EP0527276B1 - An abrasion resistant steel - Google Patents

An abrasion resistant steel Download PDF

Info

Publication number
EP0527276B1
EP0527276B1 EP91307390A EP91307390A EP0527276B1 EP 0527276 B1 EP0527276 B1 EP 0527276B1 EP 91307390 A EP91307390 A EP 91307390A EP 91307390 A EP91307390 A EP 91307390A EP 0527276 B1 EP0527276 B1 EP 0527276B1
Authority
EP
European Patent Office
Prior art keywords
steel
abrasion
abrasion resistant
resistant steel
content
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Lifetime
Application number
EP91307390A
Other languages
German (de)
French (fr)
Other versions
EP0527276A1 (en
Inventor
Nobuo c/o Patent & License Dept. Shikanai
Tetsuya c/o Patent & License Dept. Sanpei
Kazunori c/o Patent & License Dept. Yako
Kenji c/o Patent & License Dept. Hirabe
Yasunobu c/o Patent & License Dept. Kunisada
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
JFE Engineering Corp
Original Assignee
NKK Corp
Nippon Kokan Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by NKK Corp, Nippon Kokan Ltd filed Critical NKK Corp
Priority to DE1991624234 priority Critical patent/DE69124234T2/en
Priority claimed from EP95120542A external-priority patent/EP0714990A1/en
Publication of EP0527276A1 publication Critical patent/EP0527276A1/en
Application granted granted Critical
Publication of EP0527276B1 publication Critical patent/EP0527276B1/en
Anticipated expiration legal-status Critical
Expired - Lifetime legal-status Critical Current

Links

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
    • C21D8/00—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
    • 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
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium

Definitions

  • the invention relates to the field of metallurgy and particularly relates to the field of an abrasion resistant steel utilized in the field of construction, civil engineering and mining.
  • Abrasion resistant steels are utilized in the field of construction, civil engineering and mining such as in power shovel, bulldozer, hopper and bucket to keep the lives of these machines or their parts. It is well known that the steel having high hardness possesses high abrasion resistance property. For this purpose a high alloyed steel treated by quenching has commonly been utilized.
  • Japanese Patent laid open Publication Nos. 142726/19 87, 169359/1988 and 142023/1989 disclose the information about the production of the conventional abrasion resistant steel.
  • the Brinell Hardness of the steel is more than 300.
  • the improvements are aimed at the weldability, the toughness and the workability in bending, and the abrasion resistance property is realized by increasing the hardness of the steel.
  • CH-A-377540 and SU-A-271807 also relate to abrasion resistant steel compositions, consisting of: 0.15-0.3%C, 0.6-1.0%Si, 0.35-0.8% Mn, 0.1-0.6%Ti balance Fe or 0.29-0.32%C, 0.6-0.9%Si, 0.8-1.2%Mn, 0.45-0.70%Ti, balance Fe and incidental impurities, respectively.
  • the property required for the abrasion resistant steel has recently become severer and the essential solution to higher abrasion resistance of steel will not be obtained by simply enhancing the hardness of steel.
  • the hardness of steel is significantly enhanced, the weldability and the workability of steel are deteriorated due to the high alloying and the cost of producing such steels increases significantly. Accordingly in the practical point of view the significant increase in the hardness of abrasion resistant steel is facing with a difficulty with respect to the workability of the steel.
  • an abrasion resistant steel having an excellent abrasion resistance property without considerably increasing the hardness of steel.
  • an abrasion resistant steel comprises 0.2 to 0.35 wt.% C, 0.1 to 1.0 wt.% Si, 0.1 to 2.0 wt.% Mn, 0.3 to 1.0 wt.% Ti and the balance Fe as the basic elements contributing to the enhancement of the abrasion resistance property.
  • At least one element selected from the group consisting of 0.1 to 2.0 wt.% Cu, 0.1 to 10.0 wt.% Ni, 0.1 to 3.0 wt.% Cr, 0.1 to 3.0 wt.% Mo and 0.0003 to 0.01 wt.% B is added to enhance the quenching hardenability of the steel, and at least one element selected from the group consisting of 0.005 to 0.5 wt.% Nb, 0.01 to 0.5 wt% V may be added to enhance the precipitation hardenability of the steel.
  • Figure 1 is a graph showing the relationship between the added quantity of titanium and the ratio of resistance to abrasion.
  • the most significant characteristic of the invented steel is effectively utilizing of very hard TiC.
  • the purpose of the addition of titanium to steel is to react with the nitrogen so that the nitrogen is stabilized as TiN.
  • boron does not react with nitrogen since there is not enough nitrogen in the steel, and retained in the steel as a soluble boron, which enhances the quenching hardenability.
  • the quantity of the addition in this case is about 0.02 wt.% of steel.
  • the addition of a large quantity of titanium to steel is limited by the oxidation of the titanium in the steel melting stage, the clogging of the nozzle and the reaction with the oxidation preventing powder in the casting stage. Therefore the effect of the addition of a large quantity of titanium is not yet known.
  • Figure 1 is a graph showing the relationship between the added quantity of titanium and the ratio of resistance to abrasion.
  • the abscissa denotes the added quantity of titanium and the ordinate denotes the ratio of resistance to abrasion.
  • the ratio of resistance to abrasion is an index wherein the resistance to abrasion of an abrasion resistant steel is divided by that of a mild steel.
  • the resistance to abrasion is measured according to ASTM Standard G 65-85 wherein an abrasive is introduced between the test specimen and a rotating wheel with a chlorobutyl rubber tire.
  • the abrasive is a sand composed of 100% silica and of controlled size.
  • the C content of the test specimen is 0.3 wt.% and the specimen is heat treated by quenching.
  • the Brinell Hardness is below 500.
  • the ratio of resistance to abrasion linearly increases with the increase of the added quantity of titanium up to 0.5 wt.%.
  • C is an indispensable element in forming TiC and also enhances the hardness of the matrix of steel. However when C is increased too much, the weldability and the workability are deteriorated. Therefore the upper limit of C is determined to be 0.35 wt.%. As for the lower limit of C the minimum quantity of C wherein the effect of TiC is shown is 0.2 wt.%.
  • Si is an element effective in deoxidation process of steel making and a minimum addition of 0.1 wt.% is required for this purpose. Si is also an effective element for solution hardening. However when the Si content exceeds 1.0 wt.%, the toughness of steel is lowered and the inclusion in steel is increased. Therefore the Si content is determined to be 0.1 to 1.0 wt.%.
  • Mn is an element effective in quenching hardenability. At least 0.1 wt.% is required for this purpose. When the Mn content exceeds 2.0 wt.%, the weldability of steel is deteriorated. Therefore the Mn content is determined to be 0.1 to 2.0 wt.%.
  • Ti is one of the most important element as is C.
  • the addition of at least 0.3 wt.% of Ti is required to stably form a large quantity of TiC.
  • the Ti content exceeds 1.0 wt.%, the steel possesses good abrasion resistance property but high cost is required for the production, also the weldability and the workability of steel are lowered. Therefore the Ti content is required to be 0.3 to 1.0 wt.%.
  • At least one element selected from the group consisting of Cu, Ni, Cr, Mo and B is added to enhance the quenching hardenability and at least one element selected from the group consisting of Nb and V may be added to enhance the precipitation hardening.
  • Cu is an element for enhancing the quenching hardenability and effective in controlling the hardness of steel.
  • the Cu content is below 0.1 wt.%, the effect is not sufficient.
  • the Cu content exceeds 2.0 wt.%, the hot workability is lowered and the production cost is increased. Therefore the Cu content is determined to be 0.1 to 2.0 wt.%.
  • Ni is an element which enhances the quenching hardenability and the low temperature toughness. When the Ni content is below 0.1 wt.%, the effect is not sufficient. When the Ni content exceeds 10.0 wt.%, the production cost is increased significantly. Therefore the Ni content is determined to be 0.1 to 10.0 wt.%.
  • Cr is an element which enhances the quenching hardenability.
  • the Cr content is below 0.1 wt.%, the effect is not sufficient.
  • the Cr content exceeds 3.0 wt.%, the weldability is deteriorated, and the production cost is increased. Therefore the Cr content is determined to be 0.1 to 3.0 wt.%.
  • Mo is an element which enhances the quenching hardenability. When the Mo content is below 0.1 wt.%, the effect is not sufficient. When the Mo content exceeds 3.0 wt.%, the weldability is deteriorated, and the production cost is increased. Therefore the Mo content is determined to be 0.1 to 3.0 wt.%.
  • B is an element which enhances the quenching hardenability by the addition to steel even by a small amount.
  • the B content is below 0.0003 wt.% , the effect is not sufficient.
  • the B content exceeds 0.01 wt.%, the weldability is deteriorated, and the quenching hardenability is also deteriorated. Therefore the B content is determined to be 0.0003 to 0.01 wt.%.
  • Nb is an element effective in the precipitation hardening and can control the hardness of steel according to the purpose of steel.
  • the Nb content is below 0.005 wt.%, the effect is not sufficient.
  • the Nb content exceeds 0.5 wt.%, the weldability is deteriorated. Therefore the Nb content is determined to be 0.005 to 0.5 wt.%.
  • V is an element effective in the precipitation hardening and can control the hardness of steel according to the purpose of steel.
  • the V content is below 0.01 wt.%, the effect is not sufficient.
  • the V content exceeds 0.5 wt.%, the weldability is deteriorated. Therefore the V content is determined to be 0.01 to 0.5 wt.%.
  • Table 1 shows the chemical compositions of the samples of the invented and conventional steel.
  • Sanples E, J, N are made of the invented steel, whereas samples marked with an asterisk are made of the steel for comparison.
  • the chemical composition of the samples from P to R varies with respect to Ti and other alloying elements.
  • the chemical compositions of the samples P and Q are within the same range with those of the invented steel except that of Ti.
  • the chemical composition of the sample R is within the same range of the invented steel with respect to Ti, but out of the range with respect to C.
  • Table 2 shows the process of making the samples, the ratio of the resistance to abrasion and the Brinell Hardness of the samples. Samples B, C, E, I, J, N are made of the invented steel, whereas samples marked with an asterisk are made of the steel for comparison.
  • the abrasion test is carried out according to ASTM G 65-85 as described before.
  • the measurement of the abrasion is done by the change of the weight of the sample.
  • the ratio of resistance to abrasion is the ratio of the weight change of the specimen made of the invented steel versus that of the specimen made of a mild steel.
  • the processes in the table are classified as follows ; AR, as rolled; RQ, as quenched after heated to 900 °C following the rolling and air-cooling; RQT, as tempered at the temperature shown in the parenthesis after RQ treatment; DQ, as directly quenched after finish rolled at 880 °C following the heating of the slab at 1150 °C; DQT, as tempered at the temperature shown in the parenthesis following DQ.
  • the thickness of the sample is 15 mm.
  • the kind of steel in Table 1 corresponds with those in Table 2.
  • the steel for comparison P corresponds with the invented steel B-1 except that the Ti content is below the range of the invented steel. Examining the ratio of the resistance to abrasion, it is found that the ratio is 4.9 in the steel for comparison P, whereas the ratio of the invented steel B-1 is 8.3.
  • the ratio of the invented steel can be enhanced twice as much as that of the steel for comparison which is a conventional abrasion resistant steel. Moreover the hardness of the invented steel is lower than those of the steel for comparison.
  • the steel for comparison Q corresponds with the invented steel N.
  • the ratios of the resistance to abrasion in N are higher than that of Q.
  • the steel for comparison R corresponds with the invented steel B-1.
  • the C content of the steel for comparison R is below the range of the invented steel. Since the C content of the steel R is so low that the ratio of the resistance to abrasion is significantly lower than that of B-1.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Steel (AREA)
  • Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)

Description

  • The invention relates to the field of metallurgy and particularly relates to the field of an abrasion resistant steel utilized in the field of construction, civil engineering and mining.
  • Abrasion resistant steels are utilized in the field of construction, civil engineering and mining such as in power shovel, bulldozer, hopper and bucket to keep the lives of these machines or their parts. It is well known that the steel having high hardness possesses high abrasion resistance property. For this purpose a high alloyed steel treated by quenching has commonly been utilized.
  • Japanese Patent laid open Publication Nos. 142726/19 87, 169359/1988 and 142023/1989 disclose the information about the production of the conventional abrasion resistant steel. In these inventions the Brinell Hardness of the steel is more than 300. The improvements are aimed at the weldability, the toughness and the workability in bending, and the abrasion resistance property is realized by increasing the hardness of the steel.
  • CH-A-377540 and SU-A-271807 also relate to abrasion resistant steel compositions, consisting of: 0.15-0.3%C, 0.6-1.0%Si, 0.35-0.8% Mn, 0.1-0.6%Ti balance Fe or 0.29-0.32%C, 0.6-0.9%Si, 0.8-1.2%Mn, 0.45-0.70%Ti, balance Fe and incidental impurities, respectively.
  • However the property required for the abrasion resistant steel has recently become severer and the essential solution to higher abrasion resistance of steel will not be obtained by simply enhancing the hardness of steel. When the hardness of steel is significantly enhanced, the weldability and the workability of steel are deteriorated due to the high alloying and the cost of producing such steels increases significantly. Accordingly in the practical point of view the significant increase in the hardness of abrasion resistant steel is facing with a difficulty with respect to the workability of the steel.
  • It is an object of the invention to provide an abrasion resistant steel.
  • It is an object of the invention to provide an abrasion resistant steel having an excellent abrasion resistance property without considerably increasing the hardness of steel. According to the invention an abrasion resistant steel comprises 0.2 to 0.35 wt.% C, 0.1 to 1.0 wt.% Si, 0.1 to 2.0 wt.% Mn, 0.3 to 1.0 wt.% Ti and the balance Fe as the basic elements contributing to the enhancement of the abrasion resistance property.
  • In addition to the basic elements, at least one element selected from the group consisting of 0.1 to 2.0 wt.% Cu, 0.1 to 10.0 wt.% Ni, 0.1 to 3.0 wt.% Cr, 0.1 to 3.0 wt.% Mo and 0.0003 to 0.01 wt.% B is added to enhance the quenching hardenability of the steel, and at least one element selected from the group consisting of 0.005 to 0.5 wt.% Nb, 0.01 to 0.5 wt% V may be added to enhance the precipitation hardenability of the steel.
  • Figure 1 is a graph showing the relationship between the added quantity of titanium and the ratio of resistance to abrasion.
  • The most significant characteristic of the invented steel is effectively utilizing of very hard TiC. In this invention it is not necessary to enhance the hardness of the abrasion resistant steel only by transforming the microstructure of the steel to a martensite which is the conventional way to enhance the abrasion resistance of steel.
  • In the conventional way the purpose of the addition of titanium to steel is to react with the nitrogen so that the nitrogen is stabilized as TiN. As the result boron does not react with nitrogen since there is not enough nitrogen in the steel, and retained in the steel as a soluble boron, which enhances the quenching hardenability.The quantity of the addition in this case is about 0.02 wt.% of steel. The addition of a large quantity of titanium to steel is limited by the oxidation of the titanium in the steel melting stage, the clogging of the nozzle and the reaction with the oxidation preventing powder in the casting stage. Therefore the effect of the addition of a large quantity of titanium is not yet known.
  • The inventors after detailed examination found that the addition of titanium in a large quantity realizes the improvement of steel with respect to the abrasion resistance property.
  • Figure 1 is a graph showing the relationship between the added quantity of titanium and the ratio of resistance to abrasion. The abscissa denotes the added quantity of titanium and the ordinate denotes the ratio of resistance to abrasion.
  • The ratio of resistance to abrasion is an index wherein the resistance to abrasion of an abrasion resistant steel is divided by that of a mild steel. The resistance to abrasion is measured according to ASTM Standard G 65-85 wherein an abrasive is introduced between the test specimen and a rotating wheel with a chlorobutyl rubber tire. The abrasive is a sand composed of 100% silica and of controlled size. The C content of the test specimen is 0.3 wt.% and the specimen is heat treated by quenching. The Brinell Hardness is below 500.
    As shown in Figure 1, the ratio of resistance to abrasion linearly increases with the increase of the added quantity of titanium up to 0.5 wt.%.
  • The followings are the reason why the contents of the elements of the invented steel is specified.
  • C is an indispensable element in forming TiC and also enhances the hardness of the matrix of steel. However when C is increased too much, the weldability and the workability are deteriorated. Therefore the upper limit of C is determined to be 0.35 wt.%. As for the lower limit of C the minimum quantity of C wherein the effect of TiC is shown is 0.2 wt.%.
  • This is the optimum range with respect to the balance of the bending workability and the weldability of the steel and the stable abrasion resistance thereof.
  • Si is an element effective in deoxidation process of steel making and a minimum addition of 0.1 wt.% is required for this purpose. Si is also an effective element for solution hardening. However when the Si content exceeds 1.0 wt.%, the toughness of steel is lowered and the inclusion in steel is increased. Therefore the Si content is determined to be 0.1 to 1.0 wt.%.
  • Mn is an element effective in quenching hardenability. At least 0.1 wt.% is required for this purpose. When the Mn content exceeds 2.0 wt.%, the weldability of steel is deteriorated. Therefore the Mn content is determined to be 0.1 to 2.0 wt.%.
  • In this invention Ti is one of the most important element as is C. The addition of at least 0.3 wt.% of Ti is required to stably form a large quantity of TiC. When the Ti content exceeds 1.0 wt.%, the steel possesses good abrasion resistance property but high cost is required for the production, also the weldability and the workability of steel are lowered. Therefore the Ti content is required to be 0.3 to 1.0 wt.%.
  • This is the optimum range with respect to the balance of the stable abrasion resistance and the economy of the steel.
  • In this invention, in addition to the above basic elements, at least one element selected from the group consisting of Cu, Ni, Cr, Mo and B is added to enhance the quenching hardenability and at least one element selected from the group consisting of Nb and V may be added to enhance the precipitation hardening.
  • Cu is an element for enhancing the quenching hardenability and effective in controlling the hardness of steel. When the Cu content is below 0.1 wt.%, the effect is not sufficient. When the Cu content exceeds 2.0 wt.%, the hot workability is lowered and the production cost is increased. Therefore the Cu content is determined to be 0.1 to 2.0 wt.%.
  • Ni is an element which enhances the quenching hardenability and the low temperature toughness. When the Ni content is below 0.1 wt.%, the effect is not sufficient. When the Ni content exceeds 10.0 wt.%, the production cost is increased significantly. Therefore the Ni content is determined to be 0.1 to 10.0 wt.%.
  • Cr is an element which enhances the quenching hardenability. When the Cr content is below 0.1 wt.%, the effect is not sufficient. When the Cr content exceeds 3.0 wt.%, the weldability is deteriorated, and the production cost is increased. Therefore the Cr content is determined to be 0.1 to 3.0 wt.%.
  • Mo is an element which enhances the quenching hardenability. When the Mo content is below 0.1 wt.%, the effect is not sufficient. When the Mo content exceeds 3.0 wt.%, the weldability is deteriorated, and the production cost is increased. Therefore the Mo content is determined to be 0.1 to 3.0 wt.%.
  • B is an element which enhances the quenching hardenability by the addition to steel even by a small amount. When the B content is below 0.0003 wt.% , the effect is not sufficient. When the B content exceeds 0.01 wt.%, the weldability is deteriorated, and the quenching hardenability is also deteriorated. Therefore the B content is determined to be 0.0003 to 0.01 wt.%.
  • Nb is an element effective in the precipitation hardening and can control the hardness of steel according to the purpose of steel. When the Nb content is below 0.005 wt.%, the effect is not sufficient. When the Nb content exceeds 0.5 wt.%, the weldability is deteriorated. Therefore the Nb content is determined to be 0.005 to 0.5 wt.%.
  • V is an element effective in the precipitation hardening and can control the hardness of steel according to the purpose of steel. When the V content is below 0.01 wt.%, the effect is not sufficient. When the V content exceeds 0.5 wt.%, the weldability is deteriorated. Therefore the V content is determined to be 0.01 to 0.5 wt.%.
  • In this invention no specification is required as for the method of working the steel and as for the method of heat treating of the steel. The invention may not be inoperable by heat treatments such as quenching, annealing, aging and stress relief annealing.
    • EXAMPLE
  • Table 1 shows the chemical compositions of the samples of the invented and conventional steel.
  • Sanples E, J, N are made of the invented steel, whereas samples marked with an asterisk are made of the steel for comparison. The chemical composition of the samples from P to R varies with respect to Ti and other alloying elements. The chemical compositions of the samples P and Q are within the same range with those of the invented steel except that of Ti. The chemical composition of the sample R is within the same range of the invented steel with respect to Ti, but out of the range with respect to C. Table 1
    Kind of Steel C Si Mn Cu Ni Cr Mo Nb V Ti B N
    *A 0.30 0.36 0.70 - - - - - - 0.09 - 33
    *B 0.28 0.37 0.73 - - - - - - 0.37 - 38
    *C 0.29 0.37 0.74 - - - - - - 0.98 - 36
    *D 0.29 0.36 0.71 - - - - - - 1.41 - 30
    E 0.28 0.36 0.71 0.24 0.29 - - - - 0.40 - 31
    *F 0.31 0.33 0.73 - - 1.02 0.23 - - 1.08 10 32
    *G 0.19 0.33 1.44 - - 0.27 - - - 0.65 9 22
    *H 0.14 0.34 1.40 - - - - 0.025 - 0.40 - 24
    *I 0.32 0.34 0.72 - - - - - 0.045 0.41 - 21
    J 0.34 0.26 1.01 0.35 0.55 - - 0.028 0.041 0.54 - 42
    *K 0.31 0.38 0.71 - - 0.99 0.23 0.022 0.044 0.06 8 24
    *L 0.29 0.38 0.70 - - 0.99 0.23 - 0.044 0.08 9 23
    *M 0.30 0.36 0.71 0.25 - 0,55 0.23 - 0,045 0.19 8 30
    N 0.31 0.36 0.71 - - 1.02 0.23 - 0.045 0.38 8 31
    *O 0.31 0.33 0.73 - 0.36 0.63 0.34 - - 1.28 - 32
    *P 0.30 0.30 0.75 - - - - - - 0.02 - 37
    *Q 0.30 0.30 0.96 - - 1.03 0.21 - 0.045 0.01 11 47
    *R 0.03 0.30 0.75 - - - - - - 0.47 - 37
    Note: The values are in wt.% except B and N. The values of B and N are in ppm.
    Table 2.
    Process Ratio of resistance to abrasion Brinell Hardness (HB)
    * A RQ 6.5 474
    *B-1 RQ 8.3 393
    *B-2 RQT (400°C ) 6.1 277
    *C-1 DQ 9.7 335
    *C-2 DQT(400°C) 6.8 245
    * D RQ 9.3 242
    E RQ 8.6 390
    * F RQ 9.1 321
    * G RQ 4.7 302
    * H DQ 3.4 253
    * I RQ 10.1 451
    J DQ 8.9 417
    * K RQ 6.4 503
    *L-1 AR 4.5 293
    *L-2 DQ 8.2 507
    *M-1 AR 4.7 286
    *M-2 DQ 9.1 454
    N-1 AR 6.1 274
    N-2 RQ 11.6 448
    *O-1 AR 7.3 246
    *O-2 RQ 11.1 275
    * P RQ 4.9 464
    *Q-1 AR 2.8 326
    *Q-2 RQ 5.2 481
    * R RQ 1.2 122
  • Table 2 shows the process of making the samples, the ratio of the resistance to abrasion and the Brinell Hardness of the samples. Samples B, C, E, I, J, N are made of the invented steel, whereas samples marked with an asterisk are made of the steel for comparison.
  • The abrasion test is carried out according to ASTM G 65-85 as described before. The measurement of the abrasion is done by the change of the weight of the sample.
  • As described before the ratio of resistance to abrasion is the ratio of the weight change of the specimen made of the invented steel versus that of the specimen made of a mild steel.
  • The processes in the table are classified as follows ; AR, as rolled; RQ, as quenched after heated to 900 °C following the rolling and air-cooling; RQT, as tempered at the temperature shown in the parenthesis after RQ treatment; DQ, as directly quenched after finish rolled at 880 °C following the heating of the slab at 1150 °C; DQT, as tempered at the temperature shown in the parenthesis following DQ. The thickness of the sample is 15 mm. The kind of steel in Table 1 corresponds with those in Table 2.
  • The steel for comparison P corresponds with the invented steel B-1 except that the Ti content is below the range of the invented steel. Examining the ratio of the resistance to abrasion, it is found that the ratio is 4.9 in the steel for comparison P, whereas the ratio of the invented steel B-1 is 8.3.
  • This is to say that the ratio of the invented steel can be enhanced twice as much as that of the steel for comparison which is a conventional abrasion resistant steel. Moreover the hardness of the invented steel is lower than those of the steel for comparison.
  • This result agrees with the purpose of the invention wherein the invented steel possesses high resistance to abrasion and low hardness.
  • The steel for comparison Q corresponds with the invented steel N. The ratios of the resistance to abrasion in N are higher than that of Q.
  • The steel for comparison R corresponds with the invented steel B-1. The C content of the steel for comparison R is below the range of the invented steel. Since the C content of the steel R is so low that the ratio of the resistance to abrasion is significantly lower than that of B-1.

Claims (6)

  1. An abrasion resistant steel comprising the following constituents in proportions by weight:
    C   0.2 to 0.35 %
    Si   0.1 to 1.0 %
    Mn   0.1 to 2.0 %
    Ti   0.3 to 1.0 %
    and one or more quench hardening constituents from the group consisting of copper, nickel, chromium, molybdenum and boron in the following proportions by weight:
    Cu   0.1 to 2.0 %
    Ni   0.1 to 10.0 %
    Cr   0.1 to 3.0 %
    Mo   0.1 to 3.0 %
    B   0.0003 to 0.01 %
    and optionally comprising one or more precipitation hardening constituents from the group consisting of niobium and vanadium in the following proportions by weight:
    Nb   0.005 to 0.5 %
    V   0.01 to 0.5 %
    wherein the balance is Fe plus incidental impurities, if any.
  2. An abrasion resistant steel as claimed in claim 1 further characterised in that the quench hardening constituent is boron in the following proportions by weight:
    B   0.0003 to 0.01 %.
  3. An abrasion resistant steel as claimed in claim 1 further characterised in that the quench hardening constituent is copper in the following proportions by weight:
    Cu   0.1 to 2.0 %.
  4. An abrasion resistant steel as claimed in claim 1 further characterised in that the quench hardening constituent is nickel in the following proportions by weight:
    Ni   0.1 to 10.0 %.
  5. An abrasion resistant steel as claimed in claim 1 further characterised in that the quench hardening constituent is chromium in the following proportions by weight:
    Cr   0.1 to 3.0 %.
  6. An abrasion resistant steel as claimed in claim 1 further characterised in that the quench hardening constituent is molybdenum in the following proportions by weight:
    Mo   0.1 to 3.0 %.
EP91307390A 1990-06-06 1991-08-12 An abrasion resistant steel Expired - Lifetime EP0527276B1 (en)

Priority Applications (1)

Application Number Priority Date Filing Date Title
DE1991624234 DE69124234T2 (en) 1991-08-12 1991-08-12 Abrasion resistant steel

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
JP14840090 1990-06-06
JP2148399A JPH0441616A (en) 1990-06-06 1990-06-06 Production of low-hardness water-resistant steel excellent in wear resistance and bendability
EP95120542A EP0714990A1 (en) 1990-06-06 1991-08-12 Method for making an abrasion resistant steel

Publications (2)

Publication Number Publication Date
EP0527276A1 EP0527276A1 (en) 1993-02-17
EP0527276B1 true EP0527276B1 (en) 1997-01-15

Family

ID=40276095

Family Applications (2)

Application Number Title Priority Date Filing Date
EP91307393A Expired - Lifetime EP0527277B1 (en) 1990-06-06 1991-08-12 Method of making an abrasion resistant steel
EP91307390A Expired - Lifetime EP0527276B1 (en) 1990-06-06 1991-08-12 An abrasion resistant steel

Family Applications Before (1)

Application Number Title Priority Date Filing Date
EP91307393A Expired - Lifetime EP0527277B1 (en) 1990-06-06 1991-08-12 Method of making an abrasion resistant steel

Country Status (6)

Country Link
EP (2) EP0527277B1 (en)
JP (1) JPH0441616A (en)
AU (4) AU632187B2 (en)
CA (2) CA2033267C (en)
FI (2) FI93863C (en)
GB (2) GB2244718A (en)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2222630C1 (en) * 2002-08-21 2004-01-27 ООО "Сорби стил" Steel for gas and oil pipelines

Families Citing this family (22)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0441616A (en) * 1990-06-06 1992-02-12 Nkk Corp Production of low-hardness water-resistant steel excellent in wear resistance and bendability
US5403410A (en) * 1990-06-06 1995-04-04 Nkk Corporation Abrasion-resistant steel
US5236521A (en) * 1990-06-06 1993-08-17 Nkk Corporation Abrasion resistant steel
US5393358A (en) * 1990-12-03 1995-02-28 Nkk Corporation Method for producing abrasion-resistant steel having excellent surface property
JPH05239591A (en) * 1992-02-27 1993-09-17 Nkk Corp Steel excellent in wear resistance
US5292384A (en) * 1992-07-17 1994-03-08 Martin Marietta Energy Systems, Inc. Cr-W-V bainitic/ferritic steel with improved strength and toughness and method of making
US5409554A (en) * 1993-09-15 1995-04-25 The Timken Company Prevention of particle embrittlement in grain-refined, high-strength steels
US5827379A (en) * 1993-10-27 1998-10-27 Nippon Steel Corporation Process for producing extra high tensile steel having excellent stress corrosion cracking resistance
KR0153482B1 (en) * 1994-08-16 1998-11-16 코오타니 토모카쭈 Manufacturing method of track link
RU2179196C2 (en) * 1999-12-28 2002-02-10 ОАО "Северсталь" Steel
RU2180016C1 (en) * 2001-05-14 2002-02-27 Открытое акционерное общество "Северсталь" Steel for oil-trunk and gas-main pipelines
SE525378C2 (en) * 2002-01-21 2005-02-08 Sandvik Ab Elements for striking rock drilling and method for its preparation
FR2847272B1 (en) 2002-11-19 2004-12-24 Usinor METHOD FOR MANUFACTURING AN ABRASION RESISTANT STEEL SHEET AND OBTAINED SHEET
FR2847270B1 (en) 2002-11-19 2004-12-24 Usinor METHOD FOR MANUFACTURING AN ABRASION RESISTANT STEEL SHEET AND OBTAINED SHEET
JP5017937B2 (en) * 2005-12-28 2012-09-05 Ｊｆｅスチール株式会社 Wear-resistant steel plate with excellent bending workability
JP4899874B2 (en) * 2007-01-12 2012-03-21 Ｊｆｅスチール株式会社 Wear-resistant steel plate with excellent workability and method for producing the same
JP5380892B2 (en) * 2007-05-29 2014-01-08 Ｊｆｅスチール株式会社 Wear-resistant steel plate with excellent workability and method for producing the same
CN101880831B (en) * 2010-06-13 2012-07-04 东北大学 High-strength-and-toughness low alloy wear resistant steel and manufacturing method thereof
KR101271781B1 (en) 2010-12-23 2013-06-07 주식회사 포스코 Steel sheet for oil sands slurry transportation system having excellent wear resistance, corrosion resistance and low temperature toughness, and method for manufacturing the same
CN102851612A (en) * 2011-06-29 2013-01-02 鞍钢股份有限公司 Wear-resistant steel and heat treatment method thereof
CN103556081B (en) * 2013-10-30 2015-12-30 莱芜钢铁集团有限公司 A kind of wear-resisting excavator bucket teeth steel of high-strength and high ductility and manufacture method thereof
CN105779885B (en) * 2014-12-23 2018-03-27 上海梅山钢铁股份有限公司 A kind of wear-resistant hot rolling sheet metal and its manufacture method with excellent machinability

Family Cites Families (22)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE917674C (en) * 1942-09-19 1954-09-09 Rheinische Roehrenwerke Ag Steel for seals
DE861706C (en) * 1948-10-02 1953-01-05 Gussstahlwerk Bochumer Ver Ag Steel alloy for tempered locomotive wheel tires
CH377540A (en) * 1956-02-06 1964-05-15 Rheinstahl Huettenwerke Ag Wheel for rail vehicles and process for its manufacture
GB982955A (en) * 1961-07-22 1965-02-10 Hoerder Huettenunion Ag The manufacture of articles or parts by cold-working steel
NL296774A (en) * 1962-08-17
SU168323A1 (en) * 1964-02-01 1965-02-18
DE1483210A1 (en) * 1965-11-23 1969-03-20 Hoerder Huettenunion Ag Use of an unalloyed steel with good bending properties in longitudinal and transverse directions
GB1176855A (en) * 1966-12-14 1970-01-07 Nippon Kokan Kk Improvements in or relating to Non-Shielded Arc Welding
DE1803511B2 (en) * 1967-10-17 1971-07-29 HEAT TREATMENT PROCESS FOR ACHIEVING A BAINITIC STRUCTURE IN A STEEL
PL79950B1 (en) * 1968-01-31 1975-08-30 Mitsubishi Jukogyo Kabushiki Kaisha
PL79948B1 (en) * 1968-01-31 1975-08-30 Mitsubishi Jukogyo Kabushiki Kaisha
FR1600122A (en) * 1968-01-31 1970-07-20
DE1758507B1 (en) * 1968-06-15 1970-12-10 Thyssen Roehrenwerke Ag Use of high-strength manganese-alloyed fine-grain structural steel as a material for welded objects with good low-temperature properties
SU271807A1 (en) * 1969-01-22 1970-05-26 HIGH-STRENGTH ARMATURE STEEL
JPS5215523B1 (en) * 1970-11-18 1977-04-30
CA1003311A (en) * 1972-12-31 1977-01-11 Hiroshi Takechi High tensile strength structural steel and the manufacture thereof
SU441336A1 (en) * 1973-05-18 1974-08-30 Катав-Ивановский Литейно-Механический Завод Structural steel
JPS582261B2 (en) * 1973-06-11 1983-01-14 新日本製鐵株式会社 Touhou Teki Dekatsukou Engine Seino SI
US4472208A (en) * 1982-06-28 1984-09-18 Sumitomo Metal Industries, Ltd. Hot-rolled high tensile titanium steel plates and production thereof
DE3603691A1 (en) * 1986-02-06 1987-08-20 Hoesch Stahl Ag AGING-FREE STEEL
US4990196A (en) * 1988-06-13 1991-02-05 Nippon Steel Corporation Process for manufacturing building construction steel having excellent fire resistance and low yield ratio
JPH0441616A (en) * 1990-06-06 1992-02-12 Nkk Corp Production of low-hardness water-resistant steel excellent in wear resistance and bendability

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
Metalurgical Plant and Technology International, 2/1991, p. 52-60. *

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2222630C1 (en) * 2002-08-21 2004-01-27 ООО "Сорби стил" Steel for gas and oil pipelines

Also Published As

Publication number Publication date
AU6772090A (en) 1991-12-12
FI101403B1 (en) 1998-06-15
GB2244718A (en) 1991-12-11
CA2033267C (en) 1999-08-24
GB9028005D0 (en) 1991-02-13
AU1354595A (en) 1995-05-04
GB2245282A (en) 1992-01-02
FI906406A0 (en) 1990-12-27
EP0527277A1 (en) 1993-02-17
AU3111293A (en) 1993-02-25
FI93863B (en) 1995-02-28
AU6783890A (en) 1991-12-12
GB9027351D0 (en) 1991-02-06
CA2033267A1 (en) 1991-12-07
JPH0441616A (en) 1992-02-12
FI101403B (en) 1998-06-15
EP0527276A1 (en) 1993-02-17
FI906407L (en) 1991-12-07
AU632187B2 (en) 1992-12-17
FI906407A0 (en) 1990-12-27
FI93863C (en) 1995-06-12
EP0527277B1 (en) 1997-04-23
CA2033222A1 (en) 1991-12-07
FI906406L (en) 1991-12-07

Similar Documents

Publication Publication Date Title
EP0527276A1 (en) An abrasion resistant steel
JP2004169177A (en) Alloy tool steel, method for producing the same, and mold using the same
KR20050077008A (en) Alloy tool steel
EP3859043A1 (en) Abrasion resistant steel having excellent hardness and impact toughness, and manufacturing method therefor
KR950005927B1 (en) Wear resistant steel
US5403410A (en) Abrasion-resistant steel
KR100415626B1 (en) High Strength Wear Resistance Steel with Excellent Hardenability
US5284529A (en) Abrasion-resistant steel
KR20160010930A (en) (High wear-resistant cold work tool steels with enhanced impact toughness
US5236521A (en) Abrasion resistant steel
KR20230017462A (en) Hot work tool steel for Extrusion and forging die with high toughness
EP1637615B1 (en) Heat-resisting steel, heat treatment method for heat-resisting steel and high-temperature steam turbine rotor
EP0498105B1 (en) High strength and high toughness stainless steel and method of manufacturing the same
JPH04308058A (en) Steel having superior wear resistance
KR950005928B1 (en) Wear resistant steel
KR102359299B1 (en) Ultra-high strength, high co-ni secondary hardening martensitic steel and its manufacturing method
JPH04228536A (en) Steel excellent in wear resistance
EP0714990A1 (en) Method for making an abrasion resistant steel
KR102888718B1 (en) High-strength non-magnetic austentic stainless steel and method for manufacturing the same
JPH10158780A (en) Cold tool steel for plasma carburizing
KR940000822B1 (en) Wear-resistance steel
KR100263426B1 (en) Large moulding sreel having constant hardness
KR20260023923A (en) Free cutting steel and method for manufacturing the same
JPH0360899B2 (en)
KR940000823B1 (en) Method of manufacturing wear resistant steel

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

17P Request for examination filed

Effective date: 19910826

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): DE FR SE

17Q First examination report despatched

Effective date: 19941114

GRAG Despatch of communication of intention to grant

Free format text: ORIGINAL CODE: EPIDOS AGRA

GRAH Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOS IGRA

GRAH Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOS IGRA

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): DE FR SE

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: FR

Effective date: 19970115

REF Corresponds to:

Ref document number: 69124234

Country of ref document: DE

Date of ref document: 19970227

EN Fr: translation not filed
PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

26N No opposition filed
PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: DE

Payment date: 20100812

Year of fee payment: 20

Ref country code: SE

Payment date: 20100812

Year of fee payment: 20

REG Reference to a national code

Ref country code: DE

Ref legal event code: R071

Ref document number: 69124234

Country of ref document: DE

REG Reference to a national code

Ref country code: DE

Ref legal event code: R071

Ref document number: 69124234

Country of ref document: DE

REG Reference to a national code

Ref country code: SE

Ref legal event code: EUG

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: DE

Free format text: LAPSE BECAUSE OF EXPIRATION OF PROTECTION

Effective date: 20110813