of the present invention is to provide the preparation method of a kind of above-mentioned high-intensity high-tenacity bolt with steel alloy.
The used in order to reach the goal technical scheme of the present invention is:
A kind of high-intensity high-tenacity bolt steel alloy of one of the present invention comprises following alloying element according to mass percent:
0.15～0.23C; 0.10～0.35 Si; 0.20～0.45Mn; P≤0.03; S≤0.025; 1.10～1.45Cr; 3.30～3.90Ni; 0.20～0.45Mo; Cu≤0.05; Al≤0.03, all the other are Fe and impurity element.
Above-mentioned high-intensity high-tenacity bolt steel alloy comprises following alloying element according to mass percent:
0.19～0.21C; 0.20～0.32 Si; 0.32～0.40 Mn; P≤0.025; S≤0.015; 1.25～1.40Cr; 3.50～3.85Ni; 0.30～0.40Mo; Cu≤0.03; Al≤0.02, all the other are Fe and impurity element.
The present invention's two a kind of above-mentioned high-intensity high-tenacity bolt may further comprise the steps with the preparation method of steel alloy:
1) vacuum induction furnace smelting: according to chemical composition require batching, after furnace charge all melts clearly, at 1540～1560 ℃ of refining 40min, take a sample behind the insulation 20min, behind the analysis composition, adjust composition, fusing 5～10min, the casting electrode rod, tapping temperature is 1560～1580 ℃;
2) esr: with the electrode bar remelting in the step 1, teeming;
3) forge: the steel ingot in the step 2 is forged, opens forging temperature 〉=1050 ℃, final forging temperature 〉=850 ℃, forging deformation amount 〉=30%, forge the back slowly cool to room temperature anneal 680 ℃ of annealing temperatures, soaking time 2～3h again;
4) thermal treatment: the material after forging in the step 3 is heat-treated 800～890 ℃ of quenching temperatures, 420～550 ℃ of tempering temperatures, tempering time 40～190min.
High-intensity high-tenacity bolt of the present invention with the chemical composition design of steel alloy according to and limit the reasons are as follows of content range:
C is the element that improves material hardening capacity strongly, improves the intensity and the hardness of material simultaneously.But, can reduce the material toughness plasticity greatly with the increase of C content, make material that brittle rupture easily take place.When C content is low, can form toughness plasticity material preferably, but its hardening capacity and insufficient strength.Deficiency on the strength of materials can be by alloying element solution strengthening and precipitation strength wait and remedy, but be not easy to improve for the flexible deficiency.Take all factors into consideration, the C content of material should be controlled at low carbon levels, and the intensity that increases the low-carbon (LC) toughness material is main technological route of the present invention.
The avidity of Si and oxygen is only second to Al and Ti, and is better than Mn, Cr and V.Si does not form carbide in steel, but is present among α (ferrite) or the γ (austenite) with the form of sosoloid.It is extremely strong that Si improves the effect of sosoloid intensity in the steel, but also reduce the toughness plasticity of steel simultaneously to a certain extent.Si is one of element of sealing γ phase region, improves the critical transition temperature A of steel
1And A
3Si is medium to the hardening capacity influence of steel, but temper resistance and the oxidation-resistance that improves steel had very big benefit.The steel that Si content is higher, also decarburization easily of surface during annealing.
Mn is good reductor and sweetening agent, can eliminate or weaken because of S caused red brittleness, thereby improves the hot workability of steel.Mn and Fe form sosoloid, hardness and the intensity of α and γ in the raising steel.Mn is again a carbide forming element, enters to replace a part of Fe atom in the cementite.Mn when improving alloy strength, to its ductility but almost without any influence.Mn enlarges the γ phase region, steel is formed and the ability of stablizing the γ tissue is only second to Ni, and Mn also increases the hardening capacity of steel strongly.The unfavorable one side of Mn is the superheated susceptivity that increases steel, and crystal grain is easily thick, and easily increases temper brittleness, smelts the improper steel that makes easily of casting and forging rolling postcooling and produces white point.
S, P are deleterious relict elements in the steel, and S in the domestic raw materials, P content are higher relatively, so take all factors into consideration from the performance and the cost of steel, should suitably limit the content of S, P.
Cr can significantly improve the antioxidant property of steel, increases the resistance to corrosion of steel.Cr and Fe form continuous solid solution, form multiple carbide with C, and the avidity of Cr and C greater than Fe and Mn, and is lower than W, Mo etc. in the various element of formation carbide.Cr can replace a part of Fe and form compound cementite (Fe, Cr)
3C.The complicated carbide of Cr (Cr, Fe)
7C
3, (Cr, Fe)
23C
6Performance for steel has remarkable influence.Cr can significantly increase the hardening capacity of steel, but also increases the temper brittleness tendency of steel.When Cr and C form complicated carbide, and when disperse is separated out in steel, can play dispersion-strengthened action.But Cr also makes plasticity decrease when playing strengthening effect in steel, and increases temper brittleness.Therefore need to determine appropriate C r content according to requirement to obdurability.
Ni and C do not form carbide, and Ni is the main alloy element of formation and stable γ.Ni and Fe with the form of dissolving each other be present in the steel α mutually with γ mutually in, make it to strengthen, and the crystal grain by refinement α phase, improve the low-temperature performance, particularly toughness of steel.Ni is owing to each elemental diffusion speed in reduction critical transition temperature and the steel, thereby the hardening capacity of raising steel.And Ni is also not obvious to the toughness plasticity influence of steel in the solution strengthening steel strength.Because Ni worldwide is a kind of more rare element, also is a kind of important strategic material.Therefore as a kind of alloying element of steel, must be noted that rationally and the principle of saving.
Mo belongs to the element that dwindles the γ phase region, and it is present in steel in sosoloid phase and the carbide.In carbide, when Mo content is low, form the compound cementite with Fe and C; When content is higher, then form its oneself alloy carbide.Mo can significantly improve the hardening capacity of steel, can also improve the recrystallization temperature of steel simultaneously, strengthens temper resistance, can obtain the compact grained sorbite after the modifier treatment, and the obdurability of steel is improved.When forming the carbide of Mo in the steel, can play the effect of disperse or precipitation strength, Mo content is (＜0.3%) more after a little while, mainly based on solution strengthening, raising hardening capacity and temper resistance.With the increase of Mo content, the obdurability of steel is improved.The effect of Mo in steel can reduce and improve hardening capacity, improve heat resistance, prevent temper brittleness, improve the corrosion stability in some medium and prevent spot corrosion tendency etc.But Mo is a kind of important strategic material, and other has epochmaking purposes, therefore uses in steel, must be noted that rationally and few as much as possible using.
Cu also is the relict element in the steel, although Cu is useful and harmless to the mechanical property of steel, it is unfavorable that the forge hot of steel is rolled with hot workabilitys such as thermal treatments, is the main element that causes hot tearing.Moreover Cu content is higher relatively in the domestic raw materials, need be controlled.
Al is the element that dwindles the γ phase region strongly, with O, N very big avidity is arranged.The effect of Al in steel is that the nitrogen agent is decided in the deoxidation during as steel-making, and crystal grain thinning, the timeliness of preventing soft steel can alleviate the susceptibility of steel to breach, and improves the impelling strength of steel, reduce the brittle transition temperature of steel, but lax unfavorable to resisting of steel with creep-resistant property.And in the steel during deoxidation Al consumption too much, will make steel produce abnormal structure, and promote the greying tendency of steel.In ferrite and perlitic steel, to measure when higher when containing Al, its intensity and toughness are lower, and give and smelt and difficulty is brought in aspects such as casting.Though the essential crystal grain of Al refinement steel improves the temperature of crystalline grain of steel alligatoring, when the remaining aluminium in the steel (solid solution metallic aluminium) content during above certain value, the alligatoring of easily growing up all the better of the austenite crystal of steel.Therefore need the residual quantity of control Al in steel.
A kind of high-intensity high-tenacity bolt of the present invention requires lower with the alloying element content of steel alloy, the content of particularly more rare important strategic material Ni, Mo is also all lower, and every mechanical performance index all is better than or equals the mechanical performance index (asking for an interview table 2) of German 1.6772 trade mark steel, has reached international most advanced level.
Table 2 high-intensity high-tenacity bolt steel alloy mechanical performance index of the present invention:
A kind of high-intensity high-tenacity bolt of the present invention can satisfy CHTC master's threaded stud and HG rod bolt mechanical property requirements fully with steel alloy, can be equal to or equivalent substitution Germany 1.6772 trade mark steel are used to produce CHTC master's threaded stud and HG rod bolt, thereby break external blockade on new techniques, technical monopoly, this type equipment of China is produced stepped up a big step, and significantly reduce cost, be the energy security of China condition that provides safeguard.
Embodiment
Below in conjunction with embodiment the present invention is further described:
Embodiment 1
Present embodiment chemical ingredients (wt%) as shown in the table:
| Element | C | Si | Mn | P | S | Cr |
| Content | 0.19 | 0.24 | 0.39 | 0.006 | 0.0016 | 1.34 |
| Element | Ni | Mo | Cu | Al | ||
| Content | 3.65 | 0.34 | 0.01 | 0.018 |
Employing is prepared as follows the metallic substance of explained hereafter:
1) vacuum induction furnace smelting: by chemical ingredients requirement batching in the last table, furnace charge all molten clear after, at 1550 ℃ of refining 40min, sampling is one behind the insulation 20min, analyze composition after, adjust composition, fusing 8min, casting
Electrode bar, tapping temperature are 1570 ℃.
2) esr: with in the above-mentioned steps
The electrode bar remelting, casting
Steel ingot.
3) forge: the steel ingot in the above-mentioned steps is forged, open 1080 ℃ of temperature, 870 ℃ of final forging temperatures, the forging deformation amount 35% of forging.Forge the slow cool to room temperature in back and anneal 680 ℃ of annealing temperatures, soaking time 2.5h again.
4) thermal treatment: the material after forging is heat-treated, and 860 ℃ of quenching temperatures adopt oil quenching to handle, 450 ℃ of tempering temperatures, and tempering time 120min adopts air cooling to handle to room temperature.
The mechanical property of present embodiment is as shown in the table:
The present embodiment chemical ingredients is detected according to GB/T20123-2006 and GB/T20125-2006 by quality inspection portion of Golconda branch office of Shanghai Baosteel Industry Inspection Corp. and obtains, and its mechanical property is detected according to GB/T 228-2002 by national ferrous materials test center and obtains.
Embodiment 2
Present embodiment chemical ingredients (wt%) as shown in the table:
| Element | C | Si | Mn | P | S | Cr |
| Content | 0.21 | 0.21 | 0.37 | 0.0072 | 0.003 | 1.36 |
| Element | Ni | Mo | Cu | Al | ||
| Content | 3.78 | 0.33 | 0.001 | 0.014 |
Employing is prepared as follows the metallic substance of explained hereafter:
1) vacuum induction furnace smelting: by chemical ingredients requirement batching in the last table, furnace charge all molten clear after, at 1550 ℃ of refining 40min, sampling is one behind the insulation 20min, analyze composition after, adjust composition, fusing 8min, casting
Electrode bar, tapping temperature are 1570 ℃.
2) esr: with in the above-mentioned steps
The electrode bar remelting, casting
Steel ingot.
3) forge: the steel ingot in the above-mentioned steps is forged, open 1080 ℃ of temperature, 870 ℃ of final forging temperatures, the forging deformation amount 31% of forging.Forge the slow cool to room temperature of back material and anneal 680 ℃ of annealing temperatures, soaking time 2.5h again.
4) thermal treatment: the material after forging is heat-treated, and 850 ℃ of quenching temperatures adopt oil quenching to handle, 480 ℃ of tempering temperatures, and tempering time 70min adopts air cooling to handle to room temperature.
The mechanical property of present embodiment is as shown in the table:
Embodiment 3
Present embodiment chemical ingredients (wt%) as shown in the table:
| Element | C | Si | Mn | P | S | Cr |
| Content | 0.18 | 0.22 | 0.35 | 0.012 | 0.0045 | 1.40 |
| Element | Ni | Mo | Cu | Al | ||
| Content | 3.68 | 0.35 | 0.007 | 0.012 |
Employing is prepared as follows the metallic substance of explained hereafter:
1) vacuum induction furnace smelting: by chemical ingredients requirement batching in the last table, furnace charge all molten clear after, at 1550 ℃ of refining 40min, sampling is one behind the insulation 20min, analyze composition after, adjust composition, fusing 8min, casting
Electrode bar, tapping temperature are 1570 ℃.
2) esr: with in the above-mentioned steps
The electrode bar remelting, casting
Steel ingot.
3) forge: the steel ingot in the above-mentioned steps is forged, open 1080 ℃ of temperature, 870 ℃ of final forging temperatures, the forging deformation amount 32% of forging.Forge the slow cool to room temperature of back material and anneal 680 ℃ of annealing temperatures, soaking time 2.5h again.
4) thermal treatment: the material after forging is heat-treated, and 880 ℃ of quenching temperatures adopt oil quenching to handle, 500 ℃ of tempering temperatures, and tempering time 45min adopts air cooling to handle to room temperature.
The mechanical property of present embodiment is as shown in the table:
Embodiment 4
Present embodiment chemical ingredients (wt%) as shown in the table:
| Element | C | Si | Mn | P | S | Cr |
| Content | 0.17 | 0.29 | 0.30 | 0.01 | 0.007 | 1.15 |
| Element | Ni | Mo | Cu | Al | ||
| Content | 3.36 | 0.22 | 0.035 | 0.003 |
Employing is prepared as follows the metallic substance of explained hereafter:
1) vacuum induction furnace smelting: by chemical ingredients requirement batching in the last table, furnace charge all molten clear after, at 1550 ℃ of refining 40min, sampling is one behind the insulation 20min, analyze composition after, adjust composition, fusing 8min, casting
Electrode bar, tapping temperature are 1570 ℃.
2) esr: with in the above-mentioned steps
The electrode bar remelting, casting
Steel ingot.
3) forge: the steel ingot in the above-mentioned steps is forged, open 1080 ℃ of temperature, 870 ℃ of final forging temperatures, the forging deformation amount 30% of forging.Forge the slow cool to room temperature of back material and anneal 680 ℃ of annealing temperatures, soaking time 2.5h again.
4) thermal treatment: the material after forging is heat-treated, and 820 ℃ of quenching temperatures adopt oil quenching to handle, 470 ℃ of tempering temperatures, and tempering time 100min adopts air cooling to handle to room temperature.
The mechanical property of present embodiment is as shown in the table:
Embodiment 5
Present embodiment chemical ingredients (wt%) as shown in the table:
| Element | C | Si | Mn | P | S | Cr |
| Content | 0.20 | 0.21 | 0.38 | 0.008 | 0.0062 | 1.29 |
| Element | Ni | Mo | Cu | Al | ||
| Content | 3.81 | 0.24 | 0.04 | 0.006 |
Employing is prepared as follows the metallic substance of explained hereafter:
1) vacuum induction furnace smelting: by chemical ingredients requirement batching in the last table, furnace charge all molten clear after, at 1550 ℃ of refining 40min, sampling is one behind the insulation 20min, analyze composition after, adjust composition, fusing 8min, casting
Electrode bar, tapping temperature are 1570 ℃.
2) esr: with in the above-mentioned steps
The electrode bar remelting, casting
Steel ingot.
3) forge: the steel ingot in the above-mentioned steps is forged, open 1080 ℃ of temperature, 870 ℃ of final forging temperatures, the forging deformation amount 34% of forging.Forge the slow cool to room temperature of back material and anneal 680 ℃ of annealing temperatures, soaking time 2.5h again.
4) thermal treatment: the material after forging is heat-treated, and 840 ℃ of quenching temperatures adopt oil quenching to handle, 460 ℃ of tempering temperatures, and tempering time 90min adopts air cooling to handle to room temperature.
The mechanical property of present embodiment is as shown in the table:
This shows, the every mechanical performance index of the present invention all is better than or equals the mechanical performance index of German 1.6772 trade mark steel, can satisfy CHTC master's threaded stud and HG rod bolt mechanical property requirements fully, can be equal to or equivalent substitution Germany 1.6772 trade mark steel are used to produce CHTC master's threaded stud and HG rod bolt.
Above embodiment is only for the usefulness that the present invention is described, but not limitation of the present invention, person skilled in the relevant technique, under the situation that does not break away from the spirit and scope of the present invention, can also make various conversion or modification, therefore all technical schemes that are equal to also should belong to category of the present invention, should be limited by each claim.
Claims (3)
1. high-intensity high-tenacity bolt steel alloy comprises following alloying element according to mass percent:
0.15～0.23C; 0.10～0.35Si; 0.20～0.45Mn; P≤0.03; S≤0.025; 1.10～1.45Cr; 3.30～3.90Ni; 0.20～0.45Mo; Cu≤0.05; Al≤0.03, all the other are Fe and impurity element.
2. high-intensity high-tenacity bolt steel alloy as claimed in claim 1 comprises following alloying element according to mass percent:
0.19～0.21C; 0.20～0.32Si; 0.32～0.40Mn; P≤0.025; S≤0.015; 1.25～1.40Cr; 3.50～3.85Ni; 0.30～0.40Mo; Cu≤0.03; Al≤0.02, all the other are Fe and impurity element.
One kind according to claim 1 the high-intensity high-tenacity bolt may further comprise the steps with the preparation method of steel alloy:
1) vacuum induction furnace smelting: according to chemical composition require batching, after furnace charge all melts clearly, at 1540～1560 ℃ of refining 40min, take a sample behind the insulation 20min, behind the analysis composition, adjust composition, fusing 5～10min, the casting electrode rod, tapping temperature is 1560～1580 ℃;
2) esr: with the electrode bar remelting in the step 1, teeming;
3) forge: the steel ingot in the step 2 is forged, opens forging temperature 〉=1050 ℃, final forging temperature 〉=850 ℃, forging deformation amount 〉=30%, forge the back slowly cool to room temperature anneal 680 ℃ of annealing temperatures, soaking time 2～3h again;
4) thermal treatment: the material after forging in the step 3 is heat-treated 800～890 ℃ of quenching temperatures, 420～550 ℃ of tempering temperatures, tempering time 40～190min.
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|---|---|---|---|
| CN2011100496982A CN102094153B (en) | 2011-03-02 | 2011-03-02 | Preparation method of high-strength high-toughness alloy steel for bolts |
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|---|---|---|---|
| CN2011100496982A CN102094153B (en) | 2011-03-02 | 2011-03-02 | Preparation method of high-strength high-toughness alloy steel for bolts |
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| CN103643166A (en) * | 2013-11-12 | 2014-03-19 | 铜陵市肆得科技有限责任公司 | High temperature-resistant pump case alloy steel material and preparation method thereof |
| CN103753115A (en) * | 2011-12-31 | 2014-04-30 | 东莞市飞新达精密机械科技有限公司 | Method for machining plate type part with long open groove |
| CN103820712A (en) * | 2014-03-13 | 2014-05-28 | 国家电网公司 | High-strength bolting steel and preparation method thereof |
| CN103820726A (en) * | 2014-03-17 | 2014-05-28 | 河南赛诺米特种设备有限公司 | Method for manufacturing bolts with relatively high fatigue strength |
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| CN104178601A (en) * | 2014-08-17 | 2014-12-03 | 成都亨通兆业精密机械有限公司 | Surface hardening method for bolt |
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| CN103753115A (en) * | 2011-12-31 | 2014-04-30 | 东莞市飞新达精密机械科技有限公司 | Method for machining plate type part with long open groove |
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| CN103820726A (en) * | 2014-03-17 | 2014-05-28 | 河南赛诺米特种设备有限公司 | Method for manufacturing bolts with relatively high fatigue strength |
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| CN104164629A (en) * | 2014-07-25 | 2014-11-26 | 合肥市瑞宏重型机械有限公司 | High-manganese heat-resistant alloy steel and manufacturing method thereof |
| CN104178601A (en) * | 2014-08-17 | 2014-12-03 | 成都亨通兆业精密机械有限公司 | Surface hardening method for bolt |
| CN105506496A (en) * | 2014-09-24 | 2016-04-20 | 上海宝钢工业技术服务有限公司 | High-strength prestressing force bolt production method |
| CN105937015A (en) * | 2016-06-07 | 2016-09-14 | 江苏百德特种合金有限公司 | High-strength bolt and preparation method thereof |
| CN106148663A (en) * | 2016-07-06 | 2016-11-23 | 常熟市常力紧固件有限公司 | A kind of Technology for Heating Processing of automobile tire high rigidity bolt |
| CN108374124A (en) * | 2018-03-29 | 2018-08-07 | 冯满 | A kind of steel alloy |
| CN108531815A (en) * | 2018-05-24 | 2018-09-14 | 本钢板材股份有限公司 | High temperature bolt steel BG25Cr2MoVA and preparation method thereof |
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