EP0170598A1 - Process for manufacturing hot-rolled martensitic stainless steel rods or rod wire, and products obtained - Google Patents
Process for manufacturing hot-rolled martensitic stainless steel rods or rod wire, and products obtained Download PDFInfo
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- EP0170598A1 EP0170598A1 EP85420123A EP85420123A EP0170598A1 EP 0170598 A1 EP0170598 A1 EP 0170598A1 EP 85420123 A EP85420123 A EP 85420123A EP 85420123 A EP85420123 A EP 85420123A EP 0170598 A1 EP0170598 A1 EP 0170598A1
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- mpa
- hot rolling
- bars
- temperature
- resilience
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- 238000000034 method Methods 0.000 title claims abstract description 11
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 8
- 229910001105 martensitic stainless steel Inorganic materials 0.000 title claims abstract 4
- 238000005098 hot rolling Methods 0.000 claims abstract description 26
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 10
- 238000001816 cooling Methods 0.000 claims abstract description 10
- 239000010959 steel Substances 0.000 claims abstract description 10
- 239000000203 mixture Substances 0.000 claims description 7
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 4
- 239000003595 mist Substances 0.000 claims 1
- 239000012535 impurity Substances 0.000 abstract description 4
- 238000005260 corrosion Methods 0.000 abstract description 2
- 230000007797 corrosion Effects 0.000 abstract description 2
- 230000007246 mechanism Effects 0.000 abstract 1
- 238000012360 testing method Methods 0.000 description 16
- 229910000859 α-Fe Inorganic materials 0.000 description 16
- 238000005096 rolling process Methods 0.000 description 12
- 229910000734 martensite Inorganic materials 0.000 description 10
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 10
- 230000000694 effects Effects 0.000 description 7
- 229910001220 stainless steel Inorganic materials 0.000 description 6
- 238000007792 addition Methods 0.000 description 5
- 238000010791 quenching Methods 0.000 description 5
- 230000000171 quenching effect Effects 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 4
- 238000005266 casting Methods 0.000 description 3
- 238000005496 tempering Methods 0.000 description 3
- 230000009931 harmful effect Effects 0.000 description 2
- 230000000977 initiatory effect Effects 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 238000013021 overheating Methods 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 239000010935 stainless steel Substances 0.000 description 2
- 235000013405 beer Nutrition 0.000 description 1
- 238000012790 confirmation Methods 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 229940082150 encore Drugs 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 230000000750 progressive effect Effects 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 230000001131 transforming effect Effects 0.000 description 1
Images
Classifications
-
- 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
- C21D7/00—Modifying the physical properties of iron or steel by deformation
- C21D7/13—Modifying the physical properties of iron or steel by deformation by hot working
-
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
-
- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
Definitions
- the method of the present invention relates to a method of manufacturing bars or wire rod from stainless steel.
- martensitic stainless steels with good mechanical resistance correspond to the designations according to standard NF A 35-575 : "Z12C13”. "Z20C13” - “Z30C13”, with overall C 0.08 to 0.34% and Cr 11.5 at 14.0%. They are martensitic steels, that is to say having a predominantly martensite structure.
- the invention consists in a selection of composition and in the setting of hot rolling conditions which surprisingly lead to the desired levels of properties in the raw hot rolling state.
- compositions and the conditions of rolling are both necessary for obtaining these properties.
- the metallurgical examinations carried out make it possible to give qualitative indications on the effects of these conditions, effects which appear complex, and to indicate practical limits for the conditions of the process of the invention and the characteristics of the corresponding products.
- the "other elements" are in the usual contents for an elaboration in electric steelworks from scrap, their total is usually less than 0.5%. In particular, the residual Al content is less than 0.1%.
- the adjustment of the total content "C + N" is an essential point of the invention: it makes it possible to increase the mechanical resistance (R, E 0.2) of the product obtained and to maintain good resilience (KCU). An example will show the harmful influence on the resilience of a too high "C + N”.
- the method of the invention makes it possible to obtain raw hot rolling bars or wire rod which still have very interesting mechanical characteristics. With improved machinability. these products indeed have mechanical properties (R, E) of a very good level with a resilience that is lower the higher the S content, but overall greater than 40 J / cm2.
- Nb ⁇ 0.1% and V ⁇ 0.1% have a hardening effect, essentially resulting in an improvement in the breaking load "R” and especially in the elastic limit at 0.2% “E 0.2".
- An addition of nickel can be made if the cost is not considered excessive, mainly to improve the resilience. Such an addition tends to decrease the proportion of ferrite in the martensite / ferrite structure.
- the rolling conditions necessary to obtain the mechanical characteristics of the bars or machine wires according to the invention are as follows: after the possible hot coarse-graining of the product, whether or not followed by a cooling, the product must be brought to a temperature between 1050 ° C and 1160 ° C before undergoing the final hot rolling, this preliminary setting to temperature being obtained either by preheating or reheating, or by roughing conditions causing this temperature when the product arrives at the final rolling.
- the final hot rolling of the product thus brought to between 1050 and 1160 ° C is then carried out in practice at a temperature less than or equal to 1150 ° C (the product cools down by 10 ° C or more during the initiation of this rolling), and it must produce a reduction in section "S / s", where "S” is the cross section of the product at the initiation of this final hot rolling and "s" the cross section obtained at the end of said final hot rolling , at least equal to 3. Tests have shown that the final hot rolling should preferably be finished between 1050 and 950 ° C, product temperatures. Finally, the final hot rolling must be followed by homogeneous air cooling.
- Accelerated cooling means such as blown air or mists (water + air) can be used, provided that the cooling remains homogeneous, that is to say that the cooling rates must differ little from one section right to another of the product.
- Preheating before the final hot rolling can also be carried out below 1050 ° C, for example between 1000 ° C and 1050 ° C, but the process while remaining applicable becomes more difficult to implement.
- the rods or wire rod according to the invention are recognizable by all of their mechanical characteristics and their analysis. These mechanical characteristics being singular for such an analysis. They are also characterized in addition by a proportion of ferrite in martensite less than 30% and typically between 15 and 25%, as well as by an average grain or phase diameter (martensite and ferrite) equivalent to 5 to 10 ASTM (specification ASTM E 112 ), i.e. 65 ⁇ m to 11 ⁇ m. These structural characteristics are largely responsible for the mechanical characteristics.
- the bars according to the invention are in the form of raw hot rolling bars, or hot rolled then erected with optionally a surface finish, of diameter or thickness between 15 and 250 mm and preferably between 15 and 120 mm .
- the wire rod with a diameter between 5 and 35 mm according to the invention is usually in the form of a crown or erect bars.
- the cooling is mainly done in offset crowns or turns.
- the hot roughing was carried out in blooming as usual at about 1200-1250 ° C, transforming the 250 mm squares into 148 mm squares.
- the cooled 148 mm squares were then preheated in an oven at various temperatures as indicated in the table and then hot-rolled in the final by successive passes to the diameters shown in the table and cooled in air. From the measurements carried out with an optical pyrometer, it was estimated that the temperature of the bars at the end of the rolling was in all cases between 950 and 1000 ° C.
- the maximum section reduction is that of the A1 20 mm ⁇ bars with S / s - 69.
- the adjustment of the preheating and rolling temperature is certainly important for the adjustment of the ferrite content.
- the ferrite content must be minimized to obtain good resilience and good mechanical resistance, therefore preheat and laminate in a limited temperature range depending on both of this effect under real dynamic conditions and other very important factors: dissolution and maintenance of C and N in solution to strengthen the matrix. obtaining a fine-grained structure (preheating and recrystallization during rolling).
- the cast squares of 250 ⁇ 250 mm were hot transformed as before and similar tests were carried out starting from squares of 148 mm, with air cooling of the bars obtained.
- the temperature of the bars at the end of the rolling was between 950 and 1000 ° C.
- the preheating temperatures and the mechanical characteristics obtained on the bars are collated in the Table below:
- This graph shows that in the range of ferrite content ⁇ % from 18 to 35%, a reduction of ⁇ % of 10% corresponds on average to an increase of E 0.2 of approximately 100 MPa.
- Figure 3 locates on the one hand the figurative points (C%, N%) of the flows (A) - (B) and (D), on the other hand the domain (E) of contents (C%, N%) according to the invention as well as the narrowest preferential domain (F).
- the hardening of the bars depends significantly on the content of (C + N) dissolved. Small additions of Nb ⁇ 0.1% and / or V ⁇ 0.1% also play a hardening role.
- the good characteristics R and E 0.2 are linked to the high content of (C + N) and to the small additions of Nb and of V, but the contents in (C. N) are outside the scope of the invention and the resilience is very low.
- the process is particularly suitable for the production of rods or wire rod with continuous hot rolling means.
- the bars or machine wires of the invention are used in particular for the manufacture of mechanical parts resistant to corrosion, working in contact water, steam, wine or beer: such as trees, pistons, liners, valves or hardware.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Crystallography & Structural Chemistry (AREA)
- Manufacturing & Machinery (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
Description
Le procédé de la présente invention concerne une méthode de fabrication de barres ou de fil machine en acier inoxydable.The method of the present invention relates to a method of manufacturing bars or wire rod from stainless steel.
Les aciers inoxydables martensitiques usuels présentant une bonne résistance mécanique correspondent aux appellations selon la norme NF A 35-575 : "Z12C13" ."Z20C13" - "Z30C13", avec globalement C 0,08 à 0,34 % et Cr 11,5 à 14,0 %. Ce sont des aciers martensitiques, c'est-à-dire ayant une structure à prédominance de martensite.The usual martensitic stainless steels with good mechanical resistance correspond to the designations according to standard NF A 35-575 : "Z12C13". "Z20C13" - "Z30C13", with overall C 0.08 to 0.34% and Cr 11.5 at 14.0%. They are martensitic steels, that is to say having a predominantly martensite structure.
Après laminage à chaud et refroidissement, ils sont durs et fragiles, et pour leur conférer une bonne résistance mécanique, on leur applique un traitement de trempe, puis un revenu, tels que :
- - chauffage à 950 à 1050°C
- - trempe à l'huile
- - revenu entre 550 et 650°C
et on aboutit aux caractéristiques typiques suivantes :
- R - 900 à 1100 MPa - E 0,2 - 650 à 850 MPa - A - 12 à 16 % et résilience KCU - 20 à 60 J/cm2.
- - heating to 950 to 1050 ° C
- - oil quenching
- - tempering between 550 and 650 ° C
and we end up with the following typical characteristics:
- R - 900 to 1100 MPa - E 0.2 - 650 to 850 MPa - A - 12 to 16% and resilience KCU - 20 to 60 J / cm2.
Cette résilience qui rend en partie compte de la ténacité est médiocre, et on ne peut l'améliorer en restant dans le domaine des aciers inoxydables qu'en recourant à des aciers plus coûteux tels que "Z6CND 16-04" (norme NF A 35-581) et "Z6CNU 17-04-01" (norme NF A 35-574), qui à l'état trempé-revenu donnent des caractéristiques (R, E, A) du même niveau que les précédentes avec une résilience KCU améliorée : 80 à 140 J/cm2.This resilience which partly accounts for the toughness is poor, and it can only be improved by remaining in the field of stainless steels by using more expensive steels such as "Z6CND 16-04" (standard NF A 35 -581) and "Z6CNU 17-04-01" (standard NF A 35-574), which in the quenched-tempered state give characteristics (R, E, A) of the same level as the previous ones with improved KCU resilience : 80 to 140 J / cm2.
On a cherché à obtenir des barres à environ 13 % Cr ayant des caractéristiques mécaniques du même niveau que celles des aciers inoxydables plus coûteux "Z6CND 16-06" et "Z6CNU 17-04-01", en simplifiant ou en évitant le traitement thermique de trempe + revenu. On a ainsi recherché à obtenir des barres martensitiques en acier inoxydable à environ 13 % Cr possédant tout à la fois une bonne résistance mécanique, une bonne ductilité, et de façon nouvelle une bonne résilience, avec des conditions de fabrication économiques.We sought to obtain bars at around 13% Cr having mechanical characteristics of the same level as those of the more expensive stainless steels "Z6CND 16-06" and "Z6CNU 17-04-01", by simplifying or avoiding the heat treatment. quenching + tempering. We have thus sought to obtain martensitic bars of stainless steel at about 13% Cr having at the same time a good mechanical resistance, a good ductility, and in a new way a good resilience, with economical manufacturing conditions.
L'invention consiste en une sélection de composition et en la fixation de conditions de laminage à chaud qui conduisent de façon surprenante aux niveaux de propriétés recherchées dans l'état brut de laminage à chaud.The invention consists in a selection of composition and in the setting of hot rolling conditions which surprisingly lead to the desired levels of properties in the raw hot rolling state.
Les conditions de compoeition et les conditions de laminage sont les unes et les autres nécessaires pour l'obtention de ces propriétés. Les examens métallurgiques effectués permettent de donner des indications qualitatives sur les effets de ces conditions, effets qui paraissent complexes, et d'indiquer des limites pratiques pour les conditions du procédé de l'invention et les caractéristiques des produits correspondants.The conditions of composition and the conditions of rolling are both necessary for obtaining these properties. The metallurgical examinations carried out make it possible to give qualitative indications on the effects of these conditions, effects which appear complex, and to indicate practical limits for the conditions of the process of the invention and the characteristics of the corresponding products.
Les aciers inoxydables et semi-inoxydables de l'invention ont les compositions suivantes (% en poids), les intervalles préférentiels indiqués pouvant être pris séparément ou en combinaison quelconque :
- - C - 0,015 à 0,090 % et de préférence 0,030 à 0,060 %
- - N - 0,015 à 0,080 % et de préférence 0,020 à 0,050 % avec C + N - 0,05 à 0,120 % et de préférence C + N - 0,050 à 0,100%
- - Cr - 9,0 à 14,0 % et de préférence 11,0 à 14,0 % et de préférence encore 11,5 à 13,5 %
- - Nb ≤ 0,1 %
- - V ≤ 0,1 %
- - S ≤ 0,35 % avec 3 intervalles préférentiels
- S ≤ 0,03 % caractéristiques optimales
- S - 0,03 à 0,08 % caractéristiques mécaniques peu modifiées, usinabilité améliorée
- 0,08 < S ≤ 0,35 %, résilience moins bonne, usinabilité renforcée
- - Si ≤ 1,0 % - Mn ≤ 1,0 % - Ni < 2,0 % et de préférence 1,0 % - Mo ≤ 1,0%
- - P ≤ 0,040 %
- - Cu ≤ 1,0 %
- - autres éléments et Fe : le solde.
- - C - 0.015 to 0.090% and preferably 0.030 to 0.060%
- - N - 0.015 to 0.080% and preferably 0.020 to 0.050% with C + N - 0.05 to 0.120% and preferably C + N - 0.050 to 0.100%
- - Cr - 9.0 to 14.0% and preferably 11.0 to 14.0% and more preferably 11.5 to 13.5%
- - Nb ≤ 0.1%
- - V ≤ 0.1%
- - S ≤ 0.35% with 3 preferential intervals
- S ≤ 0.03% optimal characteristics
- S - 0.03 to 0.08% slightly modified mechanical characteristics, improved machinability
- 0.08 <S ≤ 0.35%, poorer resilience, enhanced machinability
- - If ≤ 1.0% - Mn ≤ 1.0% - Ni <2.0% and preferably 1.0% - Mo ≤ 1.0%
- - P ≤ 0.040%
- - Cu ≤ 1.0%
- - other elements and Fe: the balance.
Les "autres éléments" sont dans les teneurs habituelles à une élaboration en aciérie électrique à partir de ferrailles, leur total est habituellement inférieur à 0,5 %. En particulier, la teneur en Al résiduel est inférieure à 0,1 %.The "other elements" are in the usual contents for an elaboration in electric steelworks from scrap, their total is usually less than 0.5%. In particular, the residual Al content is less than 0.1%.
L'ajustement de la teneur totale "C + N" est un point essentiel de l'invention : elle permet d'élever la résistance mécanique (R, E 0,2) du produit obtenu et de conserver une bonne résilience (KCU). Un exemple montrera l'influence néfaste sur la résilience d'un "C + N" trop élevé.The adjustment of the total content "C + N" is an essential point of the invention: it makes it possible to increase the mechanical resistance (R, E 0.2) of the product obtained and to maintain good resilience (KCU). An example will show the harmful influence on the resilience of a too high "C + N".
Lorsque l'acier est chargé en S, et spécialement lorsque sa teneur en S est comprise entre 0,08 et 0,30 %, le procédé de l'invention permet d'obtenir des barres brutes de laminage à chaud ou du fil machine qui ont encore des caractéristiques mécaniques très intéressantes. Avec une usinabilité améliorée. ces produits ont en effet des propriétés mécaniques (R, E) d'un très bon niveau avec une résilience d'autant plus faible que la teneur en S est élevée, mais globalement supérieure à 40 J/cm2.When the steel is loaded with S, and especially when its S content is between 0.08 and 0.30%, the method of the invention makes it possible to obtain raw hot rolling bars or wire rod which still have very interesting mechanical characteristics. With improved machinability. these products indeed have mechanical properties (R, E) of a very good level with a resilience that is lower the higher the S content, but overall greater than 40 J / cm2.
Des additions éventuelles Nb ≤ 0.1 % et V ≤ 0,1 % ont un effet durcisseur se traduisant essentiellement par une amélioration de la charge de rupture "R" et surtout de la limite élastique à 0,2 % "E 0,2".Any additions Nb ≤ 0.1% and V ≤ 0.1% have a hardening effect, essentially resulting in an improvement in the breaking load "R" and especially in the elastic limit at 0.2% "E 0.2".
Une addition de nickel peut être faite si le coût n'en est pas jugé excessif, principalement pour améliorer la résilience. Une telle addition tend à diminuer la proportion de ferrite dans la structure martensite/ferrite.An addition of nickel can be made if the cost is not considered excessive, mainly to improve the resilience. Such an addition tends to decrease the proportion of ferrite in the martensite / ferrite structure.
Les conditions de laminage nécessaires pour obtenir les caractéristiques mécaniques des barres ou fils machine selon l'invention sont les suivantes : après le cégrossissage à chaud éventuel du produit, suivi ou non d'un refroidissement, le produit doit être porté à température comprise entre 1050°C et 1160°C avant de subir le laminage à chaud final, cette mise préalable à température étant obtenue soit par un préchauffage ou réchauffage, soit par des conditions de dégrossissage entraînant cette température lors de l'arrivée du produit au laminage final. Le laminage à chaud final du produit ainsi porté entre 1050 et 1160°C est alors effectué en pratique à température inférieure ou égale à 1150°C (le produit se refroidit de 10°C ou plus lors de l'engagement de ce laminage), et il doit produire une réduction de section "S/s", où "S" est la section droite du produit à l'engagement de ce laminage à chaud final et "s" la section droite obtenue à la fin dudit laminage à chaud final , au moins égale à 3. Les essais ont montré que le laminage à chaud final devait être terminé de préférence entre 1050 et 950°C, températures du produit. Enfin, le laminage à chaud final doit être suivi d'un refroidissement homogène à l'air. Des moyens de refroidissement accéléré tel que de l'air soufflé ou des brouillards (eau + air) peuvent être utilisés, pourvu que ie refroidissement reste homogène, c'est-à-dire que les vitesses de refroidissement doivent peu différer d'une section droite à une autre du produit. Le préchauffage avant le laminage à chaud final peut également être effectué en-dessous de 1050'C, par exemple entre 1000°C et 1050°C, mais le procédé tout en restant applicable devient plus difficile à mettre en oeuvre.The rolling conditions necessary to obtain the mechanical characteristics of the bars or machine wires according to the invention are as follows: after the possible hot coarse-graining of the product, whether or not followed by a cooling, the product must be brought to a temperature between 1050 ° C and 1160 ° C before undergoing the final hot rolling, this preliminary setting to temperature being obtained either by preheating or reheating, or by roughing conditions causing this temperature when the product arrives at the final rolling. The final hot rolling of the product thus brought to between 1050 and 1160 ° C is then carried out in practice at a temperature less than or equal to 1150 ° C (the product cools down by 10 ° C or more during the initiation of this rolling), and it must produce a reduction in section "S / s", where "S" is the cross section of the product at the initiation of this final hot rolling and "s" the cross section obtained at the end of said final hot rolling , at least equal to 3. Tests have shown that the final hot rolling should preferably be finished between 1050 and 950 ° C, product temperatures. Finally, the final hot rolling must be followed by homogeneous air cooling. Accelerated cooling means such as blown air or mists (water + air) can be used, provided that the cooling remains homogeneous, that is to say that the cooling rates must differ little from one section right to another of the product. Preheating before the final hot rolling can also be carried out below 1050 ° C, for example between 1000 ° C and 1050 ° C, but the process while remaining applicable becomes more difficult to implement.
Comme on le verra à propos des essais, l'ajustement de la température de laminage est important en même temps que l'ajustement de la composition pour ies réglages de la teneur en ferrite, de la teneur en (C + N) dissous et de la taille de grain sur produit, facteurs tous particulièrement importants pour l'obtention directe du compromis très surprenant de caractéristiques mécaniques des barres ou fil machine bruts de laminage à chaud selon l'invention :
- . si S ≤ 0,08 % - R = 900 à 1100 MPa - E 0,2 - 650 à 850 MPa - A - 12 à 16 % . résilience KCU = 80 à 140 J/cm2
- . si S est supérieur à 0,08 % et inférieur ou égal à 0,35 % - R - 900 à 1100 MPa - E 0.2 - 650 à 850 MPa - A ≥ 10 % - résilience KCU ≥ 40 J/cm2.
- . if S ≤ 0.08% - R = 900 to 1100 MPa - E 0.2 - 650 to 850 MPa - A - 12 to 16%. resilience KCU = 80 to 140 J / cm2
- . if S is greater than 0.08% and less than or equal to 0.35% - R - 900 to 1100 MPa - E 0.2 - 650 to 850 MPa - A ≥ 10% - resilience KCU ≥ 40 J / cm2.
Les barres ou fil machine selon l'invention sont reconnaissables par l'ensemble de leurs caractéristiques mécaniques et de leur analyse. ces caractéristiques mécaniques étant singulières pour une telle analyse. Ils sont aussi caractérisés en complément par une proportion de ferrite dans la martensite inférieure à 30 % et typiquement comprise entre 15 et 25 %, ainsi que par un diamètre moyen de grain ou de phases (martensite et ferrite) équivalent à 5 à 10 ASTM (spécification ASTM E 112), soit 65 µm à 11 µm. Ces caractéristiques structurales sont en bonne partie responsables des caractéristiques mécaniques.The rods or wire rod according to the invention are recognizable by all of their mechanical characteristics and their analysis. these mechanical characteristics being singular for such an analysis. They are also characterized in addition by a proportion of ferrite in martensite less than 30% and typically between 15 and 25%, as well as by an average grain or phase diameter (martensite and ferrite) equivalent to 5 to 10 ASTM (specification ASTM E 112 ), i.e. 65 µm to 11 µm. These structural characteristics are largely responsible for the mechanical characteristics.
Les barres selon l'invention se présentent sous la forme de barres brutes de laminage à chaud, ou laminées à chaud puis dressées avec éventuellement une finition de surface, de diamètre ou épaisseur compris entre 15 et 250 mm et de préférence entre 15 et 120 mm.The bars according to the invention are in the form of raw hot rolling bars, or hot rolled then erected with optionally a surface finish, of diameter or thickness between 15 and 250 mm and preferably between 15 and 120 mm .
Le fil machine de diamètre compris entre 5 et 35 mm selon l'invention se présente habituellement en couronne ou en barres dressées. A la sortie du laminage à chaud final, le refroidissement est surtout fait en couronnes ou en spires décalées.The wire rod with a diameter between 5 and 35 mm according to the invention is usually in the form of a crown or erect bars. At the end of the final hot rolling, the cooling is mainly done in offset crowns or turns.
Les résultats de quatre séries d'essais et des examens complémentaires permettront de mieux comprendre l'invention et ses divers aspects.
- La figure 1 représente l'évolution de la proportion de ferrite en fonction de la température de préchauffage, dans le cas de la coulée (A) correspondant à la première série d'essais.
- La figure 2 situe les limites élastiques E 0,2 en fonction des % ferrite pour les barres obtenues dans les première et troisième séries d'essais.
- La figure 3 représente les domaines de teneurs extrêmes (C %, N %) des barres ou fils machine de l'invention.
- FIG. 1 represents the change in the proportion of ferrite as a function of the preheating temperature, in the case of the casting (A) corresponding to the first series of tests.
- Figure 2 locates the elastic limits E 0.2 as a function of the% ferrite for the bars obtained in the first and third series of tests.
- FIG. 3 represents the domains of extreme contents (C%, N%) of the bars or machine wires of the invention.
On a effectué une coulée (A) en carrés de 250 mm ayant pour analyse (% en poids) :
- C - 0,038 - N - 0,029 donc C + N = 0,067
- Cr - 12,36 - V - 0,032 - S - 0.016 - Si - 0,27 - Mn - 0,42
- Ni - 0,28 - Mo - 0,07 - P - 0,019 . Cu - 0,11 impuretés inevitables et Fe : le solde.
- C - 0.038 - N - 0.029 so C + N = 0.067
- Cr - 12.36 - V - 0.032 - S - 0.016 - Si - 0.27 - Mn - 0.42
- Ni - 0.28 - Mo - 0.07 - P - 0.019. Cu - 0.11 unavoidable impurities and Fe: the balance.
Le dégrossissage à chaud a été effectué au blooming comme d'habitude à 1200-1250°C environ, transformant les carrés de 250 mm en carrés de 148 mm.The hot roughing was carried out in blooming as usual at about 1200-1250 ° C, transforming the 250 mm squares into 148 mm squares.
Les carrés de 148 mm refroidis ont ensuite été préchauffés dans un four à diverses températures comme indiqué dans le tableau puis laminés à chaud en final par passes successives jusqu'aux diamètres portés dans le tableau et refroidies à l'air. D'après les mesures effectuées au pyromètre optique, on a estimé que la température des barres en fin de laminage était dans tous les cas comprise entre 950 et 1000°C.The cooled 148 mm squares were then preheated in an oven at various temperatures as indicated in the table and then hot-rolled in the final by successive passes to the diameters shown in the table and cooled in air. From the measurements carried out with an optical pyrometer, it was estimated that the temperature of the bars at the end of the rolling was in all cases between 950 and 1000 ° C.
Ces résultats montrent l'excellent niveau des caractéristiques mécaniques obtenues pour les barres A1 à A5 préchauffées selon les cas entre 1080 et 1160°C et laminées selon les cas entre 1150°C et 950°C (température des barres), avec une réduction de section S/s minimale dans le cas des barres "A5" et égale alors à :
La réduction de section maximale est celle des barres A1 Ø 20 mm avec S/s - 69.The maximum section reduction is that of the
Le cas des barres "A6" préchauffées à 1240"C et donc laminées à chaud à partir de 1220-1230°C montre bien l'effet néfaste sur la ductilité (A %, Z %) et sur la résilience KCU de cette surchauffe relative. Ce sont surtout les grains beaucoup plus grossiers à mi-rayon et à coeur que dans les barres préchauffées et laminées dans les conditions de l'invention qui expliquent ces mauvais résultats. Par comparaison avec les barres "A5", on voit que la limite élastique obtenue avec ces conditions de préchauffage et de laminage à chaud est également diminuée et que la charge de rupture semble aussi légèrement affectée.The case of "A6" bars preheated to 1240 "C and therefore hot rolled from 1220-1230 ° C clearly shows the harmful effect on the ductility (A%, Z%) and on the KCU resilience of this relative overheating It is above all the grains which are much coarser at mid-radius and at the core than in the preheated and rolled bars under the conditions of the invention which explain these poor results. By comparison with the bars "A5", it can be seen that the limit elastic obtained with these conditions of preheating and hot rolling is also reduced and that the breaking load also seems slightly affected.
Une grosse barre de la coulée A a été transformée par laminage et par forgeage en plats d'épaisseur 20 mm, dont des prélèvements ont été portés 30 mn à diverses températures de réchauffage ailant de 850 à 1300°C puis refroidies rapidement par trempe à l'eau. Sur chaque prélèvement, on a déterminé sur coupe micrographique la proportion de ferrite "α %" dans de la martensite. Les résultats sont portés sur la figure 1. La courbe (f) qui relie les points figuratifs appelle les commentaires suivants : pour cette coulée A et pour des prélèvements ainsi réchauffés et trempés, α % passe par un minimum (2 %) pour la température de réchauffage de 1050°C. Les teneurs en ferrite α % < 10 sont obtenues pour des températures de préchauffage comprises entre 950 et 1150°C. On a ainsi une indication qualitative : l'ajustement de la température de préchauffage et de laminage est certainement important pour le réglage de la teneur en ferrite. Il faut minimiser la teneur en ferrite pour obtenir une bonne résilience et une bonne résistance mécanique, donc préchauffer et laminer dans un intervalle de température restreint dépendant à la fois de cet effet dans les conditions dynamiques réelles et d'autres facteurs très importants : mise en solution et maintien en solution de C et de N pour aurcir ia matrice. obtention dune structure a grain fin (préchauffage et recristallisation au cours du laminage).A large bar from casting A was transformed by rolling and forging into 20 mm thick dishes, samples of which were brought 30 min to various heating temperatures ranging from 850 to 1300 ° C and then quickly cooled by quenching at 1 'water. On each sample, the proportion of "α%" ferrite in martensite was determined on a micrographic section. The results are shown in FIG. 1. The curve (f) which connects the figurative points calls for the following comments: for this flow A and for samples thus heated and quenched, α% passes through a minimum (2%) for the temperature 1050 ° C. The ferrite contents α% <10 are obtained for preheating temperatures between 950 and 1150 ° C. There is thus a qualitative indication: the adjustment of the preheating and rolling temperature is certainly important for the adjustment of the ferrite content. The ferrite content must be minimized to obtain good resilience and good mechanical resistance, therefore preheat and laminate in a limited temperature range depending on both of this effect under real dynamic conditions and other very important factors: dissolution and maintenance of C and N in solution to strengthen the matrix. obtaining a fine-grained structure (preheating and recrystallization during rolling).
On a élaboré une coulée (B) d'analyse (% en poids) :
- C - 0,050 - N - 0.038 donc C + N - 0,088 - Cr - 12,55
- S - 0,06 - Si - 0,34 - Mn - 0,45 - Ni - 0,19 - Mo - 0,05 - P - 0,019
- Cu - 0,11 - impuretés inévitables et Fe : le solde.
- C - 0.050 - N - 0.038 so C + N - 0.088 - Cr - 12.55
- S - 0.06 - Si - 0.34 - Mn - 0.45 - Ni - 0.19 - Mo - 0.05 - P - 0.019
- Cu - 0.11 - unavoidable impurities and Fe: the balance.
Les carrés coulés de 250 x 250 mm ont été transformés à chaud comme préalablement et on a effectué des essais semblables en partant de carrés de 148 mm, avec refroidissement à l'air des barres obtenues. La température des barres en fin de laminage était comprise entre 950 et 1000°C. Les températures de préchauffage et les caractéristiques mécaniques obtenues sur les barres sont rassemblées dans le Tableau ci-dessous :
Ces essais correspondant à une teneur (C + N) plus élevée que dans les premiers essais en sont une confirmation. La température de préchauffage de 1180°C pour "B4" affecte fortement la résilience KCU et plus faiblement mais de façon nette : d'abord la ductilité (A % et Z %), et ensuite surtout E 0,2. Le rapprochement ces résultats de "B4" et "A6" montre bien l'effet progressif de la "surchauffe" par rapport à la température de préchauffage limite de 1160°C (barres "A3") selon l'invention.These tests corresponding to a higher content (C + N) than in the first tests are a confirmation of this. The preheating temperature of 1180 ° C for "B4" strongly affects the resilience KCU and more weakly but clearly: first the ductility (A% and Z%), and then especially E 0.2. Reconciling these results with "B4" and "A6" clearly shows the progressive effect "overheating" with respect to the limit preheating temperature of 1160 ° C. (bars "A3") according to the invention.
On a porté les limites élastiques des barres des deux coulées (A) et (B) (première et troisième séries d'essais) sur le graphique de la figure 2.The elastic limits of the bars of the two flows (A) and (B) (first and third series of tests) have been plotted on the graph in FIG. 2.
Ce graphique montre que dans l'intervalle de teneur en ferrite α % de 18 à 35 %, une réduction de α % de 10 % correspond en moyenne à une augmentation de E 0,2 de environ 100 MPa.This graph shows that in the range of ferrite content α% from 18 to 35%, a reduction of α% of 10% corresponds on average to an increase of E 0.2 of approximately 100 MPa.
On a testé un acier (D) à teneur en (C - N) plus élevée que celles de l'invention, d'analyse :
- C = 0,105 - N = 0,039 donc C + N = 0,144 - Cr - 12,19 - Nb - 0,073 - V = 0,073 - S - 0,015 - Si - 0,41 . Mn - 0,92 - Ni - 0,18 - Mo - 0,46 - P - 0,021 - Al - 0,02 - impuretés et Fe : le solde.
- C = 0.105 - N = 0.039 therefore C + N = 0.144 - Cr - 12.19 - Nb - 0.073 - V = 0.073 - S - 0.015 - Si - 0.41. Mn - 0.92 - Ni - 0.18 - Mo - 0.46 - P - 0.021 - Al - 0.02 - impurities and Fe: the balance.
Cet acier a été laminé en barres Ø 80 mm à 1100°C avec un rapport "S/s" de 4. Les caractéristiques mécaniques obtenues sur ces barres sont :
- R - 1210 MPa - E 0,2 - 1060 MPa - A - 15 % striction Z % - 60 - KCU 5-10 J/cm2.
- R - 1210 MPa - E 0.2 - 1060 MPa - A - 15% necking Z% - 60 - KCU 5-10 J / cm2.
On obtient donc avec (C + N) aussi éievé une résilience très faible, et lorsque (C + N), et encore plus à la fois (C + N) et S, augmentent il s'ajoute à cette résilience très faible un risque de tapure pour les barres.We thus obtain with (C + N) also a very low resilience, and when (C + N), and even more at the same time (C + N) and S, increase, there is added to this very low resilience a risk of tapure for the bars.
La figure 3 situe d'une part les points figuratifs (C %, N %) des coulées (A) - (B) et (D), d'autre part le domaine (E) de teneurs (C %, N%) selon l'invention ainsi que le domaine préférentiel (F) le plus étroit.Figure 3 locates on the one hand the figurative points (C%, N%) of the flows (A) - (B) and (D), on the other hand the domain (E) of contents (C%, N%) according to the invention as well as the narrowest preferential domain (F).
Le durcissement des barres, traduit par l'augmentation de R et de E 0,2, dépend de façon importante de la teneur en (C + N) dissous. De petites additions de Nb ≤ 0,1 % et/ou de V ≤ 0,1 % jouent également un rôle durcisseur. Dans le cas des barres (D), les bonnes caractéristiques R et E 0,2 sont liées à la teneur en (C + N) élevée et aux petites additions de Nb et de V, mais les teneurs en (C. N) sont en dehors du domaine de l'invention et la résilience est très faible.The hardening of the bars, reflected by the increase in R and E 0.2, depends significantly on the content of (C + N) dissolved. Small additions of Nb ≤ 0.1% and / or V ≤ 0.1% also play a hardening role. In the case of the bars (D), the good characteristics R and E 0.2 are linked to the high content of (C + N) and to the small additions of Nb and of V, but the contents in (C. N) are outside the scope of the invention and the resilience is very low.
On a vu par ailleurs dans les première et troisième séries d'essais l'influence de la température de préchauffage et de laminage à chaud final lorsqu'on est dans le domaine de compositions de l'invention. Par comparaison avec le traitement de trempe classique, qui comporte typiquement un chauffage de mise en solution entre 950 et 1050°C, l'effet de ce préchauffage et de ce laminage à chaud selon l'invention est de dissoudre au mieux (C et N) et de les maintenir au mieux en solution. Tandis que l'accroissement de C augmente en outre légèrement la trempabilité, l'accroissement de N peut contribuer à la finesse du grain de recristallisation au cours du laminage grâce à la précipitation de petits nitrures.We have also seen in the first and third series of tests the influence of the preheating temperature and final hot rolling when one is in the field of compositions of the invention. By comparison with the conventional quenching treatment, which typically comprises a heating for dissolving between 950 and 1050 ° C., the effect of this preheating and of this hot rolling according to the invention is to dissolve at best (C and N ) and to keep them as well as possible in solution. While the increase in C also slightly increases the hardenability, the increase in N can contribute to the fineness of the recrystallization grain during rolling thanks to the precipitation of small nitrides.
Les effets métallurgiques de C, N, C + N et des températures de préchauffage et de laminage paraissent ainsi complexes et "enchevêtrés", car ils influencent à des degrés divers :
- - la taille de grain,
- - la proportion de ferrite dans la martensite,
- - la dureté de la matrice,
dont le rôle paraît important pour comprendre qualitativement les résultats surprenants de l'invention. L'ajustement de (C + N) est un facteur particulièrement important.The metallurgical effects of C, N, C + N and the preheating and rolling temperatures thus appear complex and "entangled", because they influence in varying degrees:
- - grain size,
- - the proportion of ferrite in martensite,
- - the hardness of the matrix,
whose role seems important to understand qualitatively the surprising results of the invention. The adjustment of (C + N) is a particularly important factor.
Le procédé est particulièrement adapté à la production de barres ou fil machine avec des moyens de laminage à chaud en continu.The process is particularly suitable for the production of rods or wire rod with continuous hot rolling means.
Les barres ou fils machine de l'invention sont utilisés notamment pour la fabrication de pièces mécaniques résistant à la corrosion, travaillant au contact de l'eau, de la vapeur d'eau, de vin ou de bière : telles que des arbres, pistons, chemises, vannes ou pièces de boulonnerie.The bars or machine wires of the invention are used in particular for the manufacture of mechanical parts resistant to corrosion, working in contact water, steam, wine or beer: such as trees, pistons, liners, valves or hardware.
Claims (10)
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
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AT85420123T ATE49238T1 (en) | 1984-07-04 | 1985-07-03 | PROCESSES FOR THE MANUFACTURE OF MARTENSITIC STAINLESS STEEL BARS OR WIRE ROD AND ARTICLES SO MANUFACTURED. |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR8411050 | 1984-07-04 | ||
FR8411050A FR2567151B1 (en) | 1984-07-04 | 1984-07-04 | METHOD FOR MANUFACTURING MARTENSITIC STAINLESS STEEL BARS OR MACHINE WIRE AND CORRESPONDING PRODUCTS |
Publications (2)
Publication Number | Publication Date |
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EP0170598A1 true EP0170598A1 (en) | 1986-02-05 |
EP0170598B1 EP0170598B1 (en) | 1990-01-03 |
Family
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EP85420123A Expired - Lifetime EP0170598B1 (en) | 1984-07-04 | 1985-07-03 | Process for manufacturing hot-rolled martensitic stainless steel rods or rod wire, and products obtained |
Country Status (6)
Country | Link |
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US (1) | US4594115A (en) |
EP (1) | EP0170598B1 (en) |
JP (1) | JPS6119734A (en) |
AT (1) | ATE49238T1 (en) |
CA (1) | CA1254062A (en) |
FR (1) | FR2567151B1 (en) |
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EP0508574A1 (en) * | 1991-04-11 | 1992-10-14 | Crucible Materials Corporation | Martensitic stainless steel article and method for producing the same |
EP0945520A1 (en) * | 1998-03-23 | 1999-09-29 | Hans Kohler AG | High strenght, corrosion resistant steel for employment in construction, geotechnology and general engineering applications |
EP1233080A1 (en) * | 2001-02-14 | 2002-08-21 | BÖHLER Edelstahl GmbH | Steel for plastic molds and process of heat treatment thereof |
US6488813B2 (en) * | 2000-08-01 | 2002-12-03 | Dai-Ichi Kogyo Seiyaku Co., Ltd. | Blocked urethane prepolymers as paper wet strength agent |
CN102676941A (en) * | 2012-04-25 | 2012-09-19 | 李小强 | Tungsten carbide particle-reinforced wear-resistant corrosion-resistant stainless steel and preparation method thereof |
WO2017182896A1 (en) * | 2016-04-22 | 2017-10-26 | Aperam | A process for manufacturing a martensitic stainless steel part from a sheet |
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US11478873B2 (en) | 2017-06-30 | 2022-10-25 | Aperam | Method for welding using points of martensitic stainless steel sheets |
Also Published As
Publication number | Publication date |
---|---|
FR2567151A1 (en) | 1986-01-10 |
EP0170598B1 (en) | 1990-01-03 |
US4594115A (en) | 1986-06-10 |
JPS6119734A (en) | 1986-01-28 |
FR2567151B1 (en) | 1986-11-21 |
CA1254062A (en) | 1989-05-16 |
ATE49238T1 (en) | 1990-01-15 |
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