CN105803353A - Hot-rolled wire rod for preparation of 21-10Mn7Mo welding wire - Google Patents
Hot-rolled wire rod for preparation of 21-10Mn7Mo welding wire Download PDFInfo
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Abstract
The invention discloses a hot-rolled wire rod for preparation of a 21-10Mn7Mo welding wire, belongs to the technical field of welding and relates to a preparation method of a solid welding wire for gas protection arc welding. The invention relates to a hot rolling process and a forging process. The hot-rolled wire rod comprises, by mass, less than or equal to 0.10% of C, less than or equal to 0.8% of Si, 5.5-8.0% of Mn, less than or equal to 0.030% of P, less than or equal to 0.020% of S, 9.0-11.0% of Ni, 19.0-22.0% of Cr and 0.5-2.0% of Mo. A ratio of Mn/Mo is 7-7.5. The forging process comprises heating a blank under condition of an initial forging temperature greater than or equal to 1180 DEG C and a final forging temperature greater than or equal to 850 DEG C. In the hot rolling process of a hot-rolled wire rod, a pre-heating temperature is controlled in a range of 650-750 DEG C in heating.
Description
Technical field
This case belongs to welding technology field, relates to the preparation method of the solid core welding wire of gas shielded arc welding and intermediate maturity thereof and finished product and process equipment thereof.Relate to method and the gren rod thereof of hot rolling.
Background technology
The application in automatic technology of stainless steel welding stick, welding rod gets more and more, but to be welding wire outward appearance bad, wire feed is not sufficiently stable for the common quality problems of the stainless steel welding stick prepared of prior art, therefore, it is difficult to meet the requirement of high automatic welding equipment.
Generally known, the slight change of the chemical composition that Quality of Final Welding Wire and steel-making cause has close relation, close relation is had, it is important that process prepared by welding wire and process equipment are related to the quality of the semi-finished product of welding wire, finished product with the impurity content of material composition.Doing a lot of effort in this respect for this industry, prior art includes but not limited to:
As Chinese patent 200710093859.1 discloses a kind of austenitic stainless steel as-forged solid solution treatment process after forging, in Forging Technology, initial forging temperature is 1100 DEG C～1200 DEG C, final forging temperature is be more than or equal to 850 DEG C, the forging ratio of forging is more than or equal to 3, and the forging deflection of last fire time is more than or equal to 20%；Stove heating is entered immediately after Forging Technology, as quickly as possible temperature is risen to solutionizing temperature 1000 DEG C～1100 DEG C, is then incubated 1～4 hour, then forging is come out of the stove and immediately enters water tank and be cooled to room temperature, solid solution treatment process terminates, and roughing after carrying out, sampling, Physicochemical test step.This invention austenitic stainless steel as-forged solid solution treatment process after forging makes solid solution craft start after forging at once, and it is rapidly heated, it is simple to operate, with low cost, process-cycle is short, energy resource consumption is few, and when heavy in section, large-tonnage Austenitic stainless steel forging are carried out solutionizing process, grain size is not grown up.
Having Chinese patent 200910052322.X to disclose a kind of stainless preparation method again, the step of the method includes: raw material and converter are cleaned and dry by (1)；(2) being put in converter by raw material, and add the nonmagnetic steel deoxidizer of raw-material weight 1-2%, high temperature melting is smelt molten steel, and nonmagnetic steel deoxidizer is discharged with the nonmetal formation slag liquid in molten steel；(3) molten steel step (2) obtained puts into vacuum degassing furnace and carries out vacuum outgas, makes the oxygen content≤20ppm in molten steel, hydrogen content≤3ppm, then cast, forging, solid molten and stabilizing treatment so that it is homogenizing, obtains product.Ultra-low carbon non-magnetic rustproof steel chemical composition prepared by this inventive method, it is desirable to contribute to some extent in mechanical property and permeability.
Further, Chinese patent 200910223502.X discloses one and is suitable for aging martensitic stainless steel welding wire.The percentage by weight of the chemical composition of this welding wire is C0.01-0.09, Si0.2-0.6, Mn0.2-1.0, P≤0.025, S≤0.025, Cr14-17, Ni4.2-5.8, Cu3.0-4.0, Nb0.1-0.5, and Mo≤0.75 is remaining for Fe.This invention welding wire is used for welding 15-5PH aging martensitic stainless steel can avoid formation ferrite net in weld seam martensitic structure, makes joint plasticity and toughness be maintained, is also equipped with excellent weldability simultaneously, can be prevented effectively from HOT CRACK FOR WELDING P.Through complete heat treatment after this invention welding wire welding 15-5PH rustless steel, it is desirable to there is good combination property, be suitable for aircraft industry and the gas shielded arc welding of other industrial circle aging martensitic stainless steels.
For another example Chinese patent 200510109991.8 discloses solid wire for gas shielded arc welding.
And for example Chinese patent 200310100196.3 discloses a kind of high strength electrode.
As Chinese patent 200710103490.8 discloses a kind of solid core welding wire.
Also has prior art H1Cr21Ni10Mn6 welding wire, it is mainly used in the automatic welding such as heavy type, oversize vehicle, this case is also the further improvement as Developed Background, purpose is in that to improve further the tensile strength of welding wire, improve the tensile strength of its deposited metal, also include but not limited to for this following open:
As Chinese patent 201110104281.1 discloses a kind of welding wire, wire rod and application thereof, it relates to wire rod and welding wire.
It is urgently to be resolved hurrily to there is following problems in existing technology.
Forging problem, because of the impact by material composition, what kind of process is forging link adopt, it is directly connected to the tissue producing into forging stock and whether performance is good, industry urgently provides a kind of Forging Technology for this case welding wire and forging stock thereof, to improve tensile strength and the yield strength of welding wire, the welding wire for postorder is processed and the quality of welding wire finished product provides safeguard.
This case welding wire is the innovation on the basis of existing H1Cr21Ni10Mn6 welding wire, including adding appropriate Mo, it is correspondingly improved the content of Mn simultaneously, it has a problem in that the production in later stage can be brought difficulty in process by the change of thus material composition, generally known, molybdenum content in steel alloy is when certain limit, and molybdenum can make the plasticity of steel alloy and toughness decline, and therefore industry urgently solves such problem by including the improvement of the process of forging.
The reason of the existing component of technology reason welding wire, the preparation method of welding wire and process equipment, it is impossible to well overcome above-mentioned problem.
Summary of the invention
To be solved by this invention it has a problem in that the drawbacks described above overcoming aforementioned techniques to exist, and a kind of gren rod for preparing 21-10Mn7Mo welding wire is provided, wherein, for the blank that hot rolling processes, its chemical composition quality % includes: carbon C≤0.10, silicon Si≤0.8, manganese Mn5.5-8.0, phosphorus P≤0.030, sulfur S≤0.020, nickel 9.0-11.0, chromium Cr19.0-22.0, molybdenum Mo0.5-2.0；Mn/Mo ratio controls at 7-7.5；
Or, described blank chemical composition quality % is by carbon C≤0.10, silicon Si≤0.8, manganese Mn5.5-8.0, phosphorus P≤0.030, sulfur S≤0.020, nickel 9.0-11.0, chromium Cr19.0-22.0, molybdenum Mo0.5-2.0, and surplus is ferrum Fe and inevitable impurity composition；Mn/Mo ratio controls at 7-7.5；
Wherein, the forging step preparing described blank includes: the step of blank heating, and wherein, the charging temperature of blank controls at≤850 DEG C；
Wherein, preparing and control heat time heating time in the forging step of described blank, heat time heating time answers coincidence formula: T=aD；In formula, T refers to heating total time (min)；A refers to the coefficient relevant with size, steel grade；D refers to blank diameter or the length of side (mm)；Wherein, the coefficient a value in calculating heating total time is 0.7.
Or/and, wherein, the control of forging temperature: initial forging temperature is >=1180, final forging temperature is >=850.
The processing step of gren rod includes the step of heating, and in the step of described heating, preheating temperature controls as 650-750 DEG C；Heating and temperature control is 1180-1220 DEG C；Heat time heating time controlled as 3.5-4 hour；Finishing temperature control is >=900 DEG C；The Control for Kiln Temperature of warm-up phase is at 800 DEG C-850 DEG C.
It is previously used for preparing the gren rod of 21-10Mn7Mo welding wire, wherein, the Control for Kiln Temperature in heating and soaking stage: when keeping higher furnace temperature, be heated rapidly to initial forging temperature.
Being previously used for preparing the gren rod of 21-10Mn7Mo welding wire, wherein, the forging hammer weight dynamics control of the steel ingot forging heating is: during beginning, when the steel ingot deflection forged is not up to 30%, for light forging；After the steel ingot deflection forged reaches 30%, for weight or forging of weighing, the control heavily forged is: must not in place double hit more than three hammers.
It is previously used for preparing the gren rod of 21-10Mn7Mo welding wire, wherein, in the step of described forging molding, by the steel control of turning over forging steel ingot is: during forging, being forged steel ingot should overturn to same direction, should overturn 90 ° every time；When forging, drafts controls as uniformity.
Being previously used for preparing the gren rod of 21-10Mn7Mo welding wire, wherein, in the step of described forging molding, the forging ratio of molding forging stock part is 4～6.
Being previously used for preparing the gren rod of 21-10Mn7Mo welding wire, wherein, the step of described forging molding, wherein, forging deformation amount controls as more than 12%-20%.
Being previously used for preparing the gren rod of 21-10Mn7Mo welding wire, wherein, the step of described forging molding, wherein, the step of forging cutting, temperature controls to be not less than at the temperature of 800 DEG C and carries out；
Or/and, wherein, the step of forging cutting in the step of forging molding, wherein, just forging size includes but not limited to that Ф 135*650mm, finish-forging size include but not limited to 45*45* (800～1200) mm；
Or/and, wherein, it is swaged into square billet size and includes but not limited to 90-180mm.
The aforementioned gren rod preparing 21-10Mn7Mo welding wire, wherein, in the step of rolling, is rolled into wire rod and is of a size of Ф 5.5mm.
The aforementioned gren rod preparing 21-10Mn7Mo welding wire, wherein, the step of cooling, adopt natural cooling in air.
The aforementioned gren rod preparing 21-10Mn7Mo welding wire, wherein, the step of finishing, coil rapidly, thinning surface defect.
The drawbacks described above overcoming aforementioned techniques to exist that has a problem in that to be solved by this invention, and the forging method of a kind of 21-10Mn7Mo welding wire and the forging stock part prepared by the method are provided, and prepare forging stock part and the hot-rolling method of 21-10Mn7Mo welding wire.
This invention address that and technical problem is that and take techniques below scheme to realize, according to a kind of forging stock part preparing 21-10Mn7Mo welding wire provided by the invention, wherein, described forging stock part chemical composition quality % includes: carbon C≤0.10, silicon Si≤0.8, manganese Mn5.5-8.0, phosphorus P≤0.030, sulfur S≤0.020, nickel 9.0-11.0, chromium Cr19.0-22.0, molybdenum Mo0.5-2.0；Mn/Mo ratio controls at 7-7.5.
This case solution technical problem may also take on techniques below scheme and realizes further:
The aforesaid forging stock part preparing 21-10Mn7Mo welding wire, wherein, described forging stock part chemical composition quality % is by carbon C≤0.10, silicon Si≤0.8, manganese Mn5.5-8.0, phosphorus P≤0.030, sulfur S≤0.020, nickel 9.0-11.0, chromium Cr19.0-22.0, molybdenum Mo0.5-2.0, and surplus is ferrum Fe and inevitable impurity composition.
The aforesaid forging stock part preparing 21-10Mn7Mo welding wire, wherein, in forging stock part chemical composition, Mn/Mo ratio controls at 7-7.5.
The aforesaid forging stock part preparing 21-10Mn7Mo welding wire, wherein, in forging stock part chemical composition, Mn/Mo is 7-7.1 than controlling, or 7.2-7.3, or 7.4-7.5.
The aforesaid forging stock part preparing 21-10Mn7Mo welding wire, wherein, the forging step preparing described forging stock part includes: the step of blank heating, for improving the malleability of preamble blank；Wherein, the charging temperature of blank controls at≤850 DEG C.
The aforesaid forging stock part preparing 21-10Mn7Mo welding wire, wherein, the Control for Kiln Temperature of warm-up phase is at 800 DEG C-850 DEG C.
The aforesaid forging stock part preparing 21-10Mn7Mo welding wire, wherein, the Control for Kiln Temperature in heating and soaking stage: when keeping higher furnace temperature, be heated rapidly to initial forging temperature.
The aforesaid forging stock part preparing 21-10Mn7Mo welding wire, wherein, heat time heating time controls as answering coincidence formula heat time heating time: T=aD；In formula, T refers to heating total time (min)；A refers to the coefficient relevant with size, steel grade；D refers to blank diameter or the length of side (mm).
The aforesaid forging stock part preparing 21-10Mn7Mo welding wire, wherein, the coefficient a value in calculating heating total time is 0.7.
The aforesaid forging stock part preparing 21-10Mn7Mo welding wire, wherein, the control of forging temperature: initial forging temperature is >=1180, final forging temperature is >=850.
Thus, the configuration of blank heating temperature, forge piece blank reheating can be prevented effectively from and occur adding thermal defect, to guarantee forging quality.Further, the reasonable disposition of this case initial forging temperature and final forging temperature, also it is effectively reduced forging times, improves productivity ratio.
The aforesaid forging stock part preparing 21-10Mn7Mo welding wire, wherein, prepares the step also having forging molding in the forging step of described forging stock part, wherein, the forging hammer weight dynamics control of the steel ingot forging heating is: during beginning, when the steel ingot deflection forged is not up to 30%, for light forging；After the steel ingot deflection forged reaches 30%, for weight or forging of weighing, the control heavily forged is: must not in place double hit more than three hammers.
The aforesaid forging stock part preparing 21-10Mn7Mo welding wire, wherein, in the step of described forging molding, by the steel control of turning over forging steel ingot be: during forging, being forged steel ingot should overturn to same direction, should overturn 90 ° every time；When forging, drafts controls as uniformity.
The aforesaid forging stock part preparing 21-10Mn7Mo welding wire, wherein, in the step of described forging molding, the forging ratio of molding forging stock part is 4～6.
The aforesaid forging stock part preparing 21-10Mn7Mo welding wire, wherein, the step of described forging molding, wherein, forging deformation amount controls as more than 12%-20%.
Thus can realize the forging deformation amount technical purpose more than recrystallization critical deformation.
The aforesaid forging stock part preparing 21-10Mn7Mo welding wire, wherein, the step of described forging molding, wherein, the step of forging cutting, temperature controls to be not less than at the temperature of 800 DEG C and carries out.
The aforesaid forging stock part preparing 21-10Mn7Mo welding wire, wherein, the step of forging cutting in the step of described forging molding, wherein, just forging size includes but not limited to that Ф 135*650mm, finish-forging size include but not limited to 45*45* (800～1200) mm.
The aforesaid forging stock part preparing 21-10Mn7Mo welding wire, wherein, the step of forging cutting in the step of described forging molding, wherein, it is swaged into square billet size and includes but not limited to 90-180mm.
Thus can better control over forging ' s block dimension and surface quality thereof.
The 21-10Mn7Mo forging thus prepared, can present fine grain, can be that the requirement meeting " micro-crack of abundant seam center and hole " provides possible.
This invention address that technical problem can also is that takes techniques below scheme to realize, according to a kind of 21-10Mn7Mo hot-rolling method quoting aforementioned arbitrary forging stock part provided by the invention, including the step of heating, wherein, the step of described heating preheats temperature to control as 650-750 DEG C.
Aforesaid 21-10Mn7Mo hot-rolling method, wherein, in the step of heating, heating and temperature control is 1180-1220 DEG C.
Aforesaid 21-10Mn7Mo hot-rolling method, wherein, in the step of heating, heat time heating time controlled as 3.5-4 hour.
Aforesaid 21-10Mn7Mo hot-rolling method, wherein, in the step of heating, finishing temperature control is >=900 DEG C.
Thus can make the bulk temperature of forging stock part evenly, the phenomenons such as overheated, burning can be prevented effectively from.
This invention address that the problem of forging steel ingot used is to provide a kind of smelting process for 21-10Mn7Mo welding wire and the steel ingot prepared by the method.
This invention address that and technical problem is that and take techniques below scheme to realize, according to a kind of 21-10Mn7Mo steel ingot provided by the invention, wherein, described steel ingot chemical composition quality % includes: carbon C≤0.10, silicon Si≤0.8, manganese Mn5.5-8.0, phosphorus P≤0.030, sulfur S≤0.020, nickel 9.0-11.0, chromium Cr19.0-22.0, molybdenum Mo0.5-2.0；Mn/Mo ratio controls at 7-7.5.
Aforesaid 21-10Mn7Mo steel ingot, wherein, described steel ingot chemical composition quality % is by carbon C≤0.10, silicon Si≤0.8, manganese Mn5.5-8.0, phosphorus P≤0.030, sulfur S≤0.020, nickel 9.0-11.0, chromium Cr19.0-22.0, molybdenum Mo0.5-2.0, and surplus is ferrum Fe and inevitable impurity composition；Mn/Mo ratio controls at 7-7.5.
Aforesaid 21-10Mn7Mo steel ingot, wherein, Mn/Mo is 7-7.1 than controlling, or 7.2-7.3, or 7.4-7.5.
Thus the setting of rational component configuration and molybdenum, manganese composition ratio, can be prevented effectively from the manganese metal problem in the easy scaling loss of reflow process.It is effectively improved intensity and the corrosion resistance of steel ingot, reaches refinement steel microcosmic crystal grain and reach the technique effect of refined crystalline strengthening.The thus steel ingot of composition, its degree of purity and uniformity are better, to the processing of welding wire and below be welded with desirable influence.
This invention address that and technical problem is that and take techniques below scheme to realize, according to a kind of smelting process for preparing aforementioned steel ingot provided by the invention, this technique is the processing step of the use electric arc furnace Returning blowing keto technique smelting electroslag remelting electrode smelting described steel ingot, wherein, this step is following is referred to as first step, wherein molten steel temperature reaches 1400-1600 DEG C, at high temperature realizes high chrome liquid decarbonization and protecting chromium；The technical process of described first step is successively: fettling, charging, melting stage, the heat of oxidation, reduction period, tapping, casting resmelting electrode；Or/and, in fettling step: fettling material application salt stirs, not handy clear water stirs；Or/and, in charging procedure: the region that Ni, Mo are placed in stove relatively-high temperature, it is impossible to be placed on arcing district.
This case solution technical problem may also take on techniques below scheme and realizes further:
Aforesaid smelting process, wherein, in described first step, the control of melting stage electrode is: electrode wears the band impedance of well stage, adopts high-power power transmission；Or/and, it is dividedly in some parts Calx material, fluorite material, for stablizing electric arc；Or/and, melting stage oxygen blown control: start oxygen blast when furnace temperature reaches more than 950 DEG C, the voltage-controlled system of oxygen is being not more than 0.4MPa；Or/and, the control of melting stage dephosphorization: load melting later stage, when molten steel phosphorus content meets preset value, carry out low temperature dephosphorization, add Calx or broken ore in good time, fire door flows slag dephosphorization automatically；Or/and, described in add the opportunity of Ore and the control of amount: adding Ore in batches, every batch of ore deposit amount is set to 3-4kg or 4-5kg, 3-4 minute or 4-5 minute, interval between adjacent batch.
Thus, it is possible to control temperature and slag flow velocity, described Ore such as fluorite by being suitably added Ore.Utilize Ore to heat up slow feature, add Ore and be more conducive to dephosphorization, constantly add Ore and can keep (FeO) 10～20% in slag, carry out stream slag or skim and make phosphorus be removed in a large number automatically.Thus solve molten steel dephosphorization and slag flowability problem.
Aforesaid smelting process, wherein, in described first step, the heat of oxidation is dephosphorization, decarburization；Degasification: include denitrogenating, dehydrogenation；Remove field trash in molten steel；Its heat of oxidation dephosphorization, decarburization order be first dephosphorization, rear decarburization；Temperature Control sequence is: first low temperature, rear high temperature；Slag making order is: first volume, afterwards on a small quantity；Feed order is, first adds Ore, rear oxygen blast.
Aforesaid smelting process, wherein, the heat of oxidation slag control: by adding Ore, Calx in time, control slag flowing；Or/and, the quantity of slag of slag controls be equivalent to the 2%～3% of molten steel amount；Or/and, slag basicity controls be equivalent to 2.5～3；Or/and, sinter thickness controls be equivalent to 40mm～60mm；Aforesaid smelting process, wherein, the control task of reduction period includes deoxidation, desulfurization；And make chemical composition reach preset process condition；Molten steel temperature is made to meet the preset process condition of cast；After removing oxidizing slag, adding rapidly Calx, fluorite, ratio is 3:1；Produce thin slag, after thin slag is formed, then be dividedly in some parts Calx, adjust slag, and add electrolytic manganese；Or/and, adopt Ca-Si powder, Al powder to be diffused deoxidation, after slag is white, is sufficiently stirred for, takes Duplicate Samples and carry out complete analysis；Or/and, insulation reduction step selects small-power to heat up, and can be selected for high-power intensification before tapping.
Thus can guarantee that tapping temperature and the good mobility of slag.
So far the rational proportion of Fe content in aforesaid material composition, the good result in this performance includes:
Can effectively reduce the tendency being caused fire check by sulfur, thus improving the intensity of welding wire.
Aforesaid smelting process, wherein, in the control of tapping step: after adding alloy, the time between tapping should be relatively long, controls more than 5 minutes；Or/and, Al0.4～0.5/t is inserted in tapping；Or/and, tapping temperature selects 1580～1590 DEG C or 1590 DEG C-1600 DEG C.
Aforesaid smelting process, wherein, the control of cast resmelting electrode: cast controls after tapping opportunity, stands 3～7 minutes, measure whether temperature meets cast temperature condition；Or/and, controlling cast temperature is 1450～1460 DEG C or 1460 DEG C～1470 DEG C or 1470 DEG C-1480 DEG C.
Aforesaid smelting process, wherein, casting rate is 110～120kg/s；Or 120～130kg/s or 130～140kg/s, or 140～150kg/s；Or/and, opening stream can more greatly, and when molten steel rises to ingot body more than 1/3, or full stream is noted soon.
Thus can reach not magic flower, not conjunctiva, not cut the technological effect of note.
So far alloy melting, wherein each alloying element recovery rate is better.
The present invention compared with prior art has significant advantage and beneficial effect, from above technical scheme, the present invention is under excellent structure configuration, remarkable advantage is embodied in aforementioned and embodiment, also have: the steel ingot that this case is prepared by the smelting process method provided, prepare high-quality welding wire for postorder and lay a good foundation.After this case adopts arc smelting just ingot, then purify by the method for electroslag remelting, thus purity height can be obtained, sulfur-bearing is low, non-metallic inclusion is few, chemical composition is uniform and the ingot casting of ingot structure's even compact.The cast metals of the obtained 21-Mn7Mo of smelting process that this case provides has good structure property, and the welding wire processing for the later stage provides quality assurance.This case completes aforesaid technical purpose.
The present invention compared with prior art has significant advantage and beneficial effect, by above technical scheme it can be seen that the present invention is under excellent structure configuration, does not only have above-mentioned advantage, also has:
The forging stock part that this case is prepared by the process for forging provided, prepares high-quality welding wire for postorder and lays a good foundation.
The rational structure also having this case can make manufacturing process more optimize, and manufacturing cost is lower, industry of being more convenient for promotion and application.This case completes aforesaid technical purpose.
The specific embodiment of the present invention is shown in detail in by following example.
Accompanying drawing explanation
Fig. 1 is the macrograph of electric arc furnace smelting sample.
Fig. 2 be electric arc furnace smelting sample tissue in the distribution photo of Mn element.
Fig. 3 is the macrograph of electric arc furnace+electroslag remelting sample.
Fig. 4 be electric arc furnace+electroslag remelting sample tissue in the distribution photo of Mn element.
Fig. 5 be electric arc furnace+electroslag remelting sample tissue in the distribution photo of Mo element.
Detailed description of the invention
Below in conjunction with preferred embodiment, to according to detailed description of the invention provided by the invention, feature and effect thereof, describe in detail as after；For purposes of simplicity and clarity, the hereafter appropriate description eliminating known technology, in order to avoid those unnecessary details impact descriptions to the technical program.
The forging method of a kind of 21-10Mn7Mo welding wire and the forging stock material prepared by the method.The material composition unit of citation is unified for quality %.Do not give the amount that is particularly described, value unit meets industry general provision and usual usage, and it will not go into details.
One, the forging method of described 21-10Mn7Mo welding wire, wherein, the chemical composition quality % of 21-10Mn7Mo steel ingot should meet: carbon C≤0.10, silicon Si≤0.8, manganese Mn5.5-8.0, phosphorus P≤0.030, sulfur S≤0.020, nickel 9.0-11.0, chromium Cr19.0-22.0, molybdenum Mo0.5-2.0, or/and surplus is ferrum Fe and inevitable impurity, or/and, Mn/Mo ratio controls between 7-7.5, this reasonable disposition molybdenum manganese composition than effect include being prevented effectively from the manganese metal problem in the easy scaling loss of reflow process.
The forging method of described 21-10Mn7Mo welding wire, wherein, the smelting preparation method of 21-10Mn7Mo steel ingot, includes but not limited to the applicant's earlier application but not yet disclosed following Chinese patent application: application number 2013107561835 be called 21-10Mn7Mo steel ingot smelting process,
Application number 2013107565018 be called 21-10Mn7Mo steel ingot smelting technique,
Application number 201310756138X name be called 21-10Mn7Mo steel ingot and smelting process thereof,
Application number 2013107564829 be called 21-10Mn7Mo steel ingot,
2013107561623 smelting processes being called 21-10Mn7Mo ingot casting of application number.
Adopt 21-10Mn7Mo steel ingot and smelting process thereof that above-mentioned patent application provides, whereby, it is possible to provide better ingot casting for forging process.
Metal molybdenum, the manganese element effect in rustless steel of specific descriptions, acting as of other compositions is general it can be seen that repeat no more.
1. the effect of metal molybdenum Mo element.
1.1. molybdenum is to stainless microscopic structure and heat treated effect
Steel and other alloys are had two important effects as alloying element by molybdenum, namely improve intensity and corrosion resistance.Molybdenum can be solid-solution in ferrite, austenite and carbide in steel, and it is the element reducing austenite phase field；There is the effect refining steel microcosmic crystal grain and reach refined crystalline strengthening, when molybdenum content is relatively low, with the cementite that ferrum, carbon form compound；Then form the high rigidity alloy carbide 6-MoC/Mo2C of its own when content is higher, be the hardening constituent in steel；Molybdenum improves the quenching degree of steel, and it is strong that it acts on relatively chromium, and is slightly poorer than manganese；Molybdenum improves steel belt roof bolt stability.When existing as single alloying element, increase steel belt roof bolt fragility；With chromium or manganese etc. when depositing, molybdenum reduces again or restrains the temper brittleness because other elements cause.
The effect to stainless mechanical property of 1.2 molybdenums
Ferrite is had solution strengthening effect by molybdenum, can also form Precipitation phase in rustless steel, improves the intensity of steel, also improves the stability of carbide, thus improving the intensity of steel simultaneously；Molybdenum is to improving the ductility of steel and toughness and wearability plays advantageous effect；Owing to molybdenum makes the softening after working hardening and recovery temperature and recrystallization temperature improve, and strongly improve ferritic creep resistance, effectively suppress cementite under gathering, promote the precipitation of alloy carbide, thus become the particularly effective alloying element improving steel heat resistance, molybdenum can improve the mechanical behavior under high temperature of austenitic stainless steel, such as persistently, the performance such as creep all can obtain bigger improvement.
The effect to stainless physical chemistry and processing performance of 1.3 molybdenums
Can making steel surface passivation in reductive acid and strong oxidizing property saline solution, therefore molybdenum can generally improve the etch resistant properties of steel, it is prevented that steel spot corrosion in chloride solution；The non-oxidizability of steel is made to worsen during molybdenum content higher (> 3 mass %)；The steel less than 8 mass % containing molybdenum still can be forged, roll, but when content is higher, hot worked resistance of deformation is increased by steel.
In summary, molybdenum is to be formed and stablize ferrite and expand the element of ferrite phase region.
But, the addition of molybdenum makes the high temperature hot deformation resistance of steel increase, steel is usually present a small amount of delta ferrite in addition thus containing the stainless hot-workability of molybdenum than without molybdenum steel for poor, and molybdenum content is more high, and hot-working character is more bad；Molybdenum also promotes intermetallic phase in austenitic stainless steel, such as σ phase, κ phase, and the precipitation that Laves is equal, and corrosion resistance and mechanical property to steel all can have a negative impact, and particularly result in plasticity, and toughness declines.
For making austenitic stainless steel keep single austenite structure, along with the increase of molybdenum content in steel, the content of austenite former also to improve accordingly, to keep in steel the balance between ferrite and austenite former, therefore, after this case adds molybdenum in austenitic stainless steel, the content of manganese also improves accordingly.General known described austenite former refers to nickel, nitrogen, manganese etc..
2. the control of manganese metal Mn element
Manganese is similar to nickel for austenitic effect.But the important function of manganese does not lie in formation austenite, but is in that it reduces the critical quenching rate of steel, increases austenitic stability when cooling, it is suppressed that austenitic decomposition, makes the austenite formed under high temperature be maintained room temperature.
In improving the decay resistance of steel, the effect of manganese is little, experiments show that, the manganese content in steel changes from 0 to 10.4 quality %, and steel decay resistance in air with acid can not be made to occur significantly to change.
Further, add Mn and more nitrogen can be made to dissolve in austenite, and nitrogen is strong austenite former, containing the nitrogen of 0.25 mass %, forms austenitic ability and is equivalent to the nickel of 7.5 mass %.
Improve the content of manganese in welding wire, except deoxidation, moreover it is possible to generate Manganese monosulfide. (MnS) with sulfuration conjunction, and be removed (that is: desulfurization), therefore the tendency of the fire check caused by sulfur can be reduced, the intensity of welding wire can be improved simultaneously.But the content of manganese needs effectively to control, when the too high levels of manganese easily makes material solidification or applied at elevated temperature process in which materials tissue thick, the fragility of increase material.
3. this case 21-10Mn7Mo contrasts with the material chemical composition quality % of prior art, in Table 1.
Table 1: the chemical composition of bi-material
Referring to Fig. 1-5, test shows, is suitable for determining addition, forms new alloy, and after welding wire made by such alloy, its intensity can significantly improve.
It is general it can be seen that molybdenum and adding of manganese can increase certain difficulty to forging process.Interpolation including reason molybdenum and manganese makes the intensity of steel improve, and plasticity reduces, and thus, malleability is deteriorated.
And the quality forging blank directly affects the processing of follow-up hot rolling and cold working operation and the quality of finished product thereof.
Two, the description of the Forging Technology of 21-10Mn7Mo welding wire:
1. the concrete steps of forging include:
Reconditioning > blank heating > forging molding > forging cooling.
The step of 1.1 reconditionings.Purpose is that 21-10Mn7Mo steel ingot preamble produced carries out reconditioning, removes the defect such as surface slag blanket, folding, fine fisssure, and this step can be general prior art, and it will not go into details.
The step of 1.2 blank heating.Purpose is to improve the forgeability of preamble blank, improves its malleability.
The step of described blank heating, for the step heated stage by stage, including warm-up phase and heating and soaking stage.In reason 21-10Mn7Mo steel ingot, the factor of molybdenum and manganese composition, forging is even more important in rational temperature range.
The step of described blank heating,
Wherein, the charging temperature of blank controls at≤850 DEG C.
Wherein, the Control for Kiln Temperature of warm-up phase is at 800 DEG C-850 DEG C, and thus furnace temperature designs in order to control the firing rate to blank, reaches the slow purpose of appropriateness.
Wherein, the Control for Kiln Temperature in heating and soaking stage: when keeping higher furnace temperature, be heated rapidly to initial forging temperature.
Wherein, heat time heating time controls, and heat time heating time answers coincidence formula: T=aD；
T refers to heating total time (min)；
A refers to the coefficient relevant with size, steel grade.
D refers to blank diameter or the length of side (mm).
Wherein, the coefficient a value in calculating heating total time is 0.7.
Wherein, the control of forging temperature: initial forging temperature is >=1180, final forging temperature is >=850.
Thus, the configuration of blank heating temperature, forge piece blank reheating can be prevented effectively from and occur adding thermal defect, to guarantee forging quality.
The thus design of initial forging temperature and final forging temperature, is also effectively reduced forging times, improves productivity ratio.
The step of 1.3 forging moldings.
Quote air flat-die hammer forging method, by default opening forging, stopping forging temperature forging, when occurring lower than, when stopping forging temperature conditions, heating being melted down to satisfying condition, can be general prior art here, repeat no more.
The step of described forging molding, wherein, the forging hammer weight dynamics control of the steel ingot forging heating is: during beginning, when the steel ingot deflection forged is not up to 30%, for light forging.Described light forging is the general general knowledge in this area, and it will not go into details.After the steel ingot deflection forged reaches 30%, for weight or forging of weighing, the control heavily forged is: must not in place double hit more than three hammers.
The step of described forging molding, wherein, by the steel control of turning over forging steel ingot be: during forging, being forged steel ingot should overturn to same direction, should overturn 90 ° every time；When forging, drafts controls as uniformity；When occurring that steel material bends, overturn 180 °, forge rectification.
The step of described forging molding, wherein, the forging ratio of molding forging stock part is 4～6.Further, forging during a controlled forge process fire time in the end fire, forging ratio is relatively sufficiently large in 4～6 interval selection.
The step of described forging molding, wherein, forging deformation amount controls as more than 12%-20%.
Thus can realize the forging deformation amount technical purpose more than recrystallization critical deformation.
The step of described forging molding, wherein, the step of forging cutting, temperature controls to be not less than at the temperature of 800 DEG C and carries out.
The step of described forging molding, wherein, just forging size includes but not limited to that Ф 135*650mm, finish-forging size include but not limited to 45*45* (800～1200) mm.
It is swaged into square billet size and includes but not limited to 90-180mm.
Thus can better control over forging ' s block dimension and surface quality thereof.
The 21-10Mn7Mo forging thus prepared, can present fine grain, can be that the requirement meeting " micro-crack of abundant seam center and hole " provides possible.
Referring to table 2, which give the process conditions of forging temperature.
Table 2
The step of 1.4 forging coolings, the type of cooling, for stacking cooling, has reached the purpose of Slow cooling, and stacking cooling can be general prior art, and it will not go into details.
Thus can ensure that forging quality, be prevented effectively from reason thermal stress and the defects such as forging deformation, crackle occurs in structural stress.
It is general it can be seen that forging temperature, deformation extent, strain rate, stress state (forging method), to add rate of cooling be all the key factor affecting forging stock quality.
Forging range refers to one section of temperature interval between initial forging temperature and final forging temperature.
Determine that the basic principle of forging temperature is to ensure that metal has higher plasticity and less resistance of deformation in forging range, and obtain required tissue and performance.
The malleability of 21-10Mn7Mo material can be effectively improved with the configuration of aforesaid measure.
The welding wire good tissue of offer and performance condition can be prepared for subsequent technique with forging stock part prepared by aforesaid measure.
Three, the description of the hot-rolling method of 21-10Mn7Mo welding wire:
1. the step of gren rod includes: heating → rolling → cooling → finishing
The step of 1.1 heating, it is therefore intended that improve the plasticity of 21-10Mn7Mo forging stock part, reduce its resistance of deformation, improve material inside organization, eliminates the material property defect of forging stock part further.
The step of described heating, can adopt walking beam furnace that forging is heated, and walking beam furnace is prior art, repeats no more.Heating technique parameter configures referring to table 3.
The step of described heating, wherein, preheating temperature controls as 650-750 DEG C；
The step of described heating, wherein, heating and temperature control is 1180-1220 DEG C；
The step of described heating, wherein, heat time heating time controlled as 3.5-4 hour；
The step of described heating, wherein, finishing temperature control is >=900 DEG C.
Thus can make the bulk temperature of forging stock part evenly, the phenomenons such as overheated, burning can be prevented effectively from.
Table 3 heating technique parameter
| Steel grade | Preheating temperature | Heating-up temperature | Heat time heating time | Finishing temperature |
| 21-10Mn7Mo | 650-750℃ | 1180-1220℃ | 3.5-4 hour | ≥900℃ |
1.2. the step rolled, it is therefore intended that overall dimensions precision and the surface quality reprocessing to 21-10Mn7Mo forging stock part, accurately to adjust and to control material shape and amount of rolling, meets the requirement of lower sequence drawing,
The size being rolled into wire rod can be Ф 5.5mm.
The step of 1.3 coolings, adopts natural cooling in air.
The step of 1.4 finishing, coils rapidly, thinning surface defect.
After the preferred embodiment described in detail, being familiar with this skilled worker can be apparent from, and without departing from carrying out various change and amendment under claim described in this case and spirit, and the present invention is also not only restricted in description the embodiment of illustrated embodiment.
Claims (10)
1. the gren rod being used for preparing 21-10Mn7Mo welding wire, wherein, for the blank that hot rolling processes, its chemical composition quality % includes: carbon C≤0.10, silicon Si≤0.8, manganese Mn5.5-8.0, phosphorus P≤0.030, sulfur S≤0.020, nickel 9.0-11.0, chromium Cr19.0-22.0, molybdenum Mo0.5-2.0；Mn/Mo ratio controls at 7-7.5；
Or, described blank chemical composition quality % is by carbon C≤0.10, silicon Si≤0.8, manganese Mn5.5-8.0, phosphorus P≤0.030, sulfur S≤0.020, nickel 9.0-11.0, chromium Cr19.0-22.0, molybdenum Mo0.5-2.0, and surplus is ferrum Fe and inevitable impurity composition；Mn/Mo ratio controls at 7-7.5；
Wherein, the forging step preparing described blank includes: the step of blank heating, and wherein, the charging temperature of blank controls at≤850 DEG C；
Wherein, preparing and control heat time heating time in the forging step of described blank, heat time heating time answers coincidence formula: T=aD；In formula, T refers to heating total time (min)；A refers to the coefficient relevant with size, steel grade；D refers to blank diameter or the length of side (mm)；Wherein, the coefficient a value in calculating heating total time is 0.7.
Or/and, wherein, the control of forging temperature: initial forging temperature is >=1180, final forging temperature is >=850.
The processing step of gren rod includes the step of heating, and in the step of described heating, preheating temperature controls as 650-750 DEG C；Heating and temperature control is 1180-1220 DEG C；Heat time heating time controlled as 3.5-4 hour；Finishing temperature control is >=900 DEG C；The Control for Kiln Temperature of warm-up phase is at 800 DEG C-850 DEG C.
2. as claimed in claim 1 for preparing the gren rod of 21-10Mn7Mo welding wire, wherein, the Control for Kiln Temperature in heating and soaking stage: when keeping higher furnace temperature, be heated rapidly to initial forging temperature.
3. the forging hammer weight dynamics control of the steel ingot as claimed in claim 2 for preparing the gren rod of 21-10Mn7Mo welding wire, wherein, forging heating is: during beginning, when the steel ingot deflection forged is not up to 30%, for light forging；After the steel ingot deflection forged reaches 30%, for weight or forging of weighing, the control heavily forged is: must not in place double hit more than three hammers.
4., as claimed in claim 3 for preparing the gren rod of 21-10Mn7Mo welding wire, wherein, in the step of described forging molding, by the steel control of turning over forging steel ingot it is: during forging, being forged steel ingot should overturn to same direction, should overturn 90 ° every time；When forging, drafts controls as uniformity.
5., as claimed in claim 4 for preparing the gren rod of 21-10Mn7Mo welding wire, wherein, in the step of described forging molding, the forging ratio of molding forging stock part is 4～6.
6. as claimed in claim 5 for preparing the gren rod of 21-10Mn7Mo welding wire, wherein, the step of described forging molding, wherein, forging deformation amount controls as more than 12%-20%.
7. as claimed in claim 6 for preparing the gren rod of 21-10Mn7Mo welding wire, wherein, the step of described forging molding, wherein, the step of forging cutting, temperature controls to be not less than and carries out at the temperature of 800 DEG C；
Or/and, wherein, the step of forging cutting in the step of forging molding, wherein, just forging size includes but not limited to that Ф 135*650mm, finish-forging size include but not limited to 45*45* (800～1200) mm；
Or/and, wherein, it is swaged into square billet size and includes but not limited to 90-180mm.
8. prepare the gren rod of 21-10Mn7Mo welding wire as claimed in claim 7, wherein, in the step of rolling, be rolled into wire rod and be of a size of Ф 5.5mm.
9. prepare the gren rod of 21-10Mn7Mo welding wire as claimed in claim 8, wherein, the step of cooling, adopt natural cooling in air.
10. prepare as claimed in claim 9 the gren rod of 21-10Mn7Mo welding wire, wherein, the step of finishing, coil rapidly, thinning surface defect.
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| CN112708822A (en) * | 2019-10-24 | 2021-04-27 | 宝武特种冶金有限公司 | Manufacturing method of austenitic stainless steel wire for high-end welding |
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| CN112708822A (en) * | 2019-10-24 | 2021-04-27 | 宝武特种冶金有限公司 | Manufacturing method of austenitic stainless steel wire for high-end welding |
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